Polymers Derived from Plant Oil and Use in Rubber Compounds

This application claims the benefit of U.S. Provisional Application Serial No.

61/915,346, filed December 12, 2013, and is a continuation-in-part of U.S. Application No. 13/469,940, filed May 11, 2012, which claims the benefit of U.S. Provisional Application Serial No. 61/608,980, filed March 9, 2012, and is a continuation-in-part of International Application No. PCT/US2010/056580 (published as WO 2011/060293), filed November 12, 2010, which claims the benefit of U.S. Provisional Application Serial No. 61/281,073, filed November 12, 2009; each of which is incorporated by reference herein.

Government Funding

This invention was made with government support under N00014-07-1-1099 awarded by the Office of Naval Research. The government has certain rights in the invention.

Background

Plant oil-based materials have many applications. For example, they are in use as lubricants, cosmetics, plastics, coatings, detergents, composites and drying agents.

Commercial and industrial interest in plant oil-based materials is high due to the fact that plant oils are renewable resources and typically biodegradable. Soybean oil is the most widely used vegetable oil for non-food applications due to its low cost and availability.

Summary of the Invention

The present invention provides vinylether monomers, as well as polymers and copolymers of vinylether monomers, wherein the vinylether monomers include fatty acid ester pendent groups derived from plant oils, such as soybean oil. Also included in the invention are methods for making the monomers and polymers, and methods of using them to produce lubricating liquids such as lubricants, oils, and gels, as well as coatings, films, elastomers, surfactants, composite materials, and the like. In one aspect, the invention provides a polymer formed from vinyl ether monomers derived from plant oil and having the structure

wherein R ¹ is divalent organic group that functions as a spacer between the vinyl ether and the heteroatom; Z is a heteroatom selected from O, N or S; R ² contains an aliphatic group derived from a renewable resource such as a plant oil; and R ⁶ , R ⁷ , and R ⁸ are each independently H or alkyl.

The polymer of the invention thus preferably includes a repeating unit having the general structure

wherein R ¹ is divalent organic group that functions as a spacer between the vinyl ether and the heteroatom; Z is a heteroatom selected from O, N or S; R ² contains an aliphatic group derived from a renewable resource such as a plant oil; and R ⁶ , R ⁷ , and R ⁸ are each independently H or alkyl. The plant oil is preferably a vegetable or nut oil, more preferably soybean oil. In one embodiment, the polymer is the product of a carbocationic polymerization reaction in which the polymer molecular weight increases linearly or substantially linearly with monomer conversion. In some embodiments, a plot of molecular weight as a function of monomer conversion is approximately linear. One example of this type of carbocationic

polymerization reaction is a "living" or controlled carbocationic polymerization. A "living" polymerization is polymerization that occurs substantially without termination or chain transfer reactions resulting in the ability to produce polymers with controlled molecular weight and polymers and potentially copolymers with well-defined molecular architectures such as block copolymers, star polymers, telechelic polymers, and graft copolymers.

Optionally, the polymerization reaction, such as the living carbocationic polymerization, occurs in the absence of a Lewis base. In another embodiment, the polymer or copolymer is the product of a free radical polymerization. Optionally, the polymer has a polydispersity index of less than 1.5. The polymer can include a plurality of monomers, such that for each of the plurality of monomers, R ² is independently an aliphatic group derived from a renewable resource such as a plant oil, preferably a C8-C21 aliphatic group derived from a plant oil.

The fatty acid pendant group of the vinyl ether monomer can be derived directly or indirectly from a plant oil. For example, the vinyl ether compound can be derived from a plant oil-derived compound such as a transesterified plant oil-based long chain alkyl ester, such as a biodiesel compound, for example an alkyl soyate such as methyl soyate.

Chemical derivatives of the polymer, including but not limited to an epoxy- functional polymer, an acrylate-functional polymer and a polyol polymer, are also encompassed by the invention. An epoxy-functional polymer includes, as an R ² group, at least one aliphatic group derived from a plant oil that has been functionalized to include at least one epoxide group; an acrylate functional polymer includes, as an R ² group, at least one aliphatic group derived from a plant oil that has been functionalized to include at least one acrylate-functional group; and a polyol polymer includes, as an R ² group, at least one aliphatic group derived from a plant oil that has been functionalized to include at least one alcohol group.

The invention further includes copolymers of the vinyl ether plant oil-derived fatty acid ester monomers described herein, such as a copolymer with a poly(ethylene glycol)- functional vinylether monomer.

In another aspect, the invention provides a method for making a polymer of the invention that includes contacting vinyl ether plant oil-derived fatty acid ester monomers with an optional organic initiator molecule, and a Lewis acid, under reaction conditions to allow polymerization of the monomer. When the organic initiator is omitted, the

polymerization may, without being bound by theory, be initiated by adventitious water present in the reaction mixture. Polymerization may, or may not, be a "living"

polymerization. The polymerization reaction is optionally performed in the absence of a Lewis base. In another aspect, the invention provides a method for making a polymer from plant oil that includes polymerizing vinylether plant oil-derived fatty acid ester monomers to yield a polymer having a polydispersity index of less than 2.0, preferably less than 1.5, more preferably less than 1.2. Optionally, the methods include extracting the plant oil from a plant or plant part to obtain the oil. The method optionally further includes cleaving triglycerides found in the plant oil to yield the monomers comprising vinylethers of plant oil-derived fatty acid esters. Cleavage can be accomplished using base-catalyzed

transesterification.

In a further aspect, the invention provides a method for producing a polymer that includes contacting vinylether plant oil-derived fatty acid ester monomers with an optional initiator to form a reaction mixture; contacting the reaction mixture with a co-initiator, e.g., a Lewis acid, to initiate a polymerization reaction under conditions and for a time to allow polymerization to proceed; and terminating the polymerization reaction to yield the polymer. In another aspect, the invention provides a method for producing a copolymer that includes contacting vinylether plant oil-derived fatty acid ester monomers with at least one additional monomer and an optional initiator to form a reaction mixture; contacting the reaction mixture with a co-initiator, e.g., a Lewis acid, to initiate a polymerization reaction under conditions and for a time to allow polymerization to proceed; and terminating the

polymerization reaction to yield the copolymer. An exemplary additional monomer is a vinylether monomer such as poly(ethylene glycol)-functional vinylether monomer or tri(ethylene glycol) ethyl vinyl ether. Another exemplary additional vinylether monomer is cyclohexyl vinyl ether. Polymerization can take place at a temperature less than 10°C;

preferably less than 5°C, more preferably at about 0°C. The plant oil monomers are preferably vegetable oil or nut oil monomers, more preferably soybean oil monomers. In a preferred embodiment, the first initiator includes 1-isobutoxy ethyl acetate and the co- initiator includes ethyl aluminum sesquichloride.

Also included in the invention is a polymer or copolymer produced by a method described herein, as well a composition that includes the polymer or copolymer. The composition can be an uncured composition or a cured composition; it can be an oil, a lubricant, a detergent, a coating, a gel, a surfactant, a film, elastomer or a composite, without limitation. Also included in the invention is an article, surface or substrate that includes a polymer or copolymer, cured or uncured, as described herein, such as, without limitation, a coated article, surface or substrate, or an article formed from a composite.

In yet another aspect, the invention provides a rubber compound that incorporates a polymer or copolymer of the invention. The rubber compound of the invention includes at least one rubber component, and at least one polymer or copolymer of the invention. The rubber compound preferably possesses unsaturation. Exemplary rubber components include natural rubber (NR), styrene butadiene rubber (SBR), isoprene rubber (IR), butadiene rubber (BR), ethylene-propylene rubber (EDM/EPDM), butyl rubber (IIR), bromobutyl rubber (BUR), chloroprene rubber (CR), nitrile rubber (NBR), or any combination thereof. The polymer or copolymer component can function as a processing aid. The polymer or copolymer of the invention contains an aliphatic group derived from a renewable resource such as a plant oil, preferably soybean oil. An exemplary polymer for incorporation into the rubber compound according to the invention is poly(4-VOBS) or poly(2-VOES) or both. The aliphatic group of the polymer or copolymer useful in the rubber compound of the invention may include at least one functionality selected from the group consisting of an epoxide group, an acrylate-functional group, an alcohol group, a carboxylic acid group and an alkoxysilane group. In embodiments of the rubber compound that include a copolymer of the invention, on preferred copolymer includes at least one alkyl vinylether comonomer. Another preferred copolymer includes at least one vinyl comonomer that includes an electron-withdrawing group, such as maleic anhydride, acrylonitrile, methacrylonitrile, fumaric acid, dimethyl fumarate and dimethyl maleate. A preferred copolymer includes polyMA-2VOES or polyMA-4-VOBS or both.

Optionally, the rubber compound of the invention can include reinforcing filler, such as carbon black, silica particles (amorphous silica), or a combination thereof. The rubber compound may be a filled or unfilled rubber compound. The rubber further optionally includes at least one additive selected from the group consisting of a stabilizer, an antioxidant, a lubricant, a vulcanization agent, a plasticizer, an additional processing aid, and an accelerator, or any combination thereof. In some embodiments, the rubber compound contains a petroleum-based processing oil as a further processing aid. The rubber compound can be vulcanized or unvulcanized. In a particularly preferred embodiment, the rubber compound is one in which all or some of a petroleum-based processing oil (PPO) is substituted with or replaced by at least one polyVESFA polymer or copolymer.

The invention further includes a method of making a rubber compound, utilizing one or more rubber components as described herein, and one or more polymers or copolymers of the invention. The method includes blending at least one rubber component with a first processing aid that includes a polymer or copolymer of the invention; optionally blending at least one additive into the mixture; and subjecting the mixture to vulcanization to yield the rubber compound. Examples of additives include but are not limited to a stabilizer, an antioxidant, a lubricant, a vulcanization agent, a plasticizer, an additional processing aid, an accelerator, or any combination thereof. The method optionally includes blending a reinforcing filler into the mixture prior to vulcanization. Examples if a reinforcing filler include carbon black, silica particles, or a combination thereof. The method optionally further includes blending the rubber component and the first processing aid with a second processing aid that includes petroleum-based processing oil (PPO).

The invention further includes an article that includes or is formed from a rubber compound as described herein, such as a molded article. An example of a commercially useful article that incorporates the rubber compound of the invention is a tire.

Brief Description of the Drawings

Figure 1 shows (A) an exemplary monomeric vinyl ether of a fatty acid ester; (B) an exemplary polymer of a vinyl ether of soybean oil fatty acid ester; (C) an exemplary polymer of vinyl ether of soybean oil fatty acid esters (polyVESFA); and (D) an exemplary epoxidized polymer of vinyl ether of soybean oil fatty acid esters (E -polyVESFA).

Figure 2 is a schematic showing the difference in molecular architecture between soybean oil and polyVESFA.

Figure 3 shows an exemplary synthesis of vinyl ether of soybean oil fatty acid esters (VESFA). Figure 4 shows an exemplary synthesis of the polymer of the vinyl ether of soybean oil fatty acid esters (polyVESFA) using carbocationic polymerization.

Figure 5 shows an exemplary synthesis of epoxidized polyVESFA (E -polyVESFA) from the polymer of the vinyl ether of soybean oil fatty acid esters (polyVESFA).

Figure 6 shows a plot of number-average molecular weight (Mn) as a function of monomer conversion for the polymerization of vinyl ether of soybean oil fatty acid esters (VESFA).

Figure 7 shows an 1H NMR spectra of the polymer of the vinyl ether of soybean oil fatty acid esters (polyVESFA) and epoxidized polyVESFA (E -polyVESFA).

Figure 8 A shows real time infrared (RTIR) spectroscopy results for various coatings and Figure 8B shows differential scanning calorimeter equipped with a photocalorimetric accessory (photo-DSC) results for various coatings.

Figure 9 shows a storage modulus as a function of temperature for various coatings cured with 1 pass (Figure 9A) and 2 passes (Figure 9B) under the UV lamp using a belt speed of 24 ft/min.

Figure 10 shows a synthetic scheme for synthesis of a copolymer of VESFA and a poly(ethylene glycol)-functional vinyl ether monomer.

Figure 11 shows a synthetic scheme for synthesis of a hydrophilic vinyl ether monomer, tri(ethylene glycol) ethyl vinyl ether.

Figure 12 shows a synthetic scheme for production of cured polyVESFA films using an auto-oxidation process.

Figure 13 shows a synthetic scheme for production of cured polyVESFA films using a vulcanization process.

Figure 14 shows a synthetic scheme for production of cured E-poly VESFA films using an amine curing agent.

Figure 15 shows a synthetic scheme for production of cured E-poly VESFA radiation-curable coatings using an ultraviolet (UV) light initiated cationic polymerization process.

Figure 16 shows a synthetic scheme for production of acrylated materials using polyVESFA and E-polyVESFA.

Figure 17 shows a synthetic scheme for production of polyols using polyVESFA and E-VESFA. Figure 18 shows rheology data obtained at 140 °C.

Figure 19A shows an image of a poly(VESFA) composition cast onto a glass panel and cured at 140°C for 45 minutes. Figure 19B shows an image of a soybean oil composition cast onto a glass panel and cured at 140°C for 45 minutes.

Figure 20 shows plots of Mn as a function of VECFA conversion for

polymerizations conducted using different Eti. ₅ AlCli.5 concentrations.

Figure 21 shows a synthetic scheme used to produce OH-polyVESFA from E- polyVESFA.

Figure 22 shows a 1H NMR spectrum obtained for OH-polyVESFA.

Figure 23 shows a FTIR spectrum obtained for OH-polyVESFA.

Figure 24 shows viscoelastic properties obtained for free films produced from OH- polyVESFA and OH-SBO in a polyurethane coating system.

Figure 25 shows a synthetic scheme used to produce a poly(CHVE-b-VESFA-b- CHVE) A-B-A triblock copolymer.

Figure 26 shows a synthetic scheme used to produce BDDA.

Figure 27 shows a plot of viscosity as a function of shear rate for polyVOBS homopolymers at 25 °C.

Figure 28 shows a shear modulus as a function of time at 100 °C for a blend of E- polyVESFA and HHMPA as well as E-SBO and HHMPA. A 1/0.5 stoichiometry between the epoxy groups and anhydride groups was used.

Figure 29 shows fluorescence data used to determine CMC for Copolymer4, Copolymer5, and Copolymer6.

Figure 30 shows tensile strength (i.e. stress at break) as a function of the type and concentration of the processing oil.

Figure 31 shows stress at 100% strain as a function of the type and concentration of the processing oil.

Figure 32 shows stress at 300% strain as a function of the type and concentration of the processing oil.

Figure 33 shows elongation at break as a function of the type and concentration of the processing oil.

Figure 34 shows toughness as a function of the type and concentration of the processing oil. Figure 35 shows tensile strength (a), strain at 100 % elongation (b), strain at 300 % elongation (c), elongation at break (d), and toughness (e) as a function of processing oil composition using 15 weight % oil.

Figure 36 shows extractable content of unfilled rubber compounds as a function of process oil composition using 15 weight % processing oil.

Detailed Description of Illustrative Embodiments

The present invention provides vinylether monomers, as well as polymers and copolymers of vinylether monomers, wherein the vinylether monomers include fatty acid ester pendent groups derived from plant oils, such as soybean oil. Also included in the invention are methods for making the monomers and polymers, and methods of using them to produce lubricating liquids such as lubricants, oils, and gels, as well as coatings, films, elastomers, surfactants, composite materials, and the like. Articles, coatings, films, elastomers, detergents, composites, oils, gels and lubricants that include monomers or polymers of the invention, cured or uncured, as well as methods for making and using them, also provided by the invention.

An illustrative embodiment of the plant oil polymer of the invention is referred to herein as a polymer of a vinyl ether of soybean oil fatty acid esters (polyVESFA), although it should be understood that the polymer of the invention is not limited to a polymer produced from soybean oil. As noted elsewhere herein, any plant oil can be used, for example corn oil. The various methods and uses described herein, therefore, although described for convenience with reference to an embodiment of the polymer derived from soybean oil, apply generally to embodiments derived from any suitable plant oil. Thus, in one embodiment, the exemplary polyVESFA is synthesized from monomers derived from the transesterification of soybean oil (the exemplary plant oil) with ethylene glycol monovinylether. These exemplary monomers are referred to herein as vinyl ethers of soybean oil fatty acid esters (VESFA). Because soybean oil contains five different fatty acids (stearic acid, oleic acid, linoleic acid, palmitic and linolenic acid) the vinylether monomers produced by transesterification of soybean oil include a mixture of vinylethers of stearic acid, oleic acid, linoleic acid, palmitic acid and linolenic acid esters. The resulting polymer, polyVESFA, is heterogeneous in the sense that it contains monomers derived from all five fatty acids. PolyVESFA can be produced, for example, using carbocationic polymerization. Alternatively, polyVESFA can be produced, for example, using free radical polymerization.

The polymer of the invention can be derivatized. For example, the polymer can be subjected to epoxidation and optionally subjected to epoxy-amine curing, epoxy-anyhydride curing, cationic photocuring, and/or converted to a polyol or component for use in polyurethane; it can function as an elastomeric alcohol. The polymer can be made acrylate- functional, sulfonated to form an ionomer, vulcanized, subjected to a Diels-Alder reaction to form a film, cured to a film with a thiol using thio-ene chemistry, cured with a peroxide, or it can be air-dried under conditions to initiate crosslinking or exposed to radiation, preferably UV radiation.

Plant oils that can be used to form the monomers and polymers of the invention include vegetable oils, such soybean oil, linseed oil, tung oil, oiticica oil, perilla oil, safflower oil and corn oil; oil from trees or wood pulp such as tall oil and palm oil, or nut- based oils such as cashew oil. The vegetable oils include at least one triglyceride and contain fatty acids such as at least one of oleic acid, stearic acid, linoleic acid, linolenic acid, palmitic acid, lauric acid, myristic acid, arachidic acid, and palmitioleic acid.

Vinyl ether monomers provided by the invention include vinyl ethers of plant oil- derived fatty acids, more particularly, vinylethers of soybean oil-derived fatty acids

(VESFA). A preferred monomer has the structure R ⁶ R ⁷ C=C(R ⁸ )-0-R ¹ -Z-C(0)-R ² , wherein R ¹ is divalent organic group that functions as a spacer between the vinyl ether and the heteroatom; Z is a heteroatom selected from O, N or S; R ² contains an aliphatic group derived from a renewable resource such as a plant oil, such as soybean oil; and R ⁶ , R ⁷ , and R ⁸ are each independently H or alkyl.

A particularly preferred monomer has the structure CH ₂ =CH-0-R ¹ -Z-C(0)-R ² .

The spacer, R ¹ , can be a branched or unbranched hydrocarbon having 1 to 40 or more carbon atoms; it may be substituted or unsubstituted at one or more sites; it may be saturated or unsaturated at one or more sites; it may contain one or more monocyclic or polycyclic divalent ring structures (aliphatic or aromatic); and it may contain one or more divalent functionalities such as ether, thioether, ester, thioester, amine and amido.

In one embodiment, the spacer R ¹ is (CR ³ R ⁴ ) _m wherein, for each instance of m, each of R ³ and R ⁴ is independently selected from H, methyl, ethyl, propyl, hydroxy, methyl, methoxy, aryl, and halo, including substituted forms thereof; and wherein m is 1 to 10, more preferably m = 1, 2, 3, 4 or 5.

In another embodiment, the spacer R ¹ is (CR ³ R ⁴ ) _n -X- (CR ³ R ⁴ ) _p wherein n and p are each independently 0, 1, 2, 3, 4 or 5; X is O (ether), C(O) (carbonyl), OC(O) (ester), C(0)0 (ester), S (thioether), OS(O) (thioester), S(0)0 (thioester), N(R ⁵ ) (a secondary tertiary amine, wherein R ⁵ is H or an organic substituent), N(H)C(0) (amide) C(0)N(H) (amide), or a substituted unsubstituted monocyclic or polycyclic cycloaliphatic or aromatic moiety, preferably cyclohexyl or benzyl; and R ³ and R ⁴ are independently selected from H, methyl, ethyl, propyl, hydroxy, methyl, methoxy, aryl, and halo, including substituted forms thereof. Monomers having a spacer (R ¹ ) that contains a cycloaliphatic moiety may be expected to be more rigid, which may increase the glass transition temperature of a polymer into which it is incorporated, a property that would be desirable for many applications.

R ² is any aliphatic moiety obtained from a plant oil. R ² is preferably a C8-C21 aliphatic group, more preferably a C8-C21 alkyl group or a C8-C21 alkenyl group, even more preferably a linear C8-C21 alkyl group or a linear C8-C21 alkenyl group. The aliphatic group preferably includes a linear chain of 8, 9, 10, 11, 12, 13, 14, 15, 16, 17, 18, 19, 20, 21 or 22 carbon atoms, and preferably contains 0 (saturated), 1 (monounsaturated), 2 or 3 double bonds. Preferred polymers, co-polymers, and polymeric materials are those derived from a preferred monomer.

The monomer of the invention may contain an ester linkage (in embodiments where Z=0), an amide linkage (in embodiments where Z=N) or a thioester linkage (in

embodiments where Z=S). Embodiments having an amide linkage may be expected to exhibit certain advantages with respect to thermal and mechanical properties due to the introduction of hydrogen bonding via the amide nitrogen.

Exemplary monomers (see, e.g., Fig. 1 A), wherein R ² is derived from a plant oil, are shown below.

As used herein, the terms "aliphatic" or "aliphatic group" mean a saturated or unsaturated linear (i.e., straight chain), cyclic, or branched hydrocarbon group. The hydrocarbon or hydrocarbon group can be substituted or unsubstituted. The term "aliphatic" encompasses monovalent and divalent aliphatic groups, including alkyl (e.g., -CH ₃ ) (or alkylene if within a chain such as -CH ₂ -), alkenyl (or alkenylene if within a chain), and alkynyl (or alkynylene if within a chain) groups, as well as substituted forms thereof, for example.

The terms "alkyl" or "alkyl group" mean a saturated linear or branched hydrocarbon group including, for example, methyl, ethyl, isopropyl, t-butyl, amyl, heptyl, dodecyl, octadecyl, amyl, 2-ethylhexyl, and the like, as well as their divalent counterparts. "Alkyl" and "alkylene" are also meant to include substituted alkyls and alkylenes. Suitable substituents include aryl groups (which may themselves be substituted), as in the case where the "alkyl" is a phenyl-substituted methyl group (e.g., a benzyl moiety). Other suitable substituents include heterocyclic rings (saturated or unsaturated and optionally substituted), hydroxy groups, alkoxy groups (which is meant to include aryloxy groups (e.g., phenoxy groups)), thiol groups, alkylthio groups, arylthio groups, amine groups (which is meant to include unsubstituted, monosubstituted, or disubstituted (e.g., with aryl or alkyl groups) amine groups), carboxylic acid groups (which is meant to include COOH groups as well as carboxylic acid derivatives, e.g., carboxylic acid esters, amides, etc.), phosphine groups, sulfonic acid groups, halogen atoms (e.g., F, CI, Br, and I), and the like. Further, alkyl groups bearing one or more alkenyl or alkynyl substituents (e.g., a methyl group itself substituted with a prop-l-en-l-yl group to produce a but-2-en-l-yl substituent or a methyl group itself substituted with a vinyl group to produce an allyl substituent) are meant to be included in the meaning of "alkyl."

The terms "alkenyl" or "alkenyl group: mean an unsaturated, linear or branched monovalent or divalent hydrocarbon group with one or more olefmically unsaturated groups (i.e., carbon-carbon double bonds), such as a vinyl group. Alkenyl groups include, for example, ethenyl, propenyl, butenyl, l-methyl-2-buten-l-yl, and the like.

The term "alkynyl group" means an unsaturated, linear or branched monovalent or divalent hydrocarbon group with one or more carbon-carbon triple bonds. Representative alkynyl groups include, but are not limited to, ethynyl, 2-propynyl (propargyl), 1-propynyl, and the like.

The term "aliphatic" also encompasses monovalent or divalent cyclic hydrocarbons such as cycloaliphatic groups or heterocyclic groups. The term "cycloaliphatic" refers to a cyclic or polycyclic hydrocarbon group, which may have properties resembling those of linear aliphatic groups. Cycloaliphatic groups include, without limitation, cyclopropyl, cyclobutyl, cyclopentyl, cyclopentenyl, cyclohexyl, cyclohexenyl, cycloheptyl,

cycloheptenyl, cyclooctyl, cyclooctenyl, norbornyl, adamantyl, and cyclooctadienyl. The term "cycloaliphatic" also includes aliphatic rings that are fused to one or more aromatic or nonaromatic rings, such as decahydronaphthyl or tetrahydronaphthyl, where the radical or point of attachment is on the aliphatic ring. The term "heterocyclic group" means a cyclic or polycyclic closed ring hydrocarbon in which one or more of the atoms in the ring is an element other than carbon (e.g., nitrogen, oxygen, sulfur, etc.).

Unless otherwise specified, an aliphatic group can contain 1 or 2 or 3 or 4, and so on, up to 38 or 39 or 40 carbon atoms; that is, 1 to 40 carbon atoms. In certain embodiments, aliphatic groups contain 1 to 20 carbon atoms. In certain embodiments, aliphatic groups contain 2 to 20 carbon atoms. In certain embodiments, aliphatic groups contain 1 to 12 carbon atoms, or 1 to 8 carbon atoms, or 1 to 6 carbon atoms, 1 to 5 carbon atoms, 1 to 4 carbon atoms, 1 to 3 carbon atoms, or 1 to 2 carbons atoms. Exemplary aliphatic groups include, but are not limited to, linear or branched alkyl, alkylene, alkenyl, and alkynyl groups, and hybrids thereof such as (cycloalkyl)alkyl, (cycloalkenyl)alkyl or

(cycloalkyl)alkenyl.

The term "unsaturated", as used herein, means that a moiety has one or more double or triple bonds.

An aliphatic group may be unsubstituted, or optionally substituted with one or more substituents. "Substituted" means that one or more hydrogens of the designated moiety are replaced with a suitable substituent. Unless otherwise indicated, an "optionally substituted" group may have a suitable substituent at each substitutable position of the group, and when more than one position in any given structure may be substituted with more than one substituent selected from a specified group, the substituent may be either the same or different at every position. Combinations of substituents envisioned by this invention are preferably those that result in the formation of stable or chemically feasible compounds. The term "stable", as used herein, refers to compounds that are not substantially altered when subjected to conditions to allow for their production, detection, and, in certain embodiments, their recovery, purification, and use for one or more of the purposes disclosed herein.

Suitable substituents include, but are not limited to, alkyl, alkenyl, alkynyl, cycloalkyl, heterocycloalkyl, aryl, heteroaryl, aroyl, halo (e.g., F, CI, Br and I), hydroxy, oxo, nitro, alkoxy, amino, amido, imino, azido, mercapto, acyl, carbamoyl, carboxy, carboxamido, amidino, guanidino, thiol, alkylthiol, arylthio, sulfonyl, sulfinyl, sulfonamido, phosphine, formyl, cyano, and ureido groups.

The term "alkoxy", as used herein refers to an alkyl group, as previously defined, attached to the parent molecule through an oxygen atom. Examples of alkoxy, include but are not limited to, methoxy, ethoxy, propoxy, isopropoxy, n-butoxy, tert-butoxy, neopentoxy, and n-hexoxy.

The term "acyl", as used herein, refers to a carbonyl-containing functionality, e.g., - C(=0)R, wherein R is hydrogen or an optionally substituted aliphatic, heteroaliphatic, heterocyclic, aryl, heteroaryl group, or is a substituted (e.g., with hydrogen or aliphatic, heteroaliphatic, aryl, or heteroaryl moieties) oxygen or nitrogen containing functionality (e.g., forming a carboxylic acid, ester, or amide functionality). The term "acyloxy", as used here, refers to an acyl group attached to the parent molecule through an oxygen atom.

The terms "aromatic," "aromatic group," "aryl" and "aryl group" mean a mono- or polynuclear aromatic hydrocarbon group. These hydrocarbon groups may be substituted with heteroatoms, which can be in the form of functional groups. The term "aromatic" or "aryl" used alone or as part of a larger moiety as in "aromatic hydrocarbon," "aralkyl," "aralkoxy", or "aryloxyalkyl", refers to monocyclic and polycyclic ring systems having a total of five to 20 ring members, wherein at least one ring in the system is aromatic and wherein each ring in the system contains three to twelve ring members. The term "aryl" may be used interchangeably with the term "aryl ring" or "aromatic ring." In certain embodiments of the present invention, "aryl" refers to an aromatic ring system which includes, but is not limited to, phenyl, biphenyl, naphthyl, anthracyl and the like, which may bear one or more substituents. Also included within the scope of the term aryl", as it is used herein, is a group in which an aromatic ring is fused to one or more additional rings, such as benzofuranyl, indanyl, phthalimidyl, naphthimidyl, phenantriidinyl, or

tetrahydronaphthyl, and the like.

In describing substituents, the term "radical" is sometimes used. In this context, "radical" means a moiety or functional group having an available position for attachment to the structure on which the substituent is bound. In general the point of attachment would bear a hydrogen atom if the substituent were an independent neutral molecule rather than a substituent.

The term "heteroatom" means an element other than carbon (e.g., nitrogen, oxygen, sulfur, chlorine, etc.). A "hetero-" moiety as described herein, such as a heteroaliphatic group, a heterocyclic group and the like, refers to a moiety having, in place of one or more carbon atoms, a heteroatom independently selected from nitrogen, oxygen, or sulfur.

Examples of saturated or partially unsaturated heterocyclic groups include, without limitation, tetrahydrofuranyl, tetrahydrothienyl, pyrrolidinyl, pyrrolidonyl, piperidinyl, pyrrolinyl, tetrahydroquinolinyl, tetrahydroisoquinolinyl, decahydroquinolinyl, oxazolidinyl, piperazinyl, dioxanyl, dioxolanyl, diazepinyl, oxazepinyl, thiazepinyl, morpholinyl, and quinuclidinyl. The terms "heterocycle", "heterocyclyl", "heterocyclyl ring", "heterocyclic group", "heterocyclic moiety", and "heterocyclic radical", are used interchangeably herein, and also include groups in which a heterocyclyl ring is fused to one or more aryl, heteroaryl, or cycloaliphatic rings, such as indolinyl, 3H-indolyl, chromanyl, phenanthridinyl, or tetrahydroquinolinyl, where the radical or point of attachment is on the heterocyclyl ring. A heterocyclyl group may be mono- or bicyclic. The term "heterocyclylalkyl" refers to an alkyl group substituted by a heterocyclyl, wherein the alkyl and heterocyclyl portions independently are optionally substituted.

Preferably, the monomer is derived from a vegetable or a nut oil; more preferably, it is a derivative of one of the plant fatty acids found in soybeans: stearic acid, oleic acid, palmitic, linoleic acid or linolenic acid. The fatty acid pendant group of the vinyl ether monomer can be derived directly or indirectly from a plant oil. For example, the vinyl ether compound can be derived from a plant oil-derived compound such as a transesterified plant oil-based long chain alkyl ester, such as a biodiesel compound, for example an alkyl soyate such as methyl soyate.

In one embodiment, monomers are synthesized using base-catalyzed

transesterification of a plant oil, such as soybean oil, with ethylene glycol vinyl ether, propylene glycol vinyl ether, isopropylene glycol vinyl ether, butylene glycol vinyl ether or iso-butylene glycol vinyl ether. The base can be potassium hydroxide, sodium hydroxide, or any convenient base. Ethylene glycol vinyl ether and butylene glycol vinyl ether are relatively inexpensive chemicals, and the resulting monomers are isolated in high purity. In another embodiment, the monomer is synthesized using acid-catalyzed transesterification. More generally, any convenient transesterification method can be used to generate the vinyl ether plant oil-derived fatty acid ester monomers of the invention.

Vinyl ethers synthesized from fatty alcohols have been reported by others (see additional references, supra). Fatty alcohols are typically produced from hydrogenation of fatty acids. The conversion of the fatty alcohols to the vinyl ether was done using vinylation with acetylene, and the process involved several steps. One advantage of the present invention is that the vinyl ether is produced directly from a reaction between a vinyl ether possessing a nucleophilic group and the plant oil, preferably vegetable oil, by a single-step simple nucleophilic substitution reaction similar to the process used to produce biodiesel (i.e. methyl esters of vegetable oil fatty acids). The resulting monomer is much easier and less expensive to make. The vinyl ether reactant used to produce the monomer of the invention can be a linear (branched or unbranched) aliphatic vinyl ether, or it can contain a ring structure. It can be functionalized, for example, with an alcohol (-ΟΗ), an amino (- NH ₂ ) or a thiol (-SH). The vinyl ether monomers produced therefrom include an ester, an amide, or a thioester functionality, respectively. Exemplary vinyl ether reactants include 2- (vinyloxy)ethanol (Shanghai FWD Chemicals Limited), 4-(vinyloxy)butanol (BASF), 4- hydroxymethyl)cyclohexyl methyl vinyl ether (BASF), diethylene glycol monovinyl ether (BASF), as well as 3 -amino propyl vinyl ether (BASF).

A polymer of the invention is formed from one or more of the monomers of the invention, and optionally includes other monomers, preferably other monovinylidene monomers. A preferred polymer (see, e.g., Fig. IB) contains a repeating unit:

wherein R ¹ , R ² , R ⁶ , R ⁷ , R ⁸ , and Z are as defined above for the monomer. The polymer is optionally activated or functionalized with the aliphatic group R ² at the site of one or more double bonds, e.g., by epoxidation, acrylation, or by the incorporation of alcohol groups. The polymer preferably contains a plurality of different monomers, such that R ²

encompasses a plurality of aliphatic groups R _n where n = 1, 2, 3, 4, 5, 6, 7, 8, 9, or 10, which aliphatic groups are optionally activated. For example, when the polymer is derived from an oil such as soybean oil that contains five fatty acids, the polymer may contain monomers having five different aliphatic groups. Below is an exemplary polymer that incorporates an ethylene space between the ether and the ester functionalities, and methylene in the polymer backbone:

See, for example, Fig. 1C wherein m, n, p, q and r vary with the relative amount of each monomer, and Ri = stearate, R ₂ = oleate, R ₃ = linoleate, R ₄ = linoleate and R5 = linolenate. It should be understood that the five monomers are typically randomly dispersed throughout the polymer, according to their abundance. An exemplary composition of soybean oil is about 11% palmitic acid, about 4% stearic acid, about 23% oleic acid, about 54% linoleic acid, and about 7% linolenic acid.

In other embodiments of the polymer of the invention, the R ² group(s) can be activated at the site of one or more double bonds, e.g., by epoxidation, acrylation, or by the incorporation of alcohol groups, as described in more detail elsewhere herein. Briefly, incorporation of acrylate groups or alcohol groups typically first involves the generation of an epoxide intermediate. The double bonds can be derivatized using epoxidation, Diels- Alder chemistry, or thiol-ene chemistry. Derivatives such as epoxy-functional, acrylate - functional and alcohol-functional (polyol) polymers are likewise included in the invention.

Monomers produced from oil in accordance with the method of the invention contain an ester, amide, or thioester group. Advantageously, these monomers can be polymerized in a controlled fashion without destroying the ester functionality. In a preferred embodiment, the method of polymerizing monomers of the invention utilizes carbocationic

polymerization in which the polymer molecular weight increases linearly or substantially linearly with monomer conversion, for example, controlled or living cationic

polymerization. Typically, living carbocationic polymerization utilizes an initiating system that includes an optional organic initiator molecule, a Lewis acid (i.e., a co-initiator), and a Lewis base (i.e. electron donor), and results in controlled addition of monomers to the growing chain until all monomers are essentially consumed. Side reactions, such as chain transfer and chain termination, are kept to a minimum. Living cationic polymerization of alkyl vinyl ethers is described, for example, in US Pat. No. 5,196,491. Advantageously, the use of a carbocationic polymerization in which molecular weight increases linearly with increasing monomer conversion allows the viscosity of the liquid to be controlled. The concentration of the initiator affects the molecular weight of the resulting polymer; the lower the initiator concentration, i.e., the higher the [Monomer]: [Initiator] ratio, the higher the molecular weight of the resulting polymer.

The use of an organic initiator molecule is optional. When the organic initiator molecule is omitted, the polymerization may, without being bound by theory, be initiated by adventitious water present in the reaction mixture. Polymerization may, or may not, be a "living" polymerization.

Polymerization of vinyl ethers typically requires the inclusion of a Lewis base, such as ethylacetate, methylchloroacetate or methyldichloroacetate, to prevent uncontrolled polymerization. A Lewis base is typically included to mediate the polymerization reaction through coordination with the carbocation, thereby lowering its reactivity such that it undergoes propagation reactions but not chain termination or chain transfer reactions.

However, it has been surprisingly discovered that the inclusion of a Lewis base during polymerization of the monomers of the invention is not required and, in fact, may slow down polymerization to the point that it does not occur. Without wishing to be bound by theory, it is thought that the monomer itself provides the carbonyl or ester group needed to mediate the polymerization reaction; in other words, it is self-mediated. Thus, the polymerization method of the invention, when based on a carbocationic polymerization in which molecular weight increases linearly with increasing monomer conversion, such as controlled or living cationic polymerization, preferably omits a Lewis base, although a Lewis base may optionally be included in the reaction mixture. Optionally, when the Lewis base is omitted, the amount of the Lewis acid is increased. The amount of Lewis acid used, which is also referred to herein as a "co-initiator," affects the polydispersity in the mixture, and can be adjusted so that it is high enough to produce polymerization, but not so high as to produce an undesirably broad molecular weight dispersion. Polydispersity indices (PDI) of under 1.3, more particularly about 1.1 or 1.2, can be achieved using the polymerization method of the present invention. In one embodiment of the polymerization method, monomers derived from plant oils, preferably vegetable oils, more preferably vinylether esters of soybean fatty acids, are contacted with a carbonyl-containing initiator compound and a Lewis acid co-initiator in a reaction mixture under conditions sufficient to generate a carbocation which initiates polymerization of the monomers. Exemplary Lewis acids include Eti. ₅ AlCli.5 used in the examples below, as well as BCI3, BF ₃ , A1C1 ₃ , SnCl ₄ , TiCl ₄ , SbF ₅ , SeCl ₃ , ZnCl ₂ , FeCl ₃ and VC1 ₄ .

An exemplary method for making a polymer from vegetable oil such as soybean oils thus involves polymerizing monomers comprising vinylether esters of vegetable oil fatty acids to yield a polymer. The method optionally includes cleaving the triglycerides present in the vegetable oil, preferably in a base-catalyzed transesterification process, to yield the monomers. In a particularly preferred embodiment of the method of making the polymer, the polymerizing step comprises a carbocationic polymerization in which molecular weight increases linearly with increasing monomer conversion, such as a controlled or living carbocationic polymerization, wherein the monomers are contacted with an optional organic initiator molecule and a Lewis acid co-initiator under reaction conditions to allow polymerization of the monomer. As noted elsewhere herein, surprisingly, the

polymerization reaction can be performed in the absence of a Lewis base. The method further optionally includes extracting the vegetable oil from a plant or plant part. It is to be understood that a polymer produced by any method described herein is also provided by the invention. For example, free radical polymerization can be used to form a polymer of the invention.

Polymerization yields linear polymers which include pendent groups derived from the various fatty acids found in the oil. The polymers produced using the polymerization method are also included in the invention. When the polymerization method constitutes carbocationic polymerization in which molecular weight increases linearly with increasing monomer conversion, such as controlled or living carbocationic polymerization, the resulting polymer advantageously has a narrower molecular weight distribution compared with other polymerization methods, making the polymers especially suitable for commercial and industrial applications. The molecular weight distribution (MWD, also known as the polydispersity index, PDI) for the polymer resulting from this polymerization reaction is typically less than 2 and can be less than 1.8, less than 1.5, and is preferably less than 1.3. Thus, in one embodiment, the polymer of the invention, which is optionally activated at the site of one or more double bonds, e.g., by epoxidation, acrylation, or by the inclusion of alcohol groups; optionally has a PDI of less than 2.0, less than 1.9, less than 1.8, less than 1.7, less than 1.6, less thanl .5, less than 1.4, less than 1.3, less than 1.2, or less than 1.1. Additionally, the molecular weight of the polymers produced can be controlled by adjusting the nature or amount of the reactants or changing the reaction conditions. More particularly, the molecular weight of the polymer or copolymer can be controlled by controlling the relative amounts or concentrations of initiator, co-initiator, and monomer(s), and the time allowed for polymerization. For example, the [monomer]: [initiator] ratio can be between [10,000]:[1] to [25]:[1], with ranges bounded on the upper and lower ends by a [monomer] of any integer between 100 andl 0,000. One example of a range of [monomer]: [initiator] ratios is [5000: 1] to [100: 1]. As a further example, the [monomer]: [co-initiator] ratio can be between [2]:[1] to [200] :[1], with ranges bounded on the upper and lower ends by a

[monomer] of any integer between 1 and 200. One example of a range of [monomer] ^co- initiator] ratios is [4: 1] to [20: 1]. Generally, increasing the amount of Lewis acid (co- initiator) will result in an increase in the polymerization rate.

In another embodiment, the polymer of the invention contains the repeating unit shown in the structure above, as well as a single initiator fragment linked to the beginning of the polymer chain (e.g., at the left side of the structure above; see also Fig. ID showing an initiator fragment.

In any embodiment, the polymer can be derivatized, for example epoxidized or acrylated, as described in more detail elsewhere herein.

Importantly, polyVESFA contains significantly more fatty ester pendent groups per molecule than soybean oil triglycerides (Fig. 2). Depending on the initiator to monomer ratio used for the polymerization of VESFA, each molecule of polyVESFA can possess from 10s to 100s to 1,000s of fatty ester pendent groups as compared to just three for soybean oil triglycerides. This can be used to great advantage for many applications such as coatings, composites and lubricants. Since the unsaturated fatty acid groups in the molecule can result in a crosslink for a cured material, properties that increase with increasing crosslink density, such as modulus, hardness, chemical resistance, corrosion resistance, stain resistance, etc., are expected to be higher for materials based on polyVESFA as compared to analogous materials based on soybean oil. In addition, the higher molecular weight and higher number of fatty ester branches associated with polyVESFA are expected to reduce shrinkage upon cure which ultimately enhances adhesion in coatings and mechanical properties in composites. Advantageously, polyVESFA, like soybean oil, is a biodegradable liquid, but unlike soybean oil, it can be engineered by controlling chain length, degree of cross-linking etc., to have properties, such as viscosity, that are tailored to the particular application, significantly increasing its industrial utility.

The polymer of the invention, for example polyVESFA, can be incorporated into a liquid formulation such as a lubricant, detergent, gel or an oil. In another embodiment, the polymer can be cured and incorporated into surface treatments, coatings, films, elastomers and the like. Cross-linking and further treatment of the polymer to form a coating, film or other surface treatment can be achieved using any convenient method, for example, by air- drying or auto-oxidation (using, e.g., a cobalt, zirconium or zinc catalyst); by sulfur vulcanization (using, for example, sulfur and zinc oxide), via a Diels- Alder reaction followed by air drying, by peroxide curing, acrylate-based curing, or via thiol-ene formation and radiation curing.

The polymer of the invention, for example polyVESFA, can also be incorporated into a rubber or rubberized compound, as further described in the examples. The large number of unsaturated groups per molecule of the polymer of the invention is expected to ensure grafting of the polymer into the crosslinked rubber matrix, thereby preventing extraction of the polymer from the vulcanized rubber and enhancing mechanical properties such as modulus, strength, and abrasion resistance. In addition, and perhaps more importantly, the ability to copolymerize polyVESFA with other monomers provides a new method for tailoring basic polymer properties such as glass transition temperature, solubility parameter, tensile strength, and modulus. By proper selection of co-monomers for use in conjunction with polyVESFA copolymers, the solubility/compatibility of the copolymer with a specific type of rubber can be enhanced. In addition, appropriate functional groups can be incorporated through co-polymerization. These functional groups can be selected to provide for favorable interactions between the copolymer and specific components of the rubber compound such as filler particles. Enhancing interactions between the polymer matrix and filler particles is expected to provide dramatic enhancements in mechanical properties including modulus, tensile strength, toughness, and abrasion resistance. A practical example of the use of polyVESFA in rubber compounds is the incorporation of this polymer into rubber compounds used for making tires. Commercially useful rubber compounds contain rubber along with one or more processing aids such as processing oils and/or oil-based softeners or extenders. In some embodiments, rubber compounds additionally contain reinforcing fillers. Optionally, additives including but not limited to stabilizers, antioxidants, lubricants, vulcanization agents, plasticizers, additional processing aids, and/or accelerators are also included in rubber compounds. Suitable accelerators include dithiocarbamates, guanidines, quinones, sulfonamides, phenoldisulfides, insoluble sulfurs, diphenylamines, phthalimides, thiadiazoles, thiurams, thioureas, and thiazoles. Examples of additives include zinc oxide (ZnO), stearic acid (StA), phenolic resin, silane, sulfur, 2,2,4-trimethyl-l,2-dihydroquinoline (TMQ, an antioxidant), N-(l,3,-dimethylbutyl)-N'-phenyl-p-phenylenediamine (6PPD, an antoxidant), and N-cyclohexyl-2-benzothiazole sulfonamide (CBS, an accelerator).

The rubber component of a rubber compound can be any suitable elastomer or elastomer gum. Preferably the rubber component possesses unsaturation; for example, it can be or include an unsaturated diene. Examples of suitable rubber components include natural rubber (NR, such as Standard Indonesian Rubber, or "SIR") as well as synthetic rubbers, such as styrene butadiene rubber (SBR), isoprene rubber (IR), butadiene rubber (BR), ethylene-propylene rubber (EDM/EPDM wherein D stands for diene), butyl rubber (IIR), bromobutyl rubber (BUR), chloroprene rubber (CR) and nitrile rubber (NBR), as well as combinations thereof. Nitrile rubber is a copolymer of acrylonitrile and butadiene, and is commonly used for products that are in contact with oil and fuel. Preferred rubber components are NR, SBR, BR and NBR.

Examples of optional reinforcing fillers that can be incorporated into the rubber compound include carbon black (a form of paracrystalline carbon produced by incomplete combustion of petroleum products) and/or silica particles (e.g., amorphous silica). These filler compounds are especially useful in the automotive industry to produce tires.

Oils, softeners and extenders can be incorporated into rubber compounds to reduce viscosity of filled rubber mixes, improve processability of the rubber compounds, improve filler dispersion, and/or increase the overall quality of the rubber compounds. Historically, the processing aids and extenders incorporated into rubber compounds have been petroleum based (petroleum-based processing oils, or PPOs). PPOs commonly used to make rubber compounds include mineral oils such as paraffinic, naphthenic and aromatic oils. In the present invention, all or some of the PPO in a rubber compound is substituted or replaced with one more polyVESFA polymers or copolymers of the invention in order to employ green technology while retaining the high performance characteristics imparted by petroleum-based oils. Any rubber compound, composition, or formulation that incorporates a PPO can be reformulated by substituting or replacing all or part of the PPO component with one or more polyVESFA polymer or copolymer of the invention, to provide a higher green content while maintaining or improving commercially important characteristics or features. Incorporation of the soybean oil vinyl ether polymers and copolymers of the invention into rubber compounds may result in compounds having higher modulus, tensile strength, toughness, and/or lower rolling resistance compared to rubber compounds utilizing PPOs. Additionally, as illustrated in the examples below, incorporation of the plant vinyl ether compounds of the invention yields superior properties compared to incorporation of unmodified soybean oil (SBO). For example, unlike SBO, poly(4-VOBS) was found to be not miscible with SBR and thus does not lower the SBR glass transition temperature, Tg. Moreover, the use of poly(4-VOBS) in SBR compounds was found to give smooth sheets that were not prone to shrinkage over time. Compared to PPO and SBO, utilization of poly(4-VOBS) at concentrations of > 5% by weight in SBR rubber compounds (i.e., weight ratios of at least 5:95 poly(4-VOBS):SBR) provides higher tensile strength and toughness, with no loss of Shore A hardness. At poly(4-VOBS) concentrations > 15 %, toughness twice that of pure SBR was observed. Poly(4-VOBS) resulted in the lowest predicted rolling resistance. Also, much higher modulus at 100% and 200% strain was observed.

Overall, poly(4-VOBS) was found to impart properties to the rubber compounds that were more similar to PPO than to SBO.

Without intending to be bound by theory, it is proposed that the polymers of the invention, having a multiplicity of double bonds, form a cross-linked network upon vulcanization, thereby beneficially preventing migration of the polymer (and other processing oils, if present) to the surface of the molded article.

Nonlimiting examples of polymers of the invention that are well-suited for incorporation into rubber compounds are poly(4-VOBS) (poly((4-vinyloxy)butyl soyate) and poly(2-VOES) (poly((2-vinyloxy)ethyl soyate).

Vinylether comonomers that are particularly suitable for use in copolymers incorporated into the rubber compounds of the invention are comonomers that are relatively nonpolar or hydrophobic, such as alkyl vinylethers. Examples of suitable alkyl vinylether comonomers include n-butyl vinylether, isobutyl vinylether, n-propyl vinylether, isopropyl vinylether, dodecyl vinyl ethers, and the like. Other suitable comonomers are those that possesses an electron withdrawing group, for example comonomers that possess an anhydride or a nitrile. Examples of comonomers that possess relatively strong electron withdrawing groups are maleic anhydride, acrylonitrile, methacrylonitrile, fumaric acid, dimethyl fumarate and dimethyl maleate. Examples of copolymers of the invention that are well-suited for incorporation into rubber compounds are alternating copolymers of maleic anhydride and 2- VOES ((2-vinyloxy)ethyl soyate), referred to as polyMA-2-VOES, or maleic anhydride and 4-VOBS ((4-vinyloxy)butyl soyate), referred to as polyMA-4-VOBS).

Advantageously, the molecular weight of the polymer or copolymer of the invention can be readily tailored by adjusting the ratio of monomer to the initiator during the polymerization process to achieve the desired viscosity of the polymer or copolymer, thereby allowing customization of the mechanical properties of the rubber compound. For example, poly(4-VOBS) can be prepared with number average molecular weights, expressed relative to polystyrene standard, ranging from 1000 g/mol or lower on the lower end, to up to 50,000 g/mol, 100,000 g/mol, 120,000 g/mol or higher, depending on the intended use.

Preferred rubber compounds of the invention contain at least one rubber compound and at least one polyVESFA polymer or copolymer. Optionally, the rubber compound further contains a reinforcing filler, such as carbon black or silica particles. Also optionally, the rubber compound contains one or more additives. The one or more additives can include stabilizers, antioxidants, lubricants, vulcanization agents, plasticizers, additional processing aids, accelerators, as well as one or more petroleum-based oils (PPOs), or any combination thereof. In a preferred embodiment, the rubber compound contains at least one of ZnO, S, TBBS and stearic acid.

In some embodiments, the amount of polyVESFA polymer (or copolymer) in the rubber compound of the invention is, by weight, equal to or less than the amount of rubber component. The ratio of polyVESFA polymer (or copolymer) to the rubber component (polymer:rubber, wt/wt) in the rubber compound may be at least 2:98, or at least 5:95, or at least 10:90, or at least 15:85, or at least 20:80, or at least 25:75, or at least 30:70, or at least 35:65, or at least 40:60, or at least 45:55, or at least 50:50. In other embodiments, the amount of polyVESFA polymer (or copolymer) in the rubber compound of the invention is greater than the amount of rubber component. The ratio The ratio of polyVESFA polymer (or copolymer) to the rubber component (polymer:rubber, wt/wt) in the rubber compound may be at least 55:45, 60:40, 65:35, 70:30, or even higher. The amount of polymer or copolymer in the rubber compound can be is at least 5% by weight, at least 15% by weight, at least 25% by weight, at least 40% by weight, or at least 50% by weight. Particularly for "unfilled" rubber compounds (compounds containing little or no reinforcing filler), higher proportions of polyVESFA polymer (or copolymer) are associated with beneficial properties.

The term "rubber compound" as used herein includes rubber compositions or formulations prior to vulcanization, as well as rubber articles after vulcanization. After vulcanization, the rubber compound can assume the shape and character of a molded article; such molded articles are also included in the invention. The rubber compound can be "filled" (with a reinforcing filler) or "unfilled." The rubber compounds of the invention are typically made by first blending the rubber component with the polymer of the invention and, optionally, any other processing oils or extenders, such as PPOs or SBO, followed by the addition and blending of optional additives such as stabilizers, accelerators,

vulcanization agents, antioxidants and the like, followed by the optional addition and blending of one or more reinforcing fillers such as carbon black or silica particles, to form the unvulcanized composition. Vulcanization is then performed at high temperature and pressure to yield the vulcanized rubber compound or article. A typical vulcanization process is carried out at a pressure of 1500 to 2500 Newtons and a temperature of 130 to 170°C. Hot air vulcanization or microwave heated vulcanization can also be employed.

Vulcanization can be accomplished, for example, using one or more curing systems that employ sulfur, peroxides, urethane crosslinkers, metallic oxides and/or acetoxysilane.

The rubber compounds of the invention have many commercial uses, including but not limited to uses in fabricating tires or in other aspects of the automotive industry, in textiles, construction, consumer products, and biomedical applications.

In yet another embodiment, the polymer of the invention can be incorporated into a composite material, such as a fiber-reinforced composite.

The polymers of the invention include homopolymers, heteropolymers and co- polymers, including block co-polymers, whether cross-linked or non-cross-linked, that incorporate or contain a vegetable oil or other plant oil monomer or polymer as described herein. Plant oil monomers of the invention can be copolymerized with other monomers, such as vinyl ether monomers and styrenic monomers, to create new polymers with fatty acid ester branches. Accordingly, the invention provides copolymers of plant oil vinyl ether monomers, such as VESFA, with other monomers. Copolymerization offers tremendous potential for tailoring polymer properties for a given application and is used extensively in the polymer industry. One example of a useful copolymer is a copolymer containing vinylether monomers as described herein and polyethylene glycol (PEG) vinyl ether monomers. The resulting co-polymer is amphiphilic, further expanding its industrial utility. Other examples of useful copolymers are those containing vinylether monomers as described herein, and tri(ethylene glycol) ethyl vinyl ether, or copolymers formed from copolymerization of the vinylether monomers of the invention with styrene monomers. The copolymer of the invention is not limited by monomer that can be copolymerized with the vinyl ether monomers of the invention; examples of other monomers that can be

copolymerized with the vinylether monomers described herein can be found in Aoshima et al, Chem Rev 2009, 109, 5245-5287.

Copolymerization reactions can be using any suitable copolymerization technique.

For example, carbocationic polymerization can be used, as described in detail herein.

Another example of a polymerization reaction method that can be used is free radical polymerization. For example, the vinylether monomers of the invention can be

copolymerized with other vinyl monomers that possess strongly electron withdrawing groups, such as an anhydride, e.g. maleic anyhydride, or a nitrile, such as acrylonitrile, using free radical polymerization. Other vinyl monomers that possess relatively strong electron withdrawing groups include methacrylonitrile, fumaric acid, dimethyl fumarate and dimethyl maleate.

The monomer or polymer of the invention can be derivatized. For example, the invention includes monomers or polymers that have been activated by epoxidation, as well as acrylate-functional and polyol functional polymers synthesized using an epoxy-functional intermediate. Thus, the monomer or polymer can be chemically treated, altered or derivatized for further use according to the desired application, for example by epoxidation, acrylation, and other chemical reactions to produce epoxidized derivatives, acrylates, polyols and the like. Treatment may or may not involve polymer cross-linking. In one embodiment, the polymer is epoxidized at the sites of the double bonds on the aliphatic groups. For example, a soybean oil polymer, polyVESFA, is optionally epoxidized to yield epoxidized polyVESFA (E-polyVESFA; see Fig. ID).

Epoxidized polymers of the invention (also referred to herein as epoxy- functional or epoxide-functional), such as E-polyVESFA, are well-suited for use to produce curable coating compositions. The epoxidized coating composition can be cured using radiation e.g., UV-curing (e.g., via cationic photopolymerization), using an amine curing agent, using an anhydride-functional curing agent and optionally a tertiary amine catalyst, acid catalyst, or any suitable curing agent or method. Surface coatings can be readily generated from E- polyVESFA. Compared to analogous coatings based on commercially available epoxidized soybean oil (ESO), coatings based on E-polyVESFA display many advantageous characteristics, including unexpectedly fast cure rates which are not presently fully understood, and higher modulus in the rubbery plateau region. Without wishing to be bound by theory, it is believed that the higher rubbery plateau modulus can be attributed, at least in part, to the tertiary carbon atoms present in the polymer backbone which serve as additional crosslinks in the cured crosslinked network.

In another embodiment, the invention provides an acrylate-functional polymer. For example, an epoxidized vinyl ether fatty acid ester polymer, such as E-polyVESFA, can be reacted with acrylic acid to yield an acrylate-functional polymer; see Example VIII. The acrylated polymer can be cured, for example using radiation (e.g., UV), peroxide or a thermal curing process.

In yet another embodiment, the invention provides a polyol polymer. For example, an epoxidized vinyl ether fatty acid ester polymer, such as E-polyVESFA, can be subjected to a ring-opening reaction to produce a polyol, which finds use in the preparation of, for example, polyurethanes, alkyd resins, and the like.

In yet another embodiment, the invention provides a polymer functionalized with an acid, preferably a carboxylic acid group, or a silane, such as an alkoxy silane group.

Vegetable oil-based materials are currently commercially available for a large number on non-food applications, such as lubricants, hydraulic fluids, coatings, drying agents, plastics, composites, insulators, soaps, candles, cosmetics, etc. Essentially, and importantly, the plant oil-derived polymers of the invention, such as polymers derived from soybean oil, can be used for any application which currently utilizes soybean oil. In this regard, see Meier et al, Chem Soc. Rev., 2007, 36, 1788-1802, which reviews the utilization of plant oil as raw material for monomers and polymers, particularly as replacements for petrochemicals currently in use. Due to the renewable aspect of vegetable oil derivatives, many industries are trying to use more chemicals from renewable sources. The polymers of the invention can be used in any and all of these applications. Also included are liquids and solids, including articles of manufacture of any type, that contain monomers or polymers as described herein, including lubricating and hydraulic fluids, gels, plastics, composites, elastomers, polyurethanes, additives, adhesives and the like.

EXAMPLES

The present invention is illustrated by the following examples. It is to be understood that the particular examples, materials, amounts, and procedures are to be interpreted broadly in accordance with the scope and spirit of the invention as set forth herein.

Example I.

Synthesis and Characterization of a Novel Epoxy-Functional Polymer from Soybean Oil

A novel monomer was synthesized using base catalyzed transesterification of soybean oil with ethylene glycol vinyl ether (also referred to as 2-(vinyloxy)ethanol).

Ethylene glycol vinyl ether is a relatively inexpensive chemical and the resulting monomer, which will be referred to as the "vinylether of soybean oil fatty acids (VESFA)," was able to be isolated in high purity.

A novel polyvinylether polymer containing fatty acid ester pendent groups derived from soybean oil was also synthesized. This novel polymer is referred to as the "polymer of the vinyl ether of soybean oil fatty acid esters (polyVESFA). Using a carbocationic polymerization system with tailored reactivity, VESFA was successfully polymerized to polyVESFA homopolymer.

This example also describes epoxidation of polyVESFA to produce epoxidized polyVESFA (E-polyVESFA) and the generation of surface coatings from E-polyVESFA. Additional examples describing synthesis of a monomer (Example II), polymer (Example III), epoxidized polymer (Example VI) and surface coating using the epoxidized polymer (Example VII).

Experimental

Materials. Reagent grade ethylene glycol monovinylether (TCI America, >95%) and soybean oil (Cargill Inc.) were used as supplied. 1-isobutoxy ethyl acetate was prepared according to the procedure described by Aoshima and Higashimura {Macromolecules 1989, 22(3): 1009-13). The polymerization solvent, toluene (Sigma- Aldrich, 99.8%), was distilled over calcium hydride prior to use. Eti. ₅ AlCli.5 (25 wt. % in toluene) and 3- chloroperoxybenzoic acid (w % pure) were purchased from Sigma- Aldrich and used as received. UVR 6000 and UVI 6974 were purchased from Dow Chemical and used as received.

Synthesis of the vinyl ether of soybean fatty acid esters (VESFA). 7.5 gm of ethylene glycol monovinylether, 7.5 gm of soybean oil, and 0.21 gm of anhydrous potassium hydroxide were combined in a 100 ml, round-bottom flask and stirred at 70 °C for 3 hours. The excess ethylene glycol monovinylether was removed by rotary evaporation of the reaction mixture at 56 °C for 10 minutes at 5 millibar pressure. The crude product was cooled to 16 °C to remove the byproduct glycerol and subsequently diluted with n-hexane. The solution was washed with deionized water and dried with anhydrous magnesium sulfate. The product monomer was recovered by rotary evaporation and drying under vacuum overnight.

Synthesis of polyVESFA. VESFA was polymerized using a carbocationic

polymerization process. The characteristics of the polymerization of VESFA monomer was determined by monitoring polymer yield and polymer molecular weight as a function of polymerization time. Prior to use, VESFA was dried with magnesium sulfate. The reaction was carried out in a dry 250 ml two neck round bottom flask partially immerged into heptanes bath at 0 °C inside a dry box. In the reaction vessel, 9.1 mg of initiator (1- isobutoxyethyl acetate) and 4 gm of VESFA monomer ([M] ₀ :[I]o = 200: 1) were dissolved in 20 gm of toluene and solutions chilled to 0 °C. The polymerization was started by the addition of 1.25 ml of ethylaluminum sesquichloride solution (25 wt. %> in toluene) ([M] ₀ :[ Eti. ₅ AlCli.5]o = 200:40) to the reaction mixture. Polymers were obtained after withdrawing known weight of aliquot at different time of intervals and terminated with chilled methanol. Each polymer was isolated and washed with methanol using centrifugation. Polymer yield was determined gravimetrically after drying the purified polymer at 40 °C under vacuum overnight. Polymer molecular weight was characterized using a high-throughput Symyx Rapid Gel Permeation Chromatography equipped with an evaporative light scattering detector (PL-ELS 1000) and polystyrene standards.

A plot of number average molecular weight obtained from gel permeation chromatograph (GPC) analysis as a function of VESFA monomer conversion yielded a straight line with a slope of 72.7, a Y-axis intercept of 3511 , and correlation coefficient of 0.99. The data used to generate the plot is shown below:

the polydispersity index

Synthesis of E-poly VESFA. 4 gm of poly VESFA was dissolved in 80 ml of methylene chloride in a two-neck, round-bottom flask. Next, 4.73 gm of 3- chloroperoxybenzoic acid was added under vigorous stirring and the reaction allowed to occur over a 4 hour period at room temperature. The epoxidized polymer was isolated by precipitation into methanol and drying overnight under vacuum.

Preparation of surface coatings. E-poly VESFA was mixed with a reactive diluent (UVR 6000) and a photoinitiator (UVI 6974) at different ratios (Table 1) to produce a series of homogeneous coating solutions. The coatings were cast over Teflon® coated glass slides using a draw down bar (BYK Gardner) to produce approximately 200 μιη wet films that were subsequently cured by passing them through a F 300 UVA lamp (Fusion UV Systems, UVA light intensity ~ 1420 mW/cm ² as measured by UV Power Puck II ^® from EIT Inc) equipped with a conveyer belt set at a belt speed of 24 feet/min. Coating samples were prepared using a single pass (IP) under the lamp and two passes (2P) under the lamp.

Dynamic mechanical thermal analysis was conducted on coating free films using a TA800 from TA Instruments.

Table 1. Coatings formulations.

The kinetics of photopolymerization was investigated using a Q1000 differential scanning calorimeter equipped with a photocalorimetric accessory (photo DSC).

Experiments were performed at a UV light intensity of 50 mW/cm ² and a temperature of 30 °C. Samples were equilibrated for 1 minute and exposed to UV light for 7 minutes followed by a temperature ramp from 0 °C to 200 °C at a ramp rate of 10 °C/min.

Real time infrared spectroscopy (RTIR) experiments were carried out using a Nicolet Magna-IR 850 spectrometer Series II fitted with a 100 W DC UVA mercury vapor lamp from LESCO Super Spot MK II. Samples were spin coated and exposed to UVA light for 3 minutes followed by 2 minutes of dark cure. FTIR spectra were taken at a rate of 1 spectrum/s with a resolution of 4 cm ^"1 . Conversion of epoxy groups was monitored after integrating the base line in between 800 cm ^"1 to 860 cm ^"1 .

Results and Discussion.

Figs. 3, 4, and 5 display the synthetic schemes for producing VESFA, polyVESFA, and E-polyVESFA, respectively. Both polyVESFA and E-polyVESFA were viscous liquids at room temperature. The living nature of the carbocationic polymerization of VESFA was demonstrated by the linear relationship between number-average molecular weight (Mn) determined using gel permeation chromatograph (GPC) and VESFA conversion, as shown in Fig. 6. Additionally, the narrow molecular weight distribution (<1.4) indicated fast and efficient initiation.

The successful polymerization of polyVESFA was confirmed by the absence any peaks associated with methylene protons attached to the vinylether double bond at 6.4 ppm (Fig. 7). It should be noted that polymerization occurred exclusively through the vinylether groups. No vinyl groups in the fatty acid ester side chains were consumed during the polymerization. The synthesis of E-polyVESFA from polyVESFA was also confirmed using 1H NMR. As shown in Fig. 7, the shift of the methine proton at 5.3 ppm in polyVESFA to 2.9 ppm in E-polyVESFA was due to successful epoxidation of the double bonds in fatty acid ester side chains.

Results obtained from RTIR spectroscopy analysis (Fig. 8A) showed that the rate of epoxy consumption with E-polyVESFA was much higher than with ESO. A faster reaction rate with E-polyVESFA was also illustrated using photo-DSC (Fig. 8B).

DMTA analysis showed (Fig. 9A and 9B) that use of E-polyVESFA provided significantly higher storage modulus for the rubbery plateau region than could be obtained with commercially available ESO. The higher modulus of the rubbery plateau region can be attributed to the higher crosslink density associated with the polymeric nature of E- polyVESFA. For E-polyVESFA, each tertiary carbon in the polymer backbone serves as a crosslink in the cured film. Thus, for a given extent of epoxy conversion during cure, films based on E-polyVESFA will necessarily possess a higher crosslink density compared to analogous films based on ESO.

Conclusion

A novel monomer, VESFA, was synthesized by base-catalyzed transesterification of soybean oil with ethylene glycol monovinylether. PolyVESFA containing fatty acid ester pendent groups was synthesized using living carbocationic polymerization. It was found that the polymerization process occurred selectively through the vinyl groups of VESFA enabling the double bonds in the fatty acid esters to remain intact. PolyVESFA was successfully epoxidized to E-polyVESFA, which was subsequently used to produce UV- curable coating compositions. Compared to analogous coatings based on commercially available ESO, coatings based on E-polyVESFA displayed much faster cure rates and higher modulus in the rubbery plateau region. At present, the higher cure rate associated with use of E-polyVESFA is not fully understood. The higher rubbery plateau modulus can be attributed, at least in part, to the tertiary carbon atoms present in the polymer backbone which serve as additional crosslinks in the cured crosslinked network. Example II.

Synthesis of Vinyl Ether of Soybean Oil Fatty Acid Esters (VESFA)

One example of a synthesis of a monomeric VESFA is described in Example I.

Another exemplary synthesis of the monomer, also using the same general synthetic scheme shown in Fig. 3, is as follows: 20 g of soybean oil, 20 g of ethylene glycol monovinylether, and 0.56 g of anhydrous potassium hydroxide were added to a two-neck, 100 ml, round- bottom flask and stirred at 70 °C for 3 hours under a blanket of nitrogen. The reaction mixture was cooled to room temperature and diluted with 120 ml of n-hexane. The organic layer was separated from the aqueous layer and washed once with 35 ml of aqueous acid (pH 4) and multiple times with deionized (DI) water until the wash water was neutral as indicated by litmus paper. The hexane layer was then dried with magnesium sulfate. The product was recovered by rotary evaporation of n-hexane and dried under vacuum overnight. Proton NMR was used to confirm the production of VESFA: 1H NMR: 6.45 ppm (q, 1H, OCH=C), 4.0 - 4.2 ppm (m, 2H, C=CH ₂ ), 4.25 ppm (t, 2H, COOCH ₂ C ), 3.82 ppm (t, 2H, OCH ₂ C ), 5.3 ppm (m, 3.3H, CH=CH), 2.3 ppm (t, 2H, OCOCH ₂ ), 0.8 ppm (m, 3H, CH ₃ C), 1.55 ppm (m, 2H, COCH ₂ CH ₂ C).

Example III.

Polymerization of Soybean Oil-Derived Vinylether Monomers

One example of a synthesis of the homopolymer of VESFA (poly VESFA) is described in Example I.

Another exemplary synthesis of the homopolymer of VESFA, using the same general carbocationic polymerization scheme shown in Fig. 4 and producing a polymer referred to herein as polyVESFA-1, is as follows: Prior to use, VESFA was dried with magnesium sulfate. The dried VESFA was polymerized at 0 °C within a glove box in a three-neck, round-bottom flask baked at 200 °C prior to use. 23.4 mg of initiator (1- isobutoxyethyl acetate) and 256 g of VESFA monomer ([M] ₀ :[I]o = 5000: 1) were dissolved in 1600 ml of dry toluene and chilled to 0 °C. The polymerization was initiated by the addition of 36.05 ml of ethylaluminum sesquichloride solution (25 wt. % in toluene) ([M] ₀ :[Co-initiator]o = 200: 18). The reaction was terminated after 17 hours by the addition of 1600 ml of chilled methanol which caused the polymer to precipitate. The polymer was isolated and washed multiple times with methanol using centrifugation. The purified polymer was collected as a viscous liquid after centrifuging at 4500 rpm at 21 °C for 10 minutes and drying under vacuum overnight. This synthesis resulted in a low polydispersity index (PDI) polyVESFA, as shown below.

Yet another exemplary synthesis of polyVESFA, producing a polymer referred to herein as polyVESFA-2, and also using the same general carbocationic polymerization scheme shown in Fig. 4, is as follows: Prior to use, VESFA was dried with magnesium sulfate. The dried VESFA was polymerized at 0 °C within a glove box in a three-neck, round-bottom flask baked at 200 °C prior to use. 9.7 mg of initiator (1 -isobutoxyethyl acetate) and 105.9 g of VESFA monomer ([M]:[I] = 5000: 1) were dissolved in 643.7 ml of dry toluene and chilled to 0 °C. The polymerization was initiated by the addition of 36.5 ml of ethylaluminum sesquichloride solution (25 wt. % in toluene). ([M] ₀ :[Co-initiator] ₀ = 200:44). The reaction was terminated after 17 hours by the addition of 643 ml of methanol which caused the polymer to precipitate. The polymer was isolated and washed multiple times with methanol using centrifugation. The purified polymer was collected as a viscous liquid after centrifuging at 4500 rpm at 21 °C for 10 minutes and drying under vacuum overnight. The chemical structure of polyVESFA was confirmed using proton NMR: 1H NMR: 4.1 - 4.2 ppm (m, COOCH ₂ C), 3.4 - 3.8 ppm (m, OCH ₂ C, OCHC ), 5.2 - 5.4 ppm (m, CH=CH), 2.2 - 2.3 ppm (m, OCOCH ₂ ), 0.8 ppm (m, CH ₃ C), 1.45 - 1.7 ppm (m, COCH ₂ CH ₂ C).

The thermal properties of the polymer were determined using differential scanning calorimetry (Q1000 from TA Instruments) by first heating the sample from -120 °C to 70 °C at a heating rate of 10 °C/minute (1 ^st heat), cooling from 70 °C to -120 °C at a cooling rate of 10 °C/minute (cooling), and reheating from -120 °C to 120 °C at a heating rate 10 °C/minute (2 ^nd heat). The thermogram obtained from the 2 ^nd heat showed a glass transition at -98.7 °C and a very weak, diffuse melting transition with an enthalpy of melting of 8.43 J/gm and a peak maximum at -27.6 °C. The rheological characteristics of the polymer produced were compared to that of soybean oil using an ARES Rheometer from TA

Instruments. The shear rate was varied from 0.1 radians/sec. to 500 radians/sec. while temperature was held constant at 25 °C. Over this shear rate range, the soybean oil showed a constant shear viscosity of 45 centipoise, while the polyVESFA displayed a constant shear viscosity of 2,971 centipoise. Over a shear rate range of 500 radians/sec. to 1,000 radians/sec, the viscosity of the soybean oil remained constant at 45 centipoise while the viscosity of the polyVESFA dropped dramatically illustrating the pseudoplasticity typically seen with polymers that possess a molecular weight above the minimum required for polymer chain entanglement.

The characteristics of the polymerization of VESFA monomer was determined by monitoring polymer yield and polymer molecular weight as a function of polymerization time. The reaction was carried out in a dry 250 ml two-neck, round-bottom flask partially submerged in a heptane bath at 0 °C inside a dry box. In the reaction vessel, 14.3 mg of initiator (1-isobutoxy ethyl acetate) and 6.25 gm of VESFA monomer ([M] ₀ :[I]o = 200: 1) were dissolved in 32.06 gm of toluene and the solution chilled to 0 °C. The polymerization was started by the addition of 882 μΐ of ethylaluminum sesquichloride solution (25 wt. % in toluene) ([M]o:[Co-initiator]o = 200: 18) to the reaction mixture. Aliquots of the reaction mixture were removed from the vessel at various time intervals and terminated with chilled methanol. Polymers from each aliquot were isolated and washed with methanol using centrifugation. Polymer yield was determined gravimetrically after drying the purified polymer at 40 °C under vacuum overnight. Polymer molecular weight was characterized using a high-throughput Symyx Rapid Gel Permeation Chromatography equipped with an evaporative light scattering detector (PL-ELS 1000) and polystyrene standards.

A plot of number average molecular weight obtained from gel permeation chromatograph (GPC) analysis as a function of VESFA monomer conversion yielded a straight line that passed through the origin with a slope of 504 and correlation coefficient of 0.977. The data used to generate the plot is shown below: Reaction Time % Monomer Conversion GPC number Average PDI*

(hour) Molecular Weight

0.92 9.5 7906 1.14

1.60 15.4 10450 1.13

4.00 29.4 16640 1.13

4.08 30.0 17090 1.13

9.33 51.8 26670 1.13

13.25 62.2 30210 1.16

15.83 68.2 34020 1.13

19.75 73.1 35430 1.15 the polydispersity index

Another example of the living carbocationic polymerization of VESFA monomer is as follows: A total of eight polymerizations were carried out inside a dry box at 0 °C using dry test tubes as polymerization vessels. In each test tube, 1.6 mg of initiator (1- isobutoxy ethyl acetate) and 0.7 gm of VESFA monomer ([M]:[I] = 200: 1) were dissolved in 3.68 gm of toluene and solutions chilled to 0 °C. Each polymerization was started by the addition of 241 μΐ of ethylaluminum sesquichloride (Et _1-5 AICI ₁ .5) solution (25 wt. % in toluene) to the reaction mixture. After a predetermined time interval, 20 ml of methanol was added to the polymerization mixture to terminate the polymerization. Each polymer was isolated and washed with methanol using centrifugation. Polymer yield was determined gravimetrically after drying the purified polymer at 40 °C under vacuum overnight.

Polymer molecular weight was characterized using a high-throughput Symyx Rapid Gel Permeation Chromatography equipped with an evaporative light scattering detector (PL-ELS 1000) and polystyrene standards.

A plot of number average molecular weight obtained from gel permeation chromatograph (GPC) analysis as a function of VESFA monomer conversion yielded a straight line that passed through the origin with a slope of 347 and correlation coefficient of 0.978. The data used to generate the plot is shown below:

2.166 43.68 14880 1.17

3 46.34 17300 1.17

4.83 58.54 21580 1.18

8.133 68.5 22530 1.25

15.533 75.55 24810 1.31 the polydispersity index

The linear relationship between monomer conversion and number-average molecular obtained from the experiment showed that the polymerization was a "living"

polymerization, which occurs without termination or chain transfer reactions, resulting in the ability to produce polymers with controlled molecular weight and polymers and potentially copolymers with well-defined molecular architectures such as block copolymers, star polymers, and graft copolymers. Example IV.

Copolymers of VESFA and Other Vinylether Monomers

Copolymers of VESFA with a polyethylene glycol-functional vinylether monomer were also produced. The synthetic scheme is shown in Fig. 10.

A polyethylene glycol-functional monovinylether monomer (VEPEG) was synthesized by end-capping a commercially available polyethylene glycol monovinylether (R500 from Clariant) as follows: 20 gm of iodoethane and 8.08 gm of potassium hydroxide were added to a 500 ml, round-bottom flask and stirred at 300 rpm at 40 °C. Then, 58.8 gm of R500 was added drop-wise to the reaction mixture. After the addition was complete, the temperature was raised to 64 °C and stirring continued for 12 hours under a blanket of nitrogen. R500 possesses a hydroxy group at one end which will terminate a carbocationic polymerization, thus reaction with iodoethane was used to convert the hydroxyl group to an ethoxy group (-0-CH ₂ CH ₃ ). The reaction mixture was cooled to room temperature and then diluted with 300 ml of methylene chloride. The organic layer was filtered as a clear liquid and washed three times with 300 ml of DI water. The organic layer was then dried with anhydrous magnesium sulfate and the product monomer was recovered by rotary

evaporation of volatiles. Successful synthesis of VEPEG was confirmed by proton NMR spectra analysis: 1H NMR: 6.4 ppm (q, 1H, OCH=C), 3.9 - 4.13 ppm (dd, 2H, C=CH ₂ ), 3.4 - 3.8 ppm (m, 48H, OCH ₂ CH ₂ 0, OCH ₂ CH ₃ ), 1.2 ppm (t, 3H, CH ₃ CH ₂ ). VESFA and VEPEG were copolymerized at 0 C within a glove box in a test tube dried at 250 °C under vacuum just before use. 1 g of VEPEG, 0.61 g of VESFA, and 2.77 mg of initiator (1-isobutoxy ethyl acetate) were dissolved in 8.43 g of dry toluene and chilled to 0 °C. The polymerization was initiated with the addition of 0.417 ml of ethyl aluminum sesquichloride (25 wt. % in toluene). After 12 hours, the reaction was terminated with addition of 20 ml of methanol. The copolymer was recovered by rotatory evaporation of all the volatiles and drying under vacuum overnight. GPC using polystyrene standards showed that the polymer produced possessed a number average molecular weight of 14,350 g/mol.

A copolymer of VESFA and tri(ethylene glycol) ethyl vinyl ether (TEGEVE) was also synthesized. TEGEVE was produced using the synthetic scheme shown in Fig. 11.

In the first step, 16.5 gm of diethyleneglycol monoethylether (DEE) (99% purity from Aldrich), 8 gm of sodium hydroxide, 60 ml of tetrahydrofuran, and 40 ml of DI water were combined in a 500 ml, 3 -neck, round-bottom flask using constant stirring to produce a homogeneous solution. The mixture was cooled to 0 °C and then 25.7 gm of p- toluenesulfonyl chloride (Aldrich, 99% purity) in 50 ml of tetrahydrofuran (THF) was added to the reaction mixture drop-wise using an addition funnel and the reaction was continued for 2 hours at 0 °C. The reaction mixture was then poured into 100 ml of ice cold water and the product extracted with methylene chloride. The organic layer was washed with DI water and dried with anhydrous magnesium sulfate. The product (Ts-DEE) was recovered after rotary evaporation of all the volatiles and dried under vacuum overnight. In the second step, 1.5 gm of sodium hydride (Aldrich 95 %> purity) and 75 ml of THF were dissolved in a 500 ml, 3 -neck, round-bottom flask equipped with a nitrogen blanket. The solution was cooled at 0 °C and a solution of 4.77 gm of ethylene glycol monovinyl ether (TCI America, 95 % purity) in 30 ml THF was added drop wise. Next, a solution of 15 gm of Ts-DEVE in 45 ml THF was added to the reaction mixture and the temperature was raised to 60 °C. After 24 hours, the reaction mixture was cooled to room temperature and diluted with 150 ml of diethyl ether. The organic layer was washed three times with 75 ml of DI water and dried with anhydrous magnesium sulfate. The product monomer, TEGEVE, was collected after rotary evaporation of all volatiles and dried under vacuum overnight. Successful synthesis of TEGEVE was confirmed by proton NMR: 6.4 ppm (q, 1H, OCH=C), 4. 0 - 4.2 ppm (m, 2H, C=CH ₂ ), 3.4 - 3.8 ppm (m, 14H, OCH ₂ CH ₂ 0, OCH ₂ C), 1.2 ppm (t, 3H, CH ₃ C). VESFA and TEGEVE were copolymerized at 0 C within a glove box in a test tube dried at 200 °C under vacuum just before use. A series of copolymers were synthesized by varying the initial concentration of monomer to co-initiator (i.e. Lewis acid) ratio. The table below describes the amount of raw materials use to synthesize the copolymers. VESFA, TEGEVE, and initiator (1-isobutoxy ethyl acetate) were dissolved in dry toluene and chilled to 0 °C. Each polymerization was initiated with the addition of ethyl aluminum

sesquichloride (25 wt. % in toluene). After 17 hours, the reactions were terminated with the addition of 3 mis of methanol. 5 ml of methylene chloride was added to the terminated solutions and the organic layers were washed with 3 ml of deionized water three times to remove the initiator and co-initiator residues. The polymers were recovered by rotary evaporation of all the volatiles and drying under vacuum overnight. Successful

polymerization was demonstrated using proton NMR by observing the absence of protons associated with the vinyl ether units of the monomers. GPC using polystyrene standards showed that copolymers 1, 2, and 3 possessed number average molecular weight of 15210, 13800, and 12880 g/mol respectively.

Example V. Cured Films of Poly VESFA

Cured films of polyVESFA were prepared using an auto-oxidation process. The synthetic scheme used to produce the cured films is shown in Figure 12. An example of a cured film produced with this method is as follows: 2 g of polyVESFA was dissolved in 0.5 g toluene in a 20 ml vial equipped with an overhead stirrer. 16.6 mg of 12% cobalt octoate in mineral spirit, 55.6 mg of 18% zirconium octoate in mineral spirit, and 75 mg of 8% zinc nuxtra in mineral spirit was added to the solution and the solution stirred at 5000 rpm for 10 minutes. The liquid solution was cast over a clean aluminum panel using a draw down bar (BYK Gardner) to produce approximately a 200 micron thick film which was cured by allow the film to stand at room temperature for 2 days and then heating at 40 °C for 3 days. The thermal properties of the cured film were determined using differential scanning calorimetry (Q1000 from TA Instruments) by first heating the sample from 25 °C to 100 °C at a heating rate of 10 °C/minute (1 ^st heat), cooling from 100 °C to -120 °C at a cooling rate of 10 °C/minute (cooling), and reheating from -120 °C to 100 °C at a heating rate 10 °C/minute (2 ^nd heat). The thermogram obtained from the 2 ^nd heat showed a glass transition at -27.2 °C.

In another experiment, a series of cured films produced with this method is as follows: polyVESFA, 12% cobalt octoate in mineral spirit, 18% zirconium octoate in mineral spirit, and 8% zinc nuxtra in mineral spirit were mixed together using a FlackTek mixer at 3500 rpm for 3 minutes. The table below describes the compositions of the coatings produced. The air drying behavior of liquid coatings was characterized using a BK 3-Speed Drying Recorder (MICKLE Laboratory Engineering Co. Ltd., United Kingdom). A needle carrier holding 6 hemispherical ended needles travels across the length of six 305x25 mm glass strips with time. A weight of 5 gm is attached to each hemispherical needle to study the through drying property of coating. Each liquid coating mixture was casted over glass strips using a 25 mm cube film applicator to produce wet films about 75 microns in thickness. The coating drying time was evaluated as open time, dust free time and tack free time for 48 hour time period.

The table below lists drying time for films produced by air oxidative curing.

The rate of crosslinked network formation was characterized by a dynamic time sweep test using the ARES Rheometer. Each liquid mixture was placed in between the two parallel plates and heated for 63 minutes at a constant frequency of 10 rad/s, strain rate of 0.3 %, and temperature of 120 °C. For the coating based on PolyVESFA-1, storage modulus increased from 1.8 KPa to 46.1 KPa while the storage modulus of the reference coating based on soybean oil showed no increase in modulus at 120 °C over this time period.

In addition to curing using an auto-oxidation process, curing was also accomplished using a vulcanization process as shown in Figure 13.

One example of a cured film produced with this process is as follows: In an 8 ml glass vial, 5 g polyVESFA, 0.3 g zinc oxide, and 0.025 g stearic acid were added and stirred with an overhead stirrer at 9000 rpm for 2 minutes. Next, 0.175 g sulfur and 0.025 g tetramethylthiuram disulfide were added and the mixture stirred at 18000 rpm for 4 minutes with constant cooling by partial immersion in a water bath. The rate of development of the crosslinked network due to sulfur vulcanization reaction of C=C double bonds in fatty acid ester chains was characterized by dynamic temperature ramp test using ARES Rheometer (TA Instruments). The liquid dispersion was placed in between two parallel plates and heated at a constant temperature of 140 °C. The storage modulus was measured with time at a constant frequency of 10 radian/s and a strain of 0.3 %. Over the period of 22 minutes, storage modulus increased from about 1 Pa to 0.19 MPa and then remained relatively constant with time over a total time period of 100 minutes.

Another example of a cured film produced with this process is as follows: The table below describes the compositions of three liquid coatings produced from polyVESFA- 1, polyVESFA-2, and soybean oil. Generally, in a 20 ml glass vial, polyVESFA, zinc oxide, and stearic acid were added and stirred with an overhead stirrer at 15,000 rpm for 2 minutes. Next, sulfur and tetramethylthiuram disulfide were added and the mixture stirred at 15000 rpm for 4 minutes with constant cooling by partial immersion in a water bath. The rate of development of crosslinked network due to sulfur vulcanization reaction of C=C double bonds in fatty acid ester chains was characterized by dynamic temperature ramp test using ARES Rheometer (TA Instruments). The liquid dispersion was placed in between two parallel plates and heated at a constant temperature of 140 °C. The storage modulus was measured with time at a constant frequency of 10 radian/s and a strain of 0.3 %. Over the period of 22 minutes, the storage modulus of Formulation-2 increased from about 1 Pa to 0.19 MPa and then remained relatively constant with time over a total time period of 65 minutes. For Formulation- 1, the storage modulus increased from about 1 Pa to 0.27 MPa over a time period of 22 minutes and then remained relatively constant with time over a total time period of 54 minutes. In contrast, the reference formulation based on soybean oil showed a storage modulus value of 1.82 Pa after 4.56 h under the same curing condition.

Example VI. Epoxy-functional polyVESFA

For many material applications, soybean oil is subjected to a chemical conversion and used as one component of a formulated material. For example, epoxidized soybean oil (ESO) is a commercial product produced by epoxidation of the double bonds of soybean oil. ESO has found application as a component of epoxy-based coatings and composites. ESO has been further chemically modified to produce other reactive soybean-oil based materials such as soybean oil-based polyols, which are typically used to produce polyurethanes, and soybean oil-based acrylates, which are typically used in radiation-curable coatings.

An example of the synthesis of E-polyVESFA is as follows (see also Example I): 4 g of polyVESFA-2 was dissolved in 80 ml of methylene chloride in a round bottom flask and 4.73 g of 3-chloroperoxybenzoic acid added with vigorous stirring. The reaction was continued for 4 hours at room temperature at a stirrer speed of 650 rpm. After the reaction was complete, the polymer was precipitated into methanol, isolated by centrifugation, and dried under vacuum overnight. Successful synthesis of E-polyVESFA-2 was confirmed using proton NMR by observing the disappearance of peaks associated with CH=CH groups in the fatty acid ester chain of polyVESFA at 5.3 ppm (m) and the corresponding appearance of peaks at 2.8 - 3.1 ppm (m) associated with the glycidyl groups in E-polyVESFA-2. The thermal properties of the polymer were determined using differential scanning calorimetry by first heating the sample from -120 °C to 70 °C at a heating rate of 10 °C/minute (1 ^st heat), cooling from 70 °C to - 120 °C at a cooling rate of 10 °C/minute (cooling), and reheating from - 120 °C to 120 °C at a heating rate 10 °C/minute (2 ^nd heat). The thermogram obtained from the 2 ^nd heat showed a glass transition at -58.0 °C and a very weak, diffuse melting transition with an enthalpy of melting of 5.97 J/gm and a peak maximum at -21.7 °C.

Example VII. Cured Films from Epoxy-functional polyVESFA

From the E-polyVESFA-2 (Example VI), cured films were prepared by crosslinking using an amine curing agent as shown in Figure 14.

An example of the production of an amine-cured film produced from E-polyVESFA-

2 is as follows: 3 g of E-polyVESFA-2 (epoxy equivalent weight = 290 g/eq) and 0.421 g triethylene tertamine (technical grade 60% purity, used as received from Sigma Aldrich, amine hydrogen equivalent weight of 24.372 g/eq) were mixed with a FlackTek mixer using 3500 rpm for 3 minutes. The clear mixture was coated over a Teflon® film adhered to a glass panel. The wet film thickness was approximately 1 mm and the film cured in a forced air oven at 120 °C for 36 hours. A reference coating based on epoxidized soybean oil (Vikoflex-7170 from Arkema, epoxy equivalent weight = 233 g/eq) was produced by mixing

3 gm of the epoxidized soybean oil (ESO) with 0.524 g of triethylene tertamine using the FlackTek mixer. The coating mixture was cast over a Tefion® film adhered to a glass panel. The wet film thickness was approximately 1 mm and the film cured in a forced air oven at 120 °C for 99 hours. A cure time exceeding 36 hours was used for the reference coating because the coating was still liquid after 36 hours at 120 °C. Free films were characterized using an ARES Rheometer (TA Instruments). Cured films were placed in between two parallel plates and the storage modulus measured by ramping the temperature from - 90 °C to 120 °C at ramp rate of 5 °C/min with a constant frequency of 10 rad/s and a strain rate of 0.3 %. From the experiment, the film based on E-polyVESFA-2 gave a glass transition temperature (Tg) of 15.2 °C and a rubbery plateau modulus (at 70 °C) of 27.7 MPa. The reference coating based on ESO showed a Tg and rubbery plateau modulus (at 70 °C) of - 5.3 °C and 11.6 MPa, respectively. These results indicate a higher crosslink density was achieved with use of E-polyVESFA-2 as compared to ESO. In addition, the rate of crosslinked network formation was characterized by a dynamic time sweep using the ARES Rheometer. Each liquid mixture was placed in between the two parallel plates and heated for 20 hours at a constant frequency of 2 rad/s, strain rate of 0.1 %, and temperature of 120 °C. For the coating based on E-polyVESFA-2, storage modulus increased from 17 Pa to 778 KPa over the period of 5 hours while the storage modulus of the reference coating based on ESO showed no increase in modulus until 16 hours at 120 °C. After 20 hours, the reference coating reached a storage modulus of 4.63 KPa, while the experimental coating based on E- polyVESFA-2 reached this storage modulus after just 49 minutes at 120 °C. These results indicate that E-polyVESFA develops a crosslinked network much faster than the analogous material based on ESO.

E-polyVESFA was investigated for use in radiation-curable coatings using a ultraviolet light (UV) initiated cationic polymerization process as shown in Example I and further, as shown in Figure 15.

A series of radiation cured coatings were prepared by mixing E-polyVESFA-2, 3- methyloxetan-3-yl)methanol (Oxetane 101 from Dow Chemical), and 50 wt. %

triarylsulfonium hexafluoroantimonate salt in propylene carbonate (UVI 6974 photoinitiator from Dow Chemical) together using a FlackTek mixer at 3500 rpm for 3 minutes. An analogous series of reference coatings was produced by replacing E-polyVESFA-2 with commercially available ESO (Vikoflex-7170 from Arkema). The table below describes the compositions of the coatings produced. Each liquid coating mixture was casted over Teflon® film adhered to a glass using a square draw down bar (BYK Gardner) to produce wet films about 200 microns in thickness. The films were cured by passing coated substrates once or twice under a F300 UVA lamp from Fusion UV Systems (UVA light intensity ~ 1420 mW/cm ² as measured by UV Power Puck ^® II from EIT Inc.) equipped with a bench top conveyor belt set at a belt speed of 24 feet/min. Free films were characterized using dynamic mechanical thermal analysis (Q800 from TA Instruments). The experiment was carried out from -90 °C to 140 °C using a heating rate of 5 °C/min., frequency of 1 Hz, and strain amplitude of 0.02%. The T _g was obtained from the peak maximum in the tan δ response.

The table below lists T _g and storage modulus of the rubbery plateau region (at 70 °C) for films produced using one and two passes under the UVA lamp.

* Coating was still in the liquid state

In order to characterize cure kinetics of the UV curable materials described above, a photo DSC experiment was performed using a Q 1000 differential scanning calorimeter (TA Instruments) equipped with a photocalorimetric accessory (PCA). The experiment was carried out at a UV light intensity of 50 mW/cm ² and a temperature of 30 °C. Samples were equilibrated for 1 minute before exposure to UV light for 7 minutes followed by a temperature ramp from 0 °C to 200 °C at a rate of 10 °C/min under nitrogen to determine the residual heat associated with thermal cure of residual (unreacted functional groups). The % of total conversion was calculated by the following formula:

^n.p ₀ t ₀ p _ol y _mer i _Zar i _0n

% of Total Conversion = X 100

AHp _o t ₀ p _ol y _mer i _zar i _on ^~ H AHR _es id _ual Heat

The following table lists the time period associated with the peak maximum of the reaction exotherm (i.e. time to peak maximum) and the percent of conversion obtained by UV light exposure for both the control and experimental coatings. From the table below, it can be seen that the coatings based on E-polyVESFA-2 possess faster cure rates as indicated by the shorter time period associated with peak of the reaction exotherm and higher extent of conversion after a 2 minute UV exposure.

In addition to photo-DSC, a real-time FTIR (RTIR) instrument was used to characterize cure kinetics. The RTIR experiments were carried out using a Nicolet Magna- IR 850 spectrometer Series II. The light source was a LESCO Super Spot MK II 100W DC UVA mercury vapor short lamp. Samples were spin-coated onto a KBR plate at 4000 rpm for 20 seconds and exposed to UV light for 3 minutes followed by a dark cure of 2 minutes. FTIR spectra were taken at 1 spectrum/s with a resolution of 4 cm ^"1 . The experiment was carried out in air at 25 °C and the UV light intensity was 34 mW/cm ² as measured by UV Power Puck II from EIT Inc. The consumption of epoxy groups was determined by monitoring the peak area in between 800 cm ^"1 and 860 cm ^"1 . For Control- 1 , Control-2, Exp- 1 , and Exp-2, the percent of epoxide conversion after 2 minutes of UV light exposure were 9.7, 17.9, 78.5, and 88.4, respectively. With 3 minutes of light exposure, Control-1 ,

Control-2, Exp-1 , and Exp-2, reached epoxide conversions of 15.8 %, 25.9 %, 86.1 % and 91.8 %, respectively. This data further illustrates the surprising result that coatings based on E-polyVESFA provide much faster cationic photocure than analogous coatings based on ESO. Example VIII. Acrylated Derivatives

Acrylate-functional materials can be prepared by reaction of epoxidized polyVESFA with acrylic acid and the acrylate-functional materials used to prepare coatings produced using a radiation-cure process (Khot et al, J. Polym. Sci., Part A: Polym. Chem., 82, 703- 723 (2001)). The properties of UV-cured coatings based on acrylate-functional polyVESFA can be compared to analogous coatings based on acrylate-functional soybean oil.

Acrylated materials for use in applications such as radiation-curable coatings can be produced from E-polyVESFA and VESFA copolymers precursors by epoxide ring-opening with acrylic acid as shown in Figure 16.

An example of the synthesis of acrylated polyVESFA is as follows: In a 40 ml vial,

1.41 gm of epoxidized polyVESFA-2, 1.7 mg hydroquinone, and 8.6 mg potassium acetate were dissolved in 7.93 ml of toluene. The rapidly stirring solution was heated to 110 °C and 0.316 gm of acrylic acid was added drop wise over the period of 30 minutes. After 42 hours of reaction, the temperature was cooled to room temperature and the toluene was removed by rotary evaporation. The crude product was diluted with methylene chloride and washed with deionized water. The organic layer was dried with anhydrous magnesium sulfate. The pure polymer was isolated by rotary evaporation of methylene chloride and drying under vacuum overnight. Successful synthesis of acrylated polyVESFA was confirmed using proton NMR by observing the disappearance of peaks associated with the glycidyl groups in the fatty acid ester chains of E-poly VESFA at 2.8 - 3.1 ppm (m) and the corresponding appearance of new peaks at 4.2 - 4.3 ppm (m, CHOCO) and 3.7 - 3.8 ppm (m, CHOH) associated with ring-opening of the epoxide groups with acrylic acid. The incorporation of acrylate groups into polyVESFA was also demonstrated by the appearance of new peaks at 5.8 ppm, 6.4 ppm (m, C=CH ₂ ), and 6.1 ppm (m, C=CH) associated with the vinyl groups of acrylic acid esters.

An example of the production of a cured film produced from acrylated polyVESFA is as follows: 47 mg of Irgacure 184 photoinitiator from Ciba was dissolved in 0.178 gm of 1,6-hexanediol diacrylate. Next, 1 gm of acrylated polyVESFA-2 was added to the mixture resulting in a homogeneous solution. The solution was applied over a Teflon® film adhered to a glass panel using a drawdown bar (BYK Gardner) to produce a 200 micron thick wet film and the mixture cured by passing the coated panel through a F300 UVA lamp from Fusion UV Systems (UVA light intensity ~ 1420 mW/cm ² as measured by UV Power Puck ^® II from EIT Inc) equipped with a bench top conveyor belt running at a belt speed of 24 feet/min. A free film of the coating was characterized using dynamic mechanical thermal analysis (Q800 from TA Instruments). The experiment was carried out from -90 °C to 150 °C using a heating rate of 3 °C/min., frequency of 1 Hz, and strain amplitude of 0.03%. The T _g obtained from the peak maximum in the tan δ response was 29.9 °C.

An example of the synthesis of acrylated polyVESFA (A-polyVESFA-1) is as follows: In a 250 ml two-neck round-bottom flask, epoxidized polyVESFA- 1,

hydroquinone, and potassium acetate were dissolved in toluene. The rapidly stirring solution was heated to 110 °C and acrylic acid was added drop wise over the period of 30 minutes. After 42 hours of reaction, the temperature was cooled to room temperature. The crude product was diluted with methylene chloride and washed with deionized water. The organic layer was dried with anhydrous magnesium sulfate. The pure polymer was isolated by rotary evaporation of solvents and drying under vacuum overnight. A reference material, acrylated soybean oil, was produced from epoxidized soybean oil (Vikoflex-7170 from Arkema, epoxy equivalent weight = 233 g/eq). The following table lists the amount of raw materials used to synthesize A-polyVESFA-1 and acrylated soybean oil.

A series of radiation cured coatings were prepared by mixing A-polyVESFA-1, Irgacure 184 photoinitiator from Ciba, and 1 ,6-hexanediol diacrylate together using a FlackTek mixer at 3500 rpm for 3 minutes. An analogous series of reference coatings was produced by replacing A-polyVESFA-1 with synthesized A-soybean oil. The table below describes the compositions of the coatings produced.

In order to characterize cure kinetics of the UV curable materials described above, a photo DSC experiment was performed using a Q 1000 differential scanning calorimeter (TA Instruments) equipped with a photocalorimetric accessory (PC A). The experiment was carried out at a UV light intensity of 50 mW/cm ² and a temperature of 30 °C. Samples were equilibrated for 1 minute before exposure to UV light for 30 seconds. The following table lists the time period associated with the peak maximum of the reaction exotherm (i.e. time to peak maximum) obtained by UV light exposure for both the reference and experimental coatings. From the table below, it can be seen that the coatings based on A-polyVESFA-1 possessed faster cure rates as indicated by the shorter time period associated with peak of the reaction exotherm.

In addition to photo-DSC, a real-time FTIR (RTIR) instrument was used to characterize cure kinetics. The RTIR experiments were carried out using a Nicolet Magna- IR 850 spectrometer Series II. The light source was a LESCO Super Spot MK II 100W DC UVA mercury vapor short lamp. Samples were spin-coated onto a KBR plate at 4000 rpm for 20 seconds and exposed to UV light for 1 minute. FTIR Spectra were taken at 1 spectrum/s with a resolution of 4 cm ^"1 . The experiment was carried out in air at 25 °C and the UV light intensity was 34 mW/cm ² as measured by UV Power Puck II from EIT Inc. The consumption of C=C groups in the acrylate was determined by monitoring the peak area in between 1605 cm ^"1 and 1650 cm ^"1 . For Experimental- 1, Experimental-2, Reference-1, and Reference-2, the percent of C=C conversion after 5 seconds of UV light exposure were 72.2, 58.5, 65.5, and 34.3, respectively. With 1 minute of light exposure, Experimental- 1, Experimental-2, Reference-1, and Reference-2, reached C=C conversions of 77.1 %, 63.6 %, 74.9 % and 38.5 %, respectively. This data further illustrates the result that coatings based on A-polyVESFA provide faster free radical photocure than analogous coatings based on A-soybean oil.

Example IX. Polyols Model polymer networks based on epoxidized polyVESFA can be produced, characterized, and compared to analogous networks derived from epoxidized soybean oil. Both epoxidized polyVESFA and epoxidized soybean oil can be converted to polyol derivatives by ring-opening the epoxide groups with methanol (Zlatanic, et al., J. Polym. Sci., Part B: Polym. Phys., 42, 809-819 (2003)). The polyols can be used to prepare model polyurethane networks and the properties of the networks prepared from polyVESFA-based polyols compared to analogous polyols derived from soybean oil.

Polyols are important building-blocks for producing crosslinked materials such as crosslinked polyurethanes. Polyols can be produced from E-polyVESFA and epoxidized VESFA copolymers using a process such as that shown in Figure 17.

Example X. Utility of Novel Soybean Oil-Based Polymers in Rubber Compounds

Rubber compounds for applications such automobile tires are multicomponent materials based largely on petroleum-derived starting materials. For example, it has been shown that soybean oil and/or its derivatives can be used to improve the elongation of EPDM rubbers and displace some of the petroleum-based processing oils in tire tread compounds (Brentin and Sarnacke, "Rubber Compounds: A Market Opportunity Study"). The International Rubber Study Group reported that the total volume of rubber consumed globally in 2011 was 25.7 million metric tons with tire manufacturing consuming about 60% of the total. Based on the size of this market, it can be understood that even modest use of soybean oil-based materials in this market translates to significant volumes of soybeans. For example, if just 1% of the total volume of rubber consumed in 2011 was displaced by polyVESFA, which is 75 weight percent soybean oil, the total number of bushels of soybeans would be over 2 million bushels. Previous research has shown that soybean oil has the potential to replace some petroleum-based components in rubber compounds. Considering the enormous size of the rubber industry and the price and supply volatility of petrochemicals, this market may represent a major opportunity for the use soybean oil-based materials.

We have developed a process to produce high molecular weight polymers from a novel monomer derived from soybean oil. The novel monomer, which is being referred to as vinyl ether of soybean oil fatty acid esters (VESFA) or (2-vinyloxy)ethyl soyate (2- VOES) is 75 weight percent soybean oil and can be readily produced using a process analogous to that used to produce soy biodiesel. We have scaled the monomer synthesis up to a volume of 10 liters without issue. The polymerization process developed for VESFA allows for high molecular weight polymer to be produced without consuming the unsaturation in the fatty acid pendent groups. The polymerization process also enables control of polymer molecular weight and the production of copolymers.

The primary difference between the homopolymer of VESFA (i.e. polyVESFA) and soybean oil is the number of unsaturated groups per molecule. In contrast to soybean oil triglycerides which have three fatty acid chains per molecule, polyVESFA possesses 100s of fatty acid chains per molecule. Thus, the number of functional groups per molecule for polyVESFA is 1 to 2 orders of magnitude higher than soybean oil. This difference in chemical structure was shown to dramatically decrease cure times of coating compositions and significantly increase coating modulus/hardness. In addition, due to the higher molecular weight of polyVESFA as compared to soybean oil much less shrinkage upon cure occurs which enables higher adhesion to substrates.

With respect to rubber compounds, the polymer technology developed is expected to possess some major advantages over traditional soybean oil and soybean oil derivatives. First, the dramatically higher number of unsaturated groups per molecule associated with polyVESFA will ensure grafting of the polymer into the crosslinked rubber matrix preventing extraction of the polymer from the vulcanized rubber and enhancing mechanical properties such as modulus, strength, and abrasion resistance. In addition, and perhaps more importantly, the ability to copolymerize VESFA with other monomers provides a new method for tailoring basic polymer properties such as glass transition temperature, solubility parameter, and chemical functionality. By proper selection of comonomers for use in conjunction with VESFA copolymers, the solubility/compatibility of the copolymer with a specific type of rubber can be enhanced. In addition, appropriate functional groups can be incorporated through copolymerization that provide for favorable interactions between the copolymer and specific components of the rubber compound such as filler particles.

Enhancing interactions between the polymer matrix and filler particles can provide dramatic enhancements in mechanical properties including modulus, tensile strength, toughness, and abrasion resistance.

PolyVESFA polymers can be incorporated into rubber compounds for tires.

Vulcanized polyVESFA and VESFA copolymers may also have potential application as factice. These vulcanized polymers can be compared to soybean oil factice produced using analogous vulcanization conditions.

The soybean oil-based polymer technology of the present invention is expected to be useful for application in rubber compounds, particularly in tire tread applications.

A proof-of-concept experiment has been conducted in which a polyVESFA sample was blended with typical reagents used to vulcanize rubber and the composition cured at 140°C. For comparison, an analogous composition was prepared using conventional soybean oil in place of polyVESFA. The vulcanization process was monitored with time at 140°C using a parallel plate rheometer. As shown in Figure 18, the viscosity and shear modulus of the polyVESFA material increased by a few orders of magnitude in under 5 minutes, while that of the soybean oil-based material remained unchanged over the entire two hour period. This result indicates that polyVESFA produces a crosslinked network dramatically faster than that of soybean oil. In addition, films were cast onto glass panels and the panels placed in an oven set at 140°C for 45 minutes. As shown in Figure 19, the material based on soybean oil was still liquid while the material based on polyVESFA was a tack-free rubber. These results clearly demonstrate unique capabilities for polyVESFA as compared to conventional soybean oil in rubber compositions. This technology will have major utility in rubber compounds which will drive the utilization of soybean-based materials in the rubber industry.

Example XI. Copolymerization of VESFA and Cyclohexyl Vinyl Ether (CHVE)

Copolymers of VESFA and CHVE were successfully produce using carbocationic copolymerization as follows: Prior to use, VESFA was dried with magnesium sulfate inside a glove box. CHVE (98%) was purchased from Sigma- Aldrich and distilled over calcium hydride before use. The copolymerization was carried out in a dry 500 ml, three-neck, round-bottom flask that was partially submerged in a heptane bath located inside a dry box and cooled to 0 °C. The flask was equipped with an overhead stirrer. Within the glass vessel, the initiator (1-isobutoxy ethyl acetate), VESFA, and CHVE were dissolved in dry toluene and the mixture allowed to cool to 0 C. The copolymerization was initiated by the addition of a 25 weight percent solution of ethylaluminum sesquichloride in toluene. Table 2 lists the weights of the components used for two different copolymerizations. After 17 hours of reaction, each copolymerization was terminated with chilled methanol, which caused the copolymer to precipitate. Each copolymer was washed multiple times with methanol. Copolymer yield was determined gravimetrically after drying the purified copolymer at 48 °C under vacuum overnight. Copolymer molecular weight was characterized using a high-throughput Symyx Rapid Gel Permeation Chromatography equipped with an evaporative light scattering detector (PL-ELS 1000) and polystyrene standards. Table 3 lists the data for monomer conversion and molecular weight.

Table 2. Compositions used to produce poly(VESFA-r-CHVE).

Table 3. Data obtained from GPC and gravimetric analysis for the synthesis of

poly(VESFA-r-CHVE).

the polydispersity index The thermal properties of the poly(VESFA-r-CHVE) copolymers were determined using differential scanning calorimetry (Q1000 from TA Instruments) by first heating the sample from -120 °C to 70 °C at a heating rate of 10 °C/minute (1 ^st heat), cooling from 70 °C to -120 °C at a cooling rate of 10 °C/minute (cooling), and reheating from -120 °C to 120 °C at a heating rate 10 °C/minute (2 ^nd heat). The thermogram obtained from the 2 ^nd heat of poly(VESFA-r-CHVE)-75/25 showed a glass transition at -86 °C and a very weak, diffuse melting transition with an enthalpy of melting of 0.63 J/g and a peak maximum at -23.5 °C. The thermogram obtained from the 2 ^nd heat of poly(VESFA-r-CHVE)-50/50 showed a glass transition at 29 °C and a very weak, diffuse melting transition with an enthalpy of melting of 0.37 J/g and a peak maximum at -24.2 °C.

Example XII. Cured Films of Poly(VESFA-r-CHVE)

Since the poly(VESFA-r-CHVE) copolymers possess unsaturation as a result of the VESFA repeat units, it was of interest to determine if crosslinked coatings could be produced using an auto-oxidation process. Cured films were produced as follows:

poly(VESFA-r-CHVE), 12% cobalt octoate in mineral spirits, 18% zirconium octoate in mineral spirits, and 8% zinc Nuxtra ^® in mineral spirits, and toluene were mixed together using a FlackTek mixer at 3500 rpm for 3 minutes. Table 4 describes the compositions of the coating solutions produced. The cure/drying kinetics at ambient conditions were determined using a BK 3-Speed Drying Recorder (MICKLE Laboratory Engineering Co. Ltd., United Kingdom). Each coating mixture was casted over glass strips using a 25 mm cube film applicator to produce wet films of about 75 microns in thickness. The coating drying time was evaluated as open-time, dust- free time, and tack-free time according to the a BK 3-Speed Drying Recorder. The results obtained are shown in Table 5.

Table 4. Liquid coating compositions derived from poly(VESFA-r-CHVE) copolymers.

Table 5. Results obtained using a BK 3-Speed Drying Recorder

Example XIII. Epoxy-functional Poly(VESFA-r-CHVE) Copolymers

Epoxy-functional poly(VESFA-r-CHVE) copolymers, referred to herein as E- poly(VESFA-r-CHVE), were prepared as follows: Poly(VESFA-r-CHVE) was dissolved in methylene chloride in a 1 -liter, round-bottom flask and 3-chloroperoxybenzoic acid added with vigorous stirring. Table 6 lists the concentration of the reagents used to produce two different E-poly(VESFA-r-CHVE) copolymers. The reaction was run for 4 hours at room temperature at a stirrer speed of 650 rpm. After the reaction was complete, the polymer was precipitated into methanol, isolated by centrifugation, and dried under vacuum overnight. Successful synthesis of E-poly(VESFA-r-CHVE) was confirmed using proton NMR by observing the disappearance of peaks associated with CH=CH groups in the fatty acid ester chain of poly(VESFA-r-CHVE) at 5.3 ppm (m) and the corresponding appearance of peaks at 2.8 - 3.1 ppm (m) associated with the glycidyl groups in E-poly(VESFA-r-CHVE). Table 6. A description of the reaction mixtures used to produce two different E- poly(VESFA-r-CHVE) copolymers.

The thermal properties of the two E-poly(VESFA-r-CHVE) copolymers were determined using differential scanning calorimetry (Q1000 from TA Instruments) by first heating the sample from -120 °C to 70 °C at a heating rate of 10 °C/minute (1 ^st heat), cooling from 70 °C to -120 °C at a cooling rate of 10 °C/minute (cooling), and reheating from -120 °C to 120 °C at a heating rate 10 °C/minute (2 ^nd heat). The thermogram obtained from the 2 ^nd heat of E-poly(VESFA-r-CHVE)-75/25 showed a glass transition at - 53.5 °C and a very weak, diffuse melting transition with an enthalpy of melting of 0.57 J/g and a peak maximum at - 19.4 °C. The thermogram obtained from the 2 ^nd heat of E- poly(VESFA-r-CHVE)-50/50 showed a glass transition at 34.5 °C and a very weak, diffuse melting transition with a peak maximum at -24.5 °C.

Example XIV. Copolymers of VESFA and triethylene glycol ethyl vinyl ether (TEGEVE)

Six different copolymers of VESFA and TEGEVE were synthesized using carbocationic polymerization. A representative procedure is as follows: VESFA and TEGEVE were dried with MgS0 ₄ inside a glove box. Inside a glove box, the dry VESFA and TGEVE were copolymerized at 0 °C in a three-neck, round-bottom that had been dried by heating at 200 °C overnight. A general procedure to synthesize copolymer 1 (Table 7) is as follows: 51.43 g of VESFA, 4.0 g of TGEVE, and 130 mg of initiator (1-isobutoxy ethyl acetate (IBEA)) were dissolved in 346 mL of dry toluene and chilled to 0 °C. The polymerization was initiated by the addition of 4.56 mL of a 25 weight percent solution of ethylaluminum sesquichloride in toluene. The reaction was terminated after 18 h by the addition of 346 mL of chilled methanol, which precipitated the copolymer. The copolymer was isolated and washed four times with methanol. The purified polymer was collected as a viscous liquid after drying under vacuum (5-7 mm of Hg) overnight.

Table 7 lists the composition of the reaction mixtures used to produce the six copolymers. For copolymers 5 and 6, precipitation upon addition of methanol did not occur. As a result, methanol was removed by vacuum stripping and the copolymer purified by passing a hexane solution of the copolymer through a column packed with silica to remove unreacted VESFA and then adding methylene chloride to column to recover the copolymer. The polymer was then recovered by vacuum stripping volatives. The actual composition of the copolymers produced was determined using proton nuclear magnetic resonance spectroscopy (1H NMR) and the results are displayed in Table 8. Using differential scanning calorimetry (DSC) the thermal properties obtained for the copolymers were determined. Each copolymer displayed a single glass transition temperature (Tg) and copolymers 1, 2, and 3 displayed a weak melting endotherm. Copolymers 4, 5, and 6 did not display a distinct melting transition. The Tg and melting temperatures obtained are provided in Table 8. For comparison purposes, data for a poly VESFA homopolymer and a polyTEGEVE

homopolymer produced using carbocationic polymerization are also provided in the table. The molecular weight and molecular weight distribution (MWD) of the copolymers were characterized using gel permeation chromatography. The number-average molecular weight (Mn) and MWD data obtained are shown in Table 3. Values of Mn are expressed relative to polystyrene standards.

Table 7. Composition of the polymerization mixtures used to produce copolymers

VESFA and TEGEVE.

Copolymer5 6.25 15.00 71 2.502 132

Copolymer6 2.85 15.00 62 2.220 1 10

Table 8. Data obtained for copolymers of VESFA and TEGEVE.

All of the copolymers synthesized produced stable dispersion in water when added to water at a concentration of 30 wt%. In contrast, polyVESFA does not disperse in water and polyTEGEVE is completely soluble in water. Since these copolymers possess unsaturation in pendent groups derived from VESFA, it was of interest to determine if these copolymers could be used to produce crosslinked coatings when cast from an aqueous dispersion.

Coatings were produced by simply mixing 12 g of copolymer, 28 g of water, and a certain amount of catalyst mixture (Co, Zr & Zn), which is shown in Table 9, using a SpeedMixer™ -DAC 150 FVZ-K (Hauschild Engineering, Germany) for 10 minutes at 3500 rpm. The coatings were cast onto aluminum and glass panels and allowed to cure at ambient conditions. The cure time, defined as the time required to obtain a tack-free film as specified using a BK 3-Speed Drying Recorder (MICKLE Laboratory Engineering Co. Ltd., United Kingdom), was measured for the coatings and compared to analogous data obtained for polyVESFA. Since polyVESFA is not dispersible in water, the coating solution for this material was produced by mixing only with catalyst (i.e. no solvent was used). In addition to cure time, the Tg, hardness, water contact angle, surface energy, water contact angle hysteresis, and optical transparency of the coatings was measured. Tg was measured using DSC while water contact angle, surface energy, and water contact angle hysteresis were measured using a FTA 2000 (First Ten Angstrom, USA) instrument and FTA 32 software. Pendulum hardness was measured according to ASTM method D4366-95. Optical transparency was characterized using a UV-VIS spectrometer (Cary 50000, Varian) and scanning wavelengths ranging from 400 to 800 cm ^"1 . Table 10 displays the data obtained for the four experimental coatings and the control coating derived from polyVESFA.

Table 9. Catalyst description and composition for coating of 12 g polymer.

Table 10. Properties of coatings produced from copolymers 1, 2, 3, and 4. *RT is the reduction in transmittance compared to the uncoated glass substrate.

All of the coatings based on the VEFSA/TEGEVE copolymers cured into highly transparent coatings. Due to this result, it was interest to determine if VESFA/TEGEVE copolymers could be used to emulsify polyVESFA in water without having to use surfactant. The advantage of using a VESFA/TEGEVE copolymer as an emulsifier is that, unlike a conventional surfactant, it will crosslink into the cured polymer network and, thus, should not phase separate resulting in a reduction in the optical transparency. Table 11 describes the coating solutions prepared. The catalyst used for these coating is same as described in Table 9 for 12 g of total polymer. Table 11. Coating dispersions prepared from polyVESFA and VESFA/TEGEVE copolymers.

All six coatings formed stable dispersions that were cast onto glass panels and allowed to cure at ambient conditions. The cure time, defined as the time required to obtain a tack-free film as specified using a BK 3 -Speed Drying Recorder (MICKLE Laboratory Engineering Co. Ltd., United Kingdom), was measured for each coating along with Tg, hardness, water contact angle, surface energy, water contact angle hysteresis, and optical transparency. Table 12 lists the data obtained for these coatings. Table 12. Coating dispersions prepared from polyVESFA and VESFA/TEGEVE copolymers. *RT is the reduction in transmittance compared to the uncoated glass substrate.

As indicated by the data displayed in Table 12, all of the coatings produced highly transparent cured films indicating that VESFA/TEGEVE can be used as a reactive emulsifier for polyVESFA. For comparison purposes, a water-based coating of polyVESFA was prepared using a conventional surfactant (ETHAL OA- 23/70% and ETHAL OA- 35/70%) of 10 wt% to emulsify the polyVESFA. After drying it was found that the coating surface was not

homogeneous and non-transparent.

Example XV. Synthesis of the Vinyl Ether of Corn Oil Fatty Acid Esters (VECFA) A vinyl ether monomer based on corn oil was synthesized bas follows: 185 g of corn oil,

196 g of ethylene glycol monovinylether, and 5.56 g of anhydrous potassium hydroxide were added to a two-neck, 1000 ml, round-bottom flask and stirred at 70 °C for 3 hours under a blanket of nitrogen. The reaction mixture was cooled to room temperature and diluted with 1.1 liter of n-hexane. The organic layer was separated from the aqueous layer and washed once with 350 ml of aqueous acid (pH 4) and multiple times with deionized (DI) water until the wash water was neutral as indicated by litmus paper. The hexane layer was then dried with anhydrous magnesium sulfate. The product was recovered by rotary evaporation of n-hexane and dried under vacuum overnight. Proton NMR was used to confirm the production of VECFA: 1H NMR: 6.46 ppm (q, 1H, OCH=C), 4.0 - 4.15 ppm (m, 2H, C=CH ₂ ), 4.25 ppm (t, 2H, COOCH ₂ C ), 3.84 ppm (t, 2H, OCH ₂ C ), 5.3 ppm (m, 3.3H, CH=CH), 2.3 ppm (t, 2H, OCOCH ₂ ), 0.8 ppm (m, 3H, CH ₃ C), 1.58 ppm (m, 2H, COCH ₂ CH ₂ C).

Example XVI. Polymerization of VECFA VECFA was polymerized using carbocationic polymerization as follows: Prior to use,

VECFA was dried with magnesium sulfate inside a glove box. The reaction was carried out in a dry 1000 ml, two-neck, round-bottom flask partially submerged in a heptanes bath at 0 °C inside a dry box. In the reaction vessel 115 mg of initiator (1-isobutoxy ethyl acetate) and 50 g of VECFA were dissolved in 258 g of toluene and the solution chilled to 0 °C. The polymerization was started by the addition of 7.08 ml of a 25 weight percent solution of ethylaluminum sesquichloride in toluene. The polymerization was terminated after 18 hours by the addition of 300 ml of chilled methanol, which caused the polymer to precipitate. The polymer was washed with methanol and isolated using centrifugation. Polymer yield was determined gravimetrically after drying the purified polymer at 48 °C under vacuum overnight. The yield was found to be 78.5 weight percent. Polymer molecular weight was characterized using a high-throughput Symyx Rapid Gel Permeation Chromatography equipped with an evaporative light scattering detector (PL-ELS 1000) and polystyrene standards. The number average molecular weight and molecular weight distribution were determined as 21,400 g/mole and 1.18 respectively.

Example XVII. Characterization of the Polymerization of VECFA

The characteristics of the polymerization of VECFA were investigated as a function of coinitiator (i.e. ethylaluminum sesquichloride) concentration by monitoring polymer yield and polymer molecular weight as a function of polymerization time. Polymerization was carried out in a series of five dry 250 ml, two-neck, round-bottom flasks partially submerged in a heptane bath at 0 °C inside a dry box. Prior to use, VECFA was dried with magnesium sulfate inside the glove box. To each vessel, a cationic polymerization initiator, 1-isobutoxy ethyl acetate (IBEA), o

and VECFA were dissolved in dry toluene and chilled to 0 C. Each polymerization was initiated by the addition of a 25 weight percent solution of ethylaluminum sesquichloride in toluene. Table 13 lists the quantity of each reagent charged to individual vessels. For each

polymerization, aliquots of known weight were removed with time and terminated with chilled methanol, which caused the polymer to precipitate. Each polymer aliquot was washed multiple times with methanol and isolated using centrifugation. Polymer yield was determined

gravimetrically after drying the purified polymer at 48 °C under vacuum overnight. Polymer molecular weight was characterized using a high-throughput Symyx Rapid Gel Permeation Chromatography equipped with an evaporative light scattering detector (PL-ELS 1000) and polystyrene standards. Tables 14-18 list the data obtained from the different polymerizations. As shown in Table 14, polymerization using the lowest Eti. ₅ AlCli.5 concentration was extremely slow. As shown in Figure 20, all other polymerizations occurred within a reasonable time frame and produced polymerizations characterized by a linear relationship between number-average molecular weight (Mn) and VECFA conversion. This result indicates that all these polymerizations possessing "living" character. In addition, PDIs were relatively low. A general trend was found in which PDI increased slightly with increasing Eti. ₅ AlCli.5 concentration.

Table 13. Compositions used to investigate the effect Eti. ₅ AlCli.5 concentration on the polymerization of VECFA.

Table 14. Data obtained from Polymerization 1.

the polydispersity index

Table 15. Data obtained from Polymerization 2.

the polydispersity index

Table 16. Data obtained from Polymerization 3.

*PDI is the polydispersity index

Table 17. Data obtained from Polymerization 4. Reaction Time (hour) % Monomer GPC number Average PDI*

Conversion Molecular Weight

1.42 26.09 10720 1.18

2.33 39.98 13860 1.17

3.33 49.29 16320 1.15

4.33 55.73 18070 1.21

5.33 62.46 18470 1.22

6.33 64.79 21790 1.15

7.42 70.13 18990 1.22

8.42 69.39 20560 1.24

10.83 71.18 22210 1.26

18.42 87.97 25430 1.23

24 91.00 25970 1.26 the polydispersity index

Table 18. Data obtained from Polymerization 5.

the polydispersity index The thermal properties of polyVECFA were determined using differential scanning calorimetry (Q1000 from TA Instruments) by first heating a sample from -120 °C to 70 °C at a heating rate of 10 °C/minute (1 ^st heat), cooling from 70 °C to -120 °C at a cooling rate of 10 °C/minute (cooling), and reheating from -120 °C to 120 °C at a heating rate 10 °C/minute (2 ^nd heat). The thermogram obtained from the 2 ^nd heat showed a glass transition at -98.5 °C and a very weak, diffuse melting transition with an enthalpy of melting of 6.3 J/g and a peak maximum at -32.5 °C.

Example XVIII. Crosslinked Films of PolyVECFA

Crosslinked films of polyVECFA were prepared using an auto-oxidation process as follows: PolyVECFA, 12% cobalt octoate in mineral spirits, 18% zirconium octoate in mineral spirits, and 8% zinc Nuxtra ^® in mineral spirits were mixed together using a FlackTek mixer at 3500 rpm for 3 minutes. Table 19 describes the compositions of the liquid coatings produced. The coating based on corn oil was used a reference coating. The air-drying behavior of the coatings was characterized using a BK 3-Speed Drying Recorder (MICKLE Laboratory

Engineering Co. Ltd., United Kingdom). A needle carrier holding 6 hemispherical ended needles travel across the length of six 305 x 25 mm coated glass strips with time. A weight of 5 gm is attached to each hemispherical needle to study the curing kinetics of the coating. Each liquid coating mixture was casted over the glass strips using a 25 mm cube film applicator to produce wet films about 75 microns in thickness. The coating cure was evaluated by determining the open-time, dust-free time, and tack-free time using a BK 3-Speed Drying Recorder. The results of the experiment are shown in Table 20. As indicated by the results shown in Table 20, the use of polyVECFA provides dramatically faster cure than the reference coating based on corn oil. Table 19. Composition of a coating based on PolyVECFA and a reference coating based on corn oil.

Table 20. Results obtained using the BK 3 -Speed Drying Recorder and the coatings described in

Table 8.

Example XIX. Synthesis of 4-Vinyloxybutyl Soyate (4-VOBS)

4-VOBS was synthesized as follows: 100 g of soybean oil, 132 g of 1 ,4-Butanediol vinyl ether (99%, Sigma- Aldrich), and 3.28 g of anhydrous potassium hydroxide (> 85%, Sigma- Aldrich) were added to a two-neck, 100 ml, round-bottom flask and stirred at 70 °C for 3 hours under a blanket of nitrogen. The reaction mixture was cooled to room temperature and diluted with 600 ml of n-hexane. The organic layer was separated from the aqueous layer and washed once with 175 ml of aqueous acid (pH 4) and multiple times with deionized (DI) water until the wash water was neutral as indicated by litmus paper. The hexane layer was then dried with magnesium sulfate. The product was recovered by rotary evaporation of n-hexane and dried under vacuum overnight. Proton NMR was used to confirm the production of 4-VOBS: 1H NMR: 6.45 ppm (q, 1H, OCH=C), 3.6 - 4.2 ppm (m, 6H, C=CH ₂ , COOCH ₂ C, OCH ₂ C), 5.3 ppm (m, 3.3H, CH=CH), 2.3 ppm (t, 2H, OCOCH ₂ ), 1.7 ppm (m, 4H, OCCH ₂ CH ₂ COO), 0.8 ppm (m, 3H, CH ₃ C). Example. XX. Synthesis of Hydroxyl-Functional PolyVESFA

A hydroxyl-functional derivative of polyVESFA (OH-polyVESFA) was synthesized from E-polyVESFA using the synthetic scheme shown in Figure 21. A detailed procedure is as follows: 33.15 g of methanol and 1.94 g of tetrafluoroboric acid solution (48 wt. % in H ₂ 0,

Sigma-Aldrich) were combined in a 1 -liter round bottom flask and the temperature maintained at 30 °C. A solution of 60 g of E-polyVESFA and 340 g of toluene was added to the vessel with continuous stirring and the temperature raised to 50 °C. After 1 hour of reaction, 3.8 ml of ammonium hydroxide solution (30% v/v ΝΗ ₄ ΟΗ in water) was added to neutralize the acidity of the reaction mixture and the solution cooled to room temperature. The organic layer was washed with 300 ml of deionized water thrice and dried with anhydrous magnesium sulfate. The polymer was stored as a 20.5 weight percent solution in toluene.

For comparison purposes, a hydroxyl-functional derivative of soybean oil (OH-SBO) was synthesized from epoxidized soybean oil (E-SBO) as follows: 41.26 g of methanol and 2.41 g of tetrafluoroboric acid solution (48 wt. % in H ₂ 0, Sigma-Aldrich) were combined in a 1 -liter round bottom flask and the temperature maintained at 30 °C. A solution of 60 g of E-SBO and 340 g of toluene was added to the vessel with continuous stirring and the temperature raised to 50 °C. After 1 hour of reaction, 4.75 ml of ammonium hydroxide solution (30% v/v NH ₄ OH in water) was added to neutralize the acidity of the reaction mixture and the solution cooled to room temperature. The organic layer was washed with 300 ml of deionized water thrice and dried with anhydrous magnesium sulfate. The product was collected after rotary evaporation of toluene and dried under vacuum overnight.

Successful synthesis of OH-polyVESFA was confirmed using 1H NMR and FTIR.

Figure 22 displays the 1H NMR spectrum for OH-polyVESFA which showed peaks between 3.2 and 3.3 ppm associated with the protons of the methoxy groups. From the FTIR spectrum

(Figure 23), the broad band centered at 3400 cm ^"1 , attributed to the hydroxyl group produced by epoxy ring opening with methanol, can be easily seen.

Coatings were prepared to compare the difference between OH-polyVESFA and OH- SBO in polyurethane coating systems. A polyol-isocyanate coating solution was prepared by mixing OH-polyVESFA, isophorone diisocyanate trimer (Tolonate ^® IDT from the Perstorp

Group), dibutyl tin dilaurate (DBTDL), and toluene together using a FlackTek mixer at 3500 rpm for 3 minutes. An analogous reference coating was produced by replacing OH-polyVESFA with OH-SBO. Table 21 describes the compositions of the coatings produced.

Each liquid coating solution was cast into a template for producing free film specimens. The materials were cured by heating in an air oven at 80 °C overnight. Free films were characterized using dynamic mechanical thermal analysis.

Table 21. Compositions used to compare the difference between OH-polyVESFA and OH-SBO in polyurethane coating systems.

¹ OH-polyVESFA solution: OH-polyVESFA dissolved in toluene at 20.5 wt. % solid.

2 OH-SBO: Used as 100% solid.

³ Tolonate ^® IDT: Used as supplied (70 wt. % solid in butyl acetate).

⁴ DBTDL solution: 1 wt% DBTDL in toluene and butyl acetate mixture.

The viscoelastic properties of the polyurethanes were investigated by measuring storage modulus as a function of temperature. Table 22 lists the values of T _g , storage modulus, and crosslink density obtained from the data. The crosslink density (moles of crosslinks per unit volume) was calculated from the storage moduli in the rubbery plateau region. As shown in Figure 24, the storage modulus of cured films produced from OH-polyVESFA was significantly higher than the analogous films produced from OH-SBO. This result is due to the much higher number of hydroxyl groups per molecule for OH-polyVESFA as compared to OH-SBO, which translates to a higher crosslink density (see Table 22).

Table 22. Storage modulus and T _g data obtained from free films produced from OH-polyVESFA and OH-SBO in a polyurethane coating system.

Example XXI. Cured Films from Epoxy-functional Poly(VESFA-r-CHVE)

A series of radiation curable liquid coatings were prepared by mixing E-poly(VESFA-r- CHVE), 3-methyloxetane-3-yl)methanol (Oxetane 101 from Dow Chemical), tetrahydrofuran (THF), and 50 wt. % triarylsulfonium hexafluoroantimonate salt in propylene carbonate (UVI 6974 photoinitiator from Dow Chemical) together using a FlackTek mixer at 3500 rpm for 3 minutes. Table 23 describes the compositions of the coatings produced. Each liquid coating mixture was cast over one Teflon® coated glass, two cold rolled steel Q-panels, two aluminum Q-panels, and one glass panel using a square draw down bar (BYK Gardner) to produce wet films about 200 microns in thickness. Liquid coatings produced from

70/30CoP(50/50VESFA/CHVE)/Ox-LI were dried at room temperature for 2 hours to remove THF. The films were then cured by passing coated substrates once under a F300 UVA lamp from Fusion UV Systems (UVA light intensity ~ 1420 mW/cm ² as measured by UV Power Puck ^® II from EIT Inc.) equipped with a bench top conveyor belt set at a belt speed of 24 feet/min. Free films were characterized using dynamic mechanical thermal analysis (Q800 from TA

Instruments). The experiment was carried out from -50 °C to 120 °C using a heating rate of 5 °C/min., frequency of 1 Hz, and strain amplitude of 0.02%. The T _g was obtained from the peak maximum in the tan δ response. Cured coatings over metal substrates and the glass panel were characterized by MEK double rubs (ASTM D 5402-93), pencil hardness test (ASTM D 3363- 00), Konig pendulum hardness test (ASTM D 4366-95), impact resistance test (ASTM D 2794- 93), and mandrel bend test (ASTM D 522-90a). Table 24 lists T _g and storage modulus of the rubbery plateau region (at 90 °C) for films produced using one pass under the UVA lamp, while Table 25 lists various properties obtained from coated substrates and the use of the different ASTM methods.

Table 23. Coating compositions based on E-poly(VESFA-r-CHVE) copolymers.

Table 24. T _g and storage modulus of the rubbery plateau region (at 90 °C) for films produced from the coating compositions described in Table 23.

Table 25. The properties of cured films derived from the coating compositions described in

Table 23.

Example XXII. Block copolymers produced from VESFA and CHVE

Block copolymers of VESFA and CHVE monomers were produced by employing the carbocationic polymerization scheme shown in Figure 25. CHVE (TCI America, >95%), methyl acetate (MAc), and toluene were distilled over calcium hydride before use. VESFA was dried with magnesium sulfate before use. A di-functional initiator, 1 , 1 '-(butane- 1 ,4- diylbis(oxy))bis(ethane-l,l-diyl)diacetate (BDDA), was used to produce the A-B-A block copolymer in which the A blocks were derived from polymerization of CHVE and the B block was derived from polymerization of VESFA. The synthesis of BDDA, illustrated in Figure 26, was accomplished as follows: 7.09 g of glacial acetic acid and 6 g of 1 ,4-butanediol divinyl ether (Sigma-Aldrich, 98%) were combined in a 250 ml, 2-neck round bottom flask fitted with a reflux condenser and heated at 60 °C for 3 hours. Next, the reaction mixture was cooled down to room temperature and diluted with 100 ml of diethyl ether. The organic layer was washed thrice with deionized water (DI) and dried with anhydrous magnesium sulfate. The product was recovered by rotary evaporation of the diethyl ether and dried with anhydrous magnesium sulfate. Proton NMR was used to confirm the production of BDDA: 1H NMR (CDC1 ₃ ) 5 5.87 ppm (q, 2H, O- CH-O), 3.63, 3.46 ppm (m, 4H, 0-CH ₂ -C), 2.04 ppm (s, 6H, 0=C-CH ₃ ), 1.35 ppm (d, 6H, O-C- CH ₃ ). A poly(CHVE-b-VESFA-b-CHVE) block copolymer was synthesized as follows: To a dry 40 ml vial partially submerged in a heptanes bath at 0 °C inside a dry box, a 194 mg solution of BDDA in toluene (4.7 mg of BDDA in 189 mg of toluene) and 2.5 g of VESFA monomer ([VESFA] ₀ :[BDDA]o = 400: 1) were dissolved in 13.125 g of toluene and the solution chilled to 0 °C. The polymerization was started by the addition of 0.354 ml of ethylaluminum sesquichloride solution (25 wt. % in toluene) to the reaction mixture. After 25 hours of reaction, an aliquot (Composition- A) of known weight was removed and terminated with methanol to determine the percent conversion of VESFA, number average molecular weight, and molecular weight distribution. Next, the remaining polymerization mixture was divided into three dry, chilled 40 ml vials labeled copolymer- 1, copolymer-2, and copolymer-3. Pre-chilled toluene and methyl acetate (MAc) were added to each of the polymerization mixtures at the levels listed in Table 26 and mixed vigorously. Immediately after that, the second monomer, pre-chilled CHVE, was added and reactions were continued for 4 hours. The copolymers were precipitated from the reaction mixture by the addition of 10 ml of methanol and washed thrice with excess methanol. Poly VESFA and copolymer yields were determined gravimetrically after drying the purified polymer at 48 °C under vacuum overnight.

Table 26. Chemical composition of copolymer- 1, 2, and 3.

For comparison purposes, the homopolymer of CHVE (i.e. polyCHVE) was produced using carbocationic polymerization as follows: To a dry 500 ml two neck round bottom flask partially submerged in a heptanes bath at 0 °C inside a dry box, 108 mg of initiator (1- isobutoxyethyl acetate, IBEA), 17 g of CHVE monomer ([CHVE] ₀ :[IBEA] ₀ = 200: 1) that had been previously dried by distillation over calcium hydride, and 3.49 g of methyl acetate, MAc, ([CHVE] ₀ :[MAc]o =200:70) were dissolved in 89.25 g of dry toluene and the solution chilled to 0 °C. The polymerization was started by the addition of 1.844 ml of ethylaluminum

sesquichloride solution (25 wt. % in toluene) ([CHVE] ₀ : [Eti. ₅ AlCli.5] ₀ = 200 : 5) to the reaction mixture. The reaction was terminated after 5 minutes of reaction by the addition of 100 ml of chilled methanol which caused the polymer to precipitate. The polymer was washed with methanol thrice. Polymer yield, which was determined gravimetrically after drying the purified polymer at 60 °C under vacuum overnight, was found to be 97%. Polymer molecular weight was characterized using a high-throughput Symyx Rapid Gel Permeation Chromatography (GPC) equipped with an evaporative light scattering detector (PL-ELS 1000) and polystyrene standards. Table 27 shows the percentage of conversion, number average molecular weight (expressed relative to polystyrene standards), and molecular weight distribution for polyVESFA, polyCHVE, and copolymer- 1, 2, and 3.

Table 27. Monomer conversion, number average molecular weight (Mn), and molecular weight distribution (MWD) data obtained for polyVESFA, polyCHVE, and Copolymers 1, 2, and 3.

The thermal property of the copolymer-3 was determined using differential scanning calorimetry (Q1000 from TA Instruments) by first heating the sample from -120 °C to 70 °C at a heating rate of 10 °C/minute (1 ^st heat), cooling from 70 °C to -120 °C at a cooling rate of 10 °C/minute (cooling), and reheating from -120 °C to 120 °C at a heating rate 10 °C/minute (2 ^nd heat). The thermogram obtained from the 2 ^nd heat showed two glass transitions at -98 °C and 45 °C, and a very weak, diffuse melting transition with an enthalpy of melting of 5.8 J/g and a peak maximum at -32 °C. Example XXIII. Block copolymers produced from VECFA and CHVE

A-B-A triblock copolymers possessing A blocks derived from CHVE and a B block derived from VECFA were produced as follows: To a dry 40 ml vial partially submerged in a heptanes bath at 0 °C inside a dry box, a 194 mg solution of BDDA in toluene (4.7 mg of BDDA in 189 mg of toluene) and 2.5 g of VECFA dried over magnesium sulfate ([VECFA] ₀ :[BDDA] ₀ = 400: 1) were dissolved in 13.125 g of toluene and the solution chilled to 0 °C. The

polymerization was started by the addition of 0.354 ml of ethylaluminum sesquichloride solution (25 wt. % in toluene). After 25 hours of reaction, an aliquot of the reaction mixture

(Composition- A) was removed and terminated with methanol to determine the percent conversion of VECFA monomer, polymer number average molecular weight, and molecular weight distribution. Next, the remaining polymerization mixture was divided into two dry, chilled 40 ml vials labeled Copolymer- 1 and Copolymer-2. Pre-chilled methyl chloroacetate acetate (MCAc) was added to the Copolymer-2 mixture at the level indicated in Table 28 and mixed vigorously. Immediately after that, the second monomer, CHVE, was added to each of the two vials and reactions were continued for 17 hours. The copolymers were precipitated from the reaction mixtures by the addition of 10 ml of methanol and washed thrice with excess methanol. PolyVECFA and copolymers yields were determined gravimetrically after drying the purified polymers at 48 °C under vacuum overnight. Polymer molecular weight was characterized using a high-throughput Symyx Rapid Gel Permeation Chromatography equipped with an evaporative light scattering detector (PL-ELS 1000) and polystyrene standards. Table 29 lists the yield and molecular weight data obtained for the polymers. From Table 29, it can be seen that the addition of MCAc prior to the addition of CHVE significantly reduced the molecular weight distribution of the copolymer.

Table 28. Chemical composition data used for the production of Copolymers 1 and 2.

Table 29. Monomer conversion, number average molecular weight (Mn), and molecular weight distribution data (MWD) obtained for polyVECFA and Copolymers 1, 2, and 3.

The thermal properties of Copolymer-2 were determined using differential scanning calorimetry (Q1000 from TA Instruments) by first heating the sample from -120 °C to 70 °C at a heating rate of 10 °C/minute (1 ^st heat), cooling from 70 °C to -120 °C at a cooling rate of 10 °C/minute (cooling), and reheating from -120 °C to 120 °C at a heating rate 10 °C/minute (2 ^nd heat). The thermogram obtained from the 2 ^nd heat showed two glass transitions at -94.4 °C and 44.2 °C, and a very weak, diffuse melting transition with an enthalpy of melting of 1.27 J/g and a peak maximum at -34.9 °C.

Example XXIV. Polymerization of 4-vinyloxybutyl soyate (4-VOBS) Monomer

Homopolymers of 4-VOBS (poly((4-vinyloxy)butylsoyate)) were synthesized as follows: To a test tube dried by heating to 200 °C and partially submerged in a hexanes bath at 0 °C within a glove box, 4-VOBS, 1-isobutoxy ethyl acetate (IBEA), and dry toluene were combined in the amounts listed in Table X. Each polymerization was initiated by the addition of ethylaluminum sesquichloride solution (25 wt. % in toluene). Each polymerization was terminated after 17 hours by the addition of chilled methanol, which caused the polymer to precipitate. The polymer was isolated and washed multiple times with methanol using centrifugation. The purified polymer was collected as a viscous liquid after centrifuging at 4500 rpm at 21 °C for 5 minutes. Polymer yield was determined gravimetrically after drying the purified polymer at 48 °C under vacuum overnight. Polymer molecular weight was characterized using a high-throughput Symyx Rapid Gel Permeation Chromatography equipped with an evaporative light scattering detector (PL-ELS 1000) and polystyrene standards. Table 30 lists the monomer conversion and molecular weight data obtained for the two polymers. Table 30. Compositional information and characterization data obtained for the polymerization of 4-VOBS.

The thermal properties of polyVOBS-LMW (see Table 30) were determined using differential scanning calorimetry (Q 1000 from TA Instruments) by first heating the sample from -120 °C to 50 °C at a heating rate of 10 °C/minute (1 ^st heat), cooling from 50 °C to -120 °C at a cooling rate of 10 °C/minute (cooling), and reheating from -120 °C to 120 °C at a heating rate 10 °C/minute (2 ^nd heat). The thermogram obtained from the 2 ^nd heat showed a glass transition at - 92.3 °C and a very weak, diffuse melting transition with an enthalpy of melting of 1 1.3 J/g and a peak maximum at -29.8 °C.

The rheological properties of the two polyVOBS samples were characterized using an ARES Rheometer from TA Instruments. A cone and plate configuration was used to determine the viscosity. The shear rate was varied from 0.1 sec ^"1 to 1000 sec ^"1 while temperature was held constant at 25 °C. As shown in Figure 27, the low shear viscosity of polyVOBS-LMW was 1088 centipoise, while that of polyVOBS-HMW was 1887 centipoise. As expected, the viscosity of higher molecular weight sample, polyVOBS-HMW, exhibited higher shear sensitivity.

Example XXV. Copolymer of VESFA and Maleic Anhydride Produced Using

Free-Radical Polymerization

A copolymer derived from VESFA and maleic anhydride (MA) was synthesized as follows: To a dry 20 ml glass vial inside a glove box, 8.75 g (25 mmol) of VESFA, 2.45 g (25 mmol) of MA, 80 mg of azobisisobutyronitrile (Sigma- Aldrich), and 60 mg of 2- mercaptoethanol were combined and mixed. The resulting solution was heated to 60 °C under stirring until it became a very viscous material (3 h). The reaction mixture was cooled to room temperature before 50 ml of methanol was added to produce a white solid precipitate, which was isolated by filtration. To purify the polymer, it was dissolved in chloroform (20 ml) and the solution dripped into a large excess of rapidly stirring methanol. The purified polymer was isolated by filtration and dried under vacuum. Yield: 6.1 g (55%). 1H NMR (δ, ppm): 5.33 (bs, 3H), 4.14 (bs, 2H), 3.92 - 3.29 (m, 5H), 2.77 - 2.73 (m, 1.3H), 2.27 (b, 2.66H), 2.04 - 2.00 (m, 4H), 1.56 (bs, 2.3H), 1.29 - 1.24 (m, 18.4H), 0.88 (bs, 3H). GPC (M _n , 6532, PDI, 1.62).

The thermal properties of the copolymer produced were determined using differential scanning calorimetry (DSC Q1000 from TA Instruments). The sample size was 2.06 mg. The sample was first cooled from room temperature to -90 °C at a cooling rate 10 °C/min, heated from -90 °C to 120 °C at a heating rate 10 °C/min (1 ^st heating cycle), cooled down to -90 °C at cooling rate 10 °C/min, and reheated from -90 °C to 120 °C at a heating rate of 10 °C/min (2 ^nd heating cycle). The thermogram obtained on the 2 ^nd heating cycle displayed a single glass transition at 60 °C.

Synthesis of 2 -Hydroxy ethyl 1-Propenyl Ether

In a 1 L round bottom flask, 70g of potassium tert-butoxide and 300 mL of dimethyl sulfoxide were mixed together at room temperature. Then, 30 g of 2-allyloxyethanol was added using an addition funnel and the reaction temperature was set to 110 °C for 90 minutes. The mixture was cooled down to room temperature before adding 1L of DI water. The product was extracted with hexane and diethyl ether (1 : 1 volume ratio). To dry the solution, MgS04 was added to the mixture. After filtration of MgS04, the product was recovered by vacuum stripping of the solvents. The product was then purified by vacuum distillation at 60 °C and 15 mmHg pressure. Yield - 20g (67%). 1H NMR (400 MHz, CDC1 ₃ , TMS): δ (ppm) 5.95 (q, 1H, - OCH=CH-), 4.41 (m, 1H, -OCH=CH-), 3.82 (m, 2Η, -CH ₂ 0-), 3.75 (m, 2Η, HOCH ₂ -), 2.32 (t, 1Η, -OH). 1.56 (d, 3Η, -CH ₃ ). IR (neat, cm-1): 3371 (v _0H ), 3043 (v=c _H ), 2923, 2874 (V _CH2 ,CH ₃ ), 1670 (voc), 1106 (vc ). 13C NMR (100 MHz, CDC1 ₃ , TMS): δ (ppm) 145.5 (-OCH=),

101.8(=CH-), 73.2 (-CH ₂ 0-), 61.8 (HOCH ₂ -), 9.2 (-CH ₃ ).

Synthesis of ^' 2-(l -Propenyl)oxyethyl Soyate (POES)

POES was synthesized from 2-hydroxy ethyl 1-propenyl ether and soybean oil as follows:

0.42 g of KOH was dried in an oven for 30 minutes at 140 °C to remove moisture. Then, 15 g of soybean oil, 15 g of 2-hydroxyethyl 1-propenyl ether, and the dried KOH were mixed together in a two neck round bottom flask and stirred for 3hr at 70 °C. The reaction mixture was cooled down to room temperature and then transferred to a 250 ml separating funnel. 100 ml of n- hexane was added to mixture the product extracted into the organic layer. The organic layer was washed with acidic DI water (pH 3-3.5) for twice, followed by multiple washings with DI water, and finally with a brine solution. The organic layer was dried with MgS04 and the product isolated by vacuum stripping the volatiles. Yield: 13g (81%). 1H NMR (400 MHz, CDC1 ₃ , TMS): δ (ppm) 5.93 (dd, 1H, =CH-0-), 5.34 (m, 1.5Η, CH ₂ -CH=CH- CH ₂ ), 4.43 (q, 1H, CH ₃ - CH=), 4.24 (t, 2Η, =CH-O-CH ₂ -CH ₂ -)3.90 (t, 2H, =CH-0-CH ₂ -CH ₂ -), 2.76 (m, 1.5Η,

=CHCH ₂ CH=), 2.32 (t, 2H,-C=0CH2-). 2.03 ( m,4H, -CH ₂ CH ₂ CH=)1.57 (m, 5H, -CH3-CH=, - C=OCH ₂ CH ₂ -), 1.29 (m, 18Η, -CH ₂ CH ₂ CH ₂ -), 0.96-0.87 (m, 3H, -CHCH ₃ ). IR (neat, cm-1): 3008 (v=c. _H ), 2925, 2854 (V _CH2 ,CH ₃ ), 1741(VOO), 1669 (voc), 1112 (v _c _o). Synthesis of Poly (2-(l-Propenyl)oxyethyl Soyate) (polyPOES)

PolyPOES was synthesized as follows: First, POES was dried with MgS0 ₄ inside a glove box to remove trace amounts of moisture. All glassware used for the polymerization was baked at 200 °C. Using a dry 40 ml glass vial, 1.00 g of POES and 3.5 mg of initiator (1- isobutoxyethyl acetate (IBEA)) were dissolved in 6 mL of dry toluene and chilled to 0 °C inside a glove box. The polymerization was initiated by the addition of 300 mL of the coinitiator, ethylaluminum sesquichloride solution (25 wt% in toluene) ([M] ₀ :[Et ₃ Al ₂ Cl ₃ ] ₀ = 200:40). The reaction was terminated after 17.5 h by the addition of 6 mL of chilled methanol. Termination of the reaction by methanol caused precipitation of the polymer. The polymer was isolated and washed four times with methanol. The purified polymer was collected as a viscous liquid after drying under vacuum (5-7 mm of Hg) overnight. 1H NMR (400 MHz, CDC1 ₃ , TMS): δ (ppm) 5.36 (m, 1.5H, CH ₂ -CH=CH- C¾), 4.24 (m, 2Η, -CH-O-CH ₂ -CH ₂ -)3.90 (m, 3H, -CH-0-CH ₂ - CH2-, -OCH-(backbone)), 2.79 (m, 1.5Η, =CHCH ₂ CH=), 2.30 (m, 2H,-C=0CH2-). 2.03 (m, 4Η, -CH ₂ CH ₂ CH=), 1.9-1.57 (m, -C=OCH ₂ CH ₂ -, -CHCH ₂ CH-), 1.29 (m, 18H, -CH ₂ CH ₂ CH ₂ -), 0.96- 0.87 (m, 6H, -CH ₂ G¾, -CH3-CH-(backbone)). IR (neat, cm-1): 3008 (V= _C -H), 2925, 2854 (VCH ₂ ,CH ₃ ), 1740 (v _c =o), 1112 (v _C -o).

The thermal properties of the poly(POES) produced was determined using differential scanning calorimetry (DSC Q1000 from TA Instruments). The 6.2 mg specimen was first heated from room temp to 60 °C at a heating rate of 10°C /min (1st heat cycle), cooled from 60 to 130 °C at a cooling rate of 10 °C /min (cooling cycle), and reheated from 120 °C to 100 °C at a heating rate 10 °C /min (2nd heating cycle). The thermogram obtained from the 2 ^nd heating cycle displayed glass transition temperature at -86 °C and a small, diffuse melting endotherm at -27 °C.

The molecular weight and molecular weight distribution of the polymer were

characterized using gel permeation chromatography. The number average molecular weight expressed relative to polystyrene standard was 16,000 g/mole and the molecular weight distribution was 1.28.

Example XXVI. The Influence of the Addition of a Lewis Base (i.e. Methyl chloroacetate) on

Copolymerizations Involving VESFA

Homopolymers of VESFA, CHVE, and TEGEVE, and their random copolymers were produced as follows: Prior to use, VESFA and TEGEVE were dried with magnesium sulfate inside a glove box. CHVE, methyl chloroacetate (MCAc), and toluene were distilled over calcium hydride before use. Dried monomer, co-monomer, initiator (i.e. 1-isobutoxy ethyl acetate, IBEA), and MCAc were dissolved in dry toluene in a series of dry 40 ml vials and chilled to 0 °C. Polymerizations were initiated by the addition of ethylaluminum sesquichloride solution (25 wt. % in toluene). The reactions were terminated after 17 hours by the addition of chilled methanol, which, with the exception of polymer 5 and 9, caused the polymers to precipitate. All polymers except polymer-5 to polymer-9 were isolated and washed multiple times with methanol using centrifugation. The purified polymers were collected as viscous liquids after centrifuging at 4500 rpm at 21 °C for 5 minutes. Polymer-5 to polymer-9 were isolated after rotary evaporation of all volatiles at a temperature of 48 °C and a pressure of 5 - 7 mm of Hg for 1 hour. Polymer yields were determined gravimetrically after drying all polymers at 48 °C under vacuum (5 -7 mm of Hg) overnight. Polymer molecular weight was characterized using a high-throughput Symyx Rapid Gel Permeation Chromatography equipped with an evaporative light scattering detector (PL-ELS 1000) and polystyrene standards. Table 31 lists the compositions of the polymerization reaction mixtures produced.

Table 31. Composition of raw materials used to produce polymers and copolymers at a total polymerization time of 17 hours at 0 °C.

Monomer conversion, number average molecular weight relative to polystyrene standards (Mn), and molecular weight distribution data for the 11 polymerizations described in Table 31 are shown in Table 32. From the data shown in Table 32, it can be seen that copolymerization in the presence of MCAc resulted in narrower molecular weight distributions.

Table 32. Monomer conversion, number average molecular weight relative to

polystyrene standards (Mn), and molecular weight distribution data for the 11

polymerizations described in Table 31.

Example XXVII. Thermoset Coatings Based on PolyVESFA and an

Anhydride Curing Agent

An example of the production of an anhydride-cured film produced from E- polyVESFA is as follows: E-polyVESFA and l,8-diazabicyclo[5.4.0]undec-7-ene (BDU, Aldrich, 98%) were mixed with a FlackTek mixer using 3500 rpm for 30 seconds. Then, hexahydro-4-methylphthalic anhydride (HHMPA, Aldrich, 96%, mixture of cis and trans) was added and the mixture mixed using 3500 rpm for 1 minute. Table 33 describes the chemical compositions of the coatings produced. Each liquid coating mixture was cast over two cold rolled steel Q-panels, two aluminum Q-panels, and one glass panel using a square draw down bar (BYK Gardner) to produce wet films about 200 microns in thickness. The films were then cured by heating at 100 °C in an air oven for 12 hours. A reference coating based on epoxidized soybean oil (Vikoflex-7170 from Arkema) was produced by mixing the epoxidized soybean oil (ESO) with DBU followed by the addition of HHMPA using the FlackTek mixer and cured by heating at 100 °C in an air oven for 12 hours. Cured coatings over metal substrates and glass panels were characterized by MEK double rubs (ASTM D 5402-93), pencil hardness test (ASTM D 3363-00), Konig pendulum hardness test (ASTM D 4366-95), impact resistance test

(ASTM D 2794-93), and mandrel bend test (ASTM D 522-90a). The properties obtained for the cured materials are shown in Table 34. From Table 34, it can be seen that the use of E-polyVESFA provided enhanced hardness and chemical resistance.

Cured films over the glass substrates were peeled off carefully and the

viscoelastic properties of the free films were characterized using a TA800 dynamic mechanical thermal analyzer from TA Instruments. Temperature was ramped from 40 °C to 120 °C using a heating rate of 5 °C/min, strain rate of 0.02%, and frequency of 1 Hz. The viscoelastic properties obtained for the cured materials are shown in Table 35. The data shown in Table 35 show dramatic enhancements in moduli and Tg with the use of E- polyVESFA as opposed to ESO.

The rate of crosslinked network formation was characterized by a dynamic time sweep using an ARES Rheometer (TA Instruments). A liquid mixture (Table 33) was placed in between the two parallel plates and heated for 3.5 hours at a constant frequency of 10 rad/s, strain rate of 1%, and temperature of 100 °C. A 1/0.5 stoichiometry between the epoxy groups and anhydride groups was used. As shown in Figure 28, the coatings based on E-polyVESFA showed a sharp increase in shear modulus after 20 minutes of reaction and shear modulus increased from 5.5 KPa to 567 KPa over the period of 2 hours while the reference coating based on E-SBO showed no increase in modulus until 2 hours at 100 °C. These results indicate that E-polyVESFA develops a crosslinked network much faster than the analogous material based on E-SBO. Table 33. Chemical composition of coatings based on E-polyVESFA or ESO and cured using HHMPA.

Table 34. Properties of cured coatings described in Table 33.

Table 35. Thermal and viscoelastic properties of cured films.

Example XXVIII. The Influence of the Addition of a Lewis Base (i.e. Methyl Acetate) on

Block Copolymerizations Involving VESFA

An A-B-A triblock copolymer possessing A blocks derived from CHVE and a B block based on VESFA was synthesized as follows: The reaction was carried out in a dry 40 ml vial partially submerged in a heptanes bath at 0 °C inside a dry box. In the reaction vial, 194 mg of a solution of BDDA in toluene (4.7 mg of BDDA in 189 mg of toluene) and 2.5 g of VESFA monomer ([VESFA] ₀ :[BDDA] ₀ = 400: 1) were dissolved in 13.125 g of toluene and the solution chilled to 0 °C. The polymerization was started by the addition of 0.354 ml of ethylaluminum sesquichloride solution (25 wt. % in toluene) to the reaction mixture. After 25 hours of reaction, an aliquot (Composition-B) of known weight was terminated with methanol to determine the percent conversion of VESFA monomer, number average molecular weight, and molecular weight distribution of polyVESFA. Next, the remaining polymerization mixture was divided into two dry and previously chilled 40 ml vials labeled copolymer-4 and control polymer. Pre-chilled toluene and methyl acetate (MAc) were added to the copolymer-4 polymerization mixture and the control polymer polymerization mixture at the concentrations listed in Table 36 and mixed vigorously. Immediately after that, the second monomer, CHVE, was added to the copolymer-4 polymerization mixture and the reaction continued for 4 hours. For the Control polymer, no CHVE was added and the reaction continued for 4 hours.

The copolymer-4 and control polymer were precipitated from the reaction mixture by the addition of 10 ml methanol and washed thrice with excess methanol. PolyVESFA, copolymer-4, and control polymer yields were determined gravimetrically after drying the purified polymers at 48 °C under vacuum overnight. Table 37 lists the monomer conversion, number average molecular weight relative to polystyrene standards (Mn), and molecular weight distributions (MWDs) of the polymers. Table 36. Chemical composition of copolymer-4 and the control polymer.

Table 37. Monomer conversion, number average molecular weight relative to polystyrene standards (Mn), and molecular weight distributions (MWDs) of the polymers described.

Example XXIX. Properties of Copolymers Produced from VESFA and TEGEVE

The water solubility of the six different copolymers based on VESFA and TEGEVE was investigated using the thin film method. Following this method, various amounts of copolymer were dissolved in acetone solution of Nie Red dye (9- diethylamino-5-benzo[a]phenoxazinone) (3 mL, 0.2 mg/mL). The actual amount of polymer sample was varied in order to produce a series of resulting aqueous solutions of polymer with concentration range lxlO ^"5 - 0.2% w/w. The solvent was removed by rotary evaporation at 30 °C for 1 hour to obtain a solid dye/polymer matrix. Residual acetone remaining in the dye/polymer matrix was evaporated until constant weight of sample was reached. The resultant thin film was hydrated with Millipore water (20 mL). Temperature of Millipore water was kept at either 25 or 37 °C. To allow sufficient hydration, mixture was stirred at 500 rpm for 24 hours at 25 or 37 °C. Before examining solutions, all unincorporated dye crystals were removed by filtration through 0.45 and 0.2 μιη PTFE filters. The results showed that Copolymer 1 and Copolymer2 were essentially insoluble in water while the solubilities for Copolymer3, Copolymer4, Copolymer5, and

Copolymer6 were 0.01 , 0.30, 0.20, and 0.30, respectively. For Copolymer2, Copolymer3, Copolymer4, Copolymer5, and Copolymer6, surface tension measurements of aqueous solutions were measured by drop shape analysis on a pendant drop produced with a Contact Angle/Surface Tension Analyzer from First Ten Angstroms (FTA125). Measurements were carried out at room

temperature on polymer solutions of varying concentration (lxl 0 ^"5 - 0.2% w/w). All glassware was washed in a 1 N NaOH bath and thoroughly rinsed with acetone and Millipore water before use. Surface tensions at maximum solubility in water were determined to be 71.4, 61.2, 40.1, 39.5, and 39.2 mN/m for Copolymer2, Copolymer3, Copolymer4, Copolymer5, and Copolymer6, respectively. These results show that the copolymers possessing a TEGEVE content of 50 weight percent or higher were highly surface active.

For Copolymer4, Copolymer5, and Copolymer6, the critical micelle concentration (CMC) was measured using fluorescence spectroscopy. Each sample was prepared by adding the 20 pyrene solution (5x10 ^"4 mol/L) into an empty vial, evaporating the acetone for 2 h at room temperature, adding the copolymer solution (20 mL) and stirring the solution for at least 24 h. The final pyrene concentration in solution was 5x 10 ^"7 mol/L which is slightly below the pyrene saturation concentration in water at room temperature. For fluorescence measurements, the solution (ca. 3 mL) was placed in a 1.0 x 1.0 cm ² cell. All spectra were taken using a Fluoromax-3 Fluorescence Spectrometer (Jobin Yvon Horiba) with 90° geometry and a slit opening of 0.5 nm. For fluorescence excitation spectra, Xe _m = 390 nm was used. Spectra were recorded with an integration time of 0.5 nm/s. Figure 29 shows fluorescence intensity as a function of copolymer concentration. From the data, CMC for Copolymer4, Copolymer5, and Copolymer6 were determined to be 5xl0 ^"4 , 7xl0 ^"4 , and 3xl0 ^"4 wt./vol.%, respectively.

Example XXX. Unfilled Rubbers

Elastomers for vulcanized rubber compounds are very high molecular weight and, as a result, are very difficult to process without the addition of a "processing oil" to lower the viscosity and plasticize the polymer chains. Most processing oils are petroleum- based, relatively expensive, and some have been found to be toxic. As a result, the rubber industry has been investigating plant oils as a non-toxic, lower cost substitutes for conventional petroleum-based processing oils. Since many of the plant oil-based polyvinyl ethers described are liquids with very a low glass transition temperature (approximately -90 °C), it was of interest to evaluate their utility as a bio-based, polymeric processing oil for rubber compounds. Since these polyvinyl ethers possess a large number of double bonds per molecule, it was expected that the polymers would become part of the crosslinked network during vulcanization, which would eliminate migration of the polymeric oil to the surface of vulcanized articles. Eliminating migration of the processing oil to the vulcanized article surface is desirable, especially considering that, for some applications, the amount of processing oil (sometimes also referred to as an extender) may be equivalent or in excess of the amount of elastomer in the composition.

The following commercially available materials were used in examples XXX through XXXV:

A series of rubber compounds were produced by first blending SBR with a processing oil (i.e. PPO, SBO, P4VOBS) using a Prep-Mill® two roll mill from C. W. Brabender. The P4VOBS that was used possessed a number average molecular weight of 34,000 g/mole, expressed relative to polystyrene standards. Once the SBR and oil were thoroughly mixed StA, TBBS, S, and ZnO were added to the mixture using the two roll mill. Once these compounds were thoroughly mixed, the unvulcanized rubber compound was transferred to a hot press and vulcanized under a pressure of 2,000 Newtons using a cure temperature of 145 °C and cure time of 60 minutes. Table 38 describes the composition of the different rubber compounds produced.

Table 38. Composition of unfilled rubbers produced.

From the sheets of vulcanized rubber, ASTM D638 Type V test specimens were stamped out using a die cutter obtained from Qualitest. Stress - strain data were obtained from these test specimens using an Insight® Material Testing System from MTS. Measurements were made at ambient temperature using a crosshead speed of 20 mm/minute. Five specimens were tested for each rubber composition and the average and standard deviation for each property of interest determined. The data obtained are listed in Table 39 and shown graphically in Figures 30-34. At oil concentrations of 10 or 15 wt. %, the use of PPO or SBO showed no significant enhancements in tensile strength, modulus at 100% strain, modulus at 300% strain, and toughness compared to the vulcanized SBR (i.e. No Oil). In contrast, the use of P4VOBS as a processing oil significantly increased all of these properties. Figure 35 illustrates this result by comparing the properties of rubbers containing 15 weight percent processing oil.

Table 39. Mechanical properties determined for unfilled blends of SBR and the different processing oils. Each data point represents the average of five specimens along with the standard deviation.

Since the P4VOBS possesses over 100 double bonds per molecule, it was expected that the polymer molecules would be incorporated into the crosslinked network upon vulcanization. Incorporation of the processing oil into the crosslinked network can be expected to be beneficial since it prevents migration of the processing oil to the surface of the molded article and subsequent changes in rubber physical and mechanical properties. Figure 36 shows the weight of soluble material extracted from rubber compounds possessing 15 weight percent of the three different processing oils (i.e. PPO, SBO, and P4VOBS). The extraction was done using a Soxhlet extractor and toluene as the solvent. The extraction procedure consisted of cutting specimens into small (~3mm x 5mm x 5mm) pieces, weighing the sample, extracting in the Soxhlet extractor for 16 hours, drying the extracted samples in a vacuum oven at 60 °C for 16 hours, and weighing the extracted samples. As shown in Figure 36, the rubber compound containing P4VOBS as the processing aid had the lowest fraction of extractable materials, while the compound containing the conventional, petroleum-based processing oil (i.e. PPO) possessed the highest content of extractables. The extractable content of the rubber compound based on SBO was lower than the PPO-based compound, but higher than the P4VOBS-containing rubber compound.

Example XXXI. Carbon Black-Filled Rubbers

A series of CB-filled rubber compounds were produced by first blending SBR with a processing oil (i.e. PPO, SBO, P4VOBS) using a Prep-Mill® two roll mill from C. W. Brabender. The P4VOBS that was used possessed a number average molecular weight of 34,000 g/mole, expressed relative to polystyrene standards. Once the SBR and oil were thoroughly mixed, StA, TBBS, S, and ZnO were added to the mixture using the two roll mill. Once these compounds were thoroughly mixed, the CB was mixed in using the two roll mill. The unvulcanized rubber compound was transferred to a hot press and vulcanized under a pressure of 2,000 Newtons using a cure temperature of 145 °C and cure time of 60 minutes. Table 40 lists the composition of the different CB-filled rubber compounds produced. Table 40. Composition of the CB-filled rubbers produced.

From the sheets of vulcanized rubber, ASTM D638 Type V test specimens were stamped out using a die cutter obtained from Qualitest. Stress - strain data were obtained from these test specimens using an Insight® Material Testing System from MTS.

Measurements were made at ambient temperature using a crosshead speed of 20 mm/minute. Five specimens were tested for each rubber composition and the average and standard deviation for each property of interest determined. The data obtained are listed in Table 41. From the data listed in Table 41 , it can be seen that the use of P4VOBS provided higher tensile strength and stress at 100 and 300% elongation than the rubber compound based on SBO as the processing oil. In general, the use of P4VOBS as the processing oil provided mechanical properties that were more similar to the rubber compound based on the conventional processing oil, PPO. In contrast, the use of SBO as a renewable-based processing oil significantly reduced tensile strength and stiffness compared to PPO.

Table 41. Mechanical properties determined for CB-filled blends of SBR and the different processing oils. Each data point represents the average of five specimens along with the standard deviation.

10%PPO+CB 25.4+1.0 2.42+0.21 8.87±0.86 665±52 1,888±203

10%SBO+CB 19.7±0.5 1.58±0.01 4.80±0.05 810±17 1,741+97

10%P4VOBS+CB 24.7±0.3 2.94±0.03 10.16±0.06 618±7 1,772+44

Example XXXII. Processing Oil Blends in Unfilled Rubber Compounds

An experiment was conducted in which blends of PPO and P4VOBS or SBO and P4VOBS were used as the processing oil for unfilled rubber compounds. The molecular weight of the P4VOBS utilized was 34,000 g/mole as expressed relative to polystyrene standards. First, SBR with a processing oil (i.e. PPO, SBO, P4VOBS) or processing oil blend was mixed using a Prep-Mill® two roll mill from C. W. Brabender. Once the SBR and oil were thoroughly mixed, StA, TBBS, S, and ZnO were added to the mixture using the two roll mill. Once these compounds were thoroughly mixed, the unvulcanized rubber compound was transferred to a hot press and vulcanized under a pressure of 2,000 Newtons using a cure temperature of 145 °C and cure time of 60 minutes. Table 42 describes the compositions of the different rubber compounds produced. Table 42. A description of the compositions of rubber compounds based on binary blends of processing oils.

SBO/P4VOBS

3.75/1 1.25 85 3.75 1 1.25 2.4 1.4 1.0 0.8 SBO/P4VOBS

15P4VOBS 85 15.00 2.4 1.4 1.0 0.8

From the sheets of vulcanized rubber, ASTM D638 Type V test specimens were stamped out using a die cutter obtained from Qualitest.. Stress - strain data were obtained from these test specimens using an Insight® Material Testing System from MTS. Measurements were made at ambient temperature using a crosshead speed of 500 mm/minute. Five specimens were tested for each rubber composition and the average and standard deviation for each property of interest determined. The data obtained are listed in Table 43. In general, displacing some of the PPO or SBO with P4VOBS increased tensile strength, stress at 100% and 300% elongation, and toughness.

Table 43. The mechanical properties of rubber compounds based on blends of processing oils.

SBO/P4VOBS

15P4VOBS 3.4±0.5 0.840±0.005 1.655±0.021 729±87 347±71

Example XXXIII. Processing Oil Blends in CB-Filled Rubber Compounds An experiment was conducted in which blends of PPO and P4VOBS or SBO and

P4VOBS were used as the processing oil for CB-filled rubber compounds. The molecular weight of the P4VOBS utilized was 34,000 g/mole, as expressed relative to polystyrene standards. First, SBR with a processing oil (i.e. PPO, SBO, P4VOBS) or processing oil blend was mixed using a Prep-Mill® two roll mill from C. W. Brabender. Once the SBR and oil were thoroughly mixed, StA, TBBS, S, and ZnO were added to the mixture using the two roll mill. Once these compounds were thoroughly mixed, CB was added and thoroughly mixed using the two roll mill. The unvulcanized rubber compound was the transferred to a hot press and vulcanized under a pressure of 2,000 Newtons using a cure temperature of 145 °C and cure time of 60 minutes. Table 44 describes the compositions of the different rubber compounds produced.

Table 44. A description of the compositions of rubber compounds based on binary blends of processing oils. In addition to the components listed in the table, each composition also contained 2.4 parts of ZnO, 1.4 parts S, 1.0 parts TBBS, and 0.8 parts StA.

From the sheets of vulcanized rubber, ASTM D638 Type V test specimens were stamped out using a die cutter obtained from Qualitest. Stress - strain data were obtained from these test specimens using an Insight® Material Testing System from MTS.

Measurements were made at ambient temperature using a crosshead speed of 500 mm/minute. Five specimens were tested for each rubber composition and the average and standard deviation for each property of interest determined. The mechanical properties of the rubber compounds based on blends of PPO and P4VOBS or SBO and P4VOBS are shown in Table 45. In general, displacing some of the PPO or SBO with P4VOBS increased stress at 100% and 300% elongation, but decreased elongation at break and toughness.

Table 45. The mechanical properties of CB-filled rubber compounds based on blends of processing oils.

Example XXXIV. Influence of P4VOBS Molecular Weight in

Unfilled Rubber Compounds

For Examples 1 through 4, the P4VOBS utilized possessed a number-averagi molecular weight, as expressed relative to polystyrene standards, of 34,000 g/mole. Since the molecular weight of P4VOBS can be easily tailored, which affects the viscosity of the polymer, an experiment was conducted in which the effect of P4VOBS molecular weight on the mechanical properties of unfilled rubber compounds was determined. P4VOBS molecular weight was easily varied by adjusting the ratio of 4-VOBS to the initiator (i.e. cationogen). The three different P4VOBS samples produced possessed number average molecular weights of 5,000 g/mole, 12,000 g/mole, and 34,000 g/mole, as expressed relative to polystyrene standards. The viscosity of these three polymers was measured using an ARES Rheometer from TA Instruments operating in steady shear mode at a temperature of 23 °C. The viscosity of the P4VOBS samples at a shear rate of 10 s ^"1 are listed in Table 46 along with values for SBO and PPO.

Table 46. Viscosity of P4VOBS polymers produced.

Unfilled rubber compounds were produced by mixing SBR with a processing oil (i.e. PPO, SBO, P4VOBS) using a Prep-Mill® two roll mill from C. W. Brabender. Once the SBR and oil were thoroughly mixed, StA, TBBS, S, and ZnO were added to the mixture using the two roll mill. Once these compounds were thoroughly mixed, the unvulcanized rubber compound was transferred to a hot press and vulcanized under a pressure of 2,000 Newtons using a cure temperature of 145 °C and cure time of 60 minutes. Table 47 describes the compositions of the different rubber compounds produced. Table 47. A description of the compositions for rubber compounds based P4VOBS polymers of varying molecular weight. In addition to the components listed in the table, each composition also contained 2.4 parts of ZnO, 1.4 parts S, 1.0 parts TBBS, and 0.8 parts StA.

From the sheets of vulcanized rubber, ASTM D638 Type V test specimens were stamped out using a die cutter obtained from Qualitest. Stress - strain data were obtained from these test specimens using an Insight® Material Testing System from MTS.

Measurements were made at ambient temperature using a crosshead speed of 500 mm/minute. Five specimens were tested for each rubber composition and the average and standard deviation for each property of interest determined. Table 48 provides the data obtained. As shown in Table 48, increasing P4VOBS molecular weight increases all of the mechanical properties tested. Table 48. The mechanical properties of unfilled rubber compounds based P4VOBS of varying molecular weight as the processing oil.

Example XXXV. Influence of P4VOBS Molecular Weight in

CB-Filled Rubber Compounds

For Examples 1 through 4, the P4VOBS utilized possessed a number-average molecular weight, as expressed relative to polystyrene standards, of 34,000 g/mole.

Since the molecular weight of P4VOBS can be easily tailored, which affects the viscosity of the polymer, an experiment was conducted in which the effect of P4VOBS molecular weight on the mechanical properties of CB-filled rubber compounds was determined. P4VOBS molecular weight was easily varied by adjusting the ratio of 4-VOBS to the initiator (i.e. cationogen). The three different P4VOBS samples produced possessed number average molecular weights of 5,000 g/mole, 12,000 g/mole, and 34,000 g/mole, as expressed relative to polystyrene standards. For the production of the rubber compounds, SBR was mixed with a processing oil (i.e. PPO, SBO, P4VOBS) using a Prep-Mill® two roll mill from C. W. Brabender. Once the SBR and oil were thoroughly mixed, StA, TBBS, S, and ZnO were added to the mixture using the two roll mill. Once these compounds were thoroughly mixed, CB was added and thoroughly mixed using the two roll mill. The unvulcanized rubber compound was the transferred to a hot press and vulcanized under a pressure of 2,000 Newtons using a cure temperature of 145 °C and cure time of 60 minutes. Table 49 describes the compositions of the different rubber compounds produced.

Table 49. A description of the compositions for rubber compounds based P4VOBS polymers of varying molecular weight. In addition to the components listed in the table, each composition also contained 2.4 parts of ZnO, 1.4 parts S, 1.0 parts TBBS, and 0.8 parts StA.

10 5K P4VOBS+CB 5,000 90 — - 15 50

10 12K 12,000 90 15 50 P4VOBS+CB

10 34K 34,000 90 15 50 P4VOBS+CB

From the sheets of vulcanized rubber, ASTM D638 Type V test specimens were stamped out using a die cutter obtained from Qualitest. Stress - strain data were obtained from these test specimens using an Insight® Material Testing System from MTS.

Measurements were made at ambient temperature using a crosshead speed of 500 mm/minute. Five specimens were tested for each rubber composition and the average and standard deviation for each property of interest determined. Table 50 provides the data obtained. Table 50. The mechanical properties of CB-filled rubber compounds based P4VOBS of varying molecular weight as the processing oil.

Additional References:

Eckey et al, J. Am. Oil Chemist's Soc, 32(4):185 (1955)

Teeter et al, J. Am. Oil Chemist's Soc, 40(4): 143-156 (1963)

US Pat No. 2,692,256 (Bauer et al, 1951)

Brekke et al, J. Am. Oil Chemist's Soc, 37(11):568-570 (1963)

Dufek et al, J. Am. Oil Chemist's Soc, 37:37-40 (1960)

Teeter et al, Ind. Eng. Chem., 5o(l l): 1703-1704 (1958)

Teeter et al, J. Am. Oil Chemist's Soc, 33:399-404 (1956)

Schneider et al, J. Am. Oil Chemist's Soc, 34(5):244-247 (1957)

Gast et al, J. Org. Chem., 42:160-165 (1958)

Gast et al, J. Am. Oil Chemist's Soc, 37:78-80 (1959)

Dufek et al, J. Am. Oil Chemist's Soc, 39:238-241 (1961)

Schneider et al, J. Am. Oil Chemist's Soc, 39:241-244 (1961)

The complete disclosures of all patents, patent applications including provisional patent applications, and publications, and electronically available material cited herein are incorporated by reference. The foregoing detailed description and examples have been provided for clarity of understanding only. No unnecessary limitations are to be understood therefrom. The invention is not limited to the exact details shown and described; many variations will be apparent to one skilled in the art and are intended to be included within the invention defined by the claims.