FIELD OF THE INVENTION

The present invention relates to a novel class of impact modifiers which can improve the impact strength of polya ides with little adverse affect on the flexural modulus of the polyamide.

BACKGROUND OF THE INVENTION

Toughened thermoplastic polyamide composi¬ tions are known. See for example, U.S. Patent 4,174,358 which discloses a polyamide matrix and at least one other phase containing particles ranging from 0.01 to 10 microns of at least one specified polymer.

U.S. Patent 4,350,794 discloses a polyamide composition by melt blending of a polyamide resin and a halobutyl composition.

There is still a need to improve the impact strength of polyamide compositions, without substantial loss of the high flexural modulus of the polyamide.

It has now been found that the incorporation of certain polymer blends in polyamide compositions will produce toughened polyamide compositions having improved impact strength without substantial loss of the high flexural modulus of the polyamide.

SUMMARY OF THE INVENTION

In accordance with the present invention there is provided a polymer blend useful as an impact modifier for polyamide compositions comprising:

(a) a halogen-containing copolymer of a C4 to C7 isomonoolefin and a para-alkylstyrene; and

(b) a polyolefin component comprising an elastomeric polyolefin, a crystalline polyolefin or mixture thereof.

DETAILED DESCRIPTION OF THE INVENTION

The Copolymer Component

Suitable copolymers of a C4 to C7 isomonoolefin and an alkylstyrene which may be a mono or polyalkylstyrene. For elastomeric copolymer products, the alkylstyrene moiety may range from about 0.5 to about 20 weight percent preferably from about 1 to about 20 weight percent and most preferably about 2 to about 20 weight percent of the copolymer. The preferred copolymers are copolymers of a C4 to C7 isomonoolefin and a para-alkylstyrene. The copolymers are described in European patent application 89305395.5 filed on May 26, 1989, (Publication No. 0344021 published November 29, 1989).

The copolymers have a substantially homogeneous compositional distribution and include the para-alkylstyrene moiety represented by the formula:

in which X is halogen (preferably bromine) or hydrogen, and in which R and R ¹ are independently selected from the group consisting hydrogen, alkyl preferably having from 1 to 5 carbon atoms, primary haloalkyl, secondary haloalkyl having from 1 to 5 carbon atoms and mixtures thereof. The preferred isomonoolefin is isobutylene. The preferred para-alkylstyrene comprises para- methylstyrene.

Suitable copolymers of an isomonoolefin and a para-alkylstyrene include copolymers having a number average molecular weight (M _n ) of at least about 25,000, preferably at least about 30,000, and most preferably about 100,000. The copolymers, preferably, also have a ratio of weight average molecular weight (M _w ) to number average molecular weight (M _n ) of less than about 6, preferably less than about 4, more preferably less than about 2.5, most preferably less than about 2.0.

The broininated copolymer of the isomonoolefin and para-alkylstyrene obtained by the polymerization conditions now permit one to produce copolymers which comprise the direct reaction product (that is, in their as-polymerized form) , and which have unexpectedly homogeneous uniform compositional distributions. Thus

by utilizing the polymerization set forth herein, the copolymers suitable for the practice of the invention can be produced. These copolymers, as determined by gel permeation chromatography (GPC) demonstrate narrow molecular weight distributions and substantially homogeneous compositional distributions, or compositional uniformity over the entire range of the compositions thereof. At least about 95 weight percent of the copolymer product has a para-alkylstyrene content within about 10 weight percent, and preferably within about 7 weight percent, of the average para- alkylstyrene content for the overall composition, and preferably at least 97 weight percent of the copolymer product has a para-alkylstyrene content within about 10 weight percent and preferably about 7 weight percent, of the average para-alkylstyrene content for the overall composition. That is, with the specified copolymers, as between any selected molecular weight fraction the percentage of para-alkylstyrene therein, or the ratio of para-alkylstyrene to isoolefin, will be substantially the same.

In addition, since the relative reactivity of para-alkylstyrene with isoolefin such as isobutylene is close to one, the intercompositional distribution of these polymers will also be substantially homogeneous. That is, these copolymers are essentially random copolymers, and in any particular polymer chain the para-alkylstyrene to isoolefin, will be essentially randomly distributed throughout that chain.

Suitable halogen-containing copolymers of a C4 to C ₇ isomonoolefin and a para-alkylstyrene useful in the blends of this invention are the halogenated copolymers corresponding to the previously described isomonoolefin-alkylstyrene copolymers which may be obtained by halogenating the previously described

copolymers. The halogen content of the copolymer may range from above zero to about 7.5 weight percent, preferably from about 0.1 to about 7.5 weight percent.

The preferred halogen-containing copolymers useful in the practice of this invention have a substantially homogeneous compositional distribution and include the para-alkylstyrene moiety represented by the formula:

in which R and R ¹ are independently selected from the group consisting of hydrogen, alkyl preferably having from 1 to 5 carbon atoms, primary haloalkyl, secondary haloalkyl preferably having from 1 to 5 carbon atoms, and mixtures thereof and X is selected from the group consisting of bromine, chlorine and mixtures thereof, such as those disclosed in European patent application 89305395.9 filed May 26, 1989 (Publication No. 0344021 published November 29, 1989). Preferably, the halogen is bromine. The method of producing the copolymers and the halogenated derivatives are known as disclosed in EPA Publication No. 03 44021.

The Elastomeric Polyolefin

The elastomer component of the present invention can be selected form the group consisting of copolymers of ethylene and a higher alpha olefin and terpolymers of ethylene, a higher alpha olefin and at least one non-conjugated diene.

Suitable copolymers useful in the practice of the invention include random copolymers of ethylene and at least one higher alpha olefin. The term "higher alpha olefin" is used herein to denote an alpha olefin having a higher molecular weight than ethylene. The alpha olefin may be a C ₃ to C^s alpha olefin, such as propylene, l-butene, 1-pentene, l-hexene, 1-octene, 1- dodecene, and mixtures thereof. Preferably, the alpha olefin is propylene. The elastomeric monoolefin copolymers useful in this invention may suitably comprise from about 20 to about 90 weight percent ethylene, preferably from about 30 to about 85 weight percent ethylene. The elastomeric monoolefin copolymer will generally have an average molecular weight (M _w ) in the range of about 10,000 to about 1,000,000 or higher, typically from about 15,000 to about 500,000 and be substantially amorphous. By "substantially amorphous with reference to the monoolefin copolymer is intended herein a degree of crystallinity of less than about 26%, preferably less than about 15%, as measured by conventional test methods. The preferred elastomeric monoolefin copolymer is an ethylεne-propylene copolymer rubber, herein designated EPM. Processes for producing such elastomeric monoolefin copolymers are well known and form no part of this invention. EPM elastomers are commercially available.

The terpolymers useful in the practice of the invention include terpolymers of ethylene, at least one higher alpha olefin, and at least one nonconjugated diene. The terpolymer is generally substantially amorphous and can have a substantially random arrangement of at least the ethylene and the higher alpha olefin monomers.

The terpolymer will generally have a weight average molecular weight (M _w ) in the range between about 10,000 and 1,000,000 or higher, typically between about 15,000 and 500,000, and more typically between about 20,000 and 350,000.

Typically, the terpolymer is "substantially amorphous," and when that term is used to define the terpolymer, it is to be taken to mean that the terpolymer has a degree of crystallinity less than about 25%, preferably less than about 15 %, and more preferably less than about 10%, as measured by means well known in the art.

The terpolymer useful in the practice of the invention may comprise from about 20 to 90 weight percent ethylene, preferably about 30 to 85 weight percent ethylene, and even more preferably about 35 to

80 weight percent ethylene.

The higher alpha olefins suitable for use in the preparation of the terpolymer are preferably C ₃ -C ₁₆ alpha-olefins. Illustrative non-limiting example of such alpha-olefins are propylene, l-butene, 1-pentene, 1-hexene, 1-octene, and 1-dodecene. The alpha olefin content of the terpolymer is generally from about 10 to about 80 weight percent, preferably from about 20 to about 70 weight percent. The preferred alpha-olefin is propylene.

The non-conjugated diene suitable for use in the preparation of the terpolymer include dienes having from 6 to 15 carbon atoms. Such diene monomers are selected from polymerizable dienes. Representative examples of suitable non-conjugated dienes that may be used to prepare the terpolymer include:

a. Straight chain acyclic dienes such as: 1,4 hexadiene; l,5-heptadiene;l,6-octadiene.

b. Branched chain acyclic dienes such as: 5- methyl-1,4-hexadiene; 3,7-dimethyl 1 ,6- octadiene, and 3,7-dimethyl 1,7-octadiene.

c. Single ring alicyclic dienes such as: 4- vinylcyclohenene; 1-allyl, 4- isopropylidene cyclohexane; 3 allyl-cyclopentene; 4-allyl cyclohexane; and l-isopropenyl-4-butenyl cyc1ohexane.

d. Multi ring alicyclic fused and bridged ring dienes such as: dicyclopentadiene; alkenyl, alkylidene, cycloalkenyl and cycloalkylidene norbornenes such as: 5-methylene-2-nor- bornene; 5-methylene-6-methyl-2-norbornene; 5-methylene-6,6-dimethyl-2-norbornene; 5- propenyl-2-norbornene; 5-(3-cyclopentenyl)-2- norbornene; 5-ethylidene-2-norbornene; and 5- cyclohexylidene-norbornene, etc.

The preferred dienes are selected from the group consisting of 1,4-hexadiene; dicyclopentadiene; 5-ethylidene-2-norbornene; 5-methylene-2-norbornene; and mixtures thereof.

The total diene monomer content in the terpolymer may suitably range from about 0.1 to about

15 weight percent, preferably 0.5 to about 12 weight percent, and most preferably about 1.0 to about 6.0 weight percent.

Preparations of terpolymers of ethylene, a higher alpha olefin and a non-conjugated diene of the type described above are well known in the art and form no part of this invention. The preferred terpolymers for the practice of the invention are terpolymers of ethylene, propylene and a non-conjugated diene (EPDM) . Such terpolymers are commercially available.

The Crvstallizable Polyolefin

As discussed above, the impact modifier of the invention may also contain a crystallizable polyolefin component. This is particularly true where the impact modifier is to be pelletized before it is blended with the polyamide.

By crystallizable polyolefin is meant one which combines more than 30% crystallinity at ambient temperature as measured by conventional methods, such as X-ray diffraction or thermal analyses. Preferably >50% crystallinity; most preferably >70% crystallinity. Non-limiting example of such polymers includ high density polyethylene, polypropylene and ethylene copolymer resin.

The term "ethylene copolymer resin" is used herein to denote copolymers of ethylene and vinyl acetate, copolymers of ethylene and alpha, beta monoethylenically unsaturated monocarboxylic acid, and

copolymers of ethylene and an alkyl ester of an alpha, beta monoethylenically unsaturated carboxylic acid.

The term "polypropylene", herein also designated "PP", includes homopolymers of propylene as well as reactor copolymers of polypropylene (RCPP) which may contain from 1 to about 20 weight percent ethylene or an alpha olefin comonomer of 4 to 16 carbon atoms. The polypropylene may be highly crystalline isotactic or syndiotactic polypropylene. The density of the PP or RCPP may range from about 0.80 to about 0.92 g/cc, typically from about 0.89 to about 0.91 g/cc.

The term "High Density Polyethylene" (HDPE) refers to polyethylene polymers having a density of about 0.94 to about 0.97 g/cc. High density polyethylene is commercially available. Typically, HDPE has a relatively broad molecular weight distribution, such that its ratio of weight average molecular weight to number average molecular weight ranges from about 20 to about 40.

As discussed above the impact modifiers are designed to improve the impact strength of polyamide compositions. Thermoplastic polyamide compositions which can be modified by the impact modifiers of the present invention comprise crystalline or resinous, high molecular weight solid polymers including copolymers and terpolymers having recurring polyamide units within the polymer chain. Polyamides may be prepared by polymerization of one or more epsilon lactams such as caprolactam, pyrrolidone, lauryllactam and aminoundecanoic lactam, or a ino acid, or by condensation of dibasic acids and diamines. Both fiber forming and molding grade nylons are suitable.

Examples of such polyamides are polycaprolactam (nylon-

6) , polylaurylactam (nylon 12) , polyhexamethyl- eneadipamide (nylon 6,6), polyhexamethlene-azelamide (nylon 6,9), polyhexamethylenesebacamide (nylon 6,10), polyhexamethyleneisophthalamide (nylon 6,IP) and the condensation product of 11-aminoundecanoic acid (nylon- 11) ; partially aromatic polyamide made by polycondensation of meta xylene diamine and adipic acid such as the polyamides having the structural formula:

// H(NH-CH2~ CH2-NHCO-C4H8-COO) _n -H

Furthermore, the polyamides may be reinforced, for example, by glass fibers or mineral fillers or mixtures thereof. Pigments, such as carbon black or iron oxide may also be added. Additional examples of polyamides are described in Kirk-Othmer, Encyclopedia of Chemical Technology, v. 10, page 919, and Encyclopedia of Polymer Science and Technology, Vol. 10, pages 392-414. Commercially available thermoplastic polyamides may be advantageously used in the practice of this invention, especially those having a softening point or melting point between 160" to 215 ° .

Preparation of the Impact Modifier

The impact modifiers of the invention are prepared by blending together the copolymer, elastomer, and an optional polyolefin in a high shear mixer such as a two roll mill, or a banbury mixer to form a masterbatch. In the case where the optional polyolefin was present, high shear mixing needs to be carried out

above the melting point of the polyolefin, to flux the polyolefin. Alternatively, the copolymer, elastomer, and optional polyolefin can be used as a dry blend, if subsequent melt blending with polyamide is carried out on a compounder with good mixing provisions.

The modifiers of the invention may comprise between 85 and 32.5 weight percent copolymer and 15 and 65.5 weight percent elastomer, preferably about 75 to 40 weight percent copolymer and 25 to 60 weight percent elastomer, most preferably 65 to 30 weight percent copolymer and 35 to 70 weight percent elastomer. Where an optional polyolefin is employed, the relative amount of the three components may range from 80 to about 32.5 weight percent copolymer, 47.5 to about 20 elastomer and 20 to 5 weight percent polyolefin, preferably 65 to 32.5 weight percent copolymer, 62.5 to 30 weight percent elastomer and 15 to about 5 weight percent polyolefin.

The use of a crystalline polyolefin component is particularly preferred where the impact modifier is to be pelletized. It has been found that the use of certain amount of crystalline polyolefin in the modifier blend either alone or blended with an elastomeric polyolefin allows the modifier to be pelletized without significant loss of impact modification. Pelletization allows for easier handling by the user of the modifier and makes the blending with polyamide easier and more economical. Thus the desired amount of crystalline polyolefin should be sufficient to allow the modifier to be pelletized with out detracting form the performance of the resulting impact modifier.

EXAMPLES

The impact modifiers used in the following examples were prepared by blending together the elastomeric polyolefin, the crystallizable polyolefin or polyolefin blend with the copolymer in a Model 6VF350 6 inch (15.24 cm) two-roll mill. Where the crystallizable polyolefin was present, the rolls were steam heated to about 170"C to flux the polyolefin.

In the following examples, the styrene content and bromine content of the copolymer used in the blends was varied to demonstrate that the principles of this invention are applicable over a broad set of parameters. Table I below sets forth the composition of the different copolymers used. The tables associated with the examples sets forth which of the copolymers was used for the particular masterbatch.

The abbreviations and/or trademakrs used in the following examples are shown in Table II. The test methods used to measure the properties are shown in Table III.

EXAMPLE I

A series of masterbatches of the impact modifiers of the invention were prepared for blending with polyamide-6. The first four masterbatches were prepared from blends of the copolymer, elastomer (EPDM, Vistalon® 2505 manufactured by the Exxon Chemical Company) and polyolefin (HDPE, Escorene® HD 6705.39 manufactured by the Exxon Chemical Company) and were designated compositions A, B, C, and D. The ratios of copolymer to elastomer to polyolefin were 32.5/55.0/12.5; 43.75/43.75/12.5; 62.5/25/12.5; and

50/25/25 respectively. The HDPE content of each of these compositions was sufficient to permit the compositions to be pelletized.

In addition to the three component blends, a series of two component masterbatches were prepared. Compositions E and F were prepared by blending the copolymer with EPDM at ratios of 50/50 and 75/25 copolymer to elastomer respectively. A third two component blend, Composition G, was prepared with a 75/25 mixture of copolymer and HDPE blend. Compositions E and F were not pelletizable whereas composition G was.

Each of the masterbatches was then granulated in approximately 3.2 mm by 3.2 mm granules. A small amount of polyamide powder was introduced during the granulation of compositions E and F as a dusting agent to prevent agglomeration. After granulation, the masterbatches were then dried in a dehumidified oven at 140 ^β F (60"C) for four hours before compounding. The composition of the masterbatches can be found in Table IV.

Masterbatches A through G were then melt blended in polyamide-6 at a 70/30 polyamide/masterbatch weight ratio with the exception of Masterbatch E with was blended into the polyamide at 75/25 ratio. The melt blending was carried out by first drying pellets of polyamide-6 (PA-6, Capron® 8209F, manufactured by Allied Signal) in a dehumidified oven at 140°F (60 ^β C) for four hours. The polyamide and the masterbatches were then melt blended together in a 0.8 inch (20 mm) Welding Engineers counter-rotating twin screw extruder fitted with a strand die at the extruder exit. The extruder strands were then cooled in a water bath before being reduced by a pelletizer into approximately

3.2 mm by 3.2 mm pellets. Before being introduced into the extruder, each masterbatch was pre-dusted with 0.5 weight percent of a grafting agent catalyst, zinc oxide, per hundred part of copolymer. The catalyst helps promote the chemical reaction between the copolymer and the polyamide during compounding. All samples were dried under the same conditions set forth above for at least 4 hours to remove surface moisture prior to molding the samples into various test specimens on a 15 ton Boy injection molding machine.

Table V shows the composition of the various blends prepared in this example.

The blends were then injection molded into various ASTM test specimens for tensile, flexural, and notched Izod impact testings. These specimens were then subjected to a series of tests listed in Table III and the results of the tests are found in table V. In the table, Masterbatches A through G were used to manufacture compositions L through R respectively.

For comparative purposes, a series of specimens were prepared from either polyamide alone, polyamide blended with elastomer or polyolefin alone or polyamide blended with an impact modifier comprising a blend of elastomer and polyolefin.

In Table V, composition H is a specimen prepared from polyamide-6 (Capron® 8209F) alone;

Composition I is a 30/70 blend of elastomer (EPDM,

Vistalon® 2504) and polyamide-6 (Capron® 8109F) ;

Composition J is a 30/70 blend of polyolefin (HDPE,

Escorene® HD 6705.39) and polyamide-6 (Capron® 8209F) ; and Composition K is a 15/15/70 blend of polyolefin

(HDPE, Escorene® HD6705.39), elastomer (EPDM, Vistalon®

2504) and polyamide-6 (Capron® 8209F) .

All of the comparative compositions were formed into injection molded specimens and subjected to the test listed in Table III. The results of the tests are recorded in Table V.

As seen in Table V, at room temperature, polyamide-6 has a notched Izod value of 1. As a rule, room temperature notched Izod values of between 10 to 20 are considered superior notched Izod values. The comparative data shows that the use of the elastomer component or polyolefin component, either alone or blended with each other, did not result in a significant improvement in room temperature notched Izod values. The largest value achieved was about 2, whereas impact modifiers of the invention improved the notched Izod value to 18 to 23 at room temperature.

Compositions M, N, O, P, Q and R exhibited excellent notched Izod impact values from room temperalture down to about -10 ^β C. At about -20*C, blends having an impact modifier containing about 25 weight percent or more of the crystallizable polyolefin such as compositions 0 and R, exhibited notched Izod impact values of less than 5.

As can be seen from the data for composition L, the copolymer level is important to ensure good low temperature impact resistance. While composition L with only 32.5% copolymer in the masterbatch shows good room temmperature performance, the low temperature value is well below the other higher copolymer containing compositions.

With respect to stiffness, here the level of elastomer appears to be critical. Compositions L, M, N, 0, Q and R all show excellent stiffness retention in

that all blends show more than 200,000 psi (1379 MPa) in flexural modulus. Composition P, however, did show some degradation in stiffness in that it exhibited a flexural modulus of only 155,000 psi (1069 MPa). This deficit may be remedied by the addition of polyolefin to the impact modifier. As seen in Composition L which contains a greater amount of elastomer than Composition P, the flexural modulus is still greater than 200,000 psi (1379 MPa) . This appears to be due to the presence of HDPE which tends to enhance stiffness.

Composition S in Table V, is a specimen made from a 30/70 blend of copolymer and polyamide-6 (Capron® 8209F) . Comparison of the data for Composition S with that for Compositions N and Q reveals that it is possible to replace a substantial portion of the more expensive copolymer with a blend of relatively inexpensive HDPE and EPDM and maintain the same notched impact strength and stiffness. Moreover, the presence of HDPE permits the impact modifier to be pelletized which makes handling and processing the impact modifiers easier and less costly.

EXAMPLE II

In Table V, a second series of masterbatches were prepared for blending with polyamide-6,6. Two of these master batches, composition T and U, were two component blends of the copolymer and elastomer (EPDM, Vistalon® 2504) . The copolymer/elastomer ratios for the blends were 50/50 and 40/60 respectively. The compositions were not pelletizable.

In addition, two, three component master batches were prepared, compositions V and W. They were comprised of copolymer, elastomer (Vistalon® 2504) and

polyolefin (Escorene® HD 6705.39) in ratios of 43.3/36.7/20 and 40/50/10 respectively. These compositions were pelletizable.

These masterbatches were granulated and dried in the manner described above and were then melt blended with polyamide-6,6 (Zytel® 101, manufactured by E.I. duPont de Nemours and Company) in a manner similar to that used to melt blend the impact modifiers of the invention with polyamide-6 above. Before being introduced into the cylinder, each masterbatch was predusted with 0.5 weight percent of a grafting catalyst, magnesium oxide, per hundred part of copolymer. The resulting compositions are listed in Table VII as compositions AB, AC, AD and AE. The blends were also used to prepare test specimens as described above and were subjected to the tests listed in Table III. The results of the tests can be seen in Table VII.

Comparative specimens containing polyamide- 6,6 were also prepared. In Table VII, Composition X is a specimen prepared from polyamide 6,6 (Zytel® 101) alone; Composition Y is a 30/70 blend of elastomer (EPDM, Vistalon® 2504) and polyamide 6,6 (Zytel® 101); Composition Z is a 30/70 blend of polyolefin (HDPE, Escorene® HD 6705.39) and polyamide 6,6 (Zytel® 101); and Composition AA is a 15/15/70 blend of elastomer (EPDM, Vistalon® 2504), polyolefin (HDPE Escorene® 6705.39) and polyamide 6,6 (Zytel® 101).

Finally, a composition was prepared using the copolymer alone as an impact modifier for a polyamide composition. Composition AF in Table VII is a 30/70 blend of copolymer with polyamide 6,6 (Zytel® 101).

All of the comparative compositions were formed into specimens and subjected to the tests listed in Table III. The results of the tests are recorded in Table VII.

Compositions AB, AC, AD, and AE (all the copolymer containing compositions) showed excellent room temperature notched Izod impact values and acceptable values down to about -20 ^β C. Even at about - 20°C, all blends showed a useful 3.5 to 4 notched Izod impact strength. The compositions also showed excellent stiffness retention with all compositions showing a flexural modulus of greater than 200,000 psi (1379 MPa) .

A comparison of the data for Composition AF with that from Compositions AD and AE reveals that it is possible to replace a portion of the more costly copolymer with a combination of relatively lower costing EPDM and HDPE while still maintaining the improved impact strength and stiffness. Moreover, as stated earlier, the presence of HDPE allows the impact modifier to be pelletized.

EXAMPLE III

Two dry blends were prepared for direct letdown into the polyamide resins. They are shown as compositions AG and AH. The blend ratio for both compositions are 62.5/25/12.5 copolymer/elastomer/ polyolefin. Composition AG was melt blended with polyamide 6,6 (Zytel® 101), whereas composition AH was melt blended with polyamide 6 (Capron® 8207F) . The resulting compositions are listed as compositions AJ and Al in Table VIII. These two blends, upon proper drying to remove surface water were also used to

prepare ASTM test specimens as described above and were subject notched Izod impact testing in Table III. The result of the tests can be seen in Table III. Again excellent room temperature and low temperature impact were obtained as compared with unmodified polyamides.

TABLE I Brominated Isobutylene Paramethylstyrene Copolymer Used

(a) Total bromine on polymer by x-ray fluoresence. (b) Mole % brominated paramethylstyrene (PMS) units by Nuclear Magnetic Resonance (NMR) .

(c) Viscosity average molecular weight by dilute solution (DSV) in disobutylene at 68 ^β F (20*C) .

TABLE II ABREVIATIONS AND TRADEMARKS

INGREDIEMT DESCRIPTION

Capron® 8209F Polyamide 6 (PA-6) Allied Signal Capron® 8207F Polyamide 6 (PA-6) Allied Signal

Zytel® 101 Polyamide 6.6 (PA-6,6) E.I. DuPont

Br-XP-50 Brominated Isobutylene Exxon Chemical para-methylstyrene copolymer Irganox® B-215 33/67 Blend of Irganox Ciba Geigy 1010 and Irgafos 168

Irganox® 1010 Tetrakis (methylene (3,5- Ciba Geigy di-tert-butyl-4-hydroxy- hydrocinnamate) methane

Irgafos® 168 Tris (2,4-di-tert-butyl- Ciba Geigy phenyl) phosphate Protox® 169 Zinc Oxide

New Jersey Zinc Co.

Maglite® D Magnesium oxide C.P. Hall

Vistalon® 2504 Diene modified ethylene Exxon Chemical propylene terpolymer

Escorene® HD 6705.39 High Density Poly¬ Exxon Chemical ethylene

TABLE III - TEST METHOD

Test Test Method Tensile Strength psi ASTM D-638 Elongation % ASTM D-638 Flexural Modulus psi ASTM D-790 Notched Izod Impact ft-lb/in ASTM D-256

TABLE IV

Composition

Capron 7209F Vistalon 2504 Escorene HD 6705 39 Copolymer C ^* 30 Composition A* 30 Composition B** 30 Composition C*** 30 Composition D// 30 Composition E# 25 Composition F//// 30 Composition G////

Irganox B-215 0.1 0.1 0.1 0.1 0.1 0.1 0.1 0.1 0.1 0.1

Property

Tensile at Yield, Kpsi 10.6 5.1 5.4 5.1 5.3 5.9 5.1 Tensile at Break, Kpsi 8.5 5.5 6.8 5.9 5.5 5.4 5 Elongation at Yield, X 9 9 9 9 9 9 9 Elongation at Break, X 120 221 345 150 200 109 320

Flexural Modulus, Kpsi 385 239 284 239 218 202 199 221 155 205 219 255

1/8" Notched Izod ft-lb/in

23°C 1 1.3 1.7 23.3 22.9

0"C 0.4 20.3 24.3

-10°C 0.4 1.5 1.3 16.8 21.7

-20"C 0.7 2.6 17.2

* Dusted Composition A with 0.14 wt. % Protox 169

** Dusted Composition B with 0.22 wt.% Protox 169

*** Dusted Composition C with 0.31 wt. % Protox 169

// Dusted Composition D and E with 0.25 wt. % Protox 169 //// Dusted Compositions F and G with 0.3.75 wt. Protox 169 Dusted Composition C with 0.5 wt.X Protox\ 169

TABLE VI Br XP-50/EPDM/HDPE MASTERBATCHES

T U V W

Copolymer A 50 60 Vistalon® 2504 50 40 Escorene® HD6705.39 Irganox® B-215 0.1 0.1

Composition AF

Zytel 101 70 Vistalon 2504 Escorene HD 6705.39 Copolymer D Composition I* 30 Composition U** 30 Composition V*** 30 Composition W// 30

Irganox B-215 0.1 0.1 0.1 0.1 0.1 0.1 0.1 0.1 0.1

Property NJ

Tensile at Yield, Kpsi Tensile at Break, Kpsi Elongation at Yield, X Elongation at Break, X

Flexural Modulus, Kpsi

1/8" Notched Izod ft-lb/in

23°C

0°C

-10°C

-20°C

* Dusted Composition T with 0.25 wt.% Maglite D ** Dusted Composition U with 0.30 wt.X Maglite D *** Dusted Composition V with 0.22 wt.Z Maglite D // Dusted Compositions W and E with 0.20 wt.X Maglite ^A Dusted Copolymer D with 0.5 wt.% Maglite D

TABLE VIII - DRY BLEND/POLYAMIDE BLENDS

(DRY AS MOLDED PROPERTIES)

Composition AG AH AX M

Capron® 8307F 70 Zytel® 101 70

Copolymer D 62.5 Copolymer E 62.5

Vistalon® 2504 25 25

Escorene® HD 6705.39 12.5 12.5

Composition AG 30 Composition AH 30

Irganox® B-215 0.1 0.1

1/8" Notched Izod ft-lb/in.

23 ^β C 20.4 18

0°C 20 8.6

-10\'C 19.9 4.1

-20 ^β C 15.9 3.1