This invention relates to thermoplastic poly¬ mers having pendant hydroxyl moieties and aromatic ether moieties and to articles prepared from such polymers.

Hydroxyphenoxyether polymers are known to be useful in the fabrication of articles exhibiting barrier properties. See, for example, Reinking et al, J. Poly Sci. , Vol. 7, pp. 2135-2144, pp. 2145-2152 and pp. 2153- -2160 (1 63) and Encyclopedia of Polymer Science and Technology, Vol. 10, pp. 111-122. Such polymers generally have only moderate oxygen barrier, i.e., they generally exhibit oxygen transmission rates of 2 or more and up to 75 cπ - mil/100 in2-atm-day.

In view of the limited barrier properties of the prior art polymers having pendant hydroxyl moieties and phenoxyether moieties, it would be highly desirable to provide a polymer having a genuinely high barrier (i.e., oxygen transmission rate less than 5 preferably less than cn -mil/IOOin^-atm-day) to oxygen in both dry and moist environments. Polymers that retain such high

barrier in both dry and moist environments would be especially desirable.

The present invention is, in one aspect, a normally solid thermoplastic polymer having aromatic ether moieties and amide moieties in the backbone chain and pendant hydroxyl moieties. Surprisingly, the poly¬ mer of this invention, hereinafter called a hydroxy- -functional poly(amide-ether) , exhibits thermoplastic character and excellent barrier to oxygen in both dry and moist environments. The polymer can be exturded, molded or fabricated by other heat plastifying methods to form a variety of articles such as films, bags and tubes as well as .stand alone containers. Such polymers retain their thermoplasticity even after being subjected to such heat plastifying conditions. By "normally solid" i-t is meant that the polymer is solid at ambient temperatures, e.g. 15 to 35°C.

^In another aspect, this invention is a contain¬ er suitable for packaging oxygen-sensitive materials wherein the container is fabricated of the hydroxy-func- tional poly(amide-ether) . In yet a further aspect, this invention is a substantially impermeable film or coating of the polymer.

In addition to their use as barrier containers and films, the polymers of this invention are also use- ful as molding, extrusion and casting resins.

Preferably, the hydroxy-functional poly(amide- ether) has repeating units represented by the formula:

0 0 R ² R ² - II _Λ II , I I -(-OAr HC-R '-CNHAr ¹ 0CH ₂ CCH ₂ 0R ³ 0CH ₂ CCH ₂ -)-

OH OH

wherein each Ar ' is independently a divalent aromatic moiety, each R' is a predominantly hydrocarbylene moiety, each R ² is independently hydrogen or a monovalent aliphatic moiety, and each R ³ is independently a predominantly hydrocarbylene moiety. In the more preferred polymers, the nitrogen atom of the amide moiety

is bonded to an aromatic ring. "Predominantly hydrocarbylene" is defined as a divalent radical of which at least 50 percent by weight is hydrocarbon, but which optionally contains a minor amount of heteroatomic moiety such as oxygen, sulfur, imino, sulfonyl, sulfoxyl and the like.

The hydroxy-functional poly(amide-ethers) of this invention are more preferably those represented by the formula:

,2 _R 2

T- OAr ^" • NHC fl-R ¹ -CNHAr ¹ 0CH ₂ CCH ₂ 0R ³ 0CH ₂ CCH ₂ -)- _n }Z

OH OH

wherein Ar ¹ , R ¹ , R ² and R^ are as defined before, Y is _Q hydrogen or a monovalent organic terminating group, Z is a monovalent organic terminating group, and n is a whole number from 10 to about 1000.

In the more preferred polymers, R ¹ is a pre- 5 dominantly hydrocarbylene such as (1) alkylene which has from 1 to about 10 carbons which may contain a heteroatomic moiety such oxygen, sulfur, sulfonyl or sulfoxyl and (2) arylene which has from 5 to 25 carbons, may contain a heteroatomic moiety and may be substituted 0 with alkyl, alkoxy, halo, nitro or cycloalkyl groups. R ² is hydrogen or a hydrocarbyl or substituted hydro- carbyl wherein hydrocarbyl is a monovalent hydrocarbon such as alkyl, cycloalkyl, aralkyl, or aryl and the c substituent(s) is a monovalent moiety which is inert in the reactions used to prepare the hydroxy-functional poly(amide-ether). R3, while usually different from R ¹ , is similarly a predominantly hydrocarbylene moiety as previously defined. Ar ' is arylene or substituted 0 arylene wherein the substituent may be alkyl, alkoxy, halo, nitro or cyano. Y is hydrogen or

Z is

or

and n is a whole number from 10 to about 1000,

In the most preferred hydroxy-functional poly- (amide-ethers), R ¹ is (1) alkylene having from 1 to 10 carbons such as n-butylene, n-pentylene, n-hexylene, n-octylene; (2) alkyleneoxyalkylene such as ethylene- oxyethylene; (3) alkylenethioalkylene such as ethylene- thioethylene or alkylenesulfonylalkylene such as ethyl- enesulfonylethylene; (4) alkyleneoxyaryloxyalkylene such

as ethyleneoxyphenoxyethylene; (5) alkylenearylalkylene such as methylenephenylmethylene; or (6) arylene such as phenylene or substituted arylene such as halophenylene. Of the R ¹ groups, n-butylene is especially preferred. Most preferably, R is hydrogen or alkyl having from 1 to 4 carbons such as methyl, ethyl, propyl and butyl, with hydrogen being especially preferred. R ³ is most preferably arylene such as phenylene, biphenylene, or naphthenylene; bisphenylenealkylidene such as bisphe¬ nyleneisopropylidene, bisphenylenecyanomethane and bisphenylenemethane; bisphenyleneoxide; or bis- (phenyleneamido)alkane such as bis(phenyleneamido)bu- tane, bisphenylene sulfide, bisphenylene sulfone, bis- phenylene ketone and bisphenylene amide, with bisphenyleneisopropylidene being especially preferred. Ar ' is most preferably phenylene or substituted phenylene wherein the substituent is alkyl, halo or nitro, with phenylene being especially preferred. In the most preferred resins, n is 100-400.

The hydroxy-functional poly(amide-ethers) are preferably prepared by contacting a N,N'-bis(hydroxy- phenylamido)alkane or arene, hereinafter referred to as a dihydroxyl diamide, with a diepoxide under conditions sufficient to cause the hydroxyl moieties to react with epoxy moieties to form ether linkages, and pendant hydroxyl moieties. Surprisingly, the amide moieties do not react with the epoxy groups to form any significant cross-linkages. Conditions conventionally employed in the reaction of epoxides with phenols to form ether linkages are suitably employed in preparing the resins of this invention. In general, however, the process for preparation is carried out so that the unreacted epoxy groups in the finished polyether are minimized. By

minimizing the epoxy groups in the polyether, the essential thermoplastic character of the polymer can be retained. Preferred conditions for preparing such resins are set forth in the following working examples.

The dihydroxyl diamide is prepared by contact¬ ing a suitable diacid or diacid halide with a substan¬ tial excess of an aminoarenol under conditions suffi¬ cient to cause reaction of the amine moieties with the acid halide moieties to form amide moieties. Examples of diacids and diacid halides that are suitably employed include acids and acid halides, preferably chlorides, of the following acids: oxalic, adipic, malonic, succinic, glutaric, fumaric, maleic, pimelic, suberic, azelaic, sebacic, terephthalic, and isophthalic. Examples of aminoarenols suitably employed include the following: aminophenols such as p-aminophenol and m-aminophenol, aminonaphthols and other aminohydroxyarenes. Conditions conventionally employed for the reaction of acid chlorides with amines to form amides are suitably employed to form the dihydroxyl diamides of this inven¬ tion. Examples of such suitable conditions are set forth according to J. Preston, J. Polym. Sci. , Vol. 8, p. 3135-3144(1970). Preferred conditions for preparing the dihydroxyl diamides are set forth hereinafter in the working examples.

Examples of preferred diepoxides include the diglycidyl ethers of dihydric phenols such as 4,4'-

-isopropylidene bisphenol (Bisphenol A), 4,4'-dihydroxy- diphenylethylmethane, 3 _> 3'-dihydroxydiphenyldiethyl- methane, 3» '-dihydroxydiphenylmethylpropylmethane, bisphenol, 4,4'-dihydroxydiphenyloxide, 4, '-dihydroxy- diphenylcyanomethane, 4,4'-dihydroxybiphenyl, 4,4'-di-

hydroxybenzophenone, 4,4'-dihydroxydiphenyl sulfide, 4,4'-dihydroxydiphenyl sulfone, 2,6-dihydroxynaphtha- lene, 1 ,4'-dihydroxynaphthalene, hydroquinone, resor- cinol, catechol and other dihydric phenols listed in U.S. Patents 4,438,254 and 4,480,082 which are hereby incorporated by reference.

For the purposes of this invention, the term "barrier polymers" means that the polymer exhibits an oxygen transmission rate which is less than 5, preferably less than 1 and most preferably less than 0.5 cubic centimeters/mil/100 inch ² /atmosphere/day. Although a variety of factors such the chemical structure of the B-component and A-component and the ratio of A-component to B-component, can affect the barrier of the polymer. The barrier properties of the polymer can be significantly affected by the mole ratios of amide moieties to pendent hydroxyl moieties. Preferably this mole ratio of amide to hydroxyl is at least 1:10, more preferably at least 1:2 and most preferably about 1:1.

The barrier containers, films and coatings of this invention are fabricated from the poly(amide-ether) using conventional fabricating techniques for normally solid, thermoplastic polymers such as extrusion, compression molding, injection molding and similar fabrication techniques commonly employed to produce such articles.

The following working examples are given to illustrate the invention and should not be construed as limiting its scope. Unless otherwise indicated, all parts and percentages are by weight.

Example 1

A. Preparation of N,N'-Bis(m- hydroxyphenyl)adipamide

A solution of adipoyl chloride (5.5 g, 0.03 mole) in dry tetrahydrofuran (THF, 50 mL) is added dropwise to a magnetically stirred solution of m-amino¬ phenol (13.0 g, 0.12 mole) in 150 ml of THF. A precip¬ itate forms after 10-15 minutes and is collected by filtration and then washed with water and then with a mixture of water and tetrahydrofuran and recrystallized from an ethanol/water mixture. Analysis of the result¬ ing 8.86 g of white solid indicates it to have the fol¬ lowing structure:

Several additional bis(hydroxyphenyl)amides are prepared using the foregoing procedure, m-aminophenol and different diacid chlorides. The resulting amides are then employed according to the following procedure to make the desired hydroxy-functional poly(amide- ethers). These polymers are then evaluated for barrier properties and the results are reported in Table I.

B. Preparation of Hydroxy Poly(amide-ethers)

A 10.5-g (31.98 mmoles) portion of the adip¬ amide of Part A and diglycidyl ether of Bisphenol A

(DGBA) (11.26 g, 32.62 mmoles, epoxy equivalent weight of 172.58) in 13 mL of freshly distilled propylene gly- col phenylether are heated with stirring to 140°C-150°C under a nitrogen atmosphere. The diglycidyl ether is recrystallized from methanol twice before use. About 15-20 drops of ethyltriphenylphosphonium acetate (70 percent in methanol) are added as the catalyst and, after a brief induction period, the temperature of the reaction rises to 160°C-170°C with complete dissolution of the monomers. Upon the resultant rapid increase in viscosity of the solution, additional catalyst and sol¬ vent are added to progress the reaction to completion and to maintain effective stirring. The reaction solu¬ tion is maintained at 150°C-160°C for 20 minutes and then cooled to 100°C and diluted with 25 mL of dimethyl- - formamide (DMF). The resulting solution is poured into a rapidly stirred 1:1 methanol/water mixture (400-600 mL) to precipitate the product which is then redissolved in DMF (50 mL) and reprecipitated from the meth- anol/water mixture. The product is dried in υacuo at 90°C for 48 hours to yield 15.1 g (70 percent yield) of a pol (amide-ether) (q inh = 0.65 dL/g in DMF at 25°C and 0.5 g/dL) which is represented by the formula:

Several additional hydroxy-functional poly- (amide-ethers) are prepared using the foregoing proce¬ dure and the dihydroxyamides and diepoxides corresponding to moieties shown for R , R^ and Ar' in Table I. These polymers are generally represented by the following structural formula:

Y- OAr ¹ NHC-R ¹ -CNHAr

wherein Ar ¹ , R ¹ , and R ³ are as defined in Table I, Y is hydrogen, Z is

-12-

0

-OAr ¹ NHC-R ¹ -CNHAr ¹ OH

and n is in range of 200 to 400 and R ² is hydrogen.

C. Barrier Testing

Specimens (10 cm x 10 cm x 0.013 cm) for oxygen barrier evaluations are prepared by compression molding samples (3.5 g) of the polymer of Part B between Teflon sheets in a brass template at 200°C at 500 psi (3.5 mPa) for 8-10 minutes, then at 40,000 psi (275 mPa) for 2-4 minutes and then cooled at 40,000 psi for 10 minutes. Oxygen transmission rates are then measured for the samples and the results are reported in Table I.

Following the foregoing procedures, several other hydroxy-functional poly(amide-ethers) within the scope of this invention are similarly prepared and tested and the results are also recorded in Table I.

TABLE I

Sam¬ ple Composition ® η inh © Tg ^® OTR ^® - ^® No. (dL/g) (°C)

Ar Temp <8% 7 (°C) RH ^®"

CH

- CH ₂ -)-ι ₁ 1.65 103 23.3 1.24

CH

CH:

-frCHg- } 0.72 112 24.4 ND

CH-

CH

3 irCH ₂ ^~ - ₀ C 0.52 91 23.4 ND

CH

TABLE I (cont'd)

CH:

0.30 140 24.2 ND 1.

CH:

^■ CH ₂ -)-2, CH- 0.43 92 23.1 ND 0.

6 -frCH ₂ -h| 0.51 94 23.6 ND 0.

7 -ecH ₂ *n SO- 0.46 93 23.1 ND 0.

TABLE I (cont'd)

Sam- pie Composition ® q inh © Tg ^® No. (dL/g) (°C) OTR ^® - ^®

R ¹ R ³ Ar ¹ Temp <8% 7 i°C RH

8 -(-CH ₂ ^ 0.45 110 23.4 0.50 ( _Q

9 -eCH ₂ -hj 0.63 97 23.6 0.35

0 10 -t-CH ₂ - , c 0.54 113 23-3 ND

CN

11 - CH ₂ - , CH 0.49 98 23-4 ND 0

TABLE I (cont'd)

Sam¬ @ ple Composition ^® q inh Tg ^® No. ⁽ dL/ ^g ) i°C) OTR ^® - ^®

R R- Ar Temp <8% 70- 1°C1 RH RH

12 -fCH ₂ -h 0.65 109 23.7 ND 0.

CF:

13 CH ₂ ^ι, 0.52 120 23.6 ND 1.

CF:

14 -(-CH ₂ - , 0.54 108 23.7 ND 0.

TABLE I (cont'd)

Sam¬ ppliee Composition ^® ?, _r ^ιn J ₀ ^e _r N _M o _r .. (dL/g) iCi OTR® _' ®

Ar Temp <8 70-9 (°C) RH^ RH

15 - CH ₂ n 0.55 97 23.7 ND 0.1

16 -fCH^ 0.40 78 23.7 ND 0.

© R ² is hydrogen

^® q inh - inherent viscosity in DMF at 0.5 g/dL and 25°C

^® Tg - glass transition temperature

^® ASTM Method D-3985 measured for compression molded films

^® Oxygen transmission rate (OTR) measured in cc/mil/100 inVatm/day

^® Relative humidity of the oxygen stream

* After annealing at 270°C for 24 hours

As evidenced by the data shown in Table I, the polymers of this invention exhibit excellent barrier to oxygen transmission in a wet environment as well as in a dry environment.