BONDING COMPOSITIONS FOR POLYESTER-POLY(VINYL ALCOHOL) LAMINATES

Abstract: Bonding compositions which are useful for bonding polyesters (including copolyesters) to poly-(vinyl alcohol) (including copolymers thereof) to form a laminate. The bonding compositions comprise a poly(ester amide) having a) a thin film deformation temperature transition which is 1) greater than 70<o>C, 2) not greater than 50<o>C lower nor 25<o>C higher than the glass transition temperature of the polyester or copolyester to be bonded and b) a T-peel strength in the laminate of at least 0.02 Kg/cm.

Description: BONDING COMPOSITIONS FOR POLYESTER- POLY(VINYL ALCOHOL) LAMINATES This invention relates to bonding composi¬ tions for laminates comprising polyester or copoly- * 5 esters bound to poly(vinyl alcohol) or copolymers thereof. The laminates are characterized by greatly improved gas barrier properties and are therefore useful for containers for edible materials. U.S. Patent No. 4,261,473 discloses multi- 10 layer structures useful as packaging materials. Particularly, this patent discloses molded containers having a barrier layer interposed beteen layers of a thermoplastic polyester resin. The barrier layer typically is a blend of polymers such as ethylene- 15 vinyl alcohol copolymer and polyethylene tereph¬ thalate or a polyamide polymer. These containers may be fabricated from a coextruded pipe of five layers comprising for example a polymer outer layer, bonding layer, a barrier layer, bonding layer and a polymer 20 inner layer. Other laminates for packaging materials are disclosed in U.S. Patent 3,595,740. U.S. Patent 3,849,514 discloses that certain block polyester- polyamide copolymers are useful adhesives. However, 25 none of the prior art references suggests the solu¬ tion to the problem solved by the present invention. One particularly desirable laminate from a cost and ease of formation standpoint would be a thermally formable laminate wherein a polyester or 30 copolyester, e.g., ρoly(ethylene terephthalate) is ! bonded to poly(vinyl alcohol) or polymers thereof. The problem is that, with the adhesives of the prior art, these laminates tend to delaminate when ther¬ mally formed. As a result, gas barrier properties 35 are greatly reduced and the appearance of the result¬ ing article is adversely affected. Thus, the object of the present invention is to provide a bonding OMPI composition which will eliminate this delamination problem. This problem is solved by a bonding composi¬ tion for bonding polyesters and copolyesters to poly(vinyl alcohol) and copolymers thereof to form a laminate characterized in that the bonding composi¬ tion comprises a poly(esteramide) having a) a thin film deformation temperature transi- tion which is 1) greater than 70°C 2) not greater than 50°C lower nor 25°C higher than the glass transition temperature of the polyester or copolyester to be bonded and b) a T-peel strength in the laminate of at least .02 Kg/cm. The thin film deformation temperature transition for the poly(esteramide) bonding composi¬ tion is that temperature at which a weighted sample of the film deforms in a thermomechanical analyzer. More particularly, the deformation transition is the temperature corresponding to the intersection of the straight line portions of a deflection vs. tempera¬ ture curve for a thin film of the polymer. The measurement is preferably made on a sample of the film having a thickness of between .02 mm and .08 mm loaded to 3.5 Kg/cm 2 tensile stress and heated at a rate of 20°C per minute. The T-peel strength is measured according to ASTM D1876. A variety of poly(ester amides) have been tested and have been found to meet the above cri¬ teria. Preferred poly(ester amide) bonding composi¬ tions include: I. Poly(esteramides) having an inherent vis¬ cosity of at least 0.45 dL/g, said poly(esteramide) containing 1) repeating units derived from an acid component which is at least 80 mol percent of a dicarboxylic acid selected from pimelic, azelaic, sebacic acid or combinations thereof and optionally up to 20 mol percent of a second linear aliphatic dicarboxylic acid having at least four carbon atoms connected linearly between the two acid groups or an aromatic dicarboxylic acid and 2) repeating units derived from a diamine and glycol component which is from 5 mol percent to 20 mol percent of 1,2-ethanedi- amine and from 95 to 80 mol percent of a glycol selected from ethylene glycol, 1,4-butanediol, 1,4-cyclohexanedimethanol or combinations thereof. It is preferred that the repeating units from pimel¬ ic, azelaic or sebacic acid be present in the amount of 85 to 100 mol percent. It is most preferred that the repeating units from a dicarboxylic acid be from azelaic acid and be present in the amount of 100 mol percent. Also it is preferred that the repeating units from the 1,2-ethanediamine are present in the amount of 5 to 15 mol percent. It is preferred that the repeating units from a glycol be from 1,4-butane- diol and be present in the amount of 95 to 85 mol percent. The diamine useful in the production of the ρoly(esteramides) of this group is restricted to 1,2-ethanediamine. The diacid must be pimelic, azelaic or sebacic at about >80 mol percent. The remaining portion of the diacid (which is used to make the amide segment) may be a linear aliphatic dicarboxylic acid or an aromatic dicarboxylic acid. Aliphatic dicarboxylic acids may have no fewer than four carbon atoms connected linearly between the two acid groups. Acids such as adipic, suberic, sebacic, and 1,12-dodecanedioic acid, and 1,4-cyclohexanedi- carboxylic acid are preferred modifying aliphatic acids. Preferred aromatic modifying acids are terephthalic and isophthalic acids. The preferred diacid for the poly(esteramide) is azelaic acid as the sole diacid. Useful glycols are ethylene glycol, 1,4- butanediol and 1,4-cyclohexanedimethanol and mixtures thereof. Preferred is the use of one of these glycols as the sole glycol. Preferred as such sole glycols are 1,4-butanediol and 1,4-cyclohexanedi- ethanol. These diols, in combination with the allowed diacid, result in a low melting polyester segment having a low glass transition temperature. This overall combination of a crystalline polya ide and low Tg polyester gives poly(esteramides) that are elastomeric in nature. The inherent viscosity of the poly(ester- amide) must be at least about 0.45 dL/g and prefer¬ ably at least 0.50 dL/g. The exact I.V. above 0.45 dL/g needed is actually determined generally by the desired polymer melt viscosity. In general, the melt viscosity of the poly(esteramide) at its processing temperature should not be different from the poly¬ ester by a factor of more than about 3 for a flat film coextrusion on a feed block system or a factor of more than about 10 for a multilayer pipe or multimanifold film coextrusion. The ρoly(esteramides) of this group can be made in such a fashion as to produce some degree of blocking, i.e. deviation from ideal randomness. This is, however, not essential to obtaining useful properties for the product poly(esteramide) . II. Poly(esteramides) having an inherent vis¬ cosity of at least 0.8 dL/g, said poly(esteramide) containing 1) repeating units derived from an acid component which is at least 70 mol percent of a dicarboxylic acid selected from pimelic, azelaic, sebacic acid or combinations thereof and optionally up to 30 mol percent of a second linear aliphatic dicarboxylic acid having at least four carbon atoms connected linearly between the two acid groups or an aromatic dicarboxylic acid and 2) repeating units derived from a diamine and glycol component which is from 10 mol percent to 30 mol percent of a diamine selected from 1,6-hexanediamine, 1,4-cyclohexanebis- methylamine or .combinations thereof and from 90 to 70 mol percent of a glycol selected from ethylene glycol, 1,4-butanediol, 1,4-cyclohexanedimethanol or combinations thereof. It is preferred that the repeating units from pimelic, azelaic or sebacic acid be present in the amount of 75 to 100 mol percent. It is most preferred that the repeating units from a dicarboxylic acid be from azelaic acid and be present in the amount of 100 mol percent. Also it is pre¬ ferred that the repeating units from a diamine are present in the amount of 15 to 25 mol percent. It is more preferred that the repeating units from a diamine be from 1,6-hexanediamine in the amount of 15 to 25 mol percent. It is preferred that the repeat¬ ing units from a glycol be from 1,4-butanediol and be present in the amount of 85 to 75 mol percent. The diamines useful in the production of the poly(esteramides) of this second group are restricted to 1,6-hexanediamine and 1,4-cyclohexanebismethyl- amine. The diacid must be pimelic, azelaic or sebacic at about >70 mol percent. The remaining portion of the diacid (which is used to make the amide segment) may be a linear aliphatic dicarboxylic acid or an aromatic dicarboxylic acid. Aliphatic dicarboxylic acids may have no fewer than four carbon atoms connected linearly between the two acid groups. Acids such as adipic, suberic, sebacic, and 1,12-dodecanedioic acid, and 1,4-cyclohexanedi- carboxylic acid are preferred modifying aliphatic acids. Preferred aromatic modifying acids are terephthalic and isophthalic acids. The preferred _OMPI V# , ~ WIPO " diacid for the poly(esteramide) is azelaic acid as the sole diacid. Useful glycols are ethylene glycol, 1,4- butanediol, and 1,4-cyclohexanedimethanol and mixtures thereof. Preferred is the use of one of these glycols as the sole glycol. Preferred as such sole glycols are 1,4-butanediol and 1,4-cyclohexane- dimethanol. These diols, in combination with the allowed diacid, result in a low -melting polyester segment having a low glass transition temperature. This overall combination of a crystalline polyamide and low Tg polyester gives poly(esteramides) that are elastomeric in nature. The inherent viscosity of the polyester- amide) must be at least about 0.8 dL/g and preferably at least 1.0 dL/g and more preferably at least 1.1 dL/g. The exact I.V. above 0.8 dL/g needed is actually determined generally by the desired polymer melt viscosity. In general, the melt viscosity of the poly(esteramide) at its processing temperature should not be different from the polyester by a factor of more than about 3 for a flat film coextru¬ sion on a feed block system or a factor of more than about 10 for a multilayer pipe or multimanifold film coextrusion. The ρoly(esteramides) of this group can also be made in such a fashion as to produce some degree of blocking, i.e. deviation from ideal randomness. This is, however, not essential to obtaining useful properties for the product poly(esteramide) . III. Poly(esteramides) having an inherent vis¬ cosity of at least 0.8 dL/g, said poly(esteramide) containing 1) repeating units derived from an acid component which is 70 to 90 mol percent of a dicar¬ boxylic acid selected from adipic, pimelic, suberic, azelaic, sebacic acid or combinations thereof and 10 to 30 mol percent of a second linear aliphatic dicarboxylic acid having at least four carbon atoms connected linearly between the two acid groups or an aromatic dicarboxylic acid and 2) repeating units derived from a diamine and glycol component which is from 10 mol percent to 30 mol percent of a diamine selected from 1.,6-hexanediamine, 1,4-cyclohexanebis- methylamine or combinations thereof and from 90 to 70 mol percent of a glycol selected from ethylene glycol, 1,4-butanediol, 1,4-cyclohexanedimethanol or combinations thereof. The repeating units from the second linear aliphatic dicarboxylic acid and repeat¬ ing units from the diamine are present in equal molar amounts. It is preferred that the repeating units from adipic, pimelic, suberic, azelaic or sebacic acid be present in the amount of 75 to 85 mol per¬ cent. Also it is preferred that the repeating units from a diamine are present in the amount of 15 to 25 mol percent. It is more preferred that the repeating units from a diamine be from 1,6-hexanediamine in the amount of 15 to 25 mol percent. It is preferred that the repeating units from a glycol be from 1,4-butane- diol and be present in the amount of 85 to 75 mol percent. The diamines useful in the production of the poly(esteramides) of this third group are restricted to 1,6-hexanediamine and 1,4-cyclohexanebismethyl- amine. The diacid must be adipic, pimelic, suberic, azelaic or sebacic at 70 to 90 mol percent. The remaining portion of the diacid (which is used to make the amide segment) may be a linear aliphatic dicarboxylic acid or an aromatic dicarboxylic acid. Aliphatic dicarboxylic acids may have no fewer than four carbon atoms connected linearly between the two acid groups. Acids such as adipic, suberic, sebacic, and 1,12-dodecanedioic acid, and 1,4-cyclohexanedi- carboxylic acid are preferred modifying aliphatic OMPI acids. Preferred aromatic modifying acids are terephthalic and isophthalic acids. Useful glycols are ethylene glycol, 1,4- butanediol, and 1,4-cyclohexanedimethanol and mix- tures thereof. Preferred is the use of one of these glycols as the sole glycol. Preferred as such sole glycols are l,4ι-butanediol and 1,4-cyclohexanedi- methanol. These diols, in combination with the allowed diacid, result in a low melting polyester segment having a low glass transition temperature. This overall combination of a crystalline polyamide and low Tg polyester gives poly(esteramides) that are elastomeric in nature. The inherent viscosity of the poly(ester¬ amide) must be at least about 0.8 dL/g and preferably at least 1.0 dL/g and more preferably at least 1.1 dL/g. The exact I.V. above 0.8 dL/g needed is actually determined generally by the desired polymer melt viscosity. In general, the melt viscosity of the poly(esteramide) at its processing temperature should not be different from the polyester by a factor of more than about 3 for a flat film coextru¬ sion on a feed block system or a factor of more than about 10 for a multilayer pipe or multimanifold film coextrusion. The poly(esteramides) of this group can also be made in such a fashion as to produce some degree of blocking, i.e. deviation from ideal randomness. This is, however, not essential to obtaining useful properties for the product poly(esteramide). This invention includes laminates and shaped articles made from the laminates comprising a poly¬ ester (or copolyester) polymer layer and a poly(vinyl alcohol) (or copolymer thereof) barrier layer, the layers being bonded together with bonding composi¬ tions of this invention. It is preferred that the barrier layer be an ethylene-vinyl alcohol copolymer having an ethylene content of 30 to 50 mol percent. The shaped article may be an oriented film or an oriented bottle. Preferably the laminate includes an outer layer of poly(ethylene terephthalate), a barrier layer of an ethylene-vinyl alcohol copolymer, and an inner layer of ρoly(ethylene terephthalate), the respective layers being bonded together by bonding composition layers of the described bonding composi¬ tion disposed between the outer layer and the barrier layer and the inner layer and the barrier layer. A preferred form of the laminate is a coextruded tubular structure comprising an outer layer of poly(ethylene terephthalate), a barrier layer of ethylene-vinyl alcohol copolymer and an inner layer of poly(ethylene terephthalate), the layers being bonded together by a bonding composition layer of the composition of this invention disposed between the outer layer and the barrier layer and the inner layer and the barrier layer. The tubular structure may be formed into a parison or preform for blowing beverage bottles. The polyester polymers suitable for this invention include poly(ethylene terephthalate) and modifications thereof with aliphatic glycols contain¬ ing from 3 to 12 carbon atoms. These may be either linear or branched and may contain ring structures. Examples of especially useful modifying glycols are 1,4-butanediol, 1,6-hexanediol, 1,4-cyclohexanedi- methanol, and neopentyl glycol. The poly(ethylene terephthalate) may also be modified with diacids. Aliphatic and aromatic diacids may be used. Espe¬ cially useful as a modifying diacid is isophthalic acid. Generally, either the diol or diacid modi¬ fier may be used at up to about 50 mol 1. but the most useful materials are those where orientation can be developed by deforming heated articles, thereby restricting the useful modification level to about 15 mol % and below. Other polyesters or copolyesters may be used in this invention besides poly(ethylene terephthal¬ ate). A particularly useful group of copolyesters is the one based on 1,4-cyclohexanedicarboxylic acid, 1,4-cyclohexanedimethanol, and poly(tetramethylene oxide) glycol as described in U.S. Patent 4,349,469. Other useful polyesters are poly(l,4-cyclo- hexylenedi ethylene terephthalate) and copolymers thereof with aliphatic diols of 2 to 12 carbon atoms or aliphatic or aromatic diacids as described above. The vinyl alcohol polymers useful as the barrier layer in'the laminates include those wherein the olefin content of the copolymer is between about 7 and about 50% mol percent and the residual ester content of the vinyl alcohol portion is below 3.0%. It is preferred that the differential thermal analy¬ sis curve for the copolymer be a single narrow endotherm having a melting range of less than 30 C. Also, the olefin content of the copolymer should be maintained within a narrow distribution range and significant amounts of homopolymer segments of either olefin or vinyl alcohol should be avoided. The olefin distribution range and the presence of homopolymers is most conveniently measured using differential thermal analysis (DTA) techniques. The differential thermal analysis (DTA) is carried out according to the procedure set forth by D. A. Vassalo and J. C. Harden in Analytical Chemistry, Volume 34, January, 1962, pages 132-135, using a Du Pont 900 Differential Thermal Analyzer programmed at a 30°C/minute rate. A DTA curve wherein the curve is characterized by a single narrow melting endotherm having a range of less than 30°C indicates a narrow olefin distribution in the copoly¬ mer. Suitable vinyl esters which can be copoly- merized with the olefin comonomers and subsequently hydrolyzed to form the olefin-vinyl alcohol copoly¬ mers include vinyl ester monomers of the general formula wherein R is selected from the group comprising hydrogen, alkyl groups of from 1 to 10 carbon atoms, aryl groups of from 6 to 10 carbon atoms including the carbon atoms in ring substituted alkyl substi- tuents, e.g., vinyl formate, vinyl acetate, vinyl propionate, vinyl butyrate, vinyl benzoate, and the like. Preferably, the vinyl ester is vinyl acetate. The preferred olefin-vinyl alcohol materials are ethylene-vinyl alcohol copolymers and wherein the olefin content is from 7 to 50 mol percent based on the weight of the copolymer. The residual ester icontent of the copolymer should be less than 3% and preferably less than 2% by weight. Most preferably the residual ester content is less than IX by weight. The preferred ethylene-vinyl alcohol copoly¬ mer resins will contain less than 2% homopolymers. Especially preferred are homopolymers with less than 1% homopolymer. An example of a preferred copolymer is EVAL F (trademark) resin marketed by uraray Company. Useful olefin-vinyl alcohol polymers and their preparation are known in the art. See, for example, U.S. Patent 3,585,177. Although the described laminates can be used to advantage for any coextrusion application, the optimum advantage of the ρoly(esteramides) is for use in coextrusions which will be followed by some orientation process being performed at a temperature and conditions chosen to result in orienting the polyester portion of the coextruded structure. The oriented laminates may conveniently be prepared by the- methods disclosed in U.S. Patents 3,479,425 and 3,557,265. U.S. Patent 3,479,425 discloses a method of extruding laminar film wherein a composite stream consisting of coaxial streams of plastic is provided, passed to a sheeting die wherein the coaxial stream is deformed to provide a layered sheet. U.S. Patent 3,557,265 discloses a method whereby plastic film or sheet having a plurality of layers is formed by deforming a flowing stream having layers of diverse thermoplastic material wherein the cross-sectional configuration of the plurality of flowing streams is altered by reducing the dimension of the stream in a direction generally perpendicular to the interfaces between the individual streams and by increasing the dimension of the stream in a direction generally parallel to the interface to provide a sheet or film having a laminar structure. The extruded pipe is made in a conventional manner by coextruding through a series of plate dies to sequentially overcoat the appropriate materials in such a manner that the resulting annular structure is arranged in five layers• Different relative extruder screw speeds and take-off rates permit a variety of different tubing products to be later made into preform and later to oriented bottles. To produce a five-layer pipe having a wall thickness 0.59 mm the layers may be arranged as follows: Thickness Percent (mm) of Total Outer Layer 0.28 48.00 Bonding Composition 0.0078 1.33 Barrier Layer 0.0078 1.33 Tie Layer 0.0078 1 .33 Inner Layer 0.28 48.00 Total Thickness 0.59 100.00 The pipe is cut off to predetermined lengths and the lengths are formed into preforms or parisons to be blown into bottles. The pipe may be formed into parisons using the method disclosed in U.K. Patent Specification 1,513,067 and known as the Corpoplast* system. The parisons or preforms may also be made by the method disclosed in U.K. Patent Application GB 2052367A. A preferred method of blowing bottles using the laminates of this invention involves the use of a RHB-VII three-lane, two-stage reheat blowing machine designed to produce one-half liter bottles. This machine is manufactured by Cincinnati Milacron, Plastics Machinery Division of Batavia, Ohio. The machine comprises a parison or preform carrier loading unit, a preform carrier and conveyer system, a three-lane heating system, doubleacting toggle clamp unit, bottle ejection system and a programmable control system. The following is a generalized example of the preparation of about 0.8 mol of a poly(ester- amide) where only one diacid is present. Into a 500 mL flask is weighed 0.16 mol (for a 20 mol % diamine modification) of the 1,2-ethanedi- a ine, from 0.16 mol (for a 20 mol % diamine modifi¬ cation) to 0.80 mol of the diacid as desired, and from one-half to all of the glycol being used. The glycol excess is generally from 10 to 100 mol % depending on the glycol volatility, the higher OMPI L , WIPO , boiling the glycol, the lower the excess needed. The reaction mixture is stirred under an inert gas blanket and heated for sufficient time at about 200°C to cause a idization and some esterification to occur. Any glycol and diacid not added at the start of the reaction is then added and heating is con¬ tinued (usually, at a higher temperature, e.g. 220°C) to allow completion of the esterification reaction. The melt is then raised to the polycondensation temperature (e.g. 275°C) and a vacuum applied (usual¬ ly to a pressure of <5 torr) for sufficient time to obtain the desired molecular weight (as measured by inherent viscosity). Organo-titanates or other- active metal catalysts are usually used in the above reaction to yield acceptable reaction rates. The catalyst may be added either at the reaction start or later, such as when the temperature is brought up to the second heating level. It must be added at least prior to polycondensation. For poly(esteramides) having a different diacid in the amide segment from that of the ester segment, the above procedure is used except the diacid intended for the amide segment is added to a mixture of the diamine in some or all of the glycol as stated above. After the initial heating, the diacid intended for the ester segment is added along with any glycol not added at the start. Test for Thin Film Deformation Temperature Transition The test is conducted by first pressing a film of relatively uniform thickness of the dried poly(ester amide) bonding layer composition. The pressing is done in a press between 2.48 square cm ferrotype plates which have been coated with a backed-on silicone mold release agent. The present temperature was generally about 165°C (this depends, of course, on the melting point of the particular JϋTO^ * * OMPI ^5 , IPO Λ>J J polymer composition and needs to be high enough to ensure good flow-out and a thin enough film during the pressing operation). Generally, pressing of the film at this temperature is done for about 20 sec. of applied pressure or more. After the pressing opera¬ tion, the metal plates are removed and cooled between large aluminum blocks. The thickness of the pressed film may range from .02 mm to .08 mm with .02 mm to .04 mm being the most desirable thickness range. A sample of the film about 2.5 cm long and nominally .03 cm in width is cut being careful to maintain even width along the length of the sample. The film is mounted in the film specimen grips of a thermo- mechanical analyzer and mounted in the instrument. The film is loaded to 3.5 Kg/cm 2 tensile stress by the use of small weights and the test chamber flushed with a flow of helium gas. Heating is conducted at a rate of 20°C per minute (after thermal equilibration at a temperature above room temperature). The deflection of the film vs. temperature is recorded on the strip chart recorder. The trace is then analyzed to obtain the deformation temperature transition by drawing the initial baseline forward and the deflec¬ tion line, which after an initially curved partition tends to be straight, backward to obtain an inter¬ section of the two lines. The temperature at the intersection of the two lines is the thin film deformation temperature transition. In order for the bonding compositions to perform satisfactorily, it has been found that this temperature needs to be in the range of no more than 50°C below the glass transition temperature of the polyester polymer which represents the major portion of the structure of the laminate. The deformation temperature transition may also not exceed the glass transition temperature of the polyester layer of the laminate by more than about 25°C (preferred is 20°C) . The lower limit of OMPI the deformation temperature transition of the bonding composition is subject to the limitation that it may not be lower than about 70°C. Thus, for polyesters such as poly(ethylene terephthalate), this has the practical effect of limiting the lower limit of the deformation temperature transition to about 10°C below the glass-transition temperature of the polyester component. For the purposes of uniformity of measure- ment of the glass transition temperature, it is determined at a heating rate of 20°C per minute in a DSC instrument. The actual glass transition tempera¬ ture is defined as the midpoint of the glass to rubber transition. In addition to the above temperature test it is also necesary in defining suitable bonding compo¬ sitions to determine the T-peel strength of a lamin¬ ate of the polyester component, the bonding composi¬ tion, and the barrier composition. The peel strength of the laminate must be at least 0.1 pound per inch (.0177 Kg/cm). The laminate for testing is prepared by first extruding films of the polyester and barrier materials (such as ethylene vinyl alcohol copolymer having a 65 mol % vinyl alcohol content) to a thick- ness of approximately .02 mm. The bonding composi¬ tion is likewise extruded into film form. A three- layer laminate is assembled from strips of each of the films of about 2.5 cm width and 10 cm or more in length. The laminate, with the bonding composition in the center, is heat-sealed using a heat sealer with an approximate 177-190°C jaw temperature and a 4 to 5 second sealing time at a jaw pressure of 1.4 Kg/cm 2 . The T-peel test is run according to ASTM D1876. Poly 1 , 4-Tetramethylene Azelate Modified with 1 , 6-Hexanediamine Deformation Temperature mol % diamine Transition, °C T- ■ Peel (K /cm) 5 58 .39 7 .5 67.5 * 10 75 .66 20 87 .48 30 94.5 .02 32.5 107 * 35 109 0 *Not determined This invention can be further illustrated by the following examples. Examples All inherent viscosities are determined at 25°C in 60/40 (wt/wt) phenol/tetrachloroethane (PTCE) at a concentration of 0.5 g/100 L, and are given in units of dL/g. Group I--Poly(ester amides) Preparation I-l A poly(esteramide) is prepared by combining the following in a 500 ml three neck round bottom flask: 18.8 g (0.10 mol) azelaic acid, 3.0 g (0.05 mol) 1,2-ethanediamine, and 49.5 g (0.55 mol) 1,4- butanediol. The mixture was stirred under nitrogen and the flask immersed in a 200°C metal bath at 200°C for one hour. After that time, 75.3 g (0.40 mol) of azelaic acid was added and 45.0 g (0.45 mol) of 1,4-butanediol along with sufficient acetyl triiso- propyltitanate to give 100 ppm in the final polymer. The mixture was stirred for an additional hour at 220°C and the bath temperature raised to 275°C. The reaction mixture was put under vacuum (0.3 mm Hg) for 45 minutes, after which the flask was removed from the bath and the polymer cooled under nitrogen. The I.V. of the poly(esteramide) was 0.594. Preparation 1-2 A poly(esteramide) was prepared as above but using 6.0 g (0.10 mol) of 1,2-ethanediamine and 72.0 g (0.80 mol) of 1,4-butanediol as the total reactants (the azelaic ac.id and Ti catalyst amounts remain unchanged) . All reactants were allowed to react together at a 200°C metal bath temperature for one hour, after which the bath temperature was raised to 245°C and the melt polycondensed for 75 minutes at 0.4 torr. The resultant polymer had an I.V. of 0.569. Examples 1 St 2 Pipe coextrusion was performed using poly- (ethylene terephthalate) modified with 3.5 mol % 1,4-cyclohexanedimethanol as the polyester layer, an ethylenevinyl alcohol copolymer containing 35 mol % ethylene units as the barrier layer, and the materi¬ als of Examples 1 and 2 as bonding composition layers. The coextruded pipe had good appearance and adhesion. Bottles blown from the parisons formed from the pipe showed acceptable adhesion. Example 3 -- Comparative Pipe coextrusion was performed as in Exam- pies 1 and 2 but using a poly(esteramide) prepared as in Preparation I-l from poly(l,4-tetramethylene 1,12-dodecanedioate) and 10 mol % of 1,2-ethanedi- amine (I.V. ■ 0.50). Bottles blown from parisons formed from the coextruded pipe showed unacceptable adhesion in the bottle side walls. Group II—Poly(ester amides) Preparation II-1 A poly(esteramide) bonding composition comprising repeating units of the following reactants was prepared as follows: 150.4 g azelaic acid (0.80 mol), 115.2 g (1.28 mol, 100% excess) 1,4-butanediol, and 22.72 g (0.16 mol) 1,4-cyclohexanebismethylamine and enough Ti as acetyl triisopropyl titanate to give 150 ppm Ti in the final polymer. All of the diamine, 80% of the diacid and 50% of the diol were combined in a 500 mL, three-neck round bottom flask and the flask immersed in a 200°C metal bath. The reaction was stirred one hour after which the remainder of the reactants was added and allowed to react an addi¬ tional hour. Polycondensation at 275°C under vacuum (~0.3 torr) for two hours yielded a polymer of I.V. of 1.04 which was rubbery. Example 4 Five-layer pipe coextrusion was performed using poly(ethylene terephthalate) modified with 3 5 mol percent 1,4-cyclohexanedimethanol as the poly- ester layers (outer and inner), a poly(esteramide) having an I.V. of 1.3 prepared as described in Preparation II-l was used as the bonding composition layers and a copolymer of ethylene-vinyl alcohol containing 65 mol % vinyl alcohol was used as the barrier layer to form the five-layer pipe. The layers of the pipe exhibited excellent appearance and the pipe was formed into a preform. The preform was then blown into a bottle. The bottle exhibited no delamination, even when pressurized with carbonated water. Example 5 Pipe coextrusion was performed using poly¬ ethylene terephthalate) modified with 3.5 mol percent 1,4-cyclohexanedimethanol as the polyester, a poly(amide ester) consisting of poly(l,4-tetramethyl- ene azelate) modified with 20 mol % 1,6-hexanediamine (prepared as in Preparation II-l to give partial blocking using 20% of the azelaic acid to preform the amide segment) (I.V. ■ 1.30), and a barrier layer of a copolymer of ethylene vinyl alcohol having 65 mol percent vinyl alcohol to form a five-layer pipe. The pipe had excellent appearance and adhesion. It was formed by a series of steps into first a parison and then into a bottle. The bottle side wall was sec¬ tioned and an attempt made to separate the barrier layer from either polyester layer. The bond appeared to be virtually inseparable. Examples 6-7 Pipe coextrusion was performed as in Exam¬ ples 4 and 5, but substituting instead the following ρoly(esteramides) which had been prepared having all the reactants added to the reactor at the very beginning. The two compositions thus produced were: (1) poly(l,4-tetramethylene azelate) modified with 20 mol % 1,4-cyclohexanebismethylamine, (I.V. ■ 1.33), and (2) ρoly(l,4-tetramethylene azelate) modified with 20 mol % 1,6-hexanediamine (I.V. ■ 1.37). Pipes using both adhesives had excellent appearance and adhesion. Bottles made from the pipes also showed excellent bonding of the barrier layer to the polyester layers. Examples 8-9 Pipe coextrusion was performed as in Exam¬ ples 4 and 5, but substituting instead the following poly(esteramides) which were prepared as in Example 1 (using 20% of the diacid to preform the amide seg¬ ment) : (1) poly(l,4-tetramethylene azelate) modified with 10 mol % 1,4-cyclohexanebismethylamine (I.V. ■ 1.37), and (2) poly(l,4-tetramethylene azelate) modified with 30 mol % 1,4-cyclohexanebismethylamine (I.V. ■ 1.33). The pipe from both five-layer coextrusions had excellent appearance and adhesion. Bottles made from the pipe showed acceptable adhesion. Example 10 -- Comparative Pipe coextrusion was performed as in Exam¬ ples 2 and 3 but substituting instead the following poly(esteramide) (prepared as in Preparation II-l using 20% of the diacid to preform the amide seg¬ ment) : poly(l,4-tetramethylene adipate) modified with 1,6-hexanediamine (I.V. • 1.068). The coextruded pipe had excellent appearance and adhesion. The bottles showed unacceptable adhesion of the. barrier layer to the polyester. Example 11 -- Comparative Pipe coextrusion was performed as in Exam- pies 4 and 5 but substituting instead a poly(ester¬ amide) (prepared as in Preparation II-l using 20% of the diacid to preform the amide segment) of the following composition: poly(l,4-cyclohexylenedi- methylene 1,12-dodecanedioate) modified with 20 mol % of 1,4-cyclohexanebismethylamine (I.V. β 1.02). The pipe had excellent appearance and adhesion. The bottles blown from the pipe had unacceptable adhesion of the barrier layer to the polyester. Example 12 -- Comparative Pipe coextrusion was performed with the poly(esteramide) of Preparation II-l but using only 0.710 I.V. material. The bottles produced showed unacceptable adhesion of the barrier layer to the polyester. Examples 13-14 Pipe coextrusion was performed as in Example 4 but substituting the following pol (esteramides) (prepared as in Preparation II-l using 20% of the diacid to preform the amide segment) : (1) poly(l,4-tetramethylene 1,7-heptanedioate) modified with 20 mol % of 1,4-cyclohexanebis- methyla ine (I.V. ■ 0.81), and (2) ρoly(l,4-tetramethylene 1,10-decanedicoate) modified with 20 mol % of 1,4-cyclohexanebis- methylamine (I.V. - 0.95). OMPI The pipe showed excellent appearance and adhesion. Bottles blown from the pipes showed excel¬ lent adhesion. Example 15 -- Comparative Pipe coextrusion was performed as in Example 4 but substituting the poly(esteramide) poly(1,4- tetramethylene "1,8-octanedioate) modified with 20 mol percent of 1,4-cyclohexanebismethylamine (I.V. 1.202). The pipe had excellent appearance and adhesion. Bottles blown from the pipe showed unaccept¬ able adhesion. Example 16 — Comparative Pipe coextrusion was performed as in Example 4 but substituting a poly(esteramide) (prepared as in Preparation II-l using 20% of the diacid to preform the amide segment) of poly(l,6-hexamethylene adipate) modified with 20 mol % 1,6-hexanediamine (I.V. ■ 0.77). Pipe coextrusion was unsuccessful in this case. Example 17 Film coextrusion was performed giving a five layer construction similar to the pipe examples above using the poly(esteramide) of Preparation II-l [poly(1,4- tetramethylene azelate) modified with 20 mol % of 1,4-cyclohexanebismethylamine] and substi¬ tuting for the poly(ethylene terephthalate) a poly- (1,4-cyclohexylenedimethylene 1,4-cyclohexanedicarb- oxylate) modified with 25 wt % of 1000 mol wt poly- (oxytetramethylene) glycol and 0.5 mol % of trimelli- tic anhydride. The clear, flexible structure has very high interlayer adhesion. Example 18 — Comparative A poly(esteramide) was prepared as in Example 1 to make poly(l,4-tetramethylene adipate) modified with 20 mol % 3,3'-ethylenedioxybis(propyl- amine) (I.V. » 0.884 dL/g). Atte pted pipe coextrusion failed to give a uniform bonding composition layer distribution. Example 19 -- Comparative A poly(esteramide) was prepared as in Preparation II-l using terephthalic acid and 3,3'- ethylenedioxybis(propylamine) as the amide segment (20 mol %) and .azelaic acid and 1,4-butanediol as the ester segment. An I.V. of 1.154 was obtained. Attempted pipe coextrusion failed due to inability to achieve a uniform bonding composition layer distribution (the polymer tended to stick badly in the extruder throat) . Examples 20-21— Comparative Poly(esteramides) were prepared as in Preparation II-l: (1) ρoly(l,4-tetramethylene azelate) modified with 5 mol % 1,4-cyclohexanebismethylamine (I.V. * 1.38), and (2) poly(l,4-tetramethylene azelate) modified with 35 mol % 1,4-cyclohexanebismethylamine (I.V. ■ 1.10). Pipe coextrusion of the above gave accept¬ able adhesion for both. Bottles blown from the coextruded structures, however, had unacceptable adhesion in the bottle side wall. Group III—Poly(ester amides) Preparation III-l A poly(esteramide) bonding composition was prepared as follows: 37.6 g (0.20 mol) azelaic acid, 18.6 g (0.16 mol) 1,6-hexanediamine and 57.6 g (0.64 mol) 1,4-butanediol was combined in a three-neck 500 L round bottom flask. The flask was immersed in a metal bath held at 200°C and the mixture stirred for one hour at 200°C. After that time 87.6 g (0.60 mol) adipic acid and an additional 57.6 g (0.64 mol) of 1,4-butanediol were added along with sufficient acetyl triisopropyl titanate to give 100 pp in the final polymer. Heating was continued for one hour at -24- 220°C. The melt was then polycondensed at a bath temperature of 275°C for one hour. The resultant polymer had an I.V. of 1.123. Example 22 Five-layer pipe coextrusion was performed using poly(ethylene terephthalate) modified with 3.5 mol percent 1,4-cyclohexanedimethanol as the poly¬ ester layers (outer and inner), the poly(esteramide) of Preparation III-l as the bonding composition layers and a copolymer of ethylene-vinyl alcohol containing 65 mol % vinyl alcohol was used as the barrier layer to form the five-layer pipe. The layers of the pipe exhibited excellent appearance and the pipe was formed into a preform. The preform was then blown into a bottle. The bottle exhibited no delamination, even when pressurized with carbonated water. Example 23 Pipe coextrusion was performed as in Example 22 but substituting the following poly(esteramide) : poly(1,4-tetramethylene 1,8-octanedioate) modified with 20 mol % azelaic acid and 20 mol % 1,6-hexanedi- a ine (the amide segment is made from the diamine and azelaic acid) (I.V. » 1.13). Pipe from the coextru- sion had excellent appearance and adhesion. Bottles blown from parisons formed from the pipe showed excellent adhesion in the bottle side wall. Example 24 Pipe extrusion was performed as in Example 22 but substituting the following polyesteramide: poly(1,4-tetramethylene adipate) modified with 20 mol % 1,12-dodecanedioic acid and 20 mol % 1,6-hexanedi- amine (I.V. » 0.90), (the amide segment is made from diamine and 1,12-dodecanedioic acid). Pipe coextrusion showed good adhesion and appearance. Bottles blown from parisons formed from the pipe showed excellent adhesion in side walls. STΓREAI Example 25 A polyesteramide is prepared as in Prepara¬ tion III-l with the following composition: poly- (1,4-tetramethylene 1,12-dodecanedioate) modified with 20 mol % adipic acid and 20 mol % 1,6-hexanedi- amine (I.V. » 1.23). The adipic acid and 1,6-hexane- diamine form the amide segment of the poly(ester¬ amide) . Pipe coextrusion gave a pipe of good appear- ance but marginal adhesion. Bottles blown from parisons made from the pipe showed unacceptable adhesion of the polyester and barrier polymer layers. OMPI

Claims: Claims : 1. A bonding composition for bonding polyesters and copolyesters to poly(vinyl alcohol) and copolymers thereof to form a laminate characterized in that said bonding composi¬ tion comprises a poly(esteramide) having a) a thin film deformation temperature transi¬ tion which is 1) greater than 70°C 2) not greater than 50°C lower nor 25°C higher than the glass transition temperature of the polyester or copolyester to be bonded and b) a T-peel strength in the laminate of at least 0.02 Kg/cm. 2. A bonding composition according to claim 1 wherein said poly(ester amide) contains 1) repeating units derived from an acid compon¬ ent which is at least 80 mol percent of a dicarboxyl¬ ic acid selected from pimelic, azelaic, sebacic acid or combinations thereof and optionally up to 20 mol percent of a second linear aliphatic dicarboxylic acid having at least four carbon atoms connected linearly between the two acid groups or an aromatic dicarboxylic acid and 2) repeating units derived from a diamine and glycol component which is from 5 mol percent to 20 mol percent of 1,2-ethanediamine and from 95 to 80 mol percent of a glycol selected from ethylene glycol, 1,4-butanediol, 1,4-cyclohexanedimethanol or combinations thereof. 3. A bonding composition according to claim 1 wherein said poly(ester amide) contains 1) repeating units derived from an acid compon¬ ent which is at least 70 mol percent of a dicarboxyl- ic acid selected from pimelic, azelaic, sebacic acid or combinations thereof and optionally up to 30 mol percent of a second linear aliphatic dicarboxylic acid having at least four carbon atoms connected linearly between the two acid groups or an aromatic dicarboxylic acid and 2) repeating units derived from a diamine and glycol component which is from 10 mol percent to 30 mol percent of a diamine selected from 1,6-hexanedi- amine, 1,4-cyclohexanebismethylamine or combinations thereof and from 90 to 70 mol percent of a glycol selected from ethylene glycol, 1,4-butanediol, 1,4-cyclohexanedimethanol or. combinations thereof. 4. A bonding composition according to claim 1 wherein said poly(ester amide) contains 1) repeating units derived from an acid compon¬ ent which is 70 to 90 mol percent of a dicarboxylic acid selected from adipic, pimelic, suberic, azelaic, sebacic acid or combinations thereof and 10 to 30 mol percent of a second linear aliphatic dicarboxylic acid having at least four carbon atoms connected linearly between the two acid groups or an aromatic dicarboxylic acid and 2) repeating units derived from a diamine and glycol component which is from 10 mol percent to 30 mol percent of a diamine selected from 1,6-hexanedi- amine, 1,4-cyclohexanebismethylamine or combinations thereof and from 90 to 70 mol percent of a glycol selected from ethylene glycol, 1,4-butanediol, 1,4-cyclohexanedimethanol or combinations thereof. 5. A laminate comprising a plyester or copolyester bound to poly(vinyl alcohol) or copoly- mers thereof with a bonding composition of any previous claim. 6. The laminate according to claim 5 wherein said polyester is poly(ethylene terephthal¬ ate). 7. The laminate according to claims 5-6 wherein said copolymer of vinyl alcohol is an ethyl- ene-vinyl alcohol copolymer having an ethylene content of 30 to 50 mole percent. 8. A container made from a laminate according to claims 5-7 wheren said polyester has been oriented.

Inventors: FAGERBURG DAVID RICHARD, SAND IRVING DANIEL, SHEPHERD FREDDIE ALLEN, WRIGHT BENNY WAYNE, FAGERBURG, DAVID, RICHARD, SAND, IRVING, DANIEL, SHEPHERD, FREDDIE, ALLEN, WRIGHT, BENNY, WAYNE
Applicants: EASTMAN KODAK CO, EASTMAN KODAK COMPANY
Application year: 1984
Main classification: B32B27
IPC codes: B32B27, C08G69, C08G73, C08J5, C08L67, C08L77, C09J177, C09J179