High temperature stable, low solvent swelling thermoplastic elastomer compositions

Abstract: Thermoplastic elastomer compositions com­ prise a blend of polyester resin and a covalently-­ crosslinked acrylate rubber. Such compositions can be prepared by dynamic vulcanization of the rubber in admixture with the polyester and can exhibit high temperature dimensional stability and low oil swell.

Description: Disclosed herein are inventions of thermoplastic elastomer compositions which exhibit low solvent swelling at high temperatures. Particularly disclosed are inventions of thermoplastic elastomer compositions comprising polyester and crosslinked acrylic ester copolymer rubber. BACKGROUND Unless indicated otherwise all temperatures herein are in degrees Celsius. Thermoplastics are compositions which can be molded or otherwise shaped and reprocessed at temperatures above their melting or softening point. Thermoplastic elastomers are materials which exhibit both thermoplastic and elastomeric properties, i.e. the materials can be processed as thermoplastics but have physical properties common to elastomers. Shaped articles may be formed from thermoplastic elastomers by extrusion, injection molding or compression molding without the time-consuming cure step required with conventional vulcanizates. Elimination of the time required to effect vulcanization provides significant manufacturing advantages. Further, thermoplastic elastomers can be reprocessed without the need for reclaiming and, in addition, many thermoplastic elastomers can be thermally welded. Non-polar rubbers, e.g. polybutadiene, random, graft and block copolymers of styrene and butadiene, EPDM rubber, natural rubber and polyisoprene, are readily mixable with non-polar thermoplastics such as polypropylene, polyethylene and polystyrene. Non-polar, highly unsaturated rubbers are generally not used at temperatures above about 125°; and non-polar thermoplastics have low melting points, e.g. about 120° for crystalline polyethylene, about 170° for crystalline polypropylene and about 105° for polystyrene. Thermoplastic elastomers based on non-polar, unsaturated rubbers and thermoplastics generally comprise stabilizers to achieve desired properties in high temperature applications. For instance, known thermoplastic elastomers, e.g. as disclosed in U.S. Patents 4,104,210; 4,130,535 and 4,311,628, based on blends of diene or EPDM rubber and polyolefins are generally used at temperatures below about 120°. Non-polar rubbers are generally used in applications free from extended exposure to solvent-like fluids such as automobile transmission fluid, motor oil, antifreeze, to avoid swelling and the possible resulting reduction in performance properties. Resistance to such swelling, especially for application temperatures below about 125°, can be achieved by use of polar rubbers, e.g. nitrile rubber, chlorinated polyethylene rubber and neoprene. Because polar rubbers are not generally miscible with non-polar thermoplastic polymers such as polypropylene, it is commonly necessary to provide compatibilization. See, for instance, U.S. Patent 4,555,546 which discloses blends of polyolefins, cured acrylic ester copolymer rubber and graft copolymer having polyolefin compatibilizing segments and rubber compatibilizing segments. Alternatively, as disclosed in U.S. Patent 4,141,863 polar rubbers can be blended with polar thermoplastics, e.g. polyamides, polyesters, polyacrylates, polycarbonates. Many of the more desired polar thermoplastic polymers melt at high temperature, for instance nylon 6 melts at about 225°. Since many preferred polar rubbers may tend to degrade when melt blended for extended periods with high melt temperature polar thermoplastics, resulting thermoplastic elastomer compositions may not have optimal properties. Fortunately, certain polar acrylate rubbers are exceptionally heat stable and can be useful in blends with thermoplastics. Such rubbers include acrylic ester copolymer rubbers, including ethylene/alkyl acrylate ester copolymer rubbers and functionalized, e.g. acid-modified, derivatives thereof. See, for instance, U.S. Patents 4,310,638; 4,327,199; and 4,473,683 which disclose blends of polar thermoplastic polymers, i.e. polyamides, polyesters and styrenic polymers, respectively, with acid-containing acrylic ester copolymer rubber that is neutralized, i.e. ionically crosslinked with magnesium or zinc oxide. While such blends exhibit enhanced thermal stability, they are susceptible to solvent swelling, especially at higher temperatures where the ionic crosslink bonding becomes labile. SUMMARY OF THE INVENTION This invention provides thermoplastic elastomer compositions comprising blends of polyester resin and a dynamically vulcanized covalently-crosslinked acrylate rubber. Such blends are preferably in a weight ratio of rubber to polyester of 9:1 to 4:6. Such thermoplastic elastomer compositions exhibit excellent high temperature dimensional stability and exceptional resistance to solvent swelling. In preferred embodiments such rubber is advantageously a functionalized olefin/acrylic ester copolymer rubber that is dynamically vulcanized, e.g. by a polyfunctional, covalently crosslinking agent. In preferred embodiments the polyester is advantageously a linear polyester such as a polyalkylene terephthalate, isophthalate or copolyester thereof, e.g. polyethylene terephthalate (PET) and polytetramethylene terephthalate (PBT). As used herein the term "elastomeric" refers to thermoplastic compositions which exhibit rubber-like elasticity, i.e. have a tension set of less than about 60 percent, preferably less than about 50 percent. DESCRIPTION OF PREFERRED EMBODIMENTS POLYESTER RESIN: Suitable thermoplastic polyester resin comprises linear, crystalline, high molecular weight solid polymers having recurring groups, including groups, within the polymer chain. The term "linear" as used herein with respect to polyester describes a polymer in which the recurring ester groups are within the polymer backbone and not pendant therefrom. Linear, crystalline polyesters having a softening point above 50°C are satisfactory; polyesters having a softening point or melting point above 100°C are preferred; and polyesters having a softening point or melting point between 160 and 280° are most preferred. Although saturated linear polyesters (i.e. free of olefinic unsaturation) are preferred, unsaturated polyesters may be used provided that the rubber is crosslinked prior to blending with the polyester or provided that the rubber is dynamically crosslinked with a crosslinking agent that will not significantly induce crosslinking in the polyester. Significantly crosslinked polyesters are unsatisfactory for the practice of this invention, resulting in compositions that are not thermoplastic. The term "crystalline" as used herein means that the polyester is at least partially crystallizable. For example, PET is crystallizable but may also exist as a substantially non-crystalline glassy polymer under many conditions. Many commercially available linear, crystalline thermoplastic polyesters, including polycarbonates, may be advantageously employed in the practice of this invention. Alternatively such polyesters may be prepared by polymerization of one or more dicarboxylic acids, anhydrides or esters and one or more diols or by polymerization of one or more lactones. Exemplary satisfactory polyesters include poly(trans-1,4-cyclohexylene C2-6 alkane dicarboxylates) such as poly(trans-1,4-cyclohexylene succinate) and poly(trans-1,4-cyclohexylene adipate), poly(cis or trans-1,4-cyclohexanedimethylene C0-2 alkanedicarboxylates) such as poly(cis-1,4-cyclohexanedimethylene oxalate) and poly(cis-1,4-cyclohexanedimethylene succinate), poly(C2-4 alkylene terephthalates) such as PET and PBT, poly(C2-4 alkylene isophthalates) such as polyethylene isophthalate and polytetramethylene isophthalate, poly(p-arylene C1-8 alkane dicarboxylates) such as poly(p-phenylene glutarate), poly(p-phenylene adipate), poly(p-xylene oxalate), poly (o-xylene oxalate), poly(p-phenylene di-C1-5 alkylene terephthalates) such as poly (p-phenylene dimethylene terephthalate) and poly(p-phenylene di-1,4-butylene terephthalate), polylactones such as poly(caprolactone) and other others as disclosed in U.S. Patent 4,141,863. Preferred polyesters employed in this invention are derived from phthalic acids, e.g. terephthalic acid or isophthalic acid; more preferred polyesters are poly(alkylene terephthalates), especially PET or PBT or mixed polyphthalates derived from two or more glycols, two or more phthalic acids, or a mixture thereof such as poly(alkylene tere-co-isophthalates). ACRYLATE RUBBER: Acrylate rubbers advantageously useful in the thermoplastic elastomer compositions of this invention comprise vulcanizable, i.e. crosslinkable, acrylate rubbers such as polyacrylate rubbers and acrylic ester copolymer rubbers. Suitable polyacrylate rubbers are described in Rubber World Blue Book, 1987 Edition, at pages 393-394, and can have functional groups, e.g. acid, hydroxy, epoxy or other functional groups, as crosslinking sites; alternatively, acid group crosslinking sites can be generated in the rubber, e.g. by partial hydrolysis of ester groups. In many embodiments olefin/acrylic ester copolymer rubbers are preferred. Such rubbers can be copolymers produced by polymerizing at least one alpha olefin with at least one C₁-C₁₈ alkyl (meth)acrylate and, optionally, a minor amount of an unsaturated functionalized monomer which can provide crosslinking sites. Such functionalized monomer can comprise acid, hydroxy, epoxy, isocyanate, amine, oxazoline, diene or other reactive groups. In the absence of such functionalized monomer, crosslinking sites can be generated, e.g. by partial hydrolysis of ester groups of the rubber. Suitable alpha olefins for polymerization of such copolymer rubbers include ethylene, propylene, butene-1, isobutylene, pentenes, heptenes and octenes or mixtures thereof; C₁-C₄ alpha olefins are preferred and ethylene is often most preferred. Suitable alkyl (meth)acrylates for copolymerizing with the alkene include methyl acrylate, ethyl acrylate, t-butyl acrylate, n-butyl acrylate, 2-ethylhexyl acrylate, methyl methacrylate, ethyl methacrylate and n-butyl methacrylate; or a mixture thereof; C₁-C₁₂ alkyl (meth)acrylates are often preferred, and C₁-C₄ alkyl (meth)acrylates are most often preferred. In many cases a preferred olefin/acrylic ester copolymer rubber comprises unsaturated carboxylic acid monomer units, such as acid units, e.g. derived from (meth)acrylic acid or maleic acid, anhydride units, e.g. derived from maleic anhydride or partial ester units, e.g. derived from mono ethyl maleate. In many cases a preferred olefin/acrylic ester copolymer rubber is a terpolymer of ethylene, C₁-C₄ alkyl acrylate and an acidic monomer unit; more preferably such terpolymer comprises at least about 30 mole percent of ethylene, 10 to 69.5 mole percent of methyl acrylate and 0.5 to 10 mole percent mono ethyl maleate and 0.1 - 25 mole percent carboxylic acid. In all cases it is preferred that the acrylate rubber be essentially non-crystalline and have a glass transition temperature (T g ) below room temperature, i.e. below about 23°. CROSSLINKING AGENTS: Crosslinking agents employed in the thermoplastic elastomer compositions of this invention are polyfunctional, i.e. at least difunctional, compounds selected to cure the acrylate rubber, i.e. crosslink the rubber, by covalently bonding with the reactive functional groups of the rubber. When the rubber has carboxy functional groups, e.g. derived from acrylic or maleic acid units, the covalent crosslinking agent is advantageously a compound with an hydroxy, amine, isocyanate, epoxy or other acid reactive functional group. Effective crosslinking agents include diols such as bisphenol-A, polyols such as pentaerythritol, amines such as methylene dianiline and diphenyl guanidine, isocyanates such as toluene di-isocyanate and isocyanate-terminated polyester prepolymer and epoxides such diglycidyl ether of bisphenol-A. Generally, the amount of crosslinking agent does not exceed about 15 percent by weight of the acrylate rubber, depending on the molecular weight of the rubber and crosslinking agent. Preferred amounts of crosslinking agent are readily determined by routine experimentation to optimize desired properties of the thermoplastic elastomer compositions of this invention. The amount of crosslinking agent and the degree of crosslinking can be characterized in terms of the amount of rubber that is extractable from a thermoplastic elastomer composition. As used herein the term "extractable" refers to rubber that is extractable from a thermoplastic elastomer composition comprising a blend of a thermoplastic polyester resin and a covalently-crosslinked acrylate rubber. Rubber can be extractable, e.g. because of a low level of crosslinking agent and/or because it comprises a non-crosslinkable fraction. Extractable rubber is conveniently determined by the weight loss from thin (about 0.2 mm) pressed films of thermoplastic elastomer compositions after immersion for 48 hours in a solvent (at 23°). Such solvent is selected as one in which the rubber is substantially soluble and in which the polyester is substantially insoluble. Such solvents can include dichloromethane, toluene and tetrahydrofuran. Some preferred thermoplastic elastomer compositions will comprise sufficient crosslinking agent so that, after crosslinking, e.g. by dynamic vulcanization, no more than about 50 percent of the rubber is extractable. In other compositions, more desirable properties are achieved when not more than about 30 percent of the rubber is extractable. In still other compositions desirable properties are achieved when not more than about 20 percent of the rubber is extractable. PLASTICIZER: In certain aspects of this invention thermoplastic elastomer compositions also comprise plasticizer which extends the range of proportions of polyester to rubber in the composition while still retaining elastomeric properties. For example, without plasticizer the weight ratio of rubber to polyester generally cannot be less than about 4:6 without losing rubber-like elasticity; whereas, with plasticizer the weight of polyester can be increased. Moreover, in certain preferred aspects of this invention the incorporation of plasticizers can improve the composition's resistance to oil swelling, its heat stability, and reduce hysteresis, cost and permanent set. Generally, the quantity of plasticizer, when present, is between about 10 and 50 parts by weight of the composition. Suitable plasticizers include phthalate esters such as dicyclohexyl phthalate, dimethyl phthalate, dioctyl phthalate, butyl benzyl phthalate and benzyl phthalate; phosphates such as tributoxyethyl phosphate, tributyl phosphate, tricresyl phosphate, cresyl diphenyl phosphate, 2-ethylhexyl diphenyl phosphate, isodecyl diphenyl phosphate and triphenyl phosphate; trimellitate esters such as C1-C9 alkyl trimellitate; sulfonamides such as N-cyclohexyl-p-toluenesulfonamide, N-ethyl-o,p-toluenesulfonamide and o-toluenesulfonamide, epoxidized oils and liquid oligomeric plasticizers. Preferred plasticizers are liquids with low volatility to avoid emissions of plasticizer at the common melt temperatures of polyesters. The trimellitates and epoxidized oils are examples of commonly preferred plasticizers having low volatility. FILLERS: The properties of the thermoplastic elastomer compositions of this invention can be modified, by addition of fillers such as clay, silica, talc which improve resistance to oil swelling. Such fillers are desirably incorporated into the rubber phase, especially when the polyester is highly crystalline, to avoid imparting undue rigidity to the composition. Other ingredients can include those commonly employed in the compounding of thermoplastics and rubbers such as carbon black, titanium dioxide, pigments, zinc oxide, stearic acid, accelerators, stabilizers, antidegradants, processing aids, prevulcanization inhibitors, fire retardants and coupling agents. Properties can be affected depending on when the filler is added, e.g. before or after vulcanization of the acrylate rubber. Carbon black, which can improve tensile strength, is desirably added prior to dynamic vulcanization, for instance in a masterbatch with the acrylate rubber. Stabilizers are often desirably added after dynamic vulcanization to provide lower oil swell. Desirable amounts and methods of addition of fillers, e.g. at up to about the parts by weight of rubber and polyester, and other ingredients can be readily ascertained through routine experimentation by one skilled in the art of compounding aided by the illustrative teachings in the following examples. PREPARATION OF THERMOPLASTIC ELASTOMER COMPOSITIONS: Vulcanizable rubbers, although thermoplastic in the unvulcanized state, are often classified as thermosets because they can be cured to an unprocessable state. The improved thermoplastic elastomer compositions of this invention are processable as thermoplastics and are preferrably prepared from blends of polyester resin and vulcanizable acrylate rubber which are treated under time and temperature conditions to crosslink the rubber. Simultaneously masticating and curing such blends advantageously provides the thermoplastic compositions of this invention and avoids the production of thermosets. Thus, the thermoplastic elastomer compositions of this invention are preferably prepared by blending a mixture of vulcanizable acrylate rubber and a polyester resin at a temperature above the melting point of the polyester, adding crosslinking agent, then masticating the blend at a temperature sufficient to effect crosslink formation, using conventional masticating equipment, for example, a rubber mill, Brabender Mixer, Banbury Mixer, or a mixing extruder such as a twin screw continuous mixing extruder. The polyester resin and vulcanizable rubber are mixed at a temperature sufficient to soften the resin or, more commonly, at temperature above the melting point of the polyester resin. In many cases crosslinking agent is added after the molten polyester resin and vulcanizable rubber are intimately mixed. In other cases, e.g. where a late or delayed acting curative is employed, crosslinking agent can be added prior to intimate melt mixing of the polyester resin and the rubber. Heating and masticating at vulcanization temperatures are generally adequate to complete the crosslink formation in a few minutes or less; if shorter times are desired, higher temperatures may be used. Mastication is preferably continued for a short time after the composition reaches maximum consistency, e.g. as indicated by maximum torque exerted by the mixer. Typically, mixing times of about 0.5-30 minutes are satisfactory. When isocyanates, e.g. isocyanate-terminated polyester prepolymers, are used as crosslinking agents, mixing time can be substantially reduced by incorporation of a crosslinking accelerator such as magnesium stearate. Accordingly, also provided is an invention of an improved method for crosslinking rubbers with isocyanate functionalized compounds by crosslinking in the presence of a carboxylic acid salt of magnesium, e.g. magnesium stearate. A suitable range of temperatures for crosslink formation is from about the melting point of the polyester resin to the decomposition temperature of the rubber which range is from 100° to 350° with the maximum temperature varying somewhat depending upon the component polyester and rubber, the presence of antidegradants and the mixing time. Typically, the range is from 150° to 300°. A preferred range is from 180° to 280°. To obtain thermoplastic compositions, it is important that mixing continues without interruption until substantial crosslinking occurs. If appreciable crosslinking is allowed after mixing has stopped, a thermoset unprocessable composition may be obtained. A few simple experiments within the skill of practitioners in the art utilizing available polyester resins, vulcanizable acrylate rubbers and crosslinking agents will suffice to determine their applicability for the preparation of the improved products of this invention. The rubber can be fully dynamically vulcanized in the absence of the polyester resin, powdered, and mixed with the resin at a temperature above the melting or softening point of the polyester resin. Provided that the crosslinked rubber particles are small, e.g. not greater than about 50 micrometers (microns), well dispersed and in an appropriate concentration, the compositions of this invention are attainable by blending crosslinked rubber with polyester resin. A mixture which is outside the invention because it contains poorly dispersed or too large rubber particles can be comminuted by cold milling to reduce the weight average particle size to below about 50 microns, preferably to below about 20 microns, more preferably to below about 10 microns and even more preferably to below about 5 microns. After sufficient comminution or pulverization, a composition of this invention can be obtained. Frequently, a composition of poor dispersion or too large particle size is visibly obvious to the naked eye and observable in a molded sheet, especially in the absence of pigments and fillers; such compositions are outside the scope of this invention. The characteristics of thermoplastic elastomer compositions containing cured acrylate rubber depend upon the relative proportions of rubber and polyester. Static curing can give thermoset compositions when the blend contains more than 30 parts of cured acrylate rubber per 100 parts by weight of rubber and polyester; whereas, dynamic curing of blends containing even up to 90 parts by of cured acrylate rubber per 100 parts of rubber and polyester generally provides thermoplastic compositions. When such high rubber compositions are partially crosslinked, the rubber and polyester can comprise co-continuous phases. Generally, compositions comprising about 40 parts or more of cured acrylate rubber per 100 parts of rubber and polyester are thermoplastic and elastomeric. Moreover, unplasticized compositions comprising less than about 35 parts of cured acrylate rubber per 100 parts rubber and polyester can be considered to be toughened thermoplastics. The effect of the relative proportions on blend composition characteristics cannot be defined with precision because the limits vary depending upon a number of factors, such as, the kind of polyester and acrylate rubber, the presence of fillers, plasticizers and other ingredients, and the extent the rubber is cured. Of course, it is understood that the properties of the compositions of the invention may be modified by the addition of ingredients which are conventional in the compounding of polyesters, acrylate rubbers, and blends thereof. For additional information concerning compounding and dynamic vulcanization, refer to U. S. Patents 4,104,210; 4,130,535 and 4,141,863. The term "blend" as used herein means a mixture ranging from small particles of crosslinked rubber well dispersed in a polyester matrix to co-continuous phases of polyester and a partially-crosslinked rubber. Compositions prepared by dynamic vulcanization comprising a blend of polyester, e.g. PBT, and cured acrylate rubber, e.g. acrylic ester copolymer rubber, in the form of small particles dispersed throughout the polyester are preferred. Especially preferred are such compositions comprising such rubber and polyester in the range of 20 to 60 parts of polyester per 100 parts of rubber and polyester, more preferably less than about 55 parts of polyester. Thermoplastic elastomer compositions of this invention can be used to form a variety of molded, extruded, or calendered articles. The properties of such compositions depend upon the proportions of the components with a wide range of properties being available simply by varying such proportions. The following disclosure is provided to illustrate specific embodiments and aspects of the thermoplastic elastomer composition of this invention. The tensile properties of such compositions were determined in accordance with ASTM procedure D 638. Unless otherwise indicated specimens were pulled in a tensile tester at 50.8 cm. (20 inches) per minute to failure. Ultimate tensile stress (UTS) is the tensile strength at break and is reported in units of megaPascals (MPa). Tensile modulus at 100 percent elongation (M100) and tensile modulus at 300 percent elongation (M300) are reported in MPa. Ultimate elongation (UE) is the elongation at break and is reported as a percent of the original specimen length. Hardness (H) is reported as a Shore A hardness (A) or a Shore D hardness (D). Tension set (TS) is the extension remaining after a specimen has been stretched and held for 10 minutes at twice its original length, then allowed to retract; TS is measured as the percentage increase of the original length after 10 minutes of retraction. Oil swell (OS) is determined in accordance with ASTM procedure D 471; OS is the measured increase in specimen mass after immersion in hot oil, expressed as a percentage of original mass. Unless otherwise indicated, e.g. by a temperature in parentheses or otherwise, specimens were immersed for 70 hours in ASTM Reference Oil No. 3 at 150°. Low temperature brittle point (LTB) is determined in accordance with ASTM procedure D 746; LTB is the temperature at which the specimen fractured by brittle failure upon impact, reported in degrees Celsius. Materials used in the following examples include: Polyesters: PE-1: Gafite 1600A PBT from GAF; PE-2: Vituf 4302 mixed polyester of propane diol, butane diol and terephthalic acid and/or isophthalic acid from Goodyear, melting point: 208°; PE-3: Vitel 5126 mixed polyester from Goodyear, similar to Vituf 4302, except melting point is 174 C; PE-4: Hytrel G4074 block copolymer of PBT and polyether from DuPont; PE-5: Merlon M40F polycarbonate from Mobay; PE-6: Tenite 6P20A PBT from Eastman Kodak; PE-7: Cleartuf 1006 PET from Goodyear; and PE-8: Kodar PM6763 PETG from Eastman Kodak. Acrylate Rubbers: R-1: VAMAC-G neat terpolymer of about 73 mole percent of ethylene, about 26 mole percent of methyl acrylate and about one mole percent of carboxylic acid from DuPont; R-2: VAMAC-123 masterbatch of 100 parts of VAMAC-G 20 parts of fumed silica and 3 parts of stabilizers and processing aids; and R-3: Hycar 4404 hydroxy functionalized acrylate rubber from B. F. Goodrich. Crosslinking agents: XL-1: Mondur E-501 isocyanate-terminated polyester prepolymer from Mobay, about 19 percent NCO; XL-2: magnesium oxide; XL-3: 4,4′-methylene dianiline; XL-4: Diphenyl guanidine; XL-5: Pentaerythritol; and XL-6: Epon 828 di-glycidyl ether of bisphenol-A from Shell. Stabilizers: S-1: mixture of 0.4 pbw Ethanox 330 from Ethyl Corp., 0.3 pbw calcium stearate and 0.2 pbw disterylthiodipropionate; S-2: Naugard 445 amine antioxidant from Uniroyal; S-3: mixture of 1 pbw Irganox MD 1024 and 1 pbw Irganox 1098 antioxidants from Ciba-Geigy; and S-4: S-1, where Ethanox 330 is replaced with Topanol CA from ICI. Processing aids: MgS: Magnesium stearate. Fillers: F-1: Hysil 233 fumed silica from PPG Industries; F-2: Icecap K clay from Burgess Pigment Co.; F-3: Mistron Vapor talc from Cyprus Minerals Co.; F-4: Burgess KE clay from Burgess Pigment Co.; F-5: Cabosil TS-720 silica from Cabot Corp. Coupling Agents: C-1: LICA-12 from Kenrich Petrochemicals. Plasticizers: P-1: Santicizer 79-TM alkyl trimellitate plasticizer from Monsanto Chemical Company; P-2: Paraflex G-62 epoxidized soy bean oil from C. P. Hall Co. EXAMPLE 1 This example serves to illustrate thermoplastic elastomer compositions of this invention comprising polyester PE-1, acrylic ester copolymer rubber R-1 and varying amounts of isocyanate-terminated polyester prepolymer crosslinking agent XL-1. Controlling the degree of crosslinking, indicated by the amount of the composition, e.g. rubber, extractable in a solvent affords tailoring compositions to achieve a desired balance of properties. Compositions according to this invention comprising isocyanate-terminated polyester prepolymer crosslinking agent were prepared by melt mixing the polyester PE-1 and rubber R-1 (containing 0.9 parts stabilizer S-1 per 100 parts rubber) at 100 rpm and 240° in a Brabender mixer; after 3 minutes the isocyanate crosslinking agent XL-1 and magnesium stearate were added to the blends which were dynamically vulcanized by continued mixing for an additional 3-4 minutes after maximum consistency was reached; the blend stocks were removed, cooled then returned to the Brabender for an additional 1-2 minutes of mixing; then the stocks were cooled and compression molded at 250°. Tensile properties of specimens are evaluated on a T-500 Tensometer at a speed of 20 inches (50.8 cm) per minute. The degree of crosslinking is determined from pressed films of each composition. Films, about 0.2 mm thick, were immersed in dichloromethane at about 23° for about 48 hours. The weight loss of the composition is divided by the weight of original rubber in the composition to determine extractable rubber (Extract). The analytical results indicate that compositions having not more than about 30 percent extractable rubber are sufficiently highly crosslinked to provide thermoplastic elastomer compositions of preferred properties. R-1 60 60 60 60 60 60 60 60 60 60 PE-1 40 40 40 40 40 40 40 40 40 40 XL-1 0 0.6 1.2 1.8 2.4 3.0 3.6 4.8 6.0 7.2 S-4 0.54 0.54 0.54 0.54 0.54 0.54 0.54 0.54 0.54 0.54 MgS 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 0.3 UTS .2 2.6 5.2 12.1 14.1 20.6 21.4 21.5 22.2 23.5 M100 .7 .8 2 8.2 9.7 10.5 11.9 11.0 11.5 11.2 M300 .1 1.2 5.3 -- 14.1 18.1 19.6 20.3 20.8 22.2 UE 860 1300 460 280 300 390 350 330 320 340 H 54A 40A 56A 78A 87A 34D 37D 40D 40D 42D TS Broke 18 13 29 34 35 40 37 38 37 OS 90 90 74 60 44 40 36 35 35 LTB -34 -54 -60 -60 <-60 <-60 <-60 <-60 <-60 <-60 Extract 99 70 43 27 23 16 14 13 10 4 EXAMPLE 2 This example serves to illustrate thermoplastic elastomer compositions of this invention over a range of rubber levels, e.g. with a rubber to polyester ratio from 9:1 to 4:6, having enhanced properties, e.g. UTS, UE, H, TS, OS, and/or LTB, as compared to prior art compositions comprising no crosslinking agent or ionomeric crosslinking agent such as magnesium oxide. Prior art compositions without crosslinking agent were prepared by melt mixing polyester PE-1 and acrylic ester copolymer rubber R-1 containing 0.9 parts stabilizer S-1 per 100 parts rubber at 100 rpm and 240° for 10 minutes in a Brabender mixer; the blend stocks were removed, cooled then returned to the mixer and remixed for one additional minute; then the blend stocks were removed and compression molded at 250°. Prior art compositions comprising ionomeric crosslinking agents were prepared by melt mixing the polyester and rubber at 100 rpm and 240° in a Brabender mixer; after 2 minutes magnesium oxide XL-2 and magnesium stearate were added to the blends which were dynamically vulcanized by continued mixing for an additional 10 minutes or until 3 minutes after maximum consistency is reached; then the stocks were cooled, remixed for 1-2 minutes and then compression molded at 280°. Compositions according to this invention comprising isocyanate-terminated polyester prepolymer crosslinking agent were prepared by melt mixing the polyester and rubber at 100 rpm and 240° in a Brabender mixer; after 3 minutes the isocyanate crosslinking agent XL-1 and magnesium stearate were added to the blends which were dynamically vulcanized by continued mixing for an additional 3-4 minutes after maximum consistency was reached; the blend stocks were removed, cooled then returned to the Brabender for an additional 1-2 minutes of mixing; then the stocks were cooled and compression molded at 250°. Tensile properties of specimens are evaluated on a T-500 Tensometer at a speed of 20 inches (50.8 cm) per minute. The data shows that tensile properties are improved by vulcanization. The data also shows that properties are enhanced by use of a covalently crosslinking agent as compared to an ionomeric crosslinking agent. For instance, lower hardness, often with higher elongation, can be provided in compositions having a rubber:polyester ratio of 9:1; lower hardness can be provided in compositions having a rubber:polyester ratio of 8:2; lower oil swell can be provided in compositions having a rubber:polyester ratio of 8:2 or less; and higher tensile properties can be provided in compositions having a rubber: polyester ratio of 6:4 or less. R-1 90 90 90 90 90 90 PE-1 10 10 10 10 10 10 XL-1 0 0 1.35 1.8 2.7 3.6 XL-2 0 2.7 0 0 0 0 MgS 0 0.45 0.45 0.45 0.45 0.45 S-1 0.81 0.81 0.81 0.81 0.81 0.81 UTS 0.3 13.6 5.9 7.4 6.3 4.1 M100 0.3 2.3 0.6 0.6 1.0 1.7 M300 0.3 7.9 0.6 0.8 3.2 -- UE 850 530 1400 1120 490 220 H 17A 53A 26A 28A 35A 44A TS 40 2 16 13 7 6 OS -- 109 139 128 121 109 LTB -- <-60 <-60 <-60 <-60 <-60 R-1 80 80 80 80 80 80 PE-1 20 20 20 20 20 20 XL-1 0 0 1.6 2.4 3.2 4.0 XL-2 0 2.4 0 0 0 0 MgS 0 0.4 0.4 0.4 0.4 0.4 S-1 0.72 0.72 0.72 0.72 0.72 0.72 UTS 0.3 14.2 7.5 9.0 7.9 8.6 M100 0.3 4.7 0.8 1.7 2.7 5.7 M300 0.3 11.4 2.3 5.4 -- -- UE 790 450 930 570 260 170 H 25A 62A 35A 46A 52A 62A TS 42 5 9 8 5 7 OS -- 98 118 108 94 69 LTB -- <-60 <-60 <-60 <-60 <-60 R-1 70 70 70 70 70 PE-1 30 30 30 30 30 XL-1 0 0 2.8 4.2 5.6 XL-2 0 2.1 0 0 0 MgS 0 0.35 0.35 0.35 0.35 S-1 0.63 0.63 0.63 0.63 0.63 UTS 0.3 20.1 14.7 14.2 15.0 M100 0.4 9.4 6.7 8.4 7.8 M300 0.4 164 -- -- -- UE 650 510 270 230 270 H 45A 80A 75A 85A 84A TS 47 13 15 20 17 OS -- 66 66 53 48 LTB -- -60 <-60 <-60 <-60 R-1 60 60 60 60 60 PE-1 40 40 40 40 40 XL-1 0 0 3.6 4.8 6.0 XL-2 0 1.8 0 0 0 MgS 0 0.3 0.3 0.3 0.3 S-1 0.54 0.54 0.54 0.54 0.54 UTS 0.1 19.6 20.8 21.9 24.4 M100 1.0 11.8 12.6 11.0 10.6 M300 0.5 18.2 -- 20.8 19.6 UE 570 430 260 320 370 H 63A 36D 40D 40D 41D TS -- 26 35 35 34 OS -- 45 37 35 34 LTB --- 54 <-60 <-60 <-60 R-1 50 50 50 50 50 50 PE-1 50 50 50 50 50 50 XL-1 0 0 0 0 4.0 5.0 XL-2 0 .5 1.5 4 0 0 MgS 0 0.25 0.25 0.25 0.25 0.25 S-1 0.45 0.45 0.45 0.45 0.45 0.45 UTS 0.2 10.6 18.2 16.8 26.8 25.8 M100 0.3 9.5 14.7 16.2 14.3 14.4 M300 -- -- 18 -- 17.7 21.3 UE 130 200 390 130 390 380 H 79A 39D 44D 48D 46D 51D TS -- 51 39 37 50 52 OS -- 39 31 37 50 23 LTB -- -50 -44 -40 <-60 <-60 R-2 40 40 40 40 PE-1 60 60 60 60 XL-1 0 0 3.2 4.0 XL-2 0 1.2 0 0 MgS 0 0.2 0.2 0.2 S-1 0.36 0.36 0.36 0.36 UTS 13.7 19.8 28.7 26 M100 -- 18.4 17.3 17.7 M300 -- 19.5 21.2 21.1 UE 12 310 420 410 H 47D 54D 58D 56D TS -- 60 67 70 OS -- 22 18 16 LTB -- -40 -60 -60 EXAMPLE 3 This example serves to illustrate thermoplastic elastomer compositions based on a variety of polyesters, including the mixed polyesters PE-2 and PE-3, block polyether-polyester PE-4 and polycarbonate PE-5. The polyesters were combined with acrylic ester copolymer rubber R-2 and various crosslinkers in the proportions specified in Table 3 essentially in the manner of Examples 1 and 2. The analytical results reported in Table 3 indicate that thermoplastic elastomer compositions according to this invention can be prepared from a variety of polyesters. R-2 73.8 123 73.8 73.8 PE-2 40 0 0 0 PE-3 0 100 0 0 PE-4 0 0 40 0 PE-5 0 0 0 40 XL-1 0 10 4 0 XL-2 0 0 0 0 XL-3 .75 0 0 .75 XL-4 2.4 0 0 2.4 MgS 0 .5 0 0 S-2 0 0 1 0 UTS 7.45 23.1 9.3 11.9 M100 6.07 9.1 4.7 2.7 M300 -- 19.2 -- -- UE 180 390 190 410 H 35D 91A 70A 60A TS 15 22 9 15 OS -- 32 38 -- LTB -- <-60 -- -- EXAMPLE 4 This example serves to illustrate thermoplastic elastomer compositions dynamically vulcanized with covalently crosslinking agents exhibiting enhanced resistance to oil swell as compared to compositions dynamically vulcanized with ionically crosslinking agents. The compositions were prepared essentially in the manner of Examples 1 and 2. The analytical results reported in Table 4 indicate that covalently crosslinking agents can be used to provide thermoplastic elastomer compositions with higher tensile properties and higher resistance to oil swell. R-2 73.8 73.8 73.8 73.8 73.8 PE-6 40 40 40 40 40 XL-1 0 0 0 0 2.4 XL-2 1.8 0 0 0 0 XL-3 0 0 .6 1.2 0 XL-5 0 0 .6 0 0 XL-6 0 0.9 0 0 0 S-2 .6 .6 .6 .6 .6 UTS 17.7 19.3 23.0 22.8 25.6 M100 13.3 10.1 12.6 13.0 13.9 M300 17.6 -- -- -- -- UE 320 270 260 260 290 H 40D 36D 38D 39D 41D TS 23 27 29 29 36 OS (125°) 24 23 20 19 17 OS (150°) 30 27 23 22 20 EXAMPLE 5 This example serves to illustrate thermoplastic elastomer compositions dynamically vulcanized with covalently crosslinking agents exhibiting enhanced properties at elevated molding temperatures as compared to compositions dynamically vulcanized with ionically crosslinking agents. The compositions were prepared with the components indicated in Table 5 essentially as the manner of Examples 1 and 2. The resulting thermoplastic elastomer compositions were molded into test specimens at mold temperatures of both 250° and 280°. The analytical results reported in Table 5 indicate that covalently crosslinking agents provide thermoplastic elastomer compositions which exhibit better retention of tensile properties, resistance to oil swell and low temperature brittle point than do compositions prepared from ionically crosslinking agents. R-2 61.5 61.5 61.5 61.5 PE-1 50 50 50 50 XL-1 0 0 5 5 XL-2 1 1 0 0 MgS 0 0 .25 .25 S-4 .45 .45 .45 .45 T mold 250 280 250 280 UTS 21.8 16.1 28.2 26.9 M100 18.4 16.1 14.6 14.8 UE 260 100 320 290 H 49D 48D 49D 49D TS 35 27 42 33 OS (150°) 27 28 19 19 LTB -54 -40 -60 -60 EXAMPLE 6 This example serves to illustrate thermoplastic elastomer compositions comprising a variety of fillers. The compositions were prepared from the materials in the amounts indicated in Table 6 essentially in the manner of Examples 1 and 2. Molded specimens of each composition were aged in hot (150°) air for 168 hours. The analytical results reported in Table 6 indicate the effect of fillers on tensile properties, hardness, tension set, oil swell, low temperature brittle point and retention of properties after hot air aging. R-2 123 123 123 123 123 123 PE-1 66.7 66.7 66.7 66.7 66.7 66.7 XL-1 6 6 6 6 0 6 XL-6 0 0 0 0 8 0 S-3 .6 .6 .6 .6 .6 .6 MgS 1 1 1 1 1 1 F-1 0 20 0 0 0 0 F-2 0 0 20 0 0 0 F-3 0 0 0 20 0 0 F-4 0 0 0 0 20 0 F-5 0 0 0 0 0 20 As Molded: UTS 21.8 24.1 19.2 18.0 24.2 22.8 M100 12.7 18.0 13.7 13.4 19.9 19.0 UE 240 180 210 170 140 150 H 39D 40D 36D 37D 48D 40D TS 32 29 26 31 38 32 OS (125°) 23 22 23 22 10 10 OS (150°) 27 27 27 27 20 22 LTB -60 -50 -60 -38 -60 -50 Hot Air Aged: UTS 22.9 25.7 21.2 23.0 23.0 23.6 M100 15.9 24.3 19.7 18.2 23.0 23.6 UE 200 120 140 110 100 100 H 42D 48D 45D 44D 51D 47D EXAMPLE 7 This example serves to illustrate thermoplastic elastomer compositions of exceptional resistance to oil swell. Such compositions comprise silica filler and a high level of plasticizer. The compositions were prepared from the materials in the amounts indicated in Table 7. The compositions were prepared essentially in the manner of Examples 1 and 2, except that 100 parts of rubber R-1 was preblended with 20 parts of silica and 0.2 parts of coupling agent to provide a rubber masterbatch which was melt mixed with polyester PE-1 and plasticizer at 100 rpm and 240°. After crosslinking agent was added, mixing was continued until maximum consistency was observed, then stabilizer was added and mixing continued for about 4 minutes. Analytical results for specimens of each composition are reported in Table 7 indicating that thermoplastic elastomer compositions can be provided which exhibit low oil swell. R-1 100 100 100 100 100 F-1 20 20 20 20 20 C-1 .2 .2 .2 .2 .2 PE-1 66.7 66.7 66.7 66.7 66.7 XL-1 8 8 8 8 8 MgS .5 .5 .5 .5 .5 P-1 0 20 20 40 55 P-2 0 0 20 0 5 S-4 .9 .9 .9 .9 .9 UTS 25.2 19.8 18.4 16.1 13.8 M100 14.0 11.3 10.5 7.1 6.7 M300 24.3 17.7 -- 15.1 -- UE 320 330 210 330 230 H 43D 89A 84A 85A 85A TS 40 40 27 26 20 OS (125°) 30 20 17 14 6 OS (150°) 35 25 20 20 11 LTB -60 -60 -60 -60 -60 EXAMPLE 8 This example serves to illustrate thermoplastic elastomer compositions of this invention prepared with PE-7, a crystallizable PET polyester, as compared to compositions prepared from PE-8, an amorphous PETG polyester. Compositions were prepared with the components indicated in Table 8 essentially in the manner of Examples 1 and 2. The resulting compositions were molded into test specimens for analysis of thermoplastic elastomer properties. The analytical results reported in Table 8 indicate that thermoplastic elastomer compositions of low oil swell can be prepared from PET. Those results also indicate that compositions prepared from the amorphous PETG polyester may not be advantageous. For instance, those comprising ionomeric crosslinking agent exhibited high oil swell and those comprising covalent crosslinking agent were not elastomeric, i.e. exhibited tensile set of 86 percent. R-1 60 60 60 60 60 60 60 60 60 60 PE-7 0 0 0 40 40 40 40 40 40 40 PE-8 40 40 40 0 0 0 0 0 0 0 XL-1 0 0 0 6 0 0 2.4 3.6 4.8 7.2 XL-2 0 1.8 0 0 .6 1.8 0 0 0 0 MgS 0 .3 .3 0 .3 .3 .3 .3 .3 .3 S-4 .54 .54 .54 .54 .54 .54. .54 .54 .54 .54 UTS .1 15.9 13.2 .1 6.3 13.7 16.8 18.0 18.7 26.6 M100 .5 11.0 9.2 .5 4.5 10.8 12.3 12.8 9.4 13.0 M300 .3 15.0 12.8 .3 6.1 12.7 -- -- 7.4 23.8 UE 900 350 410 820 410 380 170 200 320 330 H 30A 82A 38D 28A 63A 68A 37D 36D 37D 37D TS 47 42 86 47 8 12 39 37 40 42 OS (125°) -- 66 61 -- 63 61 38 36 34 32 OS (150°) -- 82 72 -- 79 76 40 41 37 34 LTB >-50 -54 -60 >-50 >-50 -52 -58 <-60 <-60 <-60 EXAMPLE 9 This example serves to illustrate thermoplastic elastomer compositions prepared from an hydroxy functionalized acrylate rubber, R-3. The compositions were prepared with the components indicated in Table 9 essentially in the manner of Examples 1 and 2. The resulting compositions were molded into test specimens. The analytical results reported in Table 9 indicate that such hydroxy functionalized acrylate rubber can be used to provide thermoplastic elastomer compositions exhibiting exceptionally low oil swell. R-3 60 60 PE-1 40 40 XL-1 0 3 MgS .54 .54 UTS 2.4 15.3 M100 2.4 12.3 UE 130 160 H 64A 37D TS Failed 43 OS (125°) 48 23 OS (150°) 55 25 OS (175°) 74 33 LTB -34 -44

Claims: A thermoplastic elastomer composition comprising a blend of a thermoplastic polyester resin and a dynamically vulcanized, covalently-crosslinked, acrylate rubber. A composition according to claim 1, wherein said polyester comprises a polyalkylene terephthalate. A composition according to Claim 1, wherein said polyester comprises polyethylene terephthalate or polybutylene terephthalate or a mixture or copolymer thereof. A composition according to Claim 1, wherein said polyester comprises polyethylene terephthalate. A composition according to any of the preceding claims, wherein no more than 50 percent of said rubber is extractable. A composition according to Claim 5, wherein no more than 30 percent of said rubber is extractable. A composition according to Claim 5, wherein no more than 20 percent of said rubber is extractable. A composition according to any of the preceding claims, wherein said rubber is a polyacrylate rubber with acid, hydroxy or epoxy groups as crosslinking sites. A composition according to any of the preceding claims, wherein said acrylate rubber is an olefin/acrylic ester copolymer rubber. A composition according to any of Claims 1 to 7, wherein said rubber is a covalently-crosslinked, acid-containing, acrylic ester/olefin copolymer rubber. A composition according to Claim 10, wherein said rubber comprises 0.1-25 mole percent carboxylic acid. A composition according to any of the preceding claims, wherein said copolymer rubber is covalently crosslinked by a crosslinking agent comprising a polyamine, a polyisocyanate or a polyepoxide. A composition according to Claim 12, wherein said crosslinking agent comprises an isocyanate-terminated polyester prepolymer. A composition according to any of the preceding claims, wherein said rubber comprises a copolymer of ethylene, alkyl acrylate and unsaturated carboxylic acid. A composition according to any of the preceding claims, wherein said composition comprises 10 to 60 parts of said polyester per 100 parts of rubber and polyester. A composition according to Claim 15, wherein said composition comprises less than 55 parts of polyester per 100 parts of rubber and polyester. A composition according to any of the preceding claims, further comprising particulate filler. A composition according to any of the preceding claims, further comprising plasticizer at up to 50 parts by weight of the composition.

Inventors: PATEL RAMAN, PATEL, RAMAN
Applicants: ADVANCED ELASTOMER SYSTEMS, ADVANCED ELASTOMER SYSTEMS, L.P.
Application year: 1989
Main classification: C08L23
IPC codes: C08L67, C08L23, C08L33, C08L63, C08J3, C08L75