SOLVENT-RESISTANT, COMPATIBLE BLENDS OF POLYPHENYLENE ETHERS AND LINEAR POLYESTERS

Abstract: Impact- and solvent-resistant resin blends are prepared from a polyphenylene ether, or blend thereof with a polystyrene, a linear polyester such as a poly(alkylene dicarboxylate), at least one elastomeric polyphenylene ether-compatible impact modifier and at least one polymer containing a substantial proportion of aromatic polycarbonate units as a compatibilizing agent. There may also be present a minor amount of at least one epoxide and/or masked isocyanate such as triglycidyl isocyanurate or a glycidyl methacrylate polymer. The polyphenylene ether is preferably inactivated by reaction with at least one non-volatile carboxylic acid or anhydride and/or by extrusion with vacuum venting.

Description: SOLVENT-RESISTANT, COMPATIBLE BLENDS OF POLYPHENYLENE ETHERS AND LINEAR POLYESTERS This application is a continuation-in-part of copending applications Serial No. 761,712, filed August 2, 1985, and Serial o. 828,410, filed February 11, 1986. This invention relates to novel resinous compositions with high impact resistance, solvent resistance, tensile strength and thermal stability. More particularly, it relates to improved compositions comprising polyphenylene ethers and linear polyesters. The polyphenylene ethers are a widely used class of thermoplastic engineering resins characterized by excellent hydrolytic stability, dimensional stability, toughness, heat resistance and dielectric properties. They are also resistant to high temperature conditions under many circumstances. Because of the brittleness of many compositions containing polyphenylene ethers, they are frequently blended with impact modifiers such as elastomers to form molding compositions. A disadvantage of the polyphenylene ethers which militates against their use for molding such items as automotive parts is their low resistance to non-polar solvents such as gasoline. For increased solvent resistance, it would be desirable to blend the polyphenylene ethers with resins which have a high degree of crystallinity and therefore are highly resistant to solvents. Illustrative of such resins are the linear polyesters including poly(alkylene dicarboxylates) , especially the poly(alkylene terephthalates) . However, such blends frequently undergo phase separation and dela ination. They typically contain large, incompletely dispersed polyphenylene ether particles and no phase interaction between the two resin phases. Molded parts made from such blends are typically characterized by extremely low impact strength. SUBSTITUTE SHEET The present invention provides polymer blends having a high degree of impact resistance and solvent resistance. It also provides highly compatible polymer blends containing polyphenylene ethers and poly(alkylene dicarboxylates), and resinous molding compositions suitable for use in the fabrication of automotive parts and the like. The invention is based on the discovery of a new genus of compatible blends containing polyphenylene ethers and poly(alkylene dicarboxylates) in weight ratios as high as 1:1, or even higher under certain circumstances, and a method for their preparation. According to the invention, there are also incorporated in the resinous composition an impact modifier and a co patibilizing agent containing a substantial proportion of aromatic polycarbonate structural units. in one of its aspects, therefore, the invention is directed to resinous compositions comprising the following resinous components and any reaction products thereof, all percentage proportions being by weight of total resinous components: (A) about 10-45% of at least one polyphenylene ether, or a blend thereof with at least one polystyrene; (B) about 10-45% of at least one poly(alkylene dicarboxylate), the weight ratio of component A to component B being at most 1.2:1; (C) about 8-25% of at least one elastomeric polyphenylene ether-compatible impact modifier; and (D) from 3% to about 40% of at least one polymer containing a substantial proportion of aromatic "-- polycarbonate units and having a weight average molecular weight of-at least about 40,000 as determined by gel permeation chromatography relative to polystyrene, or a blend thereof with a styrene homopolymer. SUBSTITUTE SHEET It is not certain whether any or all of the components in these compositions interact chemically upon blending. Therefore, the invention includes compositions comprising said components and any reaction products thereof, as well as other optional components described hereinafter. The polyphenylene ethers (also known as polyphenylene oxides) used as all or part of component A in the present invention comprise a plurality of structural units having the formula In each of said units independently, each Q is independently halogen, primary or secondary lower alkyl (i.e., alkyl containing up to 7 carbon atoms), phenyl, haloalkyl, aminoalkyl, hydrocarbonoxy, or halohydrocarbonoxy wherein at least two carbon atoms 2 separate the halogen and oxygen atoms; and each Q is independently hydrogen, halogen primary or secondary lower alkyl, phenyl, haloalkyl, hydrocarbonoxy or halohydrocarbonoxy as defined for Q . Examples of suitable primary lower alkyl groups are methyl, ethyl, n-propyl, n-butyl, isobutyl, n-amyl, isoamyl, 2-methylbutyl, n-hexyl, 2,3-dimethylbutyl, 2-, 3- or 4-methylpentyl and the corresponding heptyl groups. Examples of secondary lower alkyl groups are isopropyl, sec-butyl and 3-pentyl. Preferably, any alkyl radicals are straight chain rather than branched. Most often, each Q is alkyl or phenyl, especially C, ,. alkyl, and each Q is hydrogen, suitable polyphenylene ethers are disclosed in a large number of patents. SUBSTITUTE SHEET Both homopolymer and copoly er polyphenylene ethers are included. Suitable homopoly ers are those containing, for example, 2,6-dimethyl-l,4-phenylene ether units. Suitable copolymers include random copolymers containing such units " in combination with (for example) 2,3,6-trimethyl-l,4-phenylene ether units. Many suitable random copolymers, as well as homopolymers, are disclosed in the patent literature. Also included are polyphenylene ethers containing moieties which modify properties such as molecular weight, melt viscosity and/or impact strength. Such polymers are described in the patent literature and may be prepared by grafting onto the polyphenylene ether in known manner such vinyl monomers as acrylonitrile and vinylaromatic compounds (e.g., styrene), or such polymers as polystyrenes and elastomers. The product typically contains both grafted and ungrafted moieties. Other suitable polymers are the coupled polyphenylene ethers in which the coupling agent is reacted in known manner with the hydroxy groups of two polyphenylene ether chains to produce a higher molecular weight polymer containing the reaction product of the hydroxy groups and the coupling agent. Illustrative coupling agents are low molecular weight polycarbonates, quinones, heterocycles and formals. The polyphenylene ether generally has a number average molecular weight within the range of about 3,000-40,000 and a weight average molecular weight within the range of about 20,000-80,000, as determined by gel permeation chromatography. Its intrinsic viscosity is most often in the range of about 0.15-0.6 and preferably at least 0.25 dl./g., as measured in chloroform at 25°C. The polyphenylene ethers are typically prepared by the oxidative coupling of at least one corresponding onohydroxyaromatic compound. Particularly useful and readily available monohydroxyaromatic compounds are 2,6-xylenol (wherein each Q 1 is methyl and each Q2 is SUBSTITUTE SHEET hydrogen), whereupon the polymer may be characterized as a poly(2,6-di-methyl-l,4-phenylene ether), and 2,3,6-trimethylphenol (wherein each Q 1 and one Q2 is 2 methyl and the other Q is hydrogen). 5 A variety of catalyst systems are known for the preparation of polyphenylene ethers by oxidative coupling. There is no particular limitation as to catalyst choice and any of the known catalysts can be used. For the most part, they contain at least one heavy 10 metal compound such as a copper, manganese of cobalt compound, usually in combination with various other materials. A first class of preferred catalyst systems consists of those containing a copper compound. Such 15 catalysts are disclosed, for example, in U.S. Patents 3,306,874, 3,306,875, 3,914,266 and 4,028,341. They are usually combinations of cuprous or cupric ions, halide (i.e., chloride, bromide or iodide) ions and at least one a ine. 20 catalyst systems containing manganese compounds constitute a second preferred class. They are generally alkaline systems in which divalent manganese is combined with such anions as halide, alkoxide or phenoxide. Most often, the manganese is present as a complex with one or 25 more complexing and/or chelating agents such as dialkylamines, alkanolamines, alkylenediamines, o-hydroxyaromatic aldehydes, o-hydroxyazo compounds, w-hydroxyoximes ( monomeric and polymeric), o-hydroxyaryl oximes and β-diketones. Also useful are known cobalt- 30 containing catalyst systems. Suitable manganese and cobalt-containing catalyst systems for polyphenylene ether preparation are known in the art by reason of disclosure in numerous patents and publications. The polyphenylene ethers which may be used in the 35 invention include those which comprise molecules having at least one of the end groups of the formulas SUBSTITUTE< » « erein Q and Q are as pr eviously defin. is independently hydrogen or alkyl, with the proviso that the total number of carbon atoms in both R radicals is 2 6 or less; and each R is independently hydrogen or a C 1 _ 16 primary alkyl radical. Preferably, each R is hydrogen and each R is alkyl, especially methyl or n-butyl. Polymers containing the end groups of formula II (hereinafter "aminoalkyl end groups") may be obtained by incorporating an appropriate primary or secondary monoamine as one of the constituents of the oxidative coupling reaction mixture, especially when a copper- or manganese-containing catalyst is used. Such amines, especially the dialkylamines and preferably di-n-butylamine and dimethylamine, frequently become chemically bound to the polyphenylene ether, most often by replacing one of the a-hydrogen atoms on one or more Q radicals. The principal site of reaction is the Q radical adjacent to the hydroxy group on the terminal unit of the polymer chain. During further processing and/or blending, the aminoalkyl end groups may undergo various reactions, probably involving a quinone ethide-type intermediate of the formula iζ with numerous beneficial effects often including an increase in impact strength and co patibilization with other blend components. Reference is made to U.S. Patents 4,054,553, 4,092,294, 4,477,649, 4,477,651 and 4,517,341, the disclosures of which are incorporated by reference herein. Polymers with 4-hydroxybiphenyl end groups of formula III are typically obtained from reaction mixtures in which a by-product diphenoquinone of the formula is present, especially in a copper-halide-secondary or tertiary amine system. In this regard, the disclosure of U.S. Patent 4,477,649 is again pertinent as are those of U.S. 4,234,706 and 4,482,697, which are also incorporated by reference herein, in mixtures of this type, the diphenoquinone is ultimately incorporated into the polymer in substantial proportions, largely as an end group. in many polyphenylene ethers obtained under the above-described conditions, a substantial proportion of the polymer molecules, typically constituting as much as about 90% by weight of the polymer, contain end groups having one or frequently both of formulas II and III. It T should be understood, however, that other end groups may be present and that the invention in its broadest sense may not be dependent on the molecular structures of the polyphenylene ether end groups. 5 it will be apparent to those skilled in the art from the foregoing that the polyphenylene ethers contemplated for use in the present invention include all those presently known, irrespective of variations in structural units or ancillary chemical features. 10 The use of polyphenylene ethers containing substantial amounts of unneutralized amino nitrogen may, under certain conditions, afford compositions with undesirably low impact strengths. The possible reasons for this are explained hereinafter. The amino compounds 15 include, in addition to the aminoalkyl end groups, traces of amine (particularly secondary amine) in the catalyst used to form the polyphenylene ether. It has further been found that the properties of the compositions can often be improved in several 20 respects, particularly impact strength, by removing or inactivating a substantial proportion of the amino compounds in the polyphenylene ether. Polymers so treated are sometimes referred to hereinafter as "inactivated polyphenylene ethers". They preferably contain 25 unneutralized amino nitrogen, if any, in amounts no greater than 800 ppm. and more preferably in the range of about 200-800 ppm. Various means for inactivation have been developed and any one or more thereof may be used. One such method is to preco pound the polyphenylene 30 ether with at least one non-volatile compound containing a carboxylic acid, acid anhydride or ester group, which is capable of neutralizing the amine compounds. This method is of particular interest in the preparation of compositions of this invention having high resistance to 35 heat distortion, illustrative acids, anhydrides and esters are citric acid, malic acid, agaricic acid, SUBSTITUTE SHEET succinic acid, succinic anhydride, aleic acid, maleic anhydride, citraconic acid, citraconic anhydride, itaconic acid, itaconic anhydride, fumaric acid, diethyl maleate and methyl fumarate. Because of their relatively high 5 reactivity with amino compounds, the free carboxylic acids and especially fumaric acid are generally most useful. Reaction of the polyphenylene ether with the acid or anhydride may be achieved by heating at a temperature within the range of about 230-390°C, in solution or 10 preferably in the melt, in general, about 0.3-2.0 and preferably in the melt, in general, about 0.3-2.0 and preferably about 0.5-1.5 part (by weight) of acid or anhydride is employed per 100 parts of polyphenylene ether. Said reaction may conveniently be carried out in 15 an extruder or similar equipment. Another method of inactivation is by extrusion of the polyphenylene ether under the above-described conditions with vacuum venting. This may be achieved either in a preliminary extrusion step (which is sometimes 20 preferred) or during extrusion of the composition of this invention, by connecting the vent of the extruder to a vacuum pump capable of drawing a vacuum of about 20 torr or less. It is believed that these inactivation methods aid 25 in the removal by evaporation or the neutralization of any traces of free amines (predominantly secondary amines) in the polymer, including amines generated by conversion of aminoalkyl end groups to quinone methides of the type represented by formula IV. Polyphenylene ethers having a 30 free amine nitrogen content below about 600 ppm. have been found particularly useful in this invention. However, the invention is not dependent on any theory of inactivation. The preparation of inactivated polyphenylene ethers by reaction with acids or anhydrides, together with vacuum 35 venting during extrusion, is illustrated by the following examples. All parts in the examples herein are by weight. TUTE SHEET Example 1 A mixture of 1.43 parts of maleic anhydride and 100 parts of a poly-(2,6-dimethyl-l,4-phenylene ether) having a number average molecular weight (as determined by gel permeation chromatography) of about 20,000 and an intrinsic viscosity in chloroform at 25°C. of 0.46 dl./g. was tumble-mixed for 15-30 minutes and then extruded on a 20-mm. twin screw extruder at 400 rpm. over a temperature range of about 310-325°C. The feed rate of the mixture was about 524 grams per 10 minutes. The extruder was vacuum vented with a vacuum pump to a pressure less than 20 torr during the extrusion. The product was the desired inactivated polyphenylene ether. Examples 2-5 The procedure of Example 1 was repeated, substituting 0.7, 0.8, 1.0 and 1.4 parts (respectively) of fumaric acid for the maleic anhydride and extruding over a temperature range of about 300-325°C. A similar product was obtained. Example 6 The procedure of Example 2 was repeated, substituting 0.7 part of citric acid for the fumaric acid. A similar product was obtained. Component A may also contain at least one polystyrene. The term "polystyrene" as used herein includes polymers prepared by methods known in the art including bulk, suspension and emulsion polymerization, which contain at least 25% by weight of structural units derived from a monomer of the formula 3 wherein R is hydrogen, lower alkyl or halogen; Z is vinyl, halogen or lower alkyl; and p is from 0 to 5. * •τrrυtfc fc f These resins include homopolymers of styrene, chlorostyrene and vinyltoluene, random copolymers of styrene with one or more monomers illustrated by acrylonitrile, butadiene, a-methylstyrene, ethylvinylbenzene, divinylbenzene and maleic anhydride, and rubber-modified polystyrenes comprising blends and grafts, wherein the rubber is a polybutadiene or a rubbery copolymer of about 98-70% styrene and about 2-30% diene monomer. These rubber-modified polystyrenes include high impact polystyrene, or HIPS. The proportion of polystyrene in component A is not critical, since polyphenylene ethers and polystyrenes are miscible in all proportions. Component A will generally contain about 5-50% (by weight) polystyrene, if any. Component B is at least one linear polyester. The linear polyesters include thermoplastic poly(alkylene dicarboxylates) and alicyclic analogs thereof. They typically comprise structural units of the formula 4 wherein R is a saturated divalent aliphatic or alicyclic hydrocarbon radical containing about 2-10 and usually about 2-6 carbon atoms and A is a divalent aromatic radical containing about 6-20 carbon atoms. They are ordinarily prepared by the reaction of at least one diol such as ethylene glycol, 1,4-butanediol or 1,4-cyclohexanedimethanol with at least one aromatic dicarboxylic acid such as isophthalic or terephthalic acid, or lower alkyl ester thereof. The polyalkylene terephthalates, particularly polyethylene and polybutylene terephthalate and especially the latter, are preferred. Such polyesters are known in the art as illustrated by the following patentr- - * r ^' 2 , 465 , 319 3 , 047 , 539 2 , 720 , 502 3 , 671 , 487 2 , 727 ,881 3 , 953 , 394 2 , 822 , 348 4 , 128 , 526 . 5 Because of the tendency of polyesters to undergo hydrolytic degradation at the high extrusion and molding temperatures encountered by the compositions of this invention it is preferred that the polyester used as component B be substantially free of water. 10 The polyesters generally have number average molecular weights in the range of about 20,000-70,000, as determined by intrinsic viscosity (IV) at 30°C in a mixture of 60% (by weight) phenol and 40% 1,1,2,2-tetrachloroethane. When resistance to heat 15 distortion is an important factor the polyester molecular weight should be relatively high, typically above about 40,000. Because of the presence of both poly(alkylene dicarboxylates) and polymers containing carbonate units in 20 the compositions of this invention, there is a possibility for ester-carbonate exchange resulting in degradation of one or both polymers, particularly at high molding temperatures. It is, therefore, sometimes preferred to incorporate in the compositions an agent which suppresses 25 such exchange, typically in the amount of about 0.01-7.5% by weight of total polyester. It is generally preferred to precompound said exchange suppressing agent with the polyester, since it is frequently found that the impact strengths of the compositions of this invention are 30 substantially decreased if the exchange suppressing agent is incorporated directly therein. Precompounding may be achieved by direct blending or by forming a concentrate, typically with. about 1-25% by weight of the polyester, and adding said concentrate to the remaining portion thereof. 35 illustrative exchange suppressing agents are hydroxyaromatic compounds such as the hydroxybenzophenones disclosed in U.S. Patent 4,452,932; salicylate compounds SUBSTITUTE SHEET such as methyl salicylate, disclosed in U.S. Patent 4,452,933; and sodium and potassium dihydrogen phosphates disclosed in U.S. Patent 4,532,290. The disclosures of all of the foregoing patents relating to polyesters are 5 also incorporated by reference herein. Component c is at least one elastomeric polyphenylene ether-compatible impact modifier, suitable impact modifiers include various elastomeric copolymers, of which examples are ethylene-propylene-diene polymers 10 (EPDM's), both unfunctionalized and functionalized with (for example) sulfonate or phosphonate groups; carboxylated ethylene-propylene rubbers; block copolymers of alkenylaromatic compounds such as styrene with poly erizable olefins or dienes, including butadiene, 15 isoprene, chloroprene, ethylene, propylene and butylene; and core-shell elastomers containing, for example, a poly(alkyl acrylate) core attached to a polystyrene shell via an interpenetrating network, such core-shell elastomers are more fully disclosed in copending, commonly 20 owned application Serial No. 811,800, filed December 20, 1985. The preferred impact modifiers are block (typically diblock, triblock or radial teleblock) copolymers of alkenylaromatic compounds and dienes. Most often, at 25 least one block is derived from styrene and at least one other block from at least one of butadiene and isoprene. Especially preferred are the triblock copolymers with polystyrene end blocks and diene-derived idblocks. It is frequently advantageous to remove (preferably) or reduce 30 the aliphatic unsaturation therein by selective hydrogenation. The weight average molecular weights of the impact modifiers are typically in the range of about 40,000-300,000. Block copolymers of this type are commercially available from shell chemical Company under 35 the trademark KRATON, and include KRATON DllOl, G1650, G1651, G1652, G1657 and G1702. SUBSTITUTE SHEET According to the present invention, the tendency of blends of components A and B to be incompatible is overcome by incorporating component D in the composition. The essential ingredient of component D is a polymer 5 containing a substantial proportion of aromatic polycarbonate units. Among the preferred polymers of this type are the aromatic polycarbonate homopolymers. The structural units in such homopolymers generally have the formula wherein A 2 is an aromatic radical. Suitable A2 values include m-phenylene, p-phenylene, 4,4'-biphenylene, 2,2-bis(4-phenylene)propane, 2,2-bis(3,5-dimethyl- 4-phenylene)-propane and similar radicals such as those 15 which correspond to the dihydroxyaromatic compounds disclosed by name or formula (generic or specific) in U.S. Patent 4,217,438. Also included are radicals containing non-hydrocarbon moieties. These may be substituents such as chloro, nitro, alkoxy and the like, and also linking 20 radicals such as thio, sulfoxy, sulfone, ester, amide, 2 ether and carbonyl. Most often, however, all A radicals are hydrocarbon radicals. 2 The A radicals preferably have the formula (IX) -A 3 -Y-A 4 - , 25 wherein each of A 3 and A4 is a single-ring divalent aromatic radical and Y is a bridging radical in which one to two atoms separate A 3 from A4. The free valence bonds in formula IX are usually in the meta or para positions of A 3 and A4 in relation to Y. Such A? 30 values may be considered as being derived from bisphenols of the formula HO-A 3-Y-A4OH. Frequent reference to bisphenols will be made hereinafter, but it should be SUBSTITUTESHEET 2 understood that A values derived from suitable compounds other than bisphenols may be employed as appropriate. in formula ix, the A 3 and 4 values may be 5 unsubstituted phenylene or substituted derivatives thereof, illustrative substituents (one or more) being alkyl, alkenyl (e.g., crosslinkable-graftable moieties such as vinyl and allyl), halo (especially chloro and/or bromo), nitro, alkoxy and the like, unsubstituted 10 phenylene radicals are preferred. Both A 3 and A4 are preferably p-phenylene, although both may be o- or m-phenylene or one o- or m-phenylene and the other p-phenylene. The bridging radical, Y, is one in which one or two 15 atoms, preferably one, separate A 3 and A4. It is most often a hydrocarbon radical and particularly a saturated radical such as ethylene, cyclohexylmethylene, 2-[2.2.l]-bicycloheptylmethylene, ethylene, 2,2-propylene, l,l-(2,2-dimethylpropylene) , 1,1-cyclohexylene, 20 1,1-cyclopentadecylene, 1,1-cyclododecylene or 2,2-adamantylene, especially a ge -alkylene radical. Also included, however, are unsaturated radicals and radicals which are entirely or partially composed of atoms other than carbon and hydrogen. Examples of such radicals are 25 2,2-dichloroethylidene, carbonyl, thio and sulfone. For reasons of availability and particular suitability for the purposes of this invention, the preferred radical of formula VIII is the 2,2-bis(4-phenylene)-propane radical, which is derived from bisphenol A and in which Y is 30 isopropylidene and A 3 and A4 are each p-phenylene. Various methods of preparing polycarbonate homopolymers are known, and any of them may be used for preparing component D. They include interfacial and other methods in which phosgene is reacted with bisphenols, 35 transesterification methods in which bisphenols are reacted with diaryl carbonates, and methods involving SUBSTITUTESHEET conversion of cyclic polycarbonate oligomers to linear polycarbonates. The latter method is disclosed in European patent Application 162,379 and in copending, commonly owned applications Serial No. 704,122, filed 5 February 22, 1985, and Serial No. 723,672, filed April 16, 1985. Various copolycarbonates are also useful as component D. One example thereof is the polyester- polycarbonates of the type obtained by the reaction of at 10 least one dihydroxyaromatic compound with a mixture of phosgene and at least one dicarboxylic acid chloride, especially isophthaloyl chloride, terephthaloyl chloride or both. Such polyester-polycarbonates contain structural units of formula VIII combined with units of the formula O O II 5 II 15 (X) -O-C-A -C- , 5 wherein A is an aromatic and usually a p- or m-phenylene radial. Other examples are the siloxane-carbonate block copolymers disclosed, for example, in U.S. Patents 3,189,662 and 3,419,634, and the 20 polyphenylene ether-polycarbonate block copolymers of U.S. Patents 4,374,223 and 4,436,876, which frequently provide compositions with substantially higher heat distortion temperatures than those containing homopolycarbonates. The disclosures of the patents and applications listed 25 above relating to polycarbonates and copolycarbonates are also incorporated by reference herein. The copolycarbonates should, for the most part, contain at least about 20% by weight of carbonate structural units. .When the copolymeric units are other 30 than ester units, the polymer preferably contains at least about 45% carbonate units. The weight average molecular weight of the homo- or copolycarbonate should be at least about 40,000 (as determined by gel permeation chromatography relative to SUBSTITUTE SHEET polystyrene) for maximum impact strength. It is most often in the range of about 40,000-80,000 and especially about 50,000-80,000. However, compositions in which component D has a molecular weight in the range of about 5 80,000-200,000 often have very high impact strengths, as noted hereinafter. In most instances, component D consists of the polycarbonate of copolycarbonate; that is, said polymer is the entire component except for impurities. It is within 10 the scope of the invention, however, to use as component D a blend of a polycarbonate or polyester-polycarbonate with a styrene homopolymer, typically having a number average molecular weight of about 50,000-250,000. Such blends generally contain at least 50% of the polycarbonate of 15 polyester-polycarbonate. It will be noted that various polystyrenes may be used in the invention as all or part of components A, C and D. However, the specific polystyrenes used are difference in various respects. The polystyrene in 20 component A is a homopolymer, random copolymer or rubber-modified polystyrene; component C may be a block or core-shell copolymer; and homopolymers are used in component D. Moreover, polystyrenes are ordinarily present in only one of components A and D, if in either. 25 it is also within the scope of the invention to employ a polyester-aromatic polycarbonate blend as a source of part of all of components B and D. As explained hereinafter, the use of such a blend may provide somewhat more flexibility in component proportions. 30 Particularly in compositions containing inactivated polyphenylene ethers and relatively small amounts of polycarbonate, it is frequently found that impact strength and/or resistance to heat distortion are improved if there is also blended into the composition (E) at least one 35 compound selected from those containing at least one cyanurate or isocyanurate moiety and those containing a SUBSTITUTE SHEET plurality of epoxide moieties. Illustrative cyanurates and isocyanurates are cyanuric chloride, triethyl cyanurate, triallyl cyanurate, triallyl isocyanurate and triphenyl cyanurate. Epoxide compounds include 5 homopolymers of such compounds as glycidyl acrylate and glycidyl methacrylate, as well as copolymers thereof, preferred comonomers being lower alkylacrylates, methyl methacrylate, acrylonitrile and styrene. Also useful are epoxy-substituted cyanurates and isocyanurates such as 10 triglycidyl isocyanurate. In various respects, the proportions of ingredients in the compositions of this invention are an important consideration. It is generally contemplated that components A and B will each be present in the 15 compositions described hereinabove in the amount of about 10-45%, preferably about 15-45%, of total resinous components. Moreover, the weight ratio of component A to component B should be at most 1.2:1, since if component A is present in greater amounts the impact strength of the 20 composition may decrease sharply. Said weight ratio is preferably about 0.7-1.0:1. Component C, the elastomeric impact modifier, may be present in the amount of about 8-25% and especially about 10-20%. Since a decrease in the proportion of 25 component C frequently increases heat distortion temperature, the level thereof should be minimized if high resistance to heat distortion is desired. With respect to the proportion of component D, the compatibilizing polymer, the invention includes three 30 major embodiments although species outside these embodiments are also contemplated. The first embodiment includes polymers containing about 10-40% of component D. in such compositions, component A is typically a polyphenylene ether which has not been inactivated, in 35 most instances, levels of components A, B and D of about 15-35%, 15-35% and 20-40% (respectively) are preferred in such compositions for maximum impact strength. TE SHEET When component A is not inactivated and components B and D are supplied in full or in part by a polyester-aromatic polycarbonate blend, it is frequently possible to attain the desired high impact strengths by using proportions of certain components outside of those previously described. This is true in at least two respects: the possibility of using a lower proportion of component B with respect to component A, and of employing more than 40% of component D. Thus, another aspect of the present invention is compositions comprising the following components and any reaction products thereof: about 15-35% of polyphenylene ether as component A, about 10-35% of component B, about 10-25% of component C and from 12% to about 50% of at least one aromatic polycarbonate as component D, with the provisos that all of component B and at least about 60% of component D are supplied as a poly(alkylene dicarboxylate)-aromatic polycarbonate blend, and that the weight ratio of component A to component B is at most about 1.8:1 and preferably about 0.7-1.8:1. in the second embodiment, component A is an inactivated polyphenylene ether and the proportions of components A and B are each about 30-45%. The proportion of component D is about 3-10%, and the blend may also include component E in the amount of about 0.1-3.0 and preferably at least about 0.25 part per 100 parts of total components A, B, C and D. This embodiment is often characterized by relatively high heat distortion temperatures. It is within the scope of this second embodiment to introduce component E by blending with the other components in a single blending operation. However, it is often preferred to pre ix component E with component B, typically by dry mixing followed by preextrusion. Such premixing increases the melt viscosity of component B, probably by increasing molecular weight as described hereinafter, and frequently also increases the impact strength of the composition of the invention. SUBSTITUTE SH In the third embodiment, component A is an inactivated polyphenylene ether and the polycarbonate has a weight average molecular weight in the range of about 80,000-200,000, preferably about 150,000-200,000. Compositions in which these polycarbonates and other components are present in the same proportions as in the second embodiment are generally characterized by high impact strengths even when component E is absent. The chemical roles of the inactivated polyphenylene ether and of component E in the compositions of this invention are not fully understood, and any reliance on chemical theory as a basis for the invention is specifically disclaimed. It is believed, however, that the presence of more than a certain minimum proportion of amino compounds in the polyphenylene ether can cause degradation in the molecular weight of the polycarbonate. Such amino compounds include, in addition to the aminoalkyl end groups, traces of amines (particularly secondary amine) in the catalyst used to form the polyphenylene ether. If this is true, the removal or neutralization of the greater part of such amino compounds produced an environment in which high molecular weight is maintained in the polycarbonate, thus maximizing its effect as a compatibilizing agent. The compositions of this invention have been shown by scanning electron microscopy to consist essentially of particles of polyphenylene ether (component A) dispersed in a continuous polyester-containing phase. The size and shape of said particles varies with such factors as the proportion of polyphenylene ether in the composition. The elastomeric impact modifier (component C) is present substantially entirely in the disperse phase. By reason of the size and shape of the disperse phase particles and/or their degree of adhesion to the continuous phase, the compositions are highly resistant to delamination and similar types of failure under stress. It is within the scope of the invention for the composition to contain other conventional ingredients such as fillers, flame retardants, pigments, dyes, stabilizers, anti-static agents, mold release agents and the like. The 5 presence of other resinous components is also contemplated. These include impact modifiers compatible with component B, such as various graft and core-shell copolymers of such monomers as butadiene, styrene, butyl acrylate and methyl methacrylate. It is frequently 10 preferred to preextrude such impact modifiers with component B prior to its utilization in the invention. By this method, compositions having improved ductility at low temperatures may be prepared. Also included as other resinous components are 15 other impact and processability modifiers for component A, such as olefin copolymers. In general, the amounts of any other resinous components, if present, will not exceed about 15% by weight of total resin. The preparation of the compositions of this 20 invention is normally achieved by merely blending the ingredients thereof under conditions adapted for the formation of an intimate blend. Such conditions often include extrusion, which may be conveniently effected in a screw-type or similar extruder which applies a substantial 25 shearing force to the composition, thereby decreasing the particle size thereof. The extrusion temperature is generally in the range of about 100°-325°C. The extrusion conditions may affect the impact strength and other properties of the composition. For 30 example, it is sometimes found that the impact strength of the composition is increased if it is extruded more than once, thereby insuring effective blending. In another embodiment, a single extruder is employed which has at least two ports for introduction of 35 ingredients, one such port being downstream from the other, Component A or any reactants for preparation thereof and SUBSTITUTE SHEET at least a portion of component c are introduced through the first port and extruded, preferably at a temperature in the range of about 300-350°C This portion of the extruder is preferably vacuum vented. 5 The remaining ingredients are introduced through the downstream port and extrusion is continued, preferably at a lower temperature to minimize degradation of components B and c. For further minimization of degradation, it may be advantageous to introduce a portion 10 of component C at this point. Typical extrusion temperatures at this stage are in the range of about 260-320°C. in the following examples illustrating the inventions, the blend constituents used were as follows: 15 Component A PPE - a poly(2,6-dimethyl-l,4-phenylene ether) having a number average molecular weight of about 20,000 and an intrinsic viscosity in chloroform at 25°C of 0.46 dl./g; it was found 20 to contain about 1000 ppm. nitrogen. Example 1, etc. - the products of the designated examples. The product of Example 2 contained about 600 ppm. nitrogen. Example 2 (etc.)-NW - a product similar to 25 that of Example 2 (etc.) but prepared with atmospheric rather than vacuum venting. PPE-W - PPE which has been extruded on a twin screw extruder within the temperature range of about 300-315°C, with vacuum venting to a 30 maximum pressure of 20 torr; it contained 438 ppm. nitrogen. Component B PBT(50,000) and PBT(25,000) - poly(butylene terephthalates) having number average molecular 35 weights, as determined by gel permeation chromatography, of about 50,000 and 25,000, respectively. SUBSTITUTE SHEET PBT-ES - PBT(50,000) containing aH2Pθ4 as an exchange-suppressing agent. The H2P04 was preblended with a portion of the polyester to a level of 0.18% by weight, after which 20% 5 of said polyester was blended with untreated polyester. PET(28,000) and PET(45,000) - poly(ethylene terephthalates) having number average molecular weights of about 28,000 and 45,000, 10 respectively, as determined from intrinsic viscosity at 30°C in a 3:2 (by weight) mixture of phenol and 1,1,2,2-tetrachloroethane. Component C SEBS - a commercially available triblock 15 copolymer with polystyrene end blocks having weight average molecular weights of 29,000 and a hydrogenated butadiene midblock having a weight average molecular weight of 116,000. SBS - a triblock copolymer similar to SEBS but 20 containing an unhydrogenated butadiene midblock. SB(H) - a styrene-butadiene diblock copolymer having a weight average molecular weight of about 164,000 and a butadiene-styrene weight ratio of about 2:1, in which the butadiene 25 block has been hydrogenated. CS - a core-shell polymer with a poly(butyl acrylate) core and polystyrene shell, connected via an interpenetrating network. Component p 30 PC(43,000), PC(50,000), PC(71,000), PC(192,000) - bisphenol A homopolycarbonates prepared interfacially and having weight average molecular weights of about 43,000, 50,000, 71,000 and 192,000, respectively. 35 PC-Trans - a bisphenol A homopolycarbonate prepared by transesterification of diphenyl carbonate and having a weight average molecular weight of about 37,000. SH-PC - a 2,2-bis(3,5-dimethyl-4-hydroxyphenyl)- 40 propane polycarbonate prepared interfacially and having a weight average molecular weight of about 50,000. SUBSTITUTE SHEET Allyl-PC - a copolycarbonate of 97.3 mole percent bisphenol A and 2.7 mole percent 2,2-bis(3-allyl-4-hydroxyphenyl)propane, prepared interfacially and having a weight 5 average molecular weight of about 47,000. PPE-PC - a block poly(2,6-dimethyl-l,4-phenylene ether)-bisphenol A polycarbonate copolymer in which the two blocks have approximately "equal molecular weights. 10 PE-PC - a polyester-polycarbonate containing 78 mole percent polyester and 22 mole percent polycarbonate units and having a weight average molecular weight of about 50,000, prepared by the interfacial reaction of bisphenol A with 15 phosgene and a 93:7 (by weight) mixture of isophthaloyl and terephthalate chloride. PC-SIL - a block copolymer containing 76% bisphenol A polycarbonate units and 24% poly(dimethyl siloxane) units, having a weight 20 average molecular weight of about 50,000. PS - a commercially available styrene homopolymer having a number average molecular weight of about 106,000 and an intrinsic viscosity in toluene at 25°C of 0.80 dl.g. 25 Component E TGIC - triglycidyl isocyanurate. GMA - a glycidyl methacrylate homopolymer having an intrinsic viscosity in chloroform at 25°C of 0.16. 30 GMA-AA(15) and GMA-AA(30) - commercially available terpoly ers of glycidyl methacrylate, methyl methacrylate and a lower alkyl acrylate, respectively containing 15% and 30% (by weight) glycidyl methacrylate units and having weight 35 average molecular weights of about 11,400 and 9,000. GMA-M - a commercially available copolymer of glycidyl methacrylate (50% by weight) and methyl methacrylate, having a weight average 0 molecular weight of about 10,000. GMA-S - a commercially available copolymer of glycidyl methacrylate (50% by weight) and styrene, having a weight average molecular weight of about 11,000. SUBSTITUTESHEET GMA-S-M - a commercially available terpolymer of glycidyl methacrylate (50% by weight), styrene and methyl methacrylate, having a weight average molecular weight of about 10,000. 5 GMA-S-A(IOA), GMA-S-A(IOB), GMA-S-A(20) - commercially available terpolymers of glycidyl methacrylate, styrene and acrylonitrile, respectively containing 10%, 10% and 20% (by weight) glycidyl methacrylate and having weight 10 average molecular weights of about 8,700, 50,000 and 8,100. Percentages and other proportions in the examples are by weight and are based on total resinous constituents. Impact and tensile values were determined in British units 15 and have been converted to metric units. Heat distortion temperatures are at 0.455 MPa. unless otherwise indicated. Examples 7-13 A series of compositions according to the invention was prepared by tumble mixing the ingredients in a jar 20 mill for 1/2 hour and extruding at 120-287°C. on a twin screw extruder with a screw speed of 400 rpm. The extrudate was quenched in water and pelletized. The pellets were then injection molded into test bars which were evaluated for notched Izod impact strength according 25 to ASTM procedure D256. (An impact strength greater than about 105 joules/m. is generally an indication of suitability as a molding composition, and a value above about 550 is exceptional.) Certain compositions were also tested for heat distortion temperature according to ASTM 30 procedure D648. The fracture surfaces of the izod test bars were inspected for delamination and none was detected. The relevant parameters and test results are given in Table I. TABLE 1 Example 7 8 9 10 11 12 13 Component A: PPE, % 21 27 25 25 21 21 21 Component B, %: PBT (50,000) 29 27 25 25 29 PET (28,000) 29 PET (45,000) 29 Component C, %: SEBS 14 13 19 14 14 SI(H) 19 SBS 14 Component D: PC (50,000), % 36 33 31 31 36 36 36 izod impact strength, joules/m. 603 160 609 550 198 278 598 The heat distortion temperature of the product of Example 7 was 106°C (83°C at 1.82 MPa.). Example 14 The effect of multiple extrusions and the solvent resistance of a blend identical in composition to that of Example 7 were tested. After one extrusion, the blend had an izod impact strength of 454 joules/m.; upon extrusion a second time, the impact strength was increased to 641 joules/m. In a solvent resistance test, the test specimen having an impact strength of 641 joules/m. was immersed in gasoline for two days under stress. It was then found to have an impact strength of 214 joules/m., which is still a respectably high figure. No signs of dissolution or deterioration were noted. Examples 15-20 The procedure of Example 7 was repeated, using other resins as components B and D. The relevant parameters and results are given in Table II. No delamination of any specimen was observed. SUBSTITUTESHEET TABLE II Example 15 16 17 18 19 20 Component A: PPE, % 28 28 31 31 34 34 Component B: PBT-ES, % 28 28 31 31 34 34 Component C: SEBS, % 19 19 19 19 19 19 Component D, %: PC(50,000) 25 — 19 — 12 — PC(71,000) — 25 — 19 — 12 Izod impact strength. 625 801 694 790 139 112 joules/m. Heat distortion temp., °C 111 127 — Examples 21-28 The procedure of Example 7 was repeated, using other resins as components B, C and D. The relevant parameters and test results are given in Table III. No delamination of any specimen was observed. TABLE III Example 21 22 23 24 25 26 27 28 Component A: PPE, % 21 21 21 28 21 34 31 28 Component B: PBT-ES, % 29 29 29 28 29 34 31 28 Component C: SEBS, % 14 14 14 19 14 19 13 19 Component D, %: PC(43,000) 36 — SH-PC — 36 18 PE-PC 25 PPE-PC 12 25 25 PC-SIL 25 PS ~ ~ 18 — ~ ~ — ~ Izod impact strength, 176 278 182 449 251 117 764 732 joules/m. Heat distortion temp., ' 97 150 157 149 Referring specifically to Examples 26-27 in comparison with Example 19, and Example 28 in comparison with Example 15, it will be seen that compositions containing block polyphenylene ether-polycarbonates have substantially higher heat distortion temperatures than those containing homopolycarbonates, as well as equivalent or higher impact strengths. SUBSTITUTESHEET Examples 29-31 Following the procedure of Example 7, blends were prepared in which component B was provided entirely and component D entirely or partially by a polyester-poly¬ carbonate blend containing 39% PBT-ES, 49% PC(50,000), 8.5% of a commercial tuadiene-styrene-methyl methacrylate graft copolymer and 3.5% of various fillers and stabilizers. The relevant parameters and results are given in Table IV. No delamination of any specimen was observed. TABLE IV Example 29 30 31 Polyester-polycarbonate blend 64 32 50 Polycarbonate — 32 14 Component A, % 21.7 21.5 21.6 Component B, % 25.8 12.7 20.0 Component C, % 14.5 14.3 14.4 Component D, % 32.4 48.7 39.6 Graft copolymer, % 5.6 2.8 4.4 Izod impact strength, joules/m. 481 529 534 Examples 32-34 Compositions were prepared according to the procedure of Example 7, except that the extrusion temperature range was 120-260°C. In these compositions, component A was the product of Example 1 and the other components are as listed in Table V. Test bars were molded and evaluated for notched izod impact strength, heat distortion temperature and tensile properties (ASTM procedure D638). The relevant parameters and test results are also given in Table V. SUBSTITUTESHEET TABLE V Example 32 33 34 Component A: Example 1, % 40 41.4 40 Component B: PBT(50,000), % 40 41.4 40 Component C: SEBS, % 12 9.1 12 Component D: PC(50,000), % 8.1 8 Component E: TGIC, phr. 0.5 0. izod impact strength, joules/m. 107 166 267 Heat distortion temp., °C 166 156 Tensile strength at yield, MPa. 44.9 46, Tensile elongation, % 45 58 Example 35 Test bars of the composition of Example 34 were immersed in gasoline for three days under stress. At the end of this time, the Izod impact strength was 155 joules/m., the tensile strength at yield was 27.1 MPa., and the tensile elongation was 20%. Upon immersion of similar test bars in water at room temperature or at its boiling point for three days, and upon aging at 80°C for one week, weight and dimensional changes substantially less than 1% were observed. Examples 36-43 Following the procedure of Example 32, compositions were prepared from the product of Example 3 and its atmospherically vented counterpart. The relevant parameters and test results are given in Table VI. SUBSTITUTE SHEET TABLE VI Example 36 37 38 39 40 41 42 43 Component A, %: Example 3 40 40 40 40 42 40 40 Example 3-NW 40 Component B, %: PBT(50,000) 40 40 40 40 42 — 40 40 PBT(25,000) 40 Component C, % SEBS 12 12 12 12 12 12 — 12 SB(H) 12 Component D, %: PC(50,000) 8 8 8 — — — -8 8 PC(71,000) — — — 8 4 8 OJ o Component E: TGIC, phr. 0.8 0.32 0.5 0.8 0.8 0.8 0.8 0.8 Izod impact strength, joules/m. 790 673 828 806 395 192 219 155 Heat distortion temp., °C 177 148 175 158 156 172 Tensile strength at yield, MPa. 46.9 47.9 50.1 46.9 45 47.6 Tensile elongation, % 96 54 • 106 69 48 40 Example 44 Test bars of the composition of Example 36 were immersed in gasoline for four days under stress. At the end of this time, the izod impact strength was 769 joules/m., the tensile strength at yield was 33.9 MPa. and the tensile elongation was 144%. Examples 45-48 Following the procedure of Example 32, compositions were prepared in which components A, C and D varied in additional respects. The relevant parameters and test results are given in Table VII. TABLE V Example 45 46 47 48 Component A, %: Example 6 40 PPE-W — 40 40 40 Component B: PBT(50,000), % 40 40 40 40 Component C, %: SEBS 12 12 12 — CS 12 Component D, %: PC(50,000) 8 8 — 8 PC(192,000) — — 8 — Component E: TGIC, phr. 0.8 0.5 — 0 izod impact strength, joules/m. 785 769 764 486 Heat distortion temperature, °C — 167 — — Examples 49- -51 Following the procedure of Example 32, compositions were prepared using as components B and D the following preextruded blend: PBT(50,000) 69.55% PC(50,000) 15% PBT impact modifier 15% Stabilizers, exchange suppressor 0.45% The PBT impact modifier was "KM-330", a pol (butyl acrylate)-poly(methyl methacrylate) core-shell polymer commercially available from Rohm & Haas Company. E SH E The parameters and test results for Examples 49-51 are given in Table VIII. TABLE VIII Example 49 50 51 Component A, %: Example 3 36.6 — — PPE-W — 36.6 36.6 Component B, %: 36.4 36.4 36.4 Component C: SEBS, % 11.2 11.2 11.2 Component D, %: 7.9 7.9 7.9 Component E: TGIC, phr. 0.4 0.4 — KM-330,% 7.9 7.9 7.9 izod impact strength, joules/m. 721 192 198 Example 52 A twin screw extruder with two vacuum vents and two charging ports, one downstream from the other, was used. The first port was charged with 30 parts of PPE, 14 parts of SEBS and minor proportions of stabilizers and pigments. These materials were extruded at temperatures in the range of about 315-350°C and pressures in the range of about 150-205 torr. These were added through the downstream port 46 parts of PBT(50,000) and 10 parts of PC(71,000), and extrusion was continued at temperatures in the range of 260-315°C and pressures of about 635 torr. The extrudate was the desired product. Examples 53-56 Following the procedure of Example 32, compositions were prepared in which various polycarbonates were used as component D. The relevant parameters and test results are given in Table IX. SUBSTITUTE SHEE TABLE IX Example 53 54 55 56 Component A, %: PPE-W 40 Example 2 — 40 40 40 Component B: PBT(50,000), % 40 40 40 40 Component C: SEBS, % 12 12 12 12 Component D: %: PC-Trans 8 8 8 — Allyl-PC 8 Component E: TGIC, phr. — — 0.5 — Izod impact .strength, joules/m. 182 256 828 278 Examples 57- -67 Following the procedure of Example 32, compositions were prepared containing 40% of the inactivated polyphenylene ether of Example 3, 40% PBT(50,000), 12% SEBS, 8% PC(50,000) and, as component E, various . materials. The identity of these materials and the test results are given in Table X. TABLE X Tensile Izod strength Tensile impact at elong¬ Component E strength break ation, Example Identity Amt. , phr. joules/m. MPa. % 57 ._ _ 219 38.8 45 58 TGIC 0.8 673 42.7 78 59 GMA 1.0 764 42.8 71 60 GMA-AA(15) 1.0 657 41.7 50 61 GMA-AA(30) 1.0 678 43.8 66 62 GMA-S-M 1.0 609 47.9 79 63 GMA-S 1.0 710 46.5 98 64 GMA-M 1.0 587 48.2. 86 65 GMA-S-A(IOA) 1.0 657 41.4 53 66 GMA-S-A(IOB) 1.0 684 40.2 49 67 GMA-S-A(20) 1.0 646 43.2 65 The results in Table X show the improvement in impact strength which results from the incorporation of various species of component E in the compositions of this SUBSTITUTE SHEET invention. Such compositions containing component E also have high impact strengths at low temperatures. For example, the composition of Example 67 had an izod impact strength at -40°C of 198 joules/m. Examples 68-70 Blends similar to those of Examples 57-67 were prepared, substituting PPE-W for the product of Example 2. The results are given in Table XI. TABLE XI Component E Izod impact Example Identity Amt., phr. strength, joules/m. 68 294 69 GMA 1.0 680 70 GMA-M 1.0 660 Examples 71-75 These examples show the effect on polyester melt viscosity of premixing the polyester with component E. Premixing was effected by dry blending followed by melt extrusion. The melt viscosities, or, in some cases, melt flow rates (which are inversely proportional to melt viscosities) were compared with those of controls which had been similarly extruded without the addition of component E. The melt viscosity of the polyester before extrusion was about 7,500 poises. The relative parameters and test results are given in Table XII. TABLE XII Melt Component E Melt viscosity, flow rate Example Identity Amt., % poises g./lO min. Controls — — 5,900 38.7 71 TGIC 0.5 41,9000 72 TGIC 1.0 135,000 7 733 G GMMAA 1 1..00 — 5.0 74 GMA-M 1.0 — 3.4 75 GMA-S-A(20) 1.0 — 4.5 SUBSTITUTE SHEE Examples 76-79 Following the procedure of Example 32, compositions were prepared containing 40% of the inactivated polyphenylene ether of Example 2, 40% poly(butylene terephthalate) which had been premixed with TGIC as described in Examples 71-75, 12% SEBS and 8% PC(50,000). The were compared with Controls I and II prepared from untreated poly(butylene terephthalates), and Control III, wherein the TGIC was dry blended with all of the other components. The relative parameters and test results are given in Table XIII. SUBSTITUTE SHEET TABLE XI I I Example Control 76 77 78 79 I II III Component B, ol. wt. 25,000 25,000 25,000 50,000 25,000 50,000 25,000 Component E (TGIC): % based on polyester 0.5 1.0 2.0 0.5 0 0 Amt. in blend, phr. 0.2 0.4 0.8 0.2 0.8 Izod impact strength, joules/m. 224 256 570 500 80 220 192 as I 01 c 09 Α c H m Example 80 This example demonstrates the effect on impact strength of nitrogen content and molecular weight of the polyphenylene ether. Blends were prepared by the procedure of Example 32, using as component D two different bisphenol A polycarbonates prepared interfacially and as component A a number of polyphenylene ethers prepared by procedures which did not include functionalization or vacuum venting. Components B and C were PBT(50,000) and SEBS, respectively. The results are given in Table XIV. TABLE XIV Izod Polyphenylene ether Polycar¬ impact IV, bonate strength dl./g. Nitrogen, ppm. mol. wt. • joules/m. 0.46 1020 50,000 20 0.40 1115 II 20 0.29 497 II 78 0.18 353 n 22 0.53 576 H 57 0.46 1020 71,000 26 0.40 1115 - 26 0.29 497 ■ 115 0.18 353 * 22 0.53 576 n 265 It will be seen that comparatively high impact strengths are obtained by using a polyphenylene ether having a nitrogen content no greater than 800 ppm. and an intrinsic viscosity of at least 0.25 dl./g. Example 81 This example shows the effect of fumaric acid level in the inactivated polyphenylene ether on the impact strengths of the compositions. The procedure of Example 32 was employed to prepare compositions from 40% of various fumaric acid-inactivated polyphenylene ethers, 40% PBT(50,000), 12% SEBS, 8% PC(50,000) and, in certain cases, 0.32 phr. of TGIC. The impact strengths of the compositions are given in Table XV. SUBSTITUTE S TABLE XV Impact strength, Polyphenylene ether TGIC joules/m. Ex. A NO 155 Ex. B NO 198 Ex. C NO 294 Ex. A Yes 700 EX. B Yes 774 EX. C Yes 726 It is apparent that increasing levels of fumaric acid result in substantial increases in impact strength in the absence of component E. The presence of component E inherently causes such a profound increase in impact strength that the effect of fumaric acid level becomes insignificant. Examples 82-84 Formulations having the weight ratios indicated in Table XVI were prepared by blending and extrusion of the components on a Werner-Pfleiderer twin screw extruder. The extruder had two stages. The PPE, polystyrene and half the SEBS were fed to the extruder at its throat in order to ensure intimate mixing. This first stage of the extruder had a set temperature of about 350 to 360°C and vacuum was applied to the melt. The PBT, PC and remaining SEBS were fed downstream at the second stage of the extruder which had a set temperature of about 240 to 250°C. This second stage provided adequate shear mixing of the components while avoiding potential degradation of the components due to exposure to high temperatures for longer periods. The extrudate was quenched in water and pelletized. The pellets were then injection molded into test specimens which were evaluated for heat distortion temperature, flow channel, Dynatup impact, notched Izod impact and tensile yield and elongation. Test results are given in Table XVI. SUBSTITUTE SHEET TABLE XVI ^ _ ^ Examples 82 83 84 Formulation Component A, %: PPE 31.3 28.3 28.3 Polystyrene homopolymer 3 — . 9.4 — HIPS b — — 9.4 Component B: PBT(50,000), % 47.9 43.4 43.4 Component C: SEBS, % 12.5 11.3 11.3 Component D: PC(71,000), % 8.3 7.6 7.6 Properties Heat distortion temperature, °c 147 154 150 Flow channel, cm. 39.4 53.3 48.3 Dynatup impact, joules room temperature 44.7 51.5 52.9 -29°C 47.5 50.2 56.9 Notched izod, joules/m. 828 662 651 Tensile yield, MPa. 41.4 47.6 50.3 Tensile elongation, % 43 29 • 29 Shell 203 clear crystal polystyrene American Hoechst 1897 rubber modified polystyrene Examples 85-88 in this series of examples, blends were prepared in the same manner as described above for Examples 82-84. The weight ratio of the polyphenylene ether to polystyrene (American Hoechst 1897 high impact polystyrene) was varied, in this series, component B was 45% PBT(50,000), component C was 12% SEBS and component D was 8% PC(71,000). Table XVII indicates the manner in which the polyphenylene ether and the polystyrene were varied and reports the results of the physical property tests. It is evident that the proportions of polyphenylene ether and polystyrene can be widely varied and still provide a variety of useful thermoplastic products. SUBSTITUTE SHEET TABLE XVII Example 85 86 87 88 Control Formulation Component A, %: PPE 35 30 25 20 0 HIPS 0 5 10 15 35 Properties Heat distortion temperature, °C 162 158 150 138 103 Flow channel, cm. 41.9 44. ,5 44.5 54.6 83.8 Dynatup impact, joules Room temperature 50.2 47. .5 54.2 50.2 17.6 -29°C 62.4 66. .4 54.2 47.5 Notched l2od, joules/m. 694 721 716 342 69.4 Flex, modulus, GPa. 1 85 1. .90 1.91 1.85 1.70 Flex, strength, MPa. 68 ,3 68. .9 68.9 64.8 49.6 Tensile yield, MPa. 46 , 2 49. .0 45.5 48.3 29.6 Tensile elongation, % 33 30 43 36 8 SUBSTITUTE SHEET

Claims: CLAIMS 1. A resinous composition which comprises the following resinous components and any reaction products thereof, all percentage proportions being by weight of total resinous components: (A) about 10-45% of at least one- polyphenylene ether, or a blend thereof with at least one polystyrene; (B) about 10-45% of at least one poly(alkylene dicarboxylate), the weight ratio of component A to component B being at most 1.2:1; (c) about 8-25% of at least one elastomeric polyphenylene ether-compatible impact modifier; and (D) from 3% to about 40% of at least one polymer containing a substantial proportion of aromatic polycarbonate units and having a weight average molecular weight of at least about 40,000 as determined by " gel permeation chromatography relative to polystyrene, or a blend thereof with a styrene homopolymer. 2. A composition according to Claim 1 wherein component A is a blend of said polyphenylene ether with said polystyrene. 3. A composition according to Claim 2 wherein the polyphenylene ether is a poly(2,6-dimethyl-l,4-phenylene ethe ) . 4. A composition according to Claim 3 wherein the polystyrene is a homopolymer. 5. A composition according to Claim 3 wherein the polystyrene is a rubber-modified polystyrene. 6. A composition according to Claim 2 wherein component A is a poly(2,6-dimethyl-l,4-phenylene ether). 7. A composition according to Claim 6 which comprises about 15-45% of each of components A and B. SUBSTITUTE SHEET 8. A composition according to Claim 6 wherein component B is a poly(ethylene terephthalate) or a poly(butylene terephthalate), component C is a block copolymer of at least one alkenylaromatic compound and at least one diene, and the polycarbonate units in component D are bisphenol A polycarbonate units. 9. A composition according to Claim 7 wherein component B is a poly(butylene terephthalate) having a number average molecular weight in the range of about 20,000-70,000. 10. A composition according to claim 9 wherein component C is a triblock copolymer wherein the end blocks are derived from styrene and the midblock is derived from at least one of isoprene, and butadiene. 11. A composition according to Claim 10 wherein the aliphatic unsaturation in the midblock has been removed by selective hydrogenation. 12. A composition according to Claim 9 wherein component B contains an agent which suppresses ester-carbonate exchange. 13. A composition according to Claim 12 wherein the exchange suppressing agent is sodium dihydrogen phosphate. 14. A composition according to Claim 9 wherein the proportions of components A and B are each about 15-35%, that of component C is about 10-20% and that of component D is about 20-40%. 15. A composition according to Claim 14 wherein component D is a polycarbonate homopolymer having a weight average molecular weight in the range of about 40,000- 80,000. 16. A composition according to Claim 14 wherein component D is a polyester-polycarbonate. 17. A composition according to Claim 14 wherein component D is a poly(2,6-dimethyl-l,4-phenylene ether)- polycarbonate block copolymer. SUBSTITUTE SHE 18. A composition according to Claim 9 wherein the polyphenylene ether contains no more than 800 ppm. of unneutralized amino nitrogen and has an intrinsic viscosity of at least 0.25 as measured in chloroform at 25°c, and wherein the proportions of components A and B are each about 30-45% and that of component D is about 3-10%. 19. A composition according to Claim 18 wherein component A is a polyphenylene ether which has been inactivated by at least one of precompounding with at least one non-volatile compound containing a carboxylic acid or acid anhydride group and extrusion with vacuum venting. 20. A composition according to Claim 19 wherein component B contains an agent which suppresses ester-carbonate exchange. 21. A composition according to Claim 20 wherein the exchange suppressing agent is sodium dihydrogen phosphate. 22. A composition according to Claim 21 wherein component D is a polycarbonate homopolymer having a weight average molecular weight in the range of about 80,000- 200,000. 23. A composition according to Claim 21 wherein there is also present (E) at least one compound selected from those containing at least one cyanurate or isocyanurate moiety and those containing a plurality of epoxide moieties, in the amount of about 0.1-1.0 part per 100 parts of resinous components. 24. A composition according to Claim 23 wherein component E is triallyl cyanurate, triallyl isocyanurate, triphenyl cyanurate or triglycidyl isocyanurate. 25. A composition according to Claim 24 wherein component B contains an agent which suppresses ester-carbonate exchange. SUBSTITUTE SH 26. A composition according to Claim 25 wherein the exchange suppressing agent is.sodium dihydrogen phosphate. 27. A composition according to Claim 26 wherein component D is a polycarbonate homopolymer having a weight average molecular weight in the range of about 40,000- 80,000. 28. A composition comprising the following components and any reaction products thereof, all percentage proportions being by weight of total resinous components: (A) about 15-35% of at least one polyphenylene ether; (B) about 10-35% of at least one poly(alkylene dicarboxylate); (C) about 8-25% of at least one elastomeric polyphenylene ether-compatible impact modifier; and (D) from 12% to about 50% of at least one aromatic polycarbonate; with the provisos that all of component B and at least about 60% of component D are supplied as a poly(alkylene dicarboxylate)-aromatic polycarbonate blend, and that the weight ratio of component A to component B is at most about 1.8:1. 29. A composition according to Claim 28 wherein component A is a poly(2,6-dimethyl-l,4-phenylene ether), component B is a poly(ethylene terephthalate) or a poly(butylene terephthalate) and component C is a block copolymer of at least one alkenylaromatic compound and at least one diene, and component D is a bisphenol A polycarbonate homopolymer. SUBSTITUTE SHEET 30. A composition according to Claim 29 wherein component B is a poly(butylene terephthalate) having a number average molecular weight in the range of about 20,000-70,000; component C is a triblock copolymer wherein the end blocks are derived from styrene and the midblock is derived from at least one of isoprene and butadiene and has been selectively hydrogenated to remove the aliphatic unsaturation; and component D has a weight average molecular weight in the range of about 40,000-80,000. 31. A composition according to Claim 30 wherein component B contains an agent which suppresses ester-carbonate exchange. 32. A composition according to Claim 31 wherein the exchange suppressing agent is sodium dihydrogen phosphate. 33. A composition according to Claim 32 which comprises about 10-20% of component C and about 20-40% of component D, and wherein the weight ratio of component A to component B is about 0.7-1.8:1. SUBSTITUTE SHEET

Inventors: BROWN STERLING BRUCE, LEE GIM FUN, MC FAY DENNIS JOHN, YATES JOHN BENNIE III, BROWN, STERLING, BRUCE, LEE, GIM, FUN, MC FAY, DENNIS, JOHN, YATES, JOHN, BENNIE, III
Applicants: GEN ELECTRIC, GENERAL ELECTRIC COMPANY
Application year: 1986
Main classification: C08L71
IPC codes: C08L67, C08L69, C08L71