Thermoplastic molding compositions with improved solvent resistance and impact strength, and methods for preparation thereof

Thermoplastic molding composition containing a polycarbonate, a polyester, an olefin/carbon monoxide copolymer, a mono-alkenyl aromatic/diene block copolymer and a grafted core-shell elastomer.

FIELD OF THE INVENTION 
This invention relates to compositions wherein polycarbonate has been 
blended with a combination of substances for the purpose of improving the 
solvent resistance and impact strength of such compositions, and methods 
for improving the solvent resistance and impact strength of polycarbonate 
compositions. 
BACKGROUND OF THE INVENTION 
Polycarbonate has found many uses as an engineering thermoplastic because 
it combines, in general, a high level of heat resistance, impact 
resistance and dimensional stability with good insulating and 
non-corrosive properties, and it is easily molded by conventional 
fabrication processes. It does, however, suffer from a tendency to craze 
and crack under the effects of contact with organic solvents such as 
gasoline, especially when under stress such as in flexure, tension or 
torsion. Polycarbonate which has crazed is, undesirably, more likely to 
experience brittle rather than ductile failure upon impact. This 
disadvantage has been somewhat relieved by the practice of blending 
polycarbonate with various olefin polymers such as polyethylene, 
polypropylene or polyisobutylene, as described for example in Goldblum, 
U.S. Pat. No. 3,431,224. However, they can cause delamination of the 
blended composition, as reported for example in Bussink, U.S Pat. No. 
4,122,131. 
In U.S. Pat. No. 4,859,738, a solvent-resistant blend of polycarbonate, 
polyester and ethylene/carbon monoxide copolymer is disclosed. A group of 
several different elastomeric impact modifiers is set forth therein for 
use in such blends. We have found unexpectedly that use of a combination 
of certain of those listed impact modifiers imparts particularly good 
improvement in impact strength to the polycarbonate blend while 
maintaining the resistance to solvents. 
SUMMARY OF THE INVENTION 
In one aspect, this invention involves a composition of matter containing 
(a) a polycarbonate, (b) a polyester, (c) an olefin/carbon monoxide 
copolymer, (d) a thermoplastic elastomer, and (e) a grafted core-shell 
elastomer. In another aspect, this invention involves a method of 
improving the solvent resistance and impact resistance of a composition of 
matter containing (a) a polycarbonate, (b) a polyester and (c) an 
olefin/carbon monoxide copolymer by blending such composition with both 
(d) a thermoplastic elastomer, and (e) a grafted core-shell elastomer. 
It has been found that compositions in which polycarbonate has been admixed 
in a blended composition with a polyester, an ethylene/carbon monoxide 
copolymer, and with both a thermoplastic elastomer and a grafted 
core-shell elastomer display particularly desirable levels of both solvent 
resistance, weldline strength and toughness, and show a reduced tendency 
to delaminate. 
The compositions of this invention are useful, for example, in the 
production of films, fibers, extruded sheets, multi-layer laminates and 
molded or shaped articles of virtually all varieties, especially appliance 
and instrument housings, automobile body panels and other components for 
use in the automotive and electronics industries. 
DETAILED DESCRIPTION OF THE INVENTION 
The compositions of this invention are those in which (a) polycarbonate has 
been admixed in a blended composition with (b) a polyester, (c) an 
olefin/carbon monoxide copolymer, (d) a thermoplastic elastomer, and (e) a 
grafted core-shell elastomer. Suitable ranges of content for the 
compositions of this invention, in parts by weight with reference to the 
total composition, are as follows: (a) polycarbonate from about 10 to 
about 93 parts, (b) polyester from about 5 to about 90 parts, (c) 
olefin/carbon monoxide copolymer from about 1 to about 15 parts, (d) 
thermoplastic elastomer from about 1 to about 15 parts, and (e) grafted 
core-shell elastomer from about 1 to about 30 parts. Preferred ranges of 
content for the compositions of this invention, in parts by weight with 
reference the total composition, are as follows: (a) polycarbonate from 
about 38 to about 87 parts, (b) polyester from about 10 to about 60 parts, 
(c) olefin/carbon monoxide copolymer from about 1 to about 10 parts, (d) 
thermoplastic elastomer from about 1 to about 10 parts, and (e) grafted 
core-shell elastomer from about 1 to about 20 parts. 
Preparation of the compositions of this invention can be accomplished by 
any suitable means known in the art. Typically the substances to be 
admixed with polycarbonate are dry blended in particulate form with 
sufficient agitation to obtain thorough distribution thereof. If desired, 
the dry-blended formulation can further, but need not, be melt mixed, for 
example in an extruder prior to molding. Alternatively, a master batch 
formulation can be prepared containing polycarbonate and the substances to 
be admixed or blended with it wherein polycarbonate is present in only a 
minor proportion, e.g. 20%. The master batch is then available for storage 
or shipment in commerce, and can be diluted with additional polycarbonate 
at the time of use. The compositions of this invention can be formed or 
molded using conventional techniques such as compression, injection, 
calendering, vacuum forming, extrusion and/or blow molding techniques, 
alone or in combination. The compositions can also be formed into films, 
fibers, multi-layer laminates, extruded sheets or molded articles on any 
machine suitable for such purpose. 
(a) Polycarbonate 
The aromatic polycarbonates suitable for use in this invention are produced 
by any of several conventional processes known in the art. Generally, 
aromatic polycarbonates are prepared by reacting an aromatic dihydric 
phenol with a carbonate precursor, such as phosgene, a haloformate or a 
carbonate ester. 
One suitable method for preparing an aromatic polycarbonates involves the 
use of a carbonyl halide, such as phosgene, as the carbonate precursor. 
Phosgene gas is passed into a reaction mixture containing an activated 
dihydric phenol, or containing a nonactivated dihydric phenol and an acid 
acceptor, for example pyridine, dimethyl aniline, quinoline or the like. 
The acid acceptor may be used undiluted or diluted with inert organic 
solvents, such as methylene chloride, chlorobenzene or 1,2-dichloroethane. 
Tertiary amines are advantageous for use as the acid acceptor since they 
are good solvents as well as acid acceptors during the reaction. 
The temperature at which the carbonyl halide reaction proceeds may vary 
from below 0.degree. C. to about 100.degree. C. The reaction proceeds 
satisfactorily at temperatures from room temperature to 50.degree. C. 
Since the reaction is exothermic, the rate of addition of the carbonate 
precursor may be used to control the temperature of the reaction. The 
amount of phosgene or other carbonate precursor required will generally 
depend upon the amount of dihydric phenol present. One mole of phosgene 
typically reacts with one mole of dihydric phenol to form the 
polycarbonate and two moles of HCl. The HCl is in turn taken up by the 
acid acceptor. 
When an activated diphenol is used, phosgene is added to an alkaline 
aqueous suspension of dihydric phenols. Alkali and alkaline earth oxides 
and hydroxides, such as NaOH, are useful for deprotonating the diphenol. 
This is preferably done in the presence of inert solvents such as 
methylene chloride, 1,2-dichloroethane and the like. Quaternary ammonium 
compounds may be employed to catalyze the reaction. 
Another method for preparing an aromatic polycarbonates involves the 
phosgenation of an agitated suspension of an anhydrous alkali salt of an 
aryl diol in a nonaqueous medium such as benzene, chlorobenzene or 
toluene. The reaction is illustrated by the addition of phosgene to a 
slurry of the sodium salt of, for example, 2,2-bis(4-hydroxyphenyl)propane 
("Bisphenol-A") in an inert polymer solvent such as chlorobenzene. 
Generally speaking, a haloformate such as the bis-haloformate of 
Bisphenol-A may be used in place of phosgene as the carbonate precursor in 
any of the methods described above. 
When a carbonate ester is used as the carbonate precursor in the 
polycarbonate-forming reaction, the materials are reacted at temperatures 
in excess of 100.degree. C., for times varying from 1 to 15 hours. Under 
such conditions, ester interchange occurs between the carbonate ester and 
the dihydric phenol used. The ester interchange is advantageously 
consummated at reduced pressures on the order of from about 10 to about 
100 millimeters of mercury, preferably in an inert atmosphere such as 
nitrogen or argon. Although the polymer-forming reaction may be conducted 
in the absence of a catalyst, one may, if desired, employ a typical ester 
exchange catalyst, such as metallic lithium, potassium, calcium or 
magnesium. The amount of such catalyst, if used, is usually small, ranging 
from about 0.001% to about 0.1%, based on the weight of the dihydric 
phenols employed. 
In the solution methods of preparation, the aromatic polycarbonate emerges 
from the reaction in either a true or pseudo solution depending on whether 
an aqueous base or pyridine is used as an acid acceptor. The copolymer may 
be precipitated from the solution by adding a polymer nonsolvent, such as 
heptane or isopropanol. Alternatively, the polymer solution may be heated, 
typically under reduced pressure, to evaporate the solvent. 
The methods and reactants described above for preparing carbonate polymers 
suitable for use in the practice of this invention are discussed in 
greater detail in Moyer, U.S. Pat. No. 2,970,131; Schnell, U.S. Pat. No. 
3,028,365; Campbell, U.S. Pat. No. 4,384,108: Glass U.S. Pat. No. 
4,529,791: and Grigo, U.S. Pat. No. 4,677,162, each being incorporated as 
a part hereof. 
A preferred aromatic polycarbonate is characterized by repeated units 
corresponding to the general formula: 
##STR1## 
wherein X is a divalent C.sub.1 -C.sub.15 hydrocarbon radical, a single 
bond, --O--, --S--, --S.sub.2 --, --SO--, --SO.sub.2 --, or --CO--. Each 
aromatic ring may additionally contain, instead of hydrogen, up to four 
substituents such as C.sub.1 -C.sub.4 alkyl hydrocarbon or alkoxy 
radicals, C.sub.6 -C.sub.14 aryl hydrocarbon or aryloxy radicals, or halo 
radicals, or mixtures thereof. 
Although the polycarbonates mentioned above, such as those derived from 
Bisphenol-A, from 2,2-bis(3,5-dibromo, 4-hydroxyphenyl)propane 
("Tetrabromo Bisphenol-A"), or from 1,1-bis(4-hydroxyphenyl)-1-phenyl 
ethane ("Bisphenol-AP"), can each be employed herein as a homopolymer, the 
carbonate polymers used in this invention can also be derived from two or 
more different bisphenols or other aryl dihydroxy compounds to obtain a 
carbonate copolymer. Carbonate copolymers can also be formed when a 
bisphenol is reacted with a carbonic acid derivative and a 
polydiorganosiloxane containing .alpha.,.omega.-bishydroxyaryloxy terminal 
groups to yield a siloxane/carbonate block copolymer, as are discussed in 
greater detail in Paul, U.S. Pat. No. 4,569,970, which is incorporated 
herein. Or, when an aryl dihydroxy compound is reacted with a diacid, or 
when a bisphenol is reacted with a bis(ar-haloformylaryl) carbonate, a 
copolymer in the form of a copolyestercarbonate is obtained. A 
bis(ar-haloformylaryl) carbonate is formed, for example, by reacting a 
hydroxycarboxylic acid with a carbonic acid derivative under carbonate 
forming conditions. Copolyestercarbonates are discussed in greater detail 
in Swart, U.S. Pat. No. 4,105,533, which is incorporated herein. 
The term "polycarbonate" as used herein, and in the claims appended hereto, 
should therefore be understood to include carbonate homopolymers, 
carbonate copolymers (including, but not limited to, the representative 
varieties described above), and/or blends of carbonate homopolymers and/or 
carbonate copolymers. 
(b) Polyester 
The polyester used in this invention may be made by a variety of methods. 
Although the self-esterification of hydroxycarboxylic acids is known, 
direct esterification, which involves the reaction of a diol with a 
dicarboxylic acid with the resulting elimination of water, is a more 
frequently used method for commercial production, giving an --[--AABB--]-- 
polyester. The presence of a catalyst such as p-toluene sulfonic acid, a 
titanium alkoxide or a dialkyltin oxide is helpful, but the primary 
driving force behind direct esterification reaction is heat. Temperatures 
applied exceed the melting points of the reactants, often approach the 
boiling point of the diol being used, and usually range from about 
150.degree. C. to about 280.degree. C. An excess of the diol is typically 
used, and once all of the acid has reacted with diol, the excess diol is 
removed by distillation with the application of additional heat under 
reduced pressure. The ester of the diacid initially formed from the diol, 
having --OH end groups, undergoes alcoholysis and polymerization to form 
polymeric esters and the diol is split out as a byproduct and removed from 
the reaction zone. The reaction is typically carried out in the presence 
of an inert gas. 
Alternatively, but in like manner, ester-forming derivatives of a 
dicarboxylic acid can be heated with a diol to obtain polyesters in an 
ester interchange reaction. Suitable acid derivatives for such purpose are 
esters, halides, salts or anhydrides of the acid. When a bis ester of the 
diacid is used for purposes of the interchange reaction, the alcohol from 
which the ester is formed (the alcohol to be displaced) should be lower 
boiling than the diol to be used for formation of polyester (the 
displacing alcohol). The reaction can then be conveniently run at a 
temperature at or below the boiling point of the displacing alcohol but 
well above that of the displaced alcohol, and is usually run in a 
temperature range similar to that for direct esterification. The ester 
interchange reaction is typically run in the presence of a diluent, for 
example, an inert organic solvent such as chloroform or tetrachloroethane, 
and in the presence of a base, for example a tertiary organic base such as 
pyridine. Typical catalysts used when ester interchange involves 
alcoholysis are weak bases such as carbonates or alkoxides of sodium, 
lithium. zinc, calcium, magnesium or aluminum, whereas catalysts such as 
antimony oxide, titanium butoxide or sodium acetate are often used when 
acidolysis occurs in the interchange reaction. Diol derivatives such as an 
acetate can be used effectively when it is desired to conduct acidolysis. 
Polyesters can also be produced by a ring-opening reaction of cyclic esters 
or lactones, for which organic tertiary bases and alkali and alkaline 
earth metals, hydrides and alkoxides can be used as initiators. Advantages 
offered by this type of reaction are that it can be run at lower 
temperatures, frequently under 100.degree. C., and there is no need to 
remove a condensation product from the reaction. 
An example of a method of preparing a polyester is reported in U.S. Pat. 
No. 2,465,319 as follows: "1.7 grams of terephthalic acid and 4.5 grams of 
tetramethylene glycol were heated together at 220.degree. C.-240.degree. 
C. for about 3 hours until solution was effected. The resulting melt was 
heated for 21/2 hours at 249.degree. C. with a stream of nitrogen passing 
through the molten mass, and then for a further 12 hours at 249.degree. C. 
under vacuum. The resulting highly polymeric tetramethylene terephthalate 
cooled to a crystalline, porcelain-like polymer of melting point 
208.degree. C. which could be melt-spun to give filaments possessing good 
cold-drawing properties." 
Suitable reactants for making the polyester used in this invention, in 
addition to hydroxycarboxylic acids, are diols and dicarboxylic acids 
either or both of which can be aliphatic or aromatic. A polyester which is 
a poly(alkylene alkanedicarboxylate), a poly(alkylene 
phenylenedicarboxylate), a poly(phenylene alkanedicarboxylate), or a 
poly(phenylene phenylenedicarboxylate) is therefore appropriate for use 
herein. Alkyl portions of the polymer chain can be substituted with, for 
example, halogens, alkoxy groups or alkyl side chains and can contain 
divalent heteroatomic groups (such as --O--, --S--, or --SO.sub.2 --) in 
the paraffinic segment of the chain. The chain can also contain 
unsaturation and non-aromatic rings. Aromatic rings can contain 
substituents such as halogens, alkoxy or alkyl groups, and can be joined 
to the polymer backbone in any ring position and directly to the alcohol 
or acid functionality or to intervening atoms. 
Typical alkylene diols used in ester formation are the C.sub.2 -C.sub.10 
glycols, such as ethylene-, propylene-, and butylene glycol. 
Alkanedicarboxylic acids frequently used are oxalic acid, adipic acid and 
sebacic acid. Diols which contain rings can be, for example, a 
1,4-cyclohexylenyl glycol or a 1,4-cyclohexane-dimethylene glycol, 
resorcinol, hydroquinone, 4,4'-thiodiphenol, bis-(4-hydroxyphenyl)sulfone, 
a dihydroxynaphthalene, a xylylene diol, or can be one of the many 
bisphenols such as 2,2-bis-(4-hydroxyphenyl)propane. Aromatic diacids 
include, for example, terephthalic acid, isophthalic acid, 
naphthalenedicarboxylic acid, diphenyletherdicarboxylic acid, 
diphenyldicarboxylic acid, diphenylsulfonedicarboxylic acid, 
diphenoxyethanedicarboxylic acid. 
In addition to polyesters formed from one diol and one diacid only 
("homopolyesters"), the term "polyester" as used herein and in the 
appended claims includes random, alternating, patterned or block 
copolyesters, for example those formed from two or more different diols 
and/or two or more different diacids, and/or from other divalent 
heteroatomic groups. Mixtures of such homopolyesters, mixtures of such 
copolyesters, and mixtures of members from both of such groups, are also 
all suitable for use in this invention and are included in the term 
"polyester". For example, use of cyclohexanedimethylol together with 
ethylene glycol in esterification with terephthalic acid forms a clear, 
amorphous copolyester, such as "PETG" manufactured by Eastman Kodak. Also 
contemplated are liquid crystalline polyesters derived from mixtures of 
4-hydroxybenzoic acid and 2-hydroxy-6-naphthoic acid; or mixtures of 
terephthalic acid, 4-hydroxybenzoic acid and ethylene glycol; or mixtures 
of terephthalic acid, 4hydroxybenzoic acid and 4,4'-dihydroxybiphenyl. 
Aromatic polyesters such as the poly(alkylene phenylenedicarboxylates) 
polyethylene terephthalate and polybutylene terephthalate, or mixtures 
thereof, are particularly useful in this invention. 
Methods and materials useful for the production of polyesters, as described 
above, are discussed in greater detail in Whinfield, U.S. Pat. No. 
2,465,319 Pengilly, U.S. Pat. No. 3,047,539 and Russell, U.S. Pat. No. 
3,756,986, each being incorporated herein by reference. 
(c) Olefin Copolymer 
An olefin copolymer which contains a carbonyl functionality in its backbone 
is advantageously utilized in this invention, and the preferred such 
olefin copolymer is ethylene/carbon monoxide copolymer ("ECO"). ECO is 
typically formed from ethylene and carbon monoxide in a pressure vessel 
using a peroxy catalyst, or a metallic catalyst such as palladium. A 
hydrocarbon liquid which is non-reactive under the polymerization 
conditions, for example one which acts as a solvent for the catalyst 
system and in which the catalyst is stable, can be used as a diluent and 
reaction medium. Air and water are preferably excluded from the reaction 
chamber. The polymerization can be performed at temperatures in the range 
from 10.degree. C. up to 200.degree. C., but is preferably run in the 
range of 50.degree. C. to 140.degree. C. Pressures as high as 3,000 
atmospheres (303 MPa) may be employed in the reaction, but the usual 
pressure of operation is in the range of 20 atmospheres (2.02 MPa) to 
about 1,500 atmospheres (151.5 MPa). Both yield and molecular weight 
increase with increasing pressure. Alternatively, an olefin/carbon 
monoxide copolymer can be made without solvent under high pressure 
conditions, using a free radical initiator in a stirred autoclave. 
A variety of olefin monomers in place of or in addition to ethylene, and 
numerous unsaturated monomers in addition to the olefin, can be used along 
with carbon monoxide to form the copolymer backbone. Any unsaturated 
monomer which will undergo polymerization across a &gt;C.dbd.C&lt; bond can form 
part of the olefin/carbon monoxide ("olefin/CO") copolymer, although the 
following are preferred: olefin monomers such as propylene, isobutylene, 
1-butene or other substituted and unsubstituted C.sub.3 -C.sub.8 alpha 
alkenes; and unsaturated or vinyl monomers such as butadiene; allyl 
esters; vinyl acetate; vinyl chloride; vinyl aromatics such as styrene; 
alkyl acrylates or methacrylates such as ethyl acrylate or methyl 
methacrylate; acrylonitrile; tetrafluoroethylene; or the like and mixtures 
thereof. The structure of the olefin/carbon monoxide copolymer can be 
random or alternating. The Carbon monoxide content in the olefin/CO 
copolymer is from about 0.1% to about 40%, and preferably from about 0.5% 
to about 30%, by weight. A copolymer of carbon monoxide and an 
alpha-mono-olefin, and methods for preparation thereof, are discussed in 
greater detail in Lancaster, U.S. Pat. No. 4,600,614, Brubaker, U.S. Pat. 
No. 2,495,286, Loeb, U.S. Pat. No. 3,083,184, Fenton, U.S. Pat. No. 
3,530,109 and Nozaki, U.S. Pat. No. 3,694,412, each being incorporated 
herein. 
What is set forth above concerning methods of making ECO applies equally to 
other forms of said olefin/CO copolymer which result from variation in the 
monomer mix. The olefin/CO copolymer used herein can be made from any of 
the various monomers, and can be made by any of the various methods, which 
are included above in the discussion relating specifically to the 
manufacture of ECO. However, the most preferred olefin/CO copolymer is 
ECO. 
(d) Thermoplastic Elastomer 
The thermoplastic elastomer utilized in this invention can be either linear 
or branched, and can be either a di-block ("A--B") copolymer or tri-block 
("A--B--A") copolymer with or without tapered sections, i.e. portions of 
the polymer where the monomers alternate or are in random order close to 
the point of transition between the A and B blocks. The A portion is made 
by polymerizing one or more mono-alkenyl or vinyl aromatic hydrocarbon 
monomers, and has an average molecular weight of about 4,000 to about 
115,000, and a weight preferably of about 8,000 to about 60,000. The B 
portion of the block copolymer results from polymerizing a diene and has a 
molecular weight of about 20,000 to about 450,000, and a weight preferably 
of about 50,000 to about 300,000. In the A--B di-block copolymer, each 
block, A or B, can vary from 10-90% of the total weight of the copolymer. 
In the A--B--A tri-block copolymer, the A end groups typically constitute 
about 2 wt % to about 55 wt % of the whole block copolymer, and preferably 
are between 5 wt % and 30 wt % of the whole block copolymer. 
The A block of the block copolymer has properties characteristic of 
thermoplastic substances in that it has the stability necessary for 
processing at elevated temperatures and yet possesses good strength below 
the temperature at which it softens. The A block is polymerized 
predominantly from vinyl aromatic hydrocarbons, and substituted 
derivatives thereof wherein the aromatic moiety can be either mono- or 
polycyclic. Monomers from which the thermoplastic end blocks can be formed 
are, for example, styrene and substituted derivatives thereof such as 
.alpha.-methyl styrene, vinyl xylene, vinyl naphthalene, and the like, and 
mixtures of two or more thereof. Other vinyl monomers such as methyl 
acrylate, methyl methacrylate, acrylonitrile or vinyl pyridine may be used 
in the formation of the A block together with the aromatic monomers. The 
polymerization can be initiated by lithium metal, or alkyl- or aryl 
lithium compounds such as butyl lithium or isoamyl lithium. Polymerization 
is normally conducted at temperatures ranging from about -20.degree. C. to 
about 100.degree. C., and initiator is used in as low an amount as 
possible up to about 200 ppm based on the weight of the monomers present. 
A hydrocarbon inert to the polymerization reaction, for example an alkane 
such as hexane, is used as solvent for the reaction. Polymerization is 
typically carried out under a nitrogen blanket. When the initiator is 
injected into the monomer, anionic polymerization ensues forming a 
"living" polymer which carries the charge orinally acquired from the 
initiator. 
The B block of the copolymer can be formed, for example, simply by 
injecting suitable monomer into the reaction vessel and displacing the 
lithium radical from the just-polymerized A block, which acts as an 
initiator because it is still charged. The B block is formed predominantly 
from substituted or unsubstituted C.sub.2 -C.sub.10 dienes, particularly 
conjugated dienes such as butadiene or isoprene. Other diene, vinyl or 
olefinic monomers such as chloroprene, 1,4-pentadiene, isobutylene, 
ethylene or vinyl chloride may be used in the formation of the B block 
provided that they are present at a level low enough to not alter the 
fundamental olefinic character of the B block. The mid block will be 
characterized by elastomeric properties which allow it to to absorb and 
dissipate an applied stress and then regain its shape. 
In the A--B--A tri-block copolymer, the second end block A can be formed in 
a manner similar to the first, by injecting appropriate alkenyl aromatic 
monomer (as described above) into the reaction vessel. Alternatively, a 
bivalent lithium initiator can be used, which, when brought together with 
the diene monomer under the same conditions described above, will form an 
elastomeric mid block B which carries a charge at each end. Then, upon 
addition of alkenyl aromatic monomer to the reaction mixture, a 
thermoplastic end block A will form on both ends of the mid block B, 
yielding a thermoplastic elastomeric A--B--A copolymer. 
When a coupling agent is used to form either the di-block or tri-block 
copolymer, an A block is polymerized as described above from monovinyl 
arene monomers and a B block, bearing a terminal lithium ion, is 
polymerized from diene monomer. A coupling agent such as a diester, a 
polyester, a polyhalohydrocarbon, a silicon halide or divinyl benzene, 
when then charged to the reaction mixture, will link the A and B portions 
together. If a coupling agent with a functionality of 3 or greater is 
used, a branched copolymer is obtained. 
To reduce oxidative and thermal instability, the block copolymers used 
herein can also desirably be hydrogenated to reduce the degree of 
unsaturation on the polymer chain and on the pendant aromatic rings. 
Typical hydrogenation catalysts utilized are Raney nickel, molybdenum 
sulfide, finely divided palladium and platinum oxide. The hydrogenation 
reaction is typically run at 75.degree. F.-450.degree. F. and at 100-1,000 
psig for 10-25 hours. 
The most preferred thermoplastic elastomers are vinyl aromatic/conjugated 
diene block copolymers formed from styrene and butadiene or styrene and 
isoprene. When the styrene/butadiene copolymers are hydrogenated, they are 
frequently represented as styrene/ethylene/butylene (or 
styrene/ethylene/butylene/styrene in the tri-block form) copolymers. When 
the styrene/isoprene copolymers are hydrogenated, they are frequently 
represented as styrene/ethylene/propylene (or 
styrene/ethylene/propylene/styrene in the tri-block form) copolymers. The 
thermoplastic elastomers described above are discussed in greater detail 
in Haefele, U.S. Pat. No. 3,333,024 and Wald, U.S. Pat. No. 3,595,942, 
each being incorporated herein. 
(e) Core-Shell Elastomer 
The grafted core-shell elastomer used in this invention can be based on 
either a diene rubber, an acrylate rubber or on mixtures thereof. 
A diene rubber contains a substrate latex, or core, which is made by 
polymerizing a diene, preferably a conjugated diene, or by copolymerizing 
a diene with a mono-olefin or polar vinyl compound, such as styrene, 
acrylonitrile, or an alkyl ester of an unsaturated carboxylic acid such as 
methyl methacrylate. The substrate latex is typically made up of about 
40-85% diene, preferably a conjugated diene, and about 15-60% of the 
mono-olefin or polar vinyl compound. The elastomeric core phase should 
have a glass transition temperature ("T.sub.g ") of less than about 
0.degree. C., and preferably less than about -20.degree. C. A mixture of 
monomers is then graft polymerized to the substrate latex. A variety of 
monomers may be used for this grafting purpose, of which the following are 
exemplary: vinyl compounds such as vinyl toluene or vinyl chloride; vinyl 
aromatics such as styrene, alpha-methyl styrene or halogenated styrene; 
acrylonitrile, methacrylonitrile or alpha-halogenated acrylonitrile; a 
C.sub.1 -C.sub.8 alkyl acrylate such as ethyl acrylate or hexyl acrylate; 
a C.sub.1 -C.sub.8 alkyl methacrylate such as methyl methacrylate or hexyl 
methacrylate; acrylic or methacrylic acid; and the like or a mixture of 
two or more thereof. 
The grafting monomers may be added to the reaction mixture simultaneously 
or in sequence, and, when added in sequence, layers, shells or wart-like 
appendages can be built up around the substrate latex, or core. The 
monomers can be added in various ratios to each other although, when just 
two are used, they are frequently utilized in equal amounts. A typical 
weight ratio for methyl methacrylate/butadiene/styrene copolymer ("MBS" 
rubber) is about 60-80 parts by weight substrate latex, about 10-20 parts 
by weight of each of the first and second monomers. A preferred 
formulation for an MBS rubber is one having a core built up from about 71 
parts of butadiene, about 3 parts of styrene, about 4 parts of methyl 
methacrylate and about 1 part of divinyl benzene; a second phase of about 
11 parts of styrene; and a shell phase of about 11 parts of methyl 
methacrylate and about 0.1 part of 1,3-butylene glycol dimethacrylate, 
where the parts are by weight of the total composition. A product having 
substantially such content is available commercially from Rohm and Haas 
Company as Paraloid.TM. EXL 3607 copolymer. MBS rubber and methods for 
making same, as described above, are discussed in greater detail in Saito, 
U.S. Pat. No. 3,287,443, Curfman, U.S. Pat. No. 3,657,391, and Fromuth, 
U.S. Pat. No. 4,180,494, each being incorporated herein. 
An acrylate rubber has a first phase forming an elastomeric core and a 
second phase forming a rigid thermoplastic phase about said elastomeric 
core. The elastomeric core is formed by emulsion or suspension 
polymerization of monomers which consist of at least about 50 weight 
percent alkyl and/or aralkyl acrylates having up to fifteen carbon atoms, 
and, although longer chains may be used, the alkyls are preferably C.sub.2 
-C.sub.6, most preferably butyl acrylate. The elastomeric core phase 
should have a t.sub.g of less than about 25.degree. C., and preferably 
less than about 0.degree. C. 
The rigid thermoplastic phase of the acrylate rubber is formed on the 
surface of the elastomeric core using suspension or emulsion 
polymerization techniques. The monomers necessary to create this phase 
together with necessary initiators are added directly to the reaction 
mixture in which the elastomeric core is formed, and polymerization 
proceeds until the supply of monomers is substantially exhausted. Monomers 
such as an alkyl ester of an unsaturated carboxylic acid, for example a 
C.sub.1 -C.sub.8 alkyl acrylate like methyl acrylate, hydroxy ethyl 
acrylate or hexyl acrylate, or a C.sub.1 -C.sub.8 alkyl methacrylate such 
as methyl methacrylate or hexyl methacrylate, or mixtures of any of the 
foregoing, are some of the monomers which can be used for this purpose. 
Either thermal or redox initiator systems can be used. Because of the 
presence of the graft linking agents on the surface of the elastomeric 
core, a portion of the chains which make up the rigid thermoplastic phase 
are chemically bonded to the elastomeric core. It is preferred that there 
be at least about 20% bonding of the rigid thermoplastic phase to the 
elastomeric core. 
A preferred acrylate rubber is made up of more than about 40% to about 95% 
by weight of an elastomeric core and about 60% to about 5% of a rigid 
thermoplastic phase. The elastomeric core can be polymerized from about 
75% to about 99.8% by weight C.sub.1 -C.sub.6 acrylate, preferably n-butyl 
acrylate. The rigid thermoplastic phase can be polymerized from at least 
50% by weight of C.sub.1 -C.sub.8 alkyl methacrylate, preferably methyl 
methacrylate. A product having substantially such content is available 
commercially from Rohm and Haas Company as Paraloid.TM. 3330 composite 
interpolymer. Acrylate rubbers and methods for making same, as described 
above, are discussed in greater detail in Owens, U.S. Pat. No. 3,808,180 
and Witman, U.S. Pat. No. 4,299,928, each being incorporated herein. 
Numerous additives are available for use in the compositions of this 
invention for a variety of purposes including protection against thermal, 
oxidative and ultra-violet degradation. Representative of thermal and 
oxidative stabilizers which can advantageously be utilized herein are 
hindered phenols, hydroquinones, phosphites, including substituted members 
of those groups and/or mixtures of more than one thereof. A preferred 
phenolic anti-oxidant is Irganox.TM. 1076 anti-oxidant, which is available 
from Ciba-Geigy Corp. and is discussed in greater detail in U.S. Pat. Nos. 
3,285,855 and 3,330,859, each being incorporated herein. Ultraviolet light 
stabilizers such as various substituted resorcinols, salicylates, 
benzotriazoles, benzophines and hindered phenols can also be usefully 
included herein, as can be lubricants; colorants; fillers such as talc; 
pigments; ignition resistance additives; mold release agents; and 
reinforcing agents such as fiberglass. Additives and stabilizers such as 
the foregoing, and others which have not been specifically mentioned, are 
known in the art, and the decision as to which, if any, to use is not 
critical to the invention. However, such additives, if used, will 
typically not exceed 50% by weight of the total composition, and 
preferably will not exceed 30% by weight thereof.

ILLUSTRATIVE EMBODIMENTS 
To illustrate the practice of this invention, examples of several preferred 
embodiments are set forth below. It is not intended, however, that these 
examples (Examples 1-3) should in any manner restrict the scope of this 
invention. Some of the particularly desirable features of this invention 
may be seen by contrasting the characteristics of Examples 1-3 with those 
of various controlled formulations (Controls A-E) which do not possess the 
features of, and are not therefore embodiments of, this invention. 
The respective components of Controls A-E and Examples 1-3 are dry blended 
by tumble blending for seven minutes. The components of each control and 
example are then extruded in a 30 mm co-rotating twin screw 
Werner-Phfleiderer vented extruder, however the components are not dried 
prior to the tumble blending or the extrusion. Removal of water, which 
could be detrimental to polyester, is achieved to some extent through the 
vent on the extruder, which allows the escape of any water vapor driven 
off by the heat of the melt process. A vacuum may be used at the vent to 
increase the removal of water vapor. The set temperatures on the extruder 
(.degree. C.), from front to rear, are 270, 270, 270, 270 and 200, and the 
screw speed is 250 rpm. 
The extruded pellets are dried prior to injection molding at about 
105.degree. C. for about six hours in a hot air circulating oven, and are 
then molded into test specimens using a 75-ton Arburg molding machine. The 
injection molding conditions are as follows: set temperatures (.degree. 
C.) rear 270, middle 270, front 270, nozzle 270 and mold 85; and screw 
speed 300 rpm. 
The amounts of the various components which are blended or admixed to form, 
respectively, Controls A-E and Examples 1-3 are shown in Table I, wherein 
amount, or content, is stated by wt % of the total composition. The 
following components are identified in Table I as follows: 
"(1) Polycarbonate" is Calibre.RTM.300-10 polycarbonate resin, a 10 melt 
flow value polycarbonate resin available from The Dow Chemical Company; 
"(2) Polyester" is poly(ethylene terephthalate) available from Goodyear 
Tire & Rubber Company as Traytuf.TM. 1006C polyester resin; 
"(3) ECO" is an ethylene/carbon monoxide copolymer of which the portion 
derived from carbon monoxide is 10% by weight of the copolymer; 
"(4) P-3607" is Paraloid.TM. EXL 3607 grafted core-shell elastomer, an MBS 
rubber available from Rohm & Haas Co.; 
"(5) P-3339" is Paraloid.TM. 3330 grafted core-shell elastomer, a butyl 
acrylate rubber available from Rohm & Haas Co.; 
"(6) S/E-B/S Block Copolymer" is a hydrogenated 
styrene/ethylene-butylene/styrene tri-block copolymer available from Shell 
Chemical Company as Kraton.TM. G-1651 elastomer; 
"(7) S/B Block Copolymer" is a non-hydrogenated styrene/butadiene di-block 
copolymer available from Shell Chemical Company as Kraton.TM. D-1102 
elastomer; 
"(8) ESO", epoxidized soybean oil, is used as a tackifier to cause "(9) 
IR-1076", Irganox.TM. 1076 anti-oxidant, to adhere to and be evenly 
distributed over the pellets making up the contents of each composition. 
The results of tests performed on Controls A-E and Examples 1-3 are also 
shown in Table I. 
Specular gloss is measured according to ASTM Designation D 523 by using a 
Dr. Bruno Lange Reflectometer RB. 
Tensile strength at break, and percent elongation at break, is measured in 
accordance with ASTM Designation D 638-84, with respect to a sample 
(Control B) which has been placed under 0.7% strain while submerged in a 
bath of 60 vol % isooctane and 40 vol % toluene for 5 minutes and then has 
been allowed to dry for 24 hours before testing, and with respect to 
samples (Controls A and C-E and Examples 1-3) which have been placed under 
0.5% strain while submerged in a bath of 60 vol % isooctane and 40 vol % 
toluene for 5 minutes and then have been allowed to dry for 24 hours 
before testing. 
Impact resistance is measured by the lzod test according to ASTM 
Designation D 256-84 (Method A). The notch is 10 mils (0.254 mm) in 
radius. An inverted T (.perp.) indicates that the notch is cut so that the 
flexural shock caused by the striking nose of the pendulum is propagated 
parallel to the direction of flow taken by the polymer melt during 
formation of the sample. Vertical parallel lines (.parallel.) indicate 
that the notch is cut so that the shock caused by the striking nose of the 
pendulum is propagated perpendicular to the direction of flow taken by the 
polymer melt during formation of the sample. 
Weldline Izod strength is also measured according to ASTM Designation D 
256-84 (Method A), but with respect to a sample which has been formed with 
a butt weld in a double gated mold. The sample is unnotched, and it is 
placed in the vise so that the weld is coincident with the top surface of 
the vise jaws. 
TABLE I 
__________________________________________________________________________ 
Content and Test Results 
for Controls A-E and Examples 1-3 
Con- 
Con- 
Con- 
Con- 
Con- 
trol 
trol 
trol 
trol 
trol 
A B C D E Ex. 1 
Ex. 2 
Ex. 3 
__________________________________________________________________________ 
(1) Polycar- 
70 64.7 
64.7 
64.7 
64.7 
64.7 
62.7 
64.7 
bonate 
(2) Polyester 
20 20 20 20 20 20 20 20 
(3) ECO -- -- 7 7 7 4 5 4 
(4) P-3607 
-- 8 8 -- -- 7 -- 7 
(5) P-3339 
-- -- -- -- -- -- 7 -- 
(6) S/E-B/S 
10 7 -- 8 -- 4 5 -- 
Block 
Copolymer 
(7) S/B Block 
-- -- -- -- 8 -- -- 4 
Copolymer 
(8) ESO 0.1 
0.1 0.1 
0.1 0.1 
0.1 0.1 
0.1 
(9) IR-1076 
0.2 
0.2 0.2 
0.2 0.2 
0.2 0.2 
0.2 
20.degree. gloss 
70 19 84 30 11 58 39 17 
60.degree. gloss 
95 64 96 83 59 91 88 75 
tensile 7,138 
6,389 
7,711 
6,617 
5,592 
8,143 
8,185 
7,805 
strength psi 
psi psi 
psi psi 
psi psi 
psi 
at break 
percent 6 5 121 
135 22 172 120 
127 
elongation 
at break 
Weldline 19.7 
15.3 
2.4 
2.6 1.6 
8.8 3.0 
7.1 
Izod, ft-lb/in 
Izod, .perp., 23.degree. C. 
13.6 
8.1 4.5 
7.2 5.1 
9.5 8.8 
10.2 
ft-lb/in 
Izod, .parallel., 23.degree. C. 
15.1 
13.3 
10.2 
16.1 
12.6 
15.1 
18.5 
15.1 
ft-lb/in 
Izod, .parallel., -20.degree. C. 
6.8 
11.0 
6.7 
2.4 2.9 
18.2 
4.9 
15.2 
ft-lb/in 
__________________________________________________________________________ 
The test data in Table 1 show that compositions of polycarbonate, polyester 
and olefin/carbon monoxide copolymer which contain both a thermoplastic 
elastomer and a grafted core-shell elastomer possess particularly 
desirable levels of solvent resistance, weldline strength and toughness. 
In Control A, it can be seen that when a thermoplastic elastomer is 
admixed with a polycarbonate/polyester blend without an olefinic 
copolymer, the composition possesses good weldline and impact strength, 
but has very low solvent resistance, as is evident from only a 6% 
elongation at break reading. Even the addition of a core-shell elastomer, 
as in Control B, does not improve the solvent resistance. 
Compositions which contain an olefin/carbon monoxide copolymer, such as 
Controls C-E, generally do have good solvent resistance. However, as these 
compositions contain only a thermoplastic elastomer or a core-shell 
elastomer, but not both, they do not display weldline and impact strength 
(particularly low temperature toughness) at the highly desirable levels of 
Examples 1-3. The compositions which do contain both a thermoplastic 
elastomer and a grafted core-shell elastomer (Examples 1-3) display a 
balance of particularly desirable levels of both solvent and impact 
resistance and weldline strength. This demonstrates that the use of both a 
thermoplastic elastomer and a grafted core-shell elastomer in a 
polycarbonate/polyester/olefin/CO blend, as in the compositions of this 
invention, provides compositions which have a particularly desirable 
balance of solvent and impact resistance and weldline strength as opposed 
to compositions which contain only one of those elastomers. 
It is within the skill in the art to practice this invention in numerous 
modifications and variations in light of the above teachings. It is, 
therefore, to be understood that the various embodiments of this invention 
described herein may be altered without departing from the spirit and 
scope of this invention as defined by the appended claims.