Multiphase Polymers - American Chemical Society

29 Polymer Compatibilization: Blends of Polyarylethers with Styrenic Interpolymers

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O L A G O K E OLABISI and A. G . F A R N H A M Research and Development Department, Chemicals and Plastics, U n i o n Carbide C o r p . , B o u n d Brook, N J 08805

The polymer compatibilization concept is to modify advan tageously the mechanical properties of a normally incom patible mixture by the addition of a suitable compatibilizing agent consisting usually of a block or graft copolymer. These interpolymers act as interfacial bridges between the components in the mixture. In this work, the 'compatibili zation concept' is invoked, but pendant chemical groups are the compatibilizing agents rather than the more usual co polymers. Nitrile and/or ester groups have been attached conveniently to the backbone of a series of polyarylethers to compatibilize the ethers with αmethyl styrene/methyl methacrylate/acrylonitrile interpolymers. The choice of the ap propriate pendant chemical groups was made on the basis of the observation that the styrene interpolymers are miscible with polymers that contain these specific groups.

Λ miscible polymer-polymer blend almost always yields a physicalproperty spectrum superior to the individual components, and this allows the development of a new set of products with significant savings in capital investment. Partly for this reason and partly because new and commercially viable polymers are becoming harder to 'come b y , ' the plastic industry has expended a sizeable sum towards identifying miscible high-performance polymer mixtures. Indeed, the more recent renewed ex perimental and theoretical programs have resulted in an increased number of known miscible blends. O n the commercial scene, however, successful miscible polymer-polymer blends are still rather few and are limited to 0-8412-0457-8/79/33-176-559$06.75/0 © 1979 American Chemical Society In Multiphase Polymers; Cooper, S., et al.; Advances in Chemistry; American Chemical Society: Washington, DC, 1979.


560

MULTIPHASE

POLYMERS

polystyrene-poly(2,6-dimethyl 1,4-phenylene oxide), elastomer blends, miscible polymeric coatings, and blends of P V C with its permanent plasticizers. O n the other hand, some mechanically compatible blends as well as some dispersed two-phase systems have made respectable inroads into the commercial scene. M a n y of these are blends of low-impact resins with high-impact elastomeric polymers; examples are polystyrene/rubber, poly ( styrene-co-acrylonitrile ) /rubber, poly ( methyl methacrylate ) /rub ber, poly (ethylene propylene ) /propylene rubber, and bis-A polycarbon ate/ABS as well as blends of polyvinyl chloride with A B S or P M M A or chlorinated polyethylene. Another concept which has been exploited is the 'compatibilization' technique ( 1 - 7 ) . The idea is to advantageously modify the mechanical properties of a normally incompatible mixture by the addition of suitable compatibilizing agents. Use of such agents is exemplified by the blend of poly (ethyl aery late) with polystyrene-grafted poly (ethyl acrylate ) (1,2); the mixture of polyvinyl chloride with polybutadiene that has been separately grafted onto polystyrene, poly (methyl methacrylate ), and the copolymer of the two (3); the mixture of polystyrene, poly butadiene, and polystyrene-grafted onto polybutadiene; and the mixture of polyvinyl chloride, cellulose, and poly (ethyl acrylate) grafted onto cellulose (4). A similar concept has been used in developing reinforced and filled polymer composites where glass fibers are mixed with polyester epoxy resin i n the presence of the compatibilizing graft copolymer of glass with polyester or glass with epoxy resin. In the field of adhesives, improved adhesive bond is achieved between, for example, P V C floor tiles and concrete, wood, or gypsum by using a compatibilizing agent composed of graft copolymer of P M M A with natural rubber or epoxy resin (5, 6). The common factor in all of these examples is that each system takes advantage of the compatibility of the compatibilizing agent with one or more of the components of the mixture. The agents are composed of a block or graft copolymer of one polymer molecule to another, and the generally accepted explanation is that the agents act as interfacial bridges which couple the components in the mixture. The resulting blend is usually immiscible but marginally compatible, and the degree of phase separation is reduced considerably. In the recent miscibility studies with α-methyl styrene/acrylonitrile copolymer and a α-methyl styrene/methyl methacrylate/acrylonitrile terpolymer (8), it was found that almost all miscible second components contain amides, imides, nitriles, or esters, each of which contains lonepair electrons capable of donor-acceptor complexation—a state which

In Multiphase Polymers; Cooper, S., et al.; Advances in Chemistry; American Chemical Society: Washington, DC, 1979.

29.

OLABisi

A N D

561

Polyarylethers

F A R N H A M

was earlier speculated to contribute somewhat to the formation of compatible polymer mixtures ( 9 ) . It was decided, therefore, that intro duction of these type of groups onto the backbone of a series of otherwise insoluble, high impact, high T polyarylethers might yield compatible blends of superior properties. That is, the 'compatibilization concept' is invoked, but now pendant chemical groups are the compatibilizing agents as opposed to the block and graft copolymers previously used. It may be more appropriate to refer to these pendant chemical groups as 'internal' compatibilizing agents and to the others as 'external' com patibilizing agents. Downloaded by NATL TAIWAN UNIV on June 30, 2015 | http://pubs.acs.org Publication Date: June 1, 1979 | doi: 10.1021/ba-1979-0176.ch029

g

Experimental Synthesis. Five different polyaryl ethers were made from the con densation product, resulting from the reaction of phenol and levulinic acid, commonly referred to as diphenolic acid, and one or more of the following monomers: bisphenol A , dichlorodiphenyl sulfone, 2,6-dichlorobenzonitrile, and 4,4'-difluorobenzophenone. The resulting polymers were subsequently methylated such that the common monomer becomes ( 1 ) :

CH

€M^0> CH I CH I

feN

3

2

c,

^r \

ci

X

2

e=o I

1

OCH

3

2

Six more polyaryl ethers were made from 2,6-dichlorobenzonitrile ( 2 ) and one of the following monomers: Ι,Γ-bis(4-hydroxy-3,5-dimethyl phenyl ) cyclohexane; 2,2'-bis ( 4-hydroxyphenyl ) -2-phenyl ethane; 1,3bis ( 4-hydroxyphenyl ) -1-ethyl cyclohexane; 2- ( 4^hydroxyphenyl ) -2- [3- ( 4hydroxyphenyl ) -4-methyl cyclohexyl] propane; 2,2'-bis ( 4-hydroxy-3,5dimethyl phenyl) propane; and bisphenol A . Because the procedure used i n making these polymers is similar (10), it is sufficient to describe one, namely, the syntnesis of the terpolyether from bisphenol A , diphenolic acid, and dichlorodiphenyl sulfone, whose polymerization scheme is:



562

MULTIPHASE

POLYMERS

I COONa

CH I COOCH, 2

The following were placed i n a 500-cm four-neck reaction flask fitted with stirrer, thermometer, nitrogen sparge tube, helices packed column, and Dean-Stark moisture trap with condenser: 25.68 g bisphenol A (.1125 m o l ) , 32.21 g diphenolic acid (.1125 m o l ) , 112.5 c m M e S O , and 200 c m toluene. The solution was warmed to about 50°C, air was displaced by nitrogen sparge, and 22.51 g N a O H ( .5625 mol as 50.62% solution ) was added. The mixture was stirred and heated to reflux with water separation and removal until no more water was evident i n the reflux distillate. Toluene was distilled off to a pot temperature of about 160°C, and a solution of 64.65 g 4,4'-dichlorodiphenyl sulfone (.255 mol) in 110 c m toluene was added. Toluene was removed to give a reaction temperature of 160°-165°C and maintained for about 2 hr. The mixture was cooled to 120°-125°C and methyl chloride bubbled i n at this temperature to saturation until the mixture became uniform and the p H had dropped to give an acidic test with bromo cresol purple indicator ( p H ~ 5 ) . The polymer solution was diluted with 75 c m chlorobenzene and filtered to remove salt. The clear, filtered solution was precipitated into methanol using a W a r i n g blender, and the polymer fluff was filtered and washed with fresh methanol and dried under vacuum. Yield: 100.8 g (cale 107.6), R V H C I = 0.33. I R analysis of a film showed a deep 3

3

3

3

3

C

3


2

29.

OLABisi

A N D

563

Polyarylethers

F A R N H A M

absorption band for carbonyl ( ~ 5.75 μ) but no band for free O H or carbonyl (at ~ 3 μ), indicating adequate conversion of sodium carboxylate to methyl ester. N M R Characterization. The structures of the polyarylethers A - K (Table I) were confirmed through their N M R spectra. As an example of the N M R data, observe the spectrum i n Figure 1 for sample K , the condensation product of disodium salt of diphenolic acid and 2,6-dichlorobezonitrile which was subsequently methylated as discussed above. The spectrum is separated into two regions, namely, a low-field quartet plus doublet of lines and a high-field singlet with one doublet. The low-field doublet of lines, denoted by p, constitutes those hydrogens meta i n the nitrile group, H . This doublet would appear as a singlet were it not for the proton para to the nitrile group, H . The interaction between the two magnetic nuclei is responsible for the splitting of the nuclear-spin energy levels. The quartet can be considered to be made up of a pair of doublets q and r, and such a quartet is very characteristic or para-disubstituted benzenes where the substituents are different. Proton H is not readily observable but its presence can be ascertained from the spectrum integral shown in triplicate in Figure 1.


p

8

e


564

MULTIPHASE

Table I.

Polyarylether

POLYMERS

Structures C

Polymer Designation

Polymer Repeat Unit CH

(RV)

T (°C) g

3

Polysulfone

4-

0.48

184

0.33

154

0.48

152

0.76

123


CH.,

C H .

C H ; ,

I CH, I COOCH,

CH,

Β

CH-, CH, COOCH:,

CH

3

-^-@-^®-*-φ-β-®4 CH-, ι CH,,

COOCH,


29.

OLABisi

Polyarylethers

A N D F A R N H A M

Table I.

565

Continued jjsp_ C

Polymer Designation

(RV)

Polymer Repeat Unit CH

CH,

8

T (°C) g

CN


Ε

CH,

F

—

0

— ^ —

0.61

245

0.74

185

0.77

198

0.76

212

0.94

280

0.69

170

CN 0

— ( ^ r

G

CN

CH.,

H CH,

CH;,

-I

CH,

CH,

,CH,

CH

CH,

CH

3

CH,

C_ N ~

J

3

CN

( H ^ f H ^ o - ^ p CH;,


566

MULTIPHASE

Table I.

POLYMERS

Continued C

Polymer Designation

(RV)

Polymer Repeat Unit

Κ

CH

T

g

(°C)

CN

3

-0 0.42


CH, CH

135

2

COOCH,

The high field singlet V is attributable to the carbomethoxy methyl hydrogens, and singlet V is attributable to the three equivalent methyl hydrogens designated as such on the structure i n Figure 1. Peak b, attributable to the — C H — C H — group, appears as a doublet because the methylene groups are not equivalent and they couple with each other, yielding the rather broadened doublet resonance. The relative chemical shifts of the peaks a, b, and c are as expected for aliphatic hydrogens, and the integrals are i n the approximate ratio 1:1.3:1, in excellent agreement with theory. Lastly, from the integrals, the ratio of the aromatic to the aliphatic protons is estimated to be 1:1.18; this should be compared with the theoretical value of 1:1.1 calculated from the fact that the monomer contains 11 aromatic and 10 aliphatic protons. Mechanical Characterization. The polymer-polymer blends were made by using a T w o - R o l l M i l l or a Brabender Plasticorder maintained at a temperature of ~ 250°C. Samples for the Instron tester and dynamic mechanical testing were prepared by compression molding. The heat distortion temperature ( H D T ) , izod, and flexural properties were obtained from 125-mil-thick samples, the dynamic mechanical testing was done on 20-mil-thick samples, and all other data were obtained from 15-mil-thick samples. The mechanical property data were obtained at 25°C and the dynamic mechanical testing was conducted with a torsion pendulum equipment similar i n design to that reported by Nielsen (11). Sample dimensions for the torsion pendulum were chosen to give a nominal frequency of 1 H z in the solid state. The glass-transition temperatures were obtained from resilience-temperature measurements. In using the resilience data for locating the T , one subjects a poly meric sample to a stress which is just enough to give one-percent strain at a given temperature T. O n releasing the stress, the sample completely recovers ( 100 percent resilience ) if Τ < T . As the temperature increases, the percent of recovered strain decreases, reaching a minimum at Τ « T A t temperatures just above the T the resilience increases again, reaching a maximum at a value usually less than 100 percent. A t still higher temperatures, the resilience monotonically decreases to zero unless the material crosslinks. 2

2

g

g

r

g


29.

OLABisi

A N D

F A R N H A M

Polyarylethers

567

A l l of the T data reported i n Table II were obtained with the resilience method; a few selected results were doubly checked with the values obtained from the torsion-pendulum data. Note the identical value of the T for «MS/AN/MMA measured by the resilience method and that obtained with the torsion-pendulum data on Figure 12. g

g

Results and Discussion The terpolymer of α-methyl styrene/methyl methacrylate/acrylonitrile (60/20/20) is miscible i n all proportion with poly (methyl meth acrylate) (8). Figure 2 illustrates the dependence of T and H D T on Downloaded by NATL TAIWAN UNIV on June 30, 2015 | http://pubs.acs.org Publication Date: June 1, 1979 | doi: 10.1021/ba-1979-0176.ch029

g

• HEAT DISTORTION • GLASS TRANSITION

3

O.

J 0

10

1

20

I

I

I

I

I

I

30

40

50

60

70

80

L 90

100

% TERPOLYMER Figure 2.

Composition dependence of T

ff

terpolymer/PMMA blends

and HDT


for the

568

MULTIPHASE

POLYMERS

the weight-percent terpolymer i n the P M M A / t e r p o l y m e r blends. E a c h data point corresponds to the single, distinct T or H D T for the blend. Such single, distinct T s intermediate between the pure component T s (as shown i n Figure 2) are usually considered a necessary but not a sufficient condition for the establishment of polymer-polymer miscibility. It indicates that the two component polymers are miscible u p to a scale corresponding to that responsible for the cooperative main-chain move ment associated with the glass-transition temperature. Figure 3 illustrates a significant attribute of a miscible blend, namely, that the mechanical properties of the blends at intermediate compositions are superior to those of the two constituent polymers. This point is particularly more evident i n the flexural properties. More or less similar behavior has been observed (8) i n the blends of the copolymer or the terpolymer w i t h the following: bis-A polycar bonate, polyvinyl chloride, poly (ethyl methacrylate ), and a terpolymer made from methyl methacrylate, Ν,Ν'-dimethyl acrylamide, and N phenyl-maleimide. Because of this unique miscibility characteristic of the α-methyl styrene interpolymers, an attempt was made at compatibilizing polyarylethers w i t h the interpolymers by attaching pendant chemical groups known to exist i n systems with which the interpolymers are miscible. Table I illustrates the structures of the modified polyarylethers, their glass-transition temperatures, and their reduced specific viscosities ( R V ) measured i n chloroform at 25°C at a concentration of 0.2 g/100 m L . g

g


g

Table II.

Meckanical Properties

Structure

CH

3

> ~ # 4 H ^ O - ^ 0 CH

Blends

2

^ -

3

50% 50%

«MS/AN/MAA «MS/ΑΝ Pure P S F

50% 50%

«MS/AN/MAA «MS/AN Pure A

Polysulfone

CH

:i

CH,

CH,

CH.

I COOCH,



29.

O L A B i s i AND

F A R N H A M

569

Polyarylethers

Table II contains the mechanical properties and the glass-transition tem peratures of the styrenic interpolymers, the various polyarylethers, and their 50/50 blends. The blends of polysulfone with the α-methyl styrene polymers are immiscible, as evidenced by the double glass-transition temperatures i n Table II. To improve the miscibility characteristics, polysulfone was modified i n two ways. First, 25% of the bisphenol A was replaced by monomer I which contains a pendant ester group and, when no improve ment resulted, the whole 50% of the bisphenol A was replaced. Again, the blends remain immiscible as evidenced from Figures 4 and 5 and from Table II. Further, the presence of the pendant ester group i n polymer C does not improve the miscibility picture even though one would expect a favorable contribution from the carbonyl group on account of the miscibility of polycarbonate with the α-methyl styrene polymers. A pendant nitrile group was also tried as a compatibilizing agent i n polymers E - J with no significant success. Combination of the pendant nitrile with the pendant ester groups in polymer D also fails to improve the miscibility picture. In all of these cases, two minima are exhibited in the resilience-temperature curves, examples of which appear in Figures 4, 5, 6, 7, and 8 for the 50/50 blends of polymers A , B, D , F , and H w i t h the styrenic interpolymers. The slight shifts in T which appear i n some cases indicate the 'slight' affinity of the constituent polymers, but the consistent cloudiness is a further proof of the two-phase state of the g

of Polyarylether Blends

IfoSec Modulus Strength (psi) (psi)

314,000 350,000 360,000

10,200

400,000 410,000 357,000

None " "

Strength Elong. Pendulum Elong. @ @ Impact T Break Break (ft lb/in ) (°C) ff

3

None

—

>>

^

8,900

6.0

8,500 7,400

3.5 2.5 50.0

3.6 2.3 110.0

126,171 114,164 185

— — —

8,200 5,300 8,100

2.0 1.5 2.5

3.0 1.5 7.5

126,154 110,142 154

Plaque Appearance

Cloudy

Transparent

Cloudy Transparent


570

MULTIPHASE

POLYMERS

Table

Structure

II.

Blends CH.

CH

50% 50%

«MS/AN/MAA «MS/AN Pure Β

50% 50%

«MS/AN/MAA «MS/AN

2


ι COOCH,

CH.,

I CH, CH

COOCH

3

CN

CH;,

PureC

2

50% 50%

«MS/AN/MAA «MS/AN PureD

50% 50%

«MS/AN/MAA «MS/AN Pure Ε

50% 50%

«MS/AN/MAA «MS/AN Pure F

50% 50%

«MS/AN/MAA «MS/AN Pure G

CH.

I

CH.

I COOCH,


29.

oLABisi

571

Polyarylethers

A N D F A R N H A M

Continued

l%Sec

Modulus (psi)

Yield Strength

Elong.


338,000 353,000 320,000

?> 11

404,000 411,000 320,000

Break

Pendulum Impact (ft

Ύ

Plaque

σ

lb/in )

( ° C )

3

Appearance

Cloudy

4.5 2.5 3.0

3.7 2.1 45.0

127,141 110,136 152

1.5 3.0 5.0

8.0 3.5 67.0

126 115 123

Cloudy

2.5

7,000 3,700 7,000

— — —

10,900 9,000 10,800

4.5 3.0 6.0

4.5 3.8 87.0

126,140 114,134 149

Cloudy

— — —

10,200 7,700 10,600

3.0 2.0 5.0

1.0 3.0 9.4

126,223 112,185 245

Cloudy

4.5 2.5 10.0

3.9 3.0 51.0

120,160 115,179 185

Cloudy

4.0 1.5 49.0

3.9 2.1 137.0

118,193 116,188 198

Cloudy

— —

None

@

11,300 8,300 9,300

384,000 335,000 336,000

8,600

Elong.

@

Break

(psi)

389,000 360,000 373,000

Strength

320,000 288,000 347,000

15,000

6.5

10,300 6,400 12,600

292,000 332,000 252,000

None " 12,390

— — 11.0

9,600 4,300 12,380

Transparent

Transparent

11

Transparent

11

Transparent

Transparent

Transparent


572

MULTIPHASE

POLYMERS

Table

Structure

Blends

CH,

CN

H


CH

CH,

CH

3

CH,

CH,

50% 50%

«MS/AN/MAA «MS/AN Pure H

50% 50%

«MS/AN/MAA «MS/AN Pure I

50% 50%

«MS/AN/MAA «MS/AN Pure J

50% 50%

«MS/AN/MAA «MS/AN Pure Κ

3

CH,

C N

CH,

CH,

CH.s

Κ

CN

o - © ^ - ^ - o - A CH I

CH..

1 COOCH,

CH

CH

3

I

3

I

- - C H j - C — • -CHi-CH - • CH

Break

»>

450,000

None

437,000

None

Break

Pendulum Impact (ft

Ύ

Plaque

σ

lb/in ) 3

( ° C )

Appearance

4.0 1.5 6.0

1.0 1.0 8.0

121,186 113,195 212

Cloudy Very Hazy Transparent

8.5

—

8,900 4,600 10,760

3.5 1.5 15.0

4.3 1.7 15.5

126,203 114,162 234

Cloudy Very Hazy Transparent

12,000 9,600 12,790

7.0 3.5 26.0

7.5 4.0 185.0

126,146 111,148 161

Cloudy

— 5.8

—

8,100 8,700 11,000

2.5 3.0 4.5

3.0 3.0 60.0

130 120 128

Cloudy Hazy Transparent

—

7,600

2.0

6.0

126

Transparent

8,300

2.0

3.0

108

Transparent

>> ?»

@

11,200 3,900 11,800

)1

13,000

Elong.

— —

>>

12,100

@

>>

Transparent


574

MULTIPHASE

FLEXURAL STRENGTH

•

TENSILE S T R E N G T H


•

POLYMERS

Figure 3.

Composition dependence of the flexural and tensile strengths for the terpolymer/blends


OLABisi

AND FARNHAM

Polyarylethers


29.


575

MULTIPHASE POLYMERS


576



0

20

JL

40

JL

JL 60 80

100

θ

120

%

160

180

TEMPERATURE,°C

140

200

220

JL 240

50% D 50% TERPOLYMER

50% COPOLYMER

50% D

260

280

300

Figure 6. Resilience-temperature curves for the blends of polymer D with the styrenic interpolymers

20

30 -

>

•4 "

Ξ

ο r



ζ/3

Μ

Η

>

Η

οι ο

οο

OLABisi

A N D F A R N H A M

Polyarylethers

581


29.

% α MS/AN COPOLYMER

Figure 10.

Composition dependence of T and HDT for the blends of polymer Κ with aMS/AN copolymer g


582

MULTIPHASE

POLYMERS

blends. Nonetheless, the pretty good mechanical properties indicate that the blends are mechanically compatible even though they are thermodynamically immiscible. The best results are obtained with polyarylether designated as K , and Figure 9 represents the resilience-temperature curve showing the single T for the 50/50 mixture of the polymer Κ with α-methyl styrene and co- and terpolymers. The dependence of the T and H D T on the percent polyarylether in the a M S / A N blends appears in Figure 10. E v e n though the T s and H D T s of the blends are intermediate between the pure component values, the blends are believed to be two-phase owing to their consistent opacity. Additional revealing evidence of the possible immiscibility of these mixtures is embodied in the temperature depend ence of dynamic mechanical data illustrated in Figures 11 and 12. Note g

g


g



29.

OLABisi

A N D

F A R N H A M

Polyarylethers

583

the very broad transition curves which appear to average the values of the separate component glass transitions. Although the broadening of the tan δ can be interpreted as an artifact of the instrumentation, a miscible blend would ordinarily give a sharp transition curve similar i n behavior to that of a pure polymer. That is, the behavior of the best system of this study may be that of a marginally miscible blend. The composition dependence of the flexural strength of the «MS/ANcopolymer blend with polyarylether Κ appears in Figure 13. As the composition of the copolymer increases, the strength first increases, reaches a maximum, and then decreases. It actually exhibits a minimum at about ~ 80% «MS/ΑΝ. This behavior can only substantiate earlier suggestions regarding the possible immiscibility of these systems. A l l of the other mechanical properties indicate that mixtures with polyarylether Κ may not be miscible but are mechanically compatible. Finally, it is interesting to note that at least one of the pendant chemical groups present on Κ exists on either of the α-methyl styrene interpolymers. It


584

MULTIPHASE

POLYMERS

PSI 20,000 r— 19,000

—


18,000

11,000

J

10,000 0

10

20

30

I 40

J 50

I

I

L

60

70

80

90

100

% COPOLYMER

Figure 13. Composition dependence of the flexural and tensile strengths for the blend of polymer Κ with aMS/AN copolymer may well be that the old concept of l i k e dissolves like' suffices to explain the compatibility characteristics of polyarylether K ; but then, the same concept fails when applied to polymers A - J . Conclusion α-Methyl styrene/methyl methacrylate/acrylonitrile terpolymer and α-methyl styrene/acrylonitrile copolymer are miscible with poly (methyl methacrylate ) and some other polymers containing amides, imides, nitriles, or esters, each of which contains lone-pair electrons capable of donor-acceptor complex formation. B y attaching this type of chemical groups onto the backbone of an otherwise immiscible polyarylether, it was possible to produce compatible mixtures of the styrenic interpolymers with the polyarylether.


29.

oLABisi

A N D F A R N H A M

Polyarylethers

585

The resulting mixtures exhibit single T s intermediate between the component T s, but the transition curves are broad and the plaques are opaque to light transmission. Nonetheless, the rather good mechanical properties indicate that the blends are mechanically compatible even though they are thermodynamically immiscible. That is, compatibilization has been achieved via the use of pendant chemical groups as internal compatibilizing agents. g

g


Acknowledgment W e thank the Union Carbide Corp. for permission to publish this work. Acknowledgment also goes to J. J. Bohan and L . B. Conte for their technical assistance; to A . D . Hammerich for the N M R measurements and to L . M . Robeson for the dynamic mechanical data.

Literature Cited 1. Molau, G. E., J. Polym. Sci., Part A (1965) 3, 1267. 2. Ibid., 4235. 3. Himei, S., Takine, M., Akita, K., Kanegafuchi Chemical Industry Co., Japanese Patent 866 (1967); Chem. Abstr. (1967) 67, 22418. 4. Amicon Corp., French Patent 1,539,053 (1968). 5. Bevan, A. R., Bloomfield, G. F., Adhes. Age (1964) 7(2), 36. 6. Ibid., 7(3), 34. 7. Gayyord, N. G., "Copolymers, Polyblends and Composites," ADV. CHEM. SER. (1975) 142, 76. 8. Olabisi, O., unpublished data. 9. Olabisi, O., Macromolecules (1975) 8, 316. 10. Farnham, A. G., Johnson, R. N., Union Carbide Corporation, U.S. Patent 3,332,909 (1968); U.S. Patent 4,108,837 (1978). 11. Nielson, L. E., Rev. Sci. Inst. (1951) 22, 690. RECEIVED

April 14, 1978.


Multiphase Polymers - American Chemical Society

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