Viscosity of semi-dilute polymer solutions M. Adam, M. Delsanti To cite this version: M. Adam, M. Delsanti. Viscosity of semi-dilute polymer solutions. Journal de Physique, 1982, 43 (3), pp.549-557. <10.1051/jphys:01982004303054900>. <jpa-00209425> HAL Id: jpa-00209425 https://hal.archives-ouvertes.fr/jpa-00209425 Submitted on 1 Jan 1982 HAL is a multi-disciplinary open access archive for the deposit and dissemination of scientific research documents, whether they are published or not. The documents may come from teaching and research institutions in France or abroad, or from public or private research centers. L’archive ouverte pluridisciplinaire HAL, est destinée au dépôt et à la diffusion de documents scientifiques de niveau recherche, publiés ou non, émanant des établissements d’enseignement et de recherche français ou étrangers, des laboratoires publics ou privés. J. Physique 43 (1982) 549-557 MARS 1982, 549 Classification Physics Abstracts 46.30J - 51.20 61.40K - 82.90 - Viscosity of semi-dilute polymer solutions M. Adam and M. Delsanti Laboratoire Léon-Brillouin, CEN Saclay, 91191 Gif sur Yvette Cedex, France (Reçu le 25 mai 1981, révisé le 24 aofit, accepté le 3 novembre 1981) Résumé. 2014 Nous (c* présentons des résultats de viscosité obtenus dans des solutions semi-diluées de polymères 10%). c La variation de la viscosité est indépendante de la température de transition vitreuse du polymère et compatible coefficient de frottement du monomère proportionnel à la viscosité du solvant. En fonction de la concentration dans différents systèmes, les relations suivantes sont obtenues : PIB-toluene, ~r ~ c4,1, qui est proche de la théorie de la viscosité de de Gennes, PS-benzène et PIB-cyclohexane, ~r ~ c4,6, qui peut être expliquée par la structure locale de la chaîne, 2014 solution semi-diluée à la température 03B8, ~r ~ c5, qui peut être interprétée avec un temps de reptation analogue à celui introduit dans le modèle de de Gennes et une élasticité déduite de la théorie de champ moyen. En fonction de la masse moléculaire, nous obtenons : avec un 2014 2014 ~r ~ M3,1w en accord avec le modèle de reptation. Toutefois, il semble que les lois d’échelle tive en température ne peuvent expliquer la décroissance de la viscosité rela- lorsque la température croit. We report viscosity measurements on semi-dilute solutions (c* c Abstract. 10 %). The viscosity variation is independent of the glass transition temperature of the undiluted polymer and consistent with monomer friction proportional to the solvent viscosity. With concentration, the following variations were observed : 2014 for PIB-toluene, ~r ~ c4.1, close to de Gennes’ viscosity theory, 2014 for PS-benzene and PIB-cyclohexane, ~r ~ c4.6 which seems to be influenced by local statistics in the chains, 2014 for semi-dilute 03B8 solvent conditions, ~r ~ c5 which could be interpreted using de Gennes’ theory of reptation and mean field theory of elasticity. With molecular weight we observe : 2014 ~r ~ in agreement with reptation model. However temperature scaling laws do not seem to be dence of the viscosity remains open question. Zero shear viscosity of polymer Introduction. solutions and melts have been intensively studied for many years. A good review article on the subject was written by Fox and Berry [1](1968). Our purpose is to compare de Gennes’ viscosity theory [2], which gives a new approach on the problem, to experimental results obtained with semi-dilute solutions. A semi-dilute solution may be considered as a transient network, the monomer concentration c being higher than the overlap concentration c* (c* = N/R3 [3]) but much lower than the solvent concentration. In order to be able to compare theory - M3.1w applicable. The interpretation of the temperature depen- experiments we have performed some new experiments on very high molecular weight polymer. First, we review de Gennes’ theory of semi-dilute (S.D.) polymer solutions. Then we define the experimental conditions at which the experiments were performed. Finally, we present and discuss the experimental results obtained in both, good and 0 solvents. 1. Theory. The main term in the expression for the viscosity 11 is the product of the longest relaxation time TR and the shear elastic modulus E of the tranwith - sient network : Article published online by EDP Sciences and available at http://dx.doi.org/10.1051/jphys:01982004303054900 550 Let us successively derive the two quantities E and TR from de Gennes’ theory in the simplest case of an athermal solvent (Flory-Huggins parameter z = 0). The main to consider a Following rubber elasticity theory (7), the elastic modulus of the transient network is proportional to the volume number density of strands c/g. Using the expressions (2) and (4) we obtain : E -- kT/ç3 thus : hypothesis of the de Gennes’ theory is chain (in a S.D. solution) as formed by succession of subchains of mean size ç, each subchain having g monomers. Inside a subchain, the g monomers are subject to excluded volume effects and to hydrodynamic interactions. Such interactions do not take place between two subchains; ç is a screening length for both excluded volume and hydrodynamic effects. Edwards [4] and de Gennes [5] imagine that the motion of a particular chain is a reptation in a fictitious tube, defined by all the surrounded chains. The diameter of this tube is the screening length ç : a where I is an effective length per monomer The length of the tube is : From the expressions of T R for the viscosity [10] : monomers in a since a S.D. solution is a closely packed system of subchains units. The time TR necessary for a complete renewal of the tube is the time required for chain to reptate the length of the tube [6] : we obtain Using the most accurate experimental value of [8], which corresponds to the prediction of the vector model [9], one chain and and E (9) or v n finds : We have considered above the case of an athermal solvent (x 0, v 0.588) where only one characteristic length ç exists. The quality of the solvent should have no influence on the viscosity molecular weight exponent, but it must influence strongly the concentration dependence. One may remark that, since the length ç decreases when the quality of the solvent increases (Ref [2], p. 119, 1 l, 12), the viscosity given by equation (10) must increase. In the case of a 0 solvent [13] the theory of the viscosity is much more difficult because there exist two = where N is the number of (8) = lengths [14] : - where Dt is the diffusion coefficient of the Rouse chain along its tube. Thus : - tive where qo is the solvent viscosity. Combining equations (3), (5) and (6), we the correlation length, which is the screening of the density-density correlation function : length and the mean distance between two consecu- entanglements : have : is : how the shear modulus and the time depend on ç and Ç2. In secrelaxation longest tion 3.2, we will discuss our experimental results obtained in 0 conditions and compared them with different theoretical possibilities. The thus : problem The principle of the 2. Experimental procedure. viscometer was given in our earlier paper [15]. We measure the viscous force F to which a sphere (radius 5 x 10-2 cm) is submitted when the fluid is r - Substituting the expressions (4) and (2) for g and ç in the expression of TR (7) we have : = displaced at a velocity v : 551 Characteristics of polymer solutions studied. Table I. the transition temperature of the undiluted is glass Tg polymer and X the Flory-Huggins parameter. Indexes v and t refere to X deduced from intrinsic viscosity and thermodynamic measurements, respectively. - the ratio F/v as a function of v and verify has a constant value, thus we determine the F/v zero shear viscosity of the sample. We have made various improvements [16] upon the viscometer specifications as compared to reference [15]. The force maintaining the sphere in place is transmitted magnetically and we have improved the feedback control of the current driving the field coils. This current is of the order of 1 mA and it is now measured to within 1 %. The sample flow is we measure that driven by a stepmotor and its velocity is measured to an accuracy better than 0.1 %. We made an absolute calibration of the apparatus by measuring a standard silicon oil (q 50 P at 25 OC) and our new overall precision is 2 %. From the measured viscosity, we have deduced the relative viscosity defined as the ratio of polymer solution viscosity to that of the solvent [17], given in appendix 2. Two kinds of polymer were used : poly-isobutylene and polystyrene in three different solvents whose characteristics are given in table I. In figure 1 we plot the different concentrations of the samples at which the viscosity was measured. We represent also the variation of the overlap concentration c* as a function of molecular weight. As usual [12, 15,18] we use for c* : now = where A is Avogadro’s number, p is the density of the solvent, and RG is the radius of gyration measured by light scattering [19]. For comparison, we plot (dashed line) the value of cc, for PS system : where cc (g/g) define the boundary between the entangled and non entangled regime [20]. We can note that : the cc, M-1, in good solvent cannot be justified using de Gennes’ theory, for PS good solvent (Fig. la), with our range of molecular weight, 1.5 cclc* 3, for PS-0 solvent (Fig. 1 b), cc is smaller than c* and 1.3 c*lcc 6. ~ - - - Thus for such high molecular weight polymers (M > 106), we find no significant range of concentration where the system is semi-dilute but not entangled [20]. 3 .1 3. Experimental results and discussions. 3.1.1 Concentration dependence. GOOD SOLVENT. In the PS-benzene and PIB-cyclohexane systems, the dependence of relative viscosity on concentration is, at 32 OC, identical for both systems : - - - the exponent decreases sliat 64 OC, the expothe increases, ghtly temperature nent value is 4.4 + 0.1. This has to be checked on PS-benzene at high temperature. For PIB-toluene the viscosity, for a given concentration, is much lower than for PIB-cyclohexane : For PIB-cyclohexane as Variation of the overlap concentration c* as a function of molecular weight M.. + - + PIB and .--8 PS samples on which concentration exponent values are determined. The numbers on each line represent the Mw/Mn PS-benzene c* values; values. a) Good solvent systems. .... PIB-cyclohexane c* values; ------ cc deduced from [27]. b) 6 solvent systems. PS-cyclohexane (35 OC); · · · · PIB-benzene (25 °Q ; Cc Fig. 1. - - - ------ 552 4. - Variation of the relative viscosity as function of temperature for a PIB-cyclohexane sample (c = 9.3 x 10- 2 g/g). Fig. Fig. 2. Relative viscosity at 32°C as a function of 24 x centration in 0 PS-benzene samples (MW and + PIB-cyclohexane samples (MW =1.17 x 106) - = In the PIB-toluene system, the concentration dence of the relative viscosity is : con- 106) [41]. depen- In figure 5 we present the variation of r as a function of concentration for different systems (some numerical values of q, as a function of temperature are given in appendix 3). In a dilute regime with short chains at high concen4 x 104) tration (c 9 x 10 -2 g/g, c/c* 0.6, MW the relative viscosity is very small and within experimental accuracy, independent of the temperature (20 °C T 60 OC), see figure 5. Even with 9 % solution concentration, the viscosity dependence on temperature is that of the solvent. This proves that for a monomer concentration less than 10 %, the monomer friction is proportional to the viscosity of the solvent (monomer-monomer friction can be = = in agreement with reference [21]. The concentration exponent, close to theoretical value of 3.95, is independent of the temperature. neglected). In figure 5, = observes that : PS-benzene and PIB-cyclohexane systems present the same variation of r with concentration, one - Fig. 3. ples (M, - Relative 1.17 x viscosity 106) = as a at 64 °C in PIB-toluene sam- function of concentration [41]. The main effect, 3.1.2 Temperature dependence. observed on S.D. solutions, PS-benzene and PIBcyclohexane, is that the relative viscosity q, decreases as we increase the temperature. An example of the decrease of the viscosity as a function of temperature is given in figure 4. This variation can be considered as linear and parameterizing it as : - Fig. 5. Variation of r (see text) as a function of the concentration for different good systems. + PIB-cyclohexane ; * PIB-toluene; 0 PS-benzene, M, 7.1 x 106 ; - = A c we find : F = 9 x 10- 3 in the case of figure 4. PS-benzene, MW =2 x l(f;00 PS-benzene, Mv =4 x 104, C - 0.6. 553 r being independent of the molecular weight. This temperature behaviour is not a glass transition temperature effect, because one set of experiments (on PS) was performed below, the other (on PIB) above the Tg of the respective undiluted polymer, the PIB-toluene system presents a variation of the relative viscosity with temperature which is independent of concentration. The r values are very small compared to those obtained on PIB-cyclohexane. When T increases, glgt and 1, increase and decrease, respectively. This seems to justify that in the case of PS-benzene and PIB-cyclohexane : - Qualitative interpretation of the results. polymeric systems studied (x = 0.44) the effective length I is much larger than the size of a 3.1. 3 In the monomer a. Let us suppose that : at very short distance i) rigid [22, 23], m being affected by rigidity, ii) at larger distance (r r (r ma), the chain is the number of monomers > ma) the subchain ç has a Gaussian conformation if m g gt. The excluded volume effects are dominant if g > g, [24]. In the range of molecular weight studied, we have low values of glg, in the semi-dilute range. For instance, in a PS-benzene solution, at room temperature, gt corresponds to a molecular weight M. of = 104 [25]. By comparison of diffusion coefficient at zero concentration and cooperative diffusion coefficient in semidilute solution [18], having a monomer concentration of 2 % c 10 % the corresponding Mg values are : c = 10 %, the ratio g/gt is of the order of In other words, at room temperature and for c 10 %, the effective value of the exponent v has not reached its asymptotic value. Using the assumptions i) and ii) the expressions glgt (A. 5) and r¡r (A. 6) are developed in appendix 1. In those expressions T is a constant because the systems studied (PS-benzene and PIB-cyclohexane) have very low 0 temperatures [7] and small change near room temperature does not affect the quality of solvents (T const.). If we suppose that m is inversely proportional to the temperature we obtain the following Thus, for unity. 2% = temperature dependences : independent of the molecular weight (see Fig. 5), - In the systems studied (x = 0.44) the concentration exponent values found are larger than the theoretical value developed in section 1 for an athermal solvent. In the systems PS-benzene and PIB-cyclohexane, the relative viscosity decreases as we increase the temperature. If the first result can be interpreted as due to high x values, the second result cannot be interpreted using usual temperature scaling laws [2, 11, 12] which predict a thermal effect opposite to that observed. Indeed increasing the temperature, the quality of the solvent increases and thus the viscosity should increase (see section 1). F is - the viscosity and the experimental concentration as T increases. exponent decrease In the case of PIB-toluene the independence of the relative viscosity with temperature and the low value of concentration exponent could be due to high flexibility of the polymer in this system giving a high value of g/gt. This agreement is only qualitative, we cannot go further because the effective v is an unknown function of concentration and temperature. This assumption (that v has not reached its asymptotic value) seems in contradiction with neutron measurements on ç in PS-benzene solutions [26]. But one must note that the law in which the exponent value corresponds to the asymptotic value of v, was measured in a concentration range (0.5 % c 5 %) lower than that of our viscosity measurements, hence in a higher range of gIg". Self-diffusion measurements on PS-benzene soluc tions are reported in reference [27] (2 % 20 Y.), they give the relation : Ds L-- R 2/ TR with R 2~ C- 1/4 and E - c2.2s (corresponding to v 0.6) leads to in This C3.7. agreement with exponent (3.7), q de Gennes’ prediction, is much lower than our 4.6 concentration exponent. Is the concentration exponent of the self diffusion coefficient very sensitive to the effective value of v [28] ? Due to the low value of g/gr the PS-benzene system might be used as an experimental model of mean field theory. However this theory leads to a viscosity concentration exponent of 3.5, smaller than the good solvent exponent (3.95) and thus in contradiction with our experimental results. In short, the value of the concentration exponent may, be interpreted as due to a non athermal solvent polymer system. However, the decrease of the relative viscosity with increasing temperature could not be understood in terms of the classical temperature dependence of ç, but in terms of local rigidity. Using = 3.2 0 SOLVENT :: PS-CYCLOHEXANE, PIB-BENZENE The viscosity of S.D. solutions, at SOLUTIONS. 0 temperature and at a given concentration is not very different from that of S.D. solutions in good solvents. This contrasts with what is observed in dilute solutions, (Ref [29]). On both our systems, when we increase the temperature from the 0 point, (T 2013 0 = 160) the relative viscosity, for a 9 % monomer concentration, decreases by a factor 1.6. - 554 Table II. - Different expressions of the viscosity combining the expressions of E ETR obtained 11 and T R ( 1 4 and 15). = of contact of two monomers, belonging to a Gaussian chain, because the coils are real and cannot cross each other. probability 6. Relative viscosity as a function of concentration 7 x 106), at 6 temperature 0 PS-cyclohexane (M,, T 1.17 x 106 ), T =25 °C 35 °C, + PIB-benzene (M,,, [41], the arrows represent c* values. Fig. - = = = In both cases, PS-cyclohexane (35 °C) and PIBbenzene (25°C) the relative viscosity varies with concentration as : In figure 6 the arrows represent the c* values on both systems. As soon as c > c*, the experimental points, on log log scale, lie on a straight line of slope 5. Starting from these experimental results (1,, - c5) to examine the contribution of the two characteristic lengths which are present in the system, at the 0 we want temperature. The first length is the mean distance between two consecutive entanglements or contacts : longest relaxation time (TR - N 3 cl) cora screening length proportional to c-’. In that case the fictitious tube has a length : - The responds to because and thus a diameter proportional to j. At the 0 temperature, they are contact points (entanglements) which define the transient network, but which do no show up in the correlations because the pair interaction vanishes. In order to define a correlation length ç in the density-density correlation function, one must invoke higher order interactions. However the sign of the variation of the relative viscosity with temperature cannot be rationalized with the usual temperature dependence of the characteristic length in S.D. solutions. Using this temperature dependence [11, 12], we find a relative viscosity which increases with temperature. 3. 3 MOLECULAR using this distance it The second density-density was found [14, 30] : length is the correlation correlation function : WEIGHT DEPENDENCE IN PS-BENThe polydispersity of PS samples makes the determination of the value of the molecular weight exponent very delicate. We have used the best commercial samples available. The molecular weight exponent value is independent of the quality of the solvent, thus of the concentration exponent value (see section 3.1.1). Taking the experimental value r ’" C4.6 for PS-benzene samples at 32 OC we find : ZENE SOLUTIONS. length of ç ’" c- I corresponds to the expression (2) of j where v is set equal to 1/2. Using v 1/2 in the expressions of the shear modulus (9) and of the longest relaxation time (8) one find : - = with from Toyo Soda company, having a 3.84 x 10’ of 1.04 and 1.14 for M, 6.77 x 106, respectively; and, samples polydispersity Combining the expressions of TR and E given, the different resulting viscosity expressions are reported in table II. Thus the only way to match the results is to have : Mw = experimental E - c2 Shear modulus relaxation time TR - N 3 C3 . Longest the elastic modulus corresponds to Physically : - and = with samples from dispersity of 1.15 pressure chemical having a poly4.1 x 106 and for both Mw = 7.1 x 106. This exponent value is very sensitive to polydisper- , 555 d) The viscosity of the PS-benzene and PIB-cyclohexane seems to be influenced by local conformation. e) The viscosity at the 0 temperature is much more complex than in good solvent scaling laws do not seem to be applicable. f ) The molecular weight dependence of the viscosity (~ M3-1) is close to reptation model. It appears that the concentration dependence of the relative viscosity could be interpreted using de Gennes’ theory of semi-dilute solutions. The problem posed by these experiments is the decrease of the viscosity when the temperature increases. The classical temperature dependence of the characteristic length - Fig. 7. - Molecular weight dependence of the relative viscosity from Toyo Soda samples, at c = 5 x 10 - ’ g/g [41]. sity. In fact if we use the viscosity weight Mv, we find instead of 3. l, average molecular exponent value of 3.5. There is no reason to use the Mv mean value. Making the assumption that the mean longest relaxation time of a polydisperse sample is the weight average of TR [6], since the elastic modulus is independent of the molecular weight, we have : an could not account for this variation. The authors gratefully thank J. P. Cohen Addad for the Precious PIB-sample; P. G. de Gennes, P. Pincus and R. Ball for helpful and Acknowledgments. - stimulating discussions. Appendix Let us mers a suppose that local a 1 chain follows - on m mono- rigidity : - b m. a, a being the length of a monomer and b the persistence length, on gt monomers a Gaussian conformation whose end to end distance 0 is : = - is the weight fraction of species having a molecular weight M;, the mean molecular weight to be used is closer to M,, than Mv. In fact, to our knowledge, most of the authors [33], measured the viscosity except references [21, 34] molecular weight dependence using the M, mean value. They determine the molecular weight of their samples through the Mark Houwink equation. The molecular weight exponent value (3.1) seems to be closer to reptation prediction (3) than the 3.5 Bueche prediction [35], in the case of high molecular where wi - - weight (M > Using the Flory equation for the expansion factor, following reference [29], near 0 temperature, the variation of g, with the reduced temperature r. or is 106). 4. Conclusion. These sets of experiments have demonstrated a certain number of facts concerning the viscosity behaviour of semi-dilute solutions for which the monomer concentration is less than 10 % but still higher than c*. a) The relative viscosity does not depend on the glass transition temperature of the undiluted polymer. b) Since the temperature variation of a 9 % PS- benzene solution, having a ratio of c-c* I 2IS - identical viscosity, we may conclude that the local viscosity is that of the solvent. This confirms the NMR experimental results [36]. we have considered that the effective was defined through ç of a monomer lg’ length and that the excluded volume effect is effective at any scale. In particular In part 1, = (A1) and (A. 3) are compatible only if : Substituting this expression (2) giving ç as a function mula of I (A. 4) in the forof c and I we obtain : to that of the solvent c) The relative viscosity of semi-dilute solution in good solvent, seems to be, in the case of PIB-toluene, in agreement with de Gennes theory. This fact confirms the experimental results [21]obtained a long time ago. using and 556 and U jkT, k is the Boltzmann’s constant bending energy per monomer. The temperature dependence of the quantities g/gt and q, are : Usually m = The. viscosity of the solvent the values given in reference following relations : was [17]. calculated using We obtain the and U the Appendix NUMERICAL VALUES 6, 7 ; THE RELATIVE 2 CORRESPONDING TO FIGURES VISCOSITY ACCURACY IS 2 2, 3, %. Appendix 3 TEMPERATURE DEPENDENCE OF THE RELATIVE VISCOSITY OF PIB-CYCLOHEXANE SYSTEMS AT DIFFERENT CONCENTRATIONS. References and notes [1] BERRY, G. C. and Fox, T. G., Adv. Polym. Sci. 5 (1968) 261. [2] DE GENNES, P. G., Scaling concept (Cornell University Press) [3] c* ~ N/R3 ,N in polymer physics 1979. is the number of monomers in a chain of radius R. The concentration in section 1 is expressed in volume number density of monomers, in sections 2 and 3.3 is expressed in g/g [4] EDWARDS, S. F., Proc. Phys. Soc. 92 (1967) 9. [5] DE GENNES, P. G., Macromolecules 9 (1976) 587-594. [6] DAOUD, M., DE GENNES, P. G., J. Polym. Sci. Phys. Ed. 17 (1979) 1971. [7] FLORY, P. J., Principles of Polymer Chemistry (Cornell University Press, Ithaca N.Y.) 1953. [8] COTTON, J. P., J. Physique Lett. 41 (1980) L-231. [9] LE GUILLOU, J. C., ZINN-JUSTIN, J., Phys. Rev. B 21 (1980) 3976. 557 [10] do not make a distinction between the static v, and the effective dynamic exponent, 03BDH, because the latter plays a minor role in the concentration exponent value. DAOUD, M., JANNINK, G., J. Physique 37 (1976) 973. COTTON, J. P., NIERLICH, M., BOUÉ, F., DAOUD, M., Here we exponent, [11] FARNOUX, B., JANNINK, G., DUPLESSIX, R., PICOT, C., J. Chem. Phys. 65 (1976) 1101. [12] ADAM, M., DELSANTI, M., J. Physique 41 (1980) 713. [13] One defines the 03B8 temperature as the temperature at [14] [15] [16] which the second virial coefficient is zero, for an infinite dilute solution. BROCHARD, F., DE GENNES, P. G., Macromolecules 10 ( 1977) 1157. ADAM, M., DELSANTI, M., J. Physique Lett. 40 (1979) L-523. Details on the apparatus will be published : ADAM, M., DELSANTI, M., MEYER, R., PIERANSKI, P., [17] J. Phys. Appl. For each solvent we have used the viscosity temperature dependence cient is insensible to the exact value of effective exponents 03BDH and v. [29] ISONO, Y., NAGASAWA, M., Macromolecules 13 (1980) 862. [30] DE GENNES, P. G., J. Physique Lett. 35 (1974) L-133. [31] ROOTS, J., NYSTRÖM, B., Macromolecules 13 (1980) 1595. [32] VIDAKOVIC, P., ALLAIN, C., RONDELEZ, F., J. Physique Lett. 42 (1981) L-323. [33] See for instance : ONOGI, S., KATO, H., UEKI, S., IBAGARI, T., J. Polym. Sci. C 15 (1966) 481. ALLEN, V. R., Fox, T. G., J. Chem. Phys. 41 (1964) 337. .Fox, T. G., FLORY, P. J., J. Am. Chem. Soc. 70 (1948) 2384. tabulated in : TIMMERMANS, J., Physics Chemical constants of pure organic compounds (Elsevier, Amsterdam) 1950. BRANDRUP, J., IMMERGUT, E. H., Polymer Handbook DREVAL, V. E., MALKIN, A. YA, BOTVINNIK, G. O., J. Polym. Sci. 11 (1973) 1055. (1977) ZAPAS, L. J., PADDEN, F. J., DEWITT, T. W., Special report of Federal Facilities Corporation (1954). BERRY, G. G., NAKAYASU, H., FOX, T. G., J. Polym. MATSUMOTO, T., NISHIOKA, N., FUJITA, H., J. Polym. [34] RUDD, J. F., J. Polym. Sci. 44 (1960) 459. SHAW, M. T., Polym. Eng. Sci. 17 (1977) 266. [35] BUECHE, F., J. Chem. Phys. 25 (1956) 399. [36] COHEN ADDAD, J. P., GUILLERMO, A., MESSA, J. P., (1975). [18] ADAM, M., DELSANTI, M., Macromolecules [19] [26] DAOUD, M., COTTON, J. P., FARNOUX, B., JANNINK, G., SARMA, G., BENOIT, H., DUPLESSIX, R., PICOT, C., DE GENNES, P. G., Macromolecules 8 (1975) 127. [27] HERVET, H., LÉGER, L., RONDELEZ, F., Phys. Rev. Lett. 42 (1979) 1681. [28] We know from reference [12] that the concentration exponent value of the cooperative diffusion coeffi- 1229. PS-benzene and 6 Sci. PS-cyclohexane : DECKER, D., Thesis, Strasbourg (1968). PIB-cyclohexane and PIB-03B8 solvent (IAIV) : Sci. A 2 10 (1972) 23. [20] GRAESLEY, W. W., Polymer 21 (1980) 258. [21] VON SCHURZ, J., HOCHBERGER, H., Makromol. Chem. 96 (1966) 141. [22] SCHAEFER, D. W., JOANNY, J. F., PINCUS, P., Macromolecules 13 (1980) 1280. [23] We are indebted to R. Ball for pointing out this effect. [24] WEILL, G., DES CLOIZEAUX, J., J. Physique 40 (1979) 99. ACKASU, A. Z., HAN, C. C., Macromolecules 12 (1979) 276. [25] SCHMITT, A., J. Physique Lett. 40 (1979) L-317. Phys. Ed. 17 (1979) 1825. Polymer 20 (1979) 536. [37] STRAZIELLE, C., BENOÎT, H., Macromolecules 8 (1975) 203. [38] EICHINGER, B. E., FLORY, P. J., Trans-Faraday Soc. 64 (1968) 2053. [39] KRIGBAUM, W. R., FLORY, P. J., J. Amer. Chem. Soc. 75 (1953) 1775. [40] FERRY, J. D., Viscoelastic properties of polymer (J. Wiley, N.Y.) 1970, p. 316. [41] For numerical values corresponding to figures 2-3-6-7, see appendix 2.
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