Effects of Temperature and Molecular Weight on the Porous Structure Formation of Polymer Chemical Gels

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Effects of Temperature and Molecular Weight on the Porous Structure Formation of Polymer Chemical Gels Polymer Journal. Vol. 31, No.5, pp 447-451 (1999) Effects of Temperature and Molecular Weight on the Porous Structure Formation of Polymer Chemical Gels Toshiaki MIURA, Ryoichi KISHI, and Hisao lcHuo National Institute of' Materials and Chemical Research, Twkuha. Jharaki 305 8565. Japan (Received November 5, 1998) ABSTRACT: The e!Tects of temperature and molecular weight on the formation of inhomogeneous polymer gels, in which chemical gelation and phase separation take place simultaneously, were investigated. Slow chemical gelation by gamma ray irradiation was suitable for systematic analysis. In starting from ordinary polymer solutions, the characteristic wavenumber of the porous structure decreases very sharply with depth of temperature jump. However, with appropriate amount of pre-dose, the effects of temperature are almost taken over by those of the pre-dose. The shape of the phase boundary also contributes to this temperature insensitive region. Hence, pre-dose of polymer solutions. which induces the molecular weight build up, is an important factor that facilitates controlled preparations of inhomogeneous porous structures of chemical gel networks. KEYWORDS Poly(vinylmethylether) I Chemical Gels I Porous Structure I Pre-Dose I Polymer gels continue to attract considerable interest tempts.l. 2 bulk PVME gels of porous structures were from experimental and theoretical points of view. Some obtained without temperature control. In this case. the polymer gels show sharp transition in volume by temperature of the sample cells increased gradually from changing temperature or solvent. However, the slow the room temperature to around 500C. due to the heat dynamics of gels sometimes restricts applications. One transmitted from the radiation source as shown in Figure effective method to improve this slow dynamics is to use I. However. when we tried to prepare the same porous various higher order structures instead of homogeneous PVME gels with controlled stepwise temperature jump gels. The inhomogeneous gels that have interconnected above the phase separation point. we were not able to porous structure are examples. The volume relaxation obtain such porous gels. We only found that the dense times of inhomogeneous gels of appropriate porous homogeneous gels precipitated to the bottom of sample structures are several hundred times faster than homo­ cells in most cases. This seems strange and one question geneous gels. 1 - 4 For the preparation of gel networks arises. Is the gradual temperature increase the essential with large inhomogeneity in the order of hundred mi­ factor for the preparation of inhomogeneous polymer crometers. it is very effective to use phase separations. chemical gels? In order to clarify this problem and find The phase separation produces polymer rich and solvent suitable preparation conditions, quantitative analysis rich region. The competition of the phase separation and that systematically changes the experimental conditions gelation leads to inhomogeneous gels. We reported on in the porous structure formation of polymer chemical the rapid responsive porous poly(vinylmethylether) gels is necessary. This study investigates the effects of (PVME) gels that are prepared by }'-ray irradiation 1 . preparation temperature and molecular weight of the This corresponds to the simultaneous phase separation polymer solutions in detail and finds out the essential and chemical gelation. Preparations of porous gels have factors that determine the inhomogeneity of chemical gel also been reported on other gels as poly(N-isopropyl­ networks. acrylamide) gels 5 or some physical gels. 6 - 9 some of which were prepared by freezing and toughening. Polymer solutions from which chemical gels are produced 50 have strong concentrations or molecular weight de­ pendency in viscoelastic properties, which may add additional features that are different from polymer u 40 blends. Although the studies on competitive phase ....Cl> separation have been extensive for polymer blends, 1 0 - 14 ::I there is little detailed quantitative analysis on the -nl.... Cl> formation of porous chemical gels. This is partly because 0. E 30 the control of the gelation speed is usually difficult for the polymer chemical gels. However. by adopting the chemical gelation by }'-ray irradiation, the speed of gelation reaction is directly related to the exposure. 20 2 4 6 8 10 Hence, it becomes easy to control this experimental 0 Time (h) parameter. The size of porous structure depends on the balance Figure I. Without temperature control, the temperature of the irradiation cell increases gradually due to heat transmitted from the of the phase separation speed and gelation speed. radiation source. In our previous attempts, opaque gels with the However. the actual preparation of inhomogeneous inhomogeneous porous structures were obtained only at this condition. chemical gels has been very difficult. In previous at- Dashed line indicates the point where phase separation begins. 447 T. MIURA, R. KISHI, and H. !CHIJO Temperature r -ray Cross-linking Temperature u Jump __T_.' +-C---------1--------J 35 e::I 41 Time c.. E 30 1-phase region {! Gelation Time Molecular Weight 25 0 20 40 60 80 100 Concentration(%) Figure 3. A phase diagram of PVME solutions. Filled circles indicate the boundary of one-phase region and two-phase region. Above the open circles, phase separation takes place very rapidly. Inhomogeneous gels thus obtained were cooled and immersed in water at 25oC for observation. Porous A structures of thin gel films were observed using a phase contrast optical microscope. Microscopic images were Time recorded on videotape. Characteristic length of these porous gels was calculated by image analysis using a personal computer. Two-dimensional Fourier transfor­ Gelation Time mation of a real space image gives us the wave space information, equivalent to the results that can be Gelation Threshold obtained by light scattering. Since the microscopic images are not periodic, the procedure to reduce the edge effect Figure 2. Experimental scheme to change chemical gelation speed. is necessary. We cut the original images whose sizes are 640 x 480 pixels to those of 400 x 400 pixels. These images EXPERIMENTAL were extrapolated to 512 x 512 by zero padding. The fast Fourier transformation (FFT) was applied using the Aqueous solution of PVME (Tokyo Kasei Co., Ltd.) hamming window function. Since these gels are isotropic, was used without further purification. Weight-averaged we calculated the radial distribution of FFT intensity by molecular weight was 92000 (M,) Mn = 3.3) measured averaging the two-dimensional FFT results for all from GPC. We prepared narrowly distributed PVME directions. The scattering functions were averaged over samples by GPC fractionation. Fractionated PVME many snapshots of gels. was weight-averaged molecular weight of 83000 with polydispersity of 1.24. The phase diagram of PVME RESULTS AND DISCUSSION solutions was determined by phase contrast microscope (Olympus BH-2) and differential scanning calorimeter Since the phase separation temperature is the baseline (Seiko Instruments SSC5200). to determine the depth of the temperature jump, we first PVME solution of 30wt% becomes gel with irradia­ determined the phase diagram of our PVME samples tion of 21.4 kGy (21.4 kJ kg -l) of the y-ray from the with narrow molecular weight distribution. As shown 6 °Co source (IIOTBq). The dose rate was 8.56kGyh- 1 . in Figure 3, the PVME solution becomes two-phase in the The gelation threshold of PVME solution depends on high temperature region. Although the phase boundary the concentrations of polymers as reported elsewhere. 15 between the mixed region and two-phase region has Temperature jump was carried out by circulating the unique dependency on the polymer concentration, phase temperature-controlled water around the sample cells. separation becomes very fast over 35°C, from which Experimental conditions of the temperature jump and endothermic also showed a sharp increase. Opaque irradiation are illustrated in Figure 2. In addition to the inhomogeneous gels were not obtained below 35°C. The temperature factor. we changed the molecular weight of shape of the phase diagram of PVME does not come polymer solution by pre-dose. By inducing the molecular from the polydispersity effect of the polymer samples, weight build up of polymer sample, the gelation time since we used fractionated samples. It may be ascribed decreases. Specifically, when the original polymer to the specific hydrophobic interaction of PVME. There solution becomes gel with the irradiation of time tgei• we was no significant difference in the transition points prepare samples that are irradiated for 0.2tgei• 0.4tgei• between fractionated samples and original ones. Hence, 0.6! gel· and 0.8/ gel at room temperature before simul­ we used the original PVME samples hereafter. taneous phase separation and chemical gelation. As Figure 4 shows typical results of image analysis for shown in Figure 2, pre-dosed polymer solutions form the inhomogeneous gel samples. The temperature of gels with irradiation of 0.8/gei• 0.6tgei• 0.4tgeb 0.2/gel re­ the preparation was 39oC and pre-dose amount was spectively, which are faster than the original polymer 17.1 kGy. As with ordinary phase separation of binary solution. solutions, the scattering function of inhomogeneous gels 448 Polym. J., Vol. 31, No. 5, 1999 Porous Structure Formation of Polymer Chemical Gels 0.2 48 46 Ill VI 544 c: 0.1 Ill 'Iii c: lii 42 - 0. E40 38 0 104 105 10' 107 Wavenumber (m.') 5 10 15 Pre-dose (kGy) Figure 4. Typical example of the scattering functions of the in­ homogeneous chemical gels. Figure 5. Structure mapping of inhomogeneous PVME gels obtained from 30 wt% solutions. The darkness represents the characteristic showed a broad peak. Hereafter, we use this peak porous size of gels. This chart is painted with seven ranges in the darkness, in which the brighter part indicates the larger porous wavenumber as the convenient characteristic length of structure. The length range is from 25 .urn to 210 .urn. Boundaries of the porous structure.
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