Constitutive equations are derived for compressible glassy polymers at non-isothermal loading with ®nite strains. The model is based on the theory of temporary networks in its version of adaptive links concept. The stress±strain relations are applied to the analysis of uniaxial extension of a viscoelastic bar. Explicit formulas are developed for time-dependent Young's modulus and Poisson's ratio of the bar at small strains. Results of numerical simulation are compared with experimental data for polycarbonate, polyethylene, and poly(methyl methacrylate). It is demonstrated that (i) longitudinal stresses do not affect the speci®c free volume in the region of linear viscoelasticity at strains up to about 0.2%, and cause substantial changes in the free volume in the region of nonlinear viscoelasticity at strains about 1.0%; (ii) in the latter case, the increment of the free-volume fraction is proportional to the increase in the speci®c volume.
IntroductionThe study is concerned with the kinetics of volume relaxation in glassy polymers at ®nite and small strains. This subject has attracted substantial attention in the past decade, see, e.g. [5,7,24,25,29] and the references therein, which may be explained by the following reasons:1. To correctly predict stresses in polymeric materials at three-dimensional loading, adequate constitutive equations are necessary. Even for a linear isotropic viscoelastic medium at small strains, stress±strain relations contain two kernels which characterize the material response in shear and hydrostatic tension±compression. Experimental determination of these kernels requires a complicated testing program, see, e.g. [1,24,25]. On the other hand, conventional simpli®cations of the model, based on the assumption regarding the constancy of Poisson's ratio or the neglect of volume relaxation, entail signi®cant deviations of numerical results from observations. In particular, constitutive equations with a constant Poisson ratio cannot predict nonmonotonic changes in the speci®c volume observed in tensile relaxation tests on polycarbonate and poly(methyl methacrylate) [2, 7], whereas stress±strain relations neglecting volume relaxation fail to describe mechanically induced densi®cation observed in tensile and compressive relaxation tests on polycarbonate [5]. A model is therefore necessary that would imply some relations between relaxation kernels or their analogs, and would thus reduce the number of experimental data to be used. 2. The region of linear viscoelasticity for polymeric glasses is rather narrow (usually, strains should not exceed 0.5% [14]), which implies that most problems of interest in polymer engineering are described by nonlinear stress±strain relations. A conventional approach to designing nonlinear analogs for linear constitutive models consists in the introduction of some material time [20] which governs reformation of polymeric networks. This time is