A mesomechanics parametric finite element study of damage growth and coalescence in polymers using an Elastoviscoelastic-Viscoplastic internal state variable model

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Abstract Biaxial loading of a 9x9 mm Polycarbonate plate with 2 defects showing interacting stress fields. A split-level factorial design of experiments (DOE) parametric study using a two-dimensional mesoscale Finite Element Analysis (FEA) was executed to elicit the most essential aspects pertaining to void/crack growth and void/crack coalescence in polymers above the glass transition temperature. The FEA was coupled to a physically based, strain rate and temperature dependent, elastoviscoelastic-viscoplastic internal state variable polymer model that was calibrated to physical experiments. The DOE method examined the relative influences of seven independent parameters related to mechanics (stress state, strain rate, and temperature) and materials science (polymer blend, number of initial defects, defect type, and initial microporosity—also called the subscale free volume) with respect to both void/crack growth and void/crack coalescence in polymers. The results of the DOE algorithm clearly illustrated that the stress state and applied strain rate were the most critical factors affecting void/crack growth. For void/crack coalescence, the stress state and number of defects were the crucial parameters. The conclusions of this study gives insight for the development of a macroscale damage model for polymers. Authors W. B. Lawrimore II, D. K. Francis, J. L. Bouvard, Mark F. Horstemeyer Publication Mechanics of Materials 96 Methodology This study compares the relative parametric influences between the chosen parameters on damage growth and coalescence in polymers. Having seven parameters quantified at two levels yields 128 ($2^7$) unique simulations (one for each possible parameter grouping). The DOE technique is essentially a tool that selects a minimum spanning set for the simulation space based on some criteria. The DOE method creates a linear mapping from a set of influences, {A}, to a set of responses, {R}, through a parameter matrix, {P} corresponding to the orthogonal array with $\begin{Bmatrix} R \end{Bmatrix} = \begin{bmatrix} P \end{bmatrix} \begin{Bmatrix} A \end{Bmatrix}$ where: $\begin{Bmatrix} R \end{Bmatrix} = \begin{Bmatrix} R_0\\ R_1\\ R_2\\ R_3\\ R_4\\ R_5\\ R_6\\ R_7 \end{Bmatrix}, \begin{Bmatrix} A \end{Bmatrix} = \begin{Bmatrix} A_0\\ A_1\\ A_2\\ A_3\\ A_4\\ A_5\\ A_6\\ A_7 \end{Bmatrix}, \begin{bmatrix} P \end{bmatrix} = \begin{bmatrix} +1 & -1 & -1 & -1 & -1 & -1 & -1 & -1 \\ +1 & -1 & -1 & -1 & +1 & +1 & +1 & +1 \\ +1 & -1 & +1 & +1 & -1 & -1 & +1 & +1 \\ +1 & -1 & +1 & +1 & +1 & +1 & -1 & -1 \\ +1 & +1 & -1 & +1 & -1 & +1 & -1 & +1 \\ +1 & +1 & -1 & +1 & +1 & -1 & +1 & -1 \\ +1 & +1 & +1 & -1 & -1 & +1 & -1 & +1 \\ +1 & +1 & +1 & -1 & +1 & -1 & +1 & -1 \\\end{bmatrix}$ By inverting the equation, one can solve for {A}: $\begin{Bmatrix} A \end{Bmatrix} = \begin{Bmatrix} R \end{Bmatrix} \begin{bmatrix} P \end{bmatrix}^{-1}$ The Taguchi logarithmic parametric array is shown below: Calc Material Particle/Void One/Two Defect(s) Temperature (K) Stress State Strain Rate (1/s) Microporosity (Vol Frac) 1 ABS Void One 253 Uniaxial 0.001 0 2 ABS Void One 323 Biaxial 0.1 0.001 3 ABS Particle Two 253 Uniaxial 0.1 0.001 4 ABS Particle Two 323 Biaxial 0.001 0 5 PC Void Two 253 Biaxial 0.001 0.001 6 PC Void Two 323 Uniaxial 0.1 0 7 PC Particle One 253 Biaxial 0.1 0 8 PC Particle One 323 Uniaxial 0.001 0.001 Material Model A physically-based, rate and temperature dependent ISV model for polymers developed by Bouvard et al. (2013) was used to accurately represent both ABS and PC. The ISV model was calibrated to physical experiments at a variety of temperatures and strain rates for both materials. The constitutive model features three ISVs to account for inelastic dissipation mechanisms in polymers. $\xi_1$ is a strain-like scalar that accounts for dissipation induced from polymer chain entanglement points. $\xi_2$ is a strain-like scalar that represents material hardening resulting from polymer chain alignment and coiling at large strains. Lastly, $\alpha$ is a strain-like tensor that accounts for hardening induced by polymer chain orientation and stretching at large strains. The ISV model calibrations to physical experiments are shown below. True stress–true strain curves under tension comparing the thermoplastic internal state variable model over a range of temperatures with experiments for acrylonitrile butadiene styrene (ABS). True stress–true strain curves under tension comparing the thermoplastic internal state variable model over a range of strain rates with experiments for acrylonitrile butadiene styrene (ABS). True stress–true strain curves under tension comparing the thermoplastic internal state variable model over a range of temperatures with experiments for polycarbonate (PC). True stress–true strain curves under tension comparing the thermoplastic internal state variable model over a range of strain rates with experiments for polycarbonate (PC). Finite Element Results Stress Triaxiality Max Inelastic Strain Stress triaxiality contour plots from each design of experiments finite element computations at the peak load. Schematic showing equivalent inelastic strain (SDV42) contour plots for each design of experiments simulation at the peak load. Parametric Results Stress Triaxiality Max Inelastic Strain Void Volume Fraction Normalized influence of each design of experiments parameter on the aggregate stress triaxiality. Normalized influence of each design of experiments parameter on the local maximum equivalent inelastic strain. Normalized influence of each dsign of experiments parameter on the void volume fraction. Summary A DOE parametric study was conducted to discover the crucial influence parameters affecting damage growth and coalescence in polymers. The parametric study employed a finite element analysis coupled with an experimentally calibrated time and temperature sensitive elastoviscoelastic-viscoplastic ISV model for polymers. The analysis revealed that the stress state that induced a particular stress triaxiality was the most important parameter for damage growth. Researchers have argued that viscoelastic materials, such as the structural polymers represented in this study, have a strong strain rate and time sensitivity. Although these polymers do exhibit a strain rate and time sensitivity, the mechanism that induces void growth and coalescence the strongest is a large stress triaxiality arising from an elevated applied stress state with secondary contributions from the material having a larger yield stress and a higher temperature. References