In transformation induced plasticity (TRIP) steel a diffusionless austenitic-martensitic phase transformation induced by plastic deformation can be observed, resulting in excellent macroscopic properties. In particular low-alloyed TRIP steels, which can be obtained at lower production costs than high-alloyed TRIP steel, combine this mechanism with a heterogeneous arrangement of different phases at the microscale, namely ferrite, bainite, and retained austenite. The macroscopic behavior is governed by a complex interaction of the phases at the micro-level and the inelastic phase transformation from retained austenite to martensite. A reliable model for low-alloyed TRIP steel should therefore account for these microstructural processes to achieve an accurate macroscopic prediction. To enable this, we focus on a multiscale method often referred to as FE 2 approach, see [6]. In order to obtain a reasonable representative volume element, a three-dimensional statistically similar representative volume element (SSRVE) [1] can be used. Thereby, also computational costs associated with FE 2 calculations can be significantly reduced at a comparable prediction quality. The material model used here to capture the above mentioned microstructural phase transformation is based on [3] which was proposed for high alloyed TRIP steels, see also e.g. [8].Computations based on the proposed two-scale approach are presented here for a three dimensional boundary value problem to show the evolution of phase transformation at the microscale and its effects on the macroscopic properties.
Material model and numerical exampleThe material model in [3], originally proposed for high-alloyed TRIP steels, has been adopted here and suited for application to the retained austenite phase in low-alloyed TRIP steels. The hyperelastic-plastic formulation at large strains uses a multiplicative decomposition of the deformation gradient, F = F e F in where F in represents all inelastic processes.The free energy function is additively decomposed into elastic, plastic, chemical and phase transformation parts,Here, b e is the finger deformation tensor, α pl , α pt are the internal variables for plasticity and phase transformation and f γ , f α are the volume fractions for austenite and martensite, respectively. The two inelastic processes at the microstructure have been described using two independent limit surfaces: rate independent plasticity of von Mises type and the transformation criterion. The handling of two limit surfaces, that may simultaneously be active, is done by means of the operator split return mapping algorithm in [2] combined with the associative multi-surface plasticity algorithm in [5], which has been extended here for large strains. The von Mises plasticity possesses an isotropic exponential hardening and incorporates a non-linear rule of mixtures (m) to appropriately scale the initial yield stress based on f α . The associated yield criterion reads,The hyperbolic transformation surface where, I 1 is the first invariant of Kirchoff str...