Abstract
Crystal plasticity finite element models have been extensively used to simulate various aspects of polycrystalline deformations. A common weakness of practically all models lies in a relatively large number of constitutive modeling parameters that, in principle, would require dedicated measurements on proper length scales in order to perform reliable model calibration. It is important to realize that the obtained data at different scales should be properly accounted for in the models. In this work, a two-scale calibration procedure is proposed to identify (conventional) crystal plasticity model parameters on a grain scale from tensile test experiments performed on both single crystals and polycrystals. The need for proper adjustment of the polycrystalline tensile data is emphasized and demonstrated by subtracting the length scale effect, originating due to grain boundary strengthening, following the Hall–Petch relation. A small but representative volume element model of the microstructure is identified for fast and reliable identification of modeling parameters. Finally, a simple hardening model upgrade is proposed to incorporate the grain size effects in conventional crystal plasticity. The calibration strategy is demonstrated on tensile test measurements on 316L austenitic stainless steel obtained from the literature.
Highlights
Crystal plasticity theory has been extensively employed in the research of metal plasticity.Since the introduction of the concept of dislocations [1,2], many advances in the understanding of slip systems, work hardening and texture evolution have been made
These findings led to the development of crystal plasticity (CP) models and their implementation into commercial finite element (FE) solvers
There is a growing tendency of building [15] and using FE models that resemble true grain topology, true texture and/or realistic loading conditions with the intention to compare the predictions of emerging local phenomena of the underlying CP models directly with measurements
Summary
Crystal plasticity theory has been extensively employed in the research of metal plasticity.Since the introduction of the concept of dislocations [1,2], many advances in the understanding of slip systems, work hardening and texture evolution have been made. There is a growing tendency of building [15] and using FE models that resemble true grain topology, true texture and/or realistic loading conditions with the intention to compare the predictions of emerging local phenomena of the underlying CP models (e.g., grain boundary stress concentrations [16,17,18], plastic strain localization and the formation of slip bands [19,20], crack initiation and propagation [6,19,21]) directly with measurements In such cases, appropriately-calibrated constitutive laws would certainly be required, which, is not a trivial task.
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