Abstract:A void coalescence term was proposed as an addition to the original void nucleation and growth (NAG) model to accurately describe void evolution under dynamic loading. The new model, termed as modified void nucleation and growth model (MNAG model), incorporated analytic equations to explicitly account for the evolution of the void number density and the void volume fraction (damage) during void nucleation, growth, as well as the coalescence stage. The parameters in the MNAG model were fitted to molecular dynam… Show more
“…However, it may also be due, in part, to the void growth rate not being constant across the damage plane or throughout time. This is an important observation to make, as many currently used damage models implement a single void growth rate function for all voids across a sample ( 28 , 29 , 31 ). While these calculations do require assumptions of negligible tilt and void layering, as discussed above, this estimate is the first time such a rate has been experimentally quantified.…”
Section: Resultsmentioning
confidence: 99%
“…Many analytical void damage models have been developed that attempt to predict spall strength and void evolution over time ( 5 , 27 ). Models have incorporated effects such as void nucleation and growth ( 28 ), rate dependency ( 29 , 30 ), and void coalescence ( 31 ), to name a few, with varied degrees of success in predicting experimental data.…”
Section: Introductionmentioning
confidence: 99%
“…This is particularly relevant to the gas gun impact experiments shown herein (with strain rates ≲10 5 s −1 ) and is important because it has been shown that strain rate has a notable effect on total damage in materials ( 35 ). Deficiencies in current analytical strain-equivalent damage models ( 5 , 27 – 29 , 31 ) for nucleation and growth include assumptions and simplifications of the initial positioning of void nucleation sites, void growth rates, and void shapes. This lack of understanding is, in part, related to the absence of direct, real-time quantitative measurements of void nucleation and early-stage growth.…”
Accurate modeling and prediction of damage induced by dynamic loading in materials have long proved to be a difficult task. Examination of postmortem recovered samples cannot capture the time-dependent evolution of void nucleation and growth, and attempts at analytical models are hindered by the necessity to make simplifying assumptions, because of the lack of high-resolution, in situ, time-resolved experimental data. We use absorption contrast imaging to directly image the time evolution of spall damage in metals at ∼1.6-μm spatial resolution. We observe a dependence of void distribution and size on time and microstructure. The insights gained from these data can be used to validate and improve dynamic damage prediction models, which have the potential to lead to the design of superior damage-resistant materials.
“…However, it may also be due, in part, to the void growth rate not being constant across the damage plane or throughout time. This is an important observation to make, as many currently used damage models implement a single void growth rate function for all voids across a sample ( 28 , 29 , 31 ). While these calculations do require assumptions of negligible tilt and void layering, as discussed above, this estimate is the first time such a rate has been experimentally quantified.…”
Section: Resultsmentioning
confidence: 99%
“…Many analytical void damage models have been developed that attempt to predict spall strength and void evolution over time ( 5 , 27 ). Models have incorporated effects such as void nucleation and growth ( 28 ), rate dependency ( 29 , 30 ), and void coalescence ( 31 ), to name a few, with varied degrees of success in predicting experimental data.…”
Section: Introductionmentioning
confidence: 99%
“…This is particularly relevant to the gas gun impact experiments shown herein (with strain rates ≲10 5 s −1 ) and is important because it has been shown that strain rate has a notable effect on total damage in materials ( 35 ). Deficiencies in current analytical strain-equivalent damage models ( 5 , 27 – 29 , 31 ) for nucleation and growth include assumptions and simplifications of the initial positioning of void nucleation sites, void growth rates, and void shapes. This lack of understanding is, in part, related to the absence of direct, real-time quantitative measurements of void nucleation and early-stage growth.…”
Accurate modeling and prediction of damage induced by dynamic loading in materials have long proved to be a difficult task. Examination of postmortem recovered samples cannot capture the time-dependent evolution of void nucleation and growth, and attempts at analytical models are hindered by the necessity to make simplifying assumptions, because of the lack of high-resolution, in situ, time-resolved experimental data. We use absorption contrast imaging to directly image the time evolution of spall damage in metals at ∼1.6-μm spatial resolution. We observe a dependence of void distribution and size on time and microstructure. The insights gained from these data can be used to validate and improve dynamic damage prediction models, which have the potential to lead to the design of superior damage-resistant materials.
“…In [3], Chen et al proposed the modified void nucleation and growth model (MNAG model) in which the original void nucleation and growth model (NAG model) was extended by added a term to account for the void coalescence. The MNAG model was parameterized with molecular dynamics (MD) shock data of single crystal and nanocrystalline Ta.…”
“…Currently, ductile damage in materials is represented using various models such as TEPLA, TONKS, MNAG etc. [1][2][3][4]. However, these models need to be parameterized using experimental velocity-time and porosity position data.…”
Damage models for ductile materials typically need to be parameterized, often with the appropriate parameters changing for a given material depending on the loading conditions. This can make parameterizing these models computationally expensive, since an inverse problem must be solved for each loading condition. Using standard inverse modeling techniques typically requires hundreds or thousands of high-fidelity computer simulations to estimate the optimal parameters. Additionally, the time of human expert is required to set up the inverse model. Machine learning has recently emerged as an alternative approach to inverse modeling in these settings, where the machine learning model is trained in an offline manner and new parameters can be quickly generated on the fly, after training is complete. This work utilizes such a workflow to enable the rapid parameterization of a ductile damage model called TEPLA with a machine learning inverse model. The machine learning model can estimate parameters in under a second while a traditional approach takes hundreds of CPU hours. The results demonstrate good accuracy on a held-out, synthetic test dataset and is validated against experimental data.
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