Pub Date : 2025-02-01DOI: 10.1016/j.ijplas.2024.104228
Namit Pai, Indradev Samajdar, Anirban Patra
<div><div>This work presents a combined experimental and crystal plasticity finite element modeling study on the development of bulk and local residual strains during tensile and cyclic deformation of an austenitic stainless steel. The <span><math><mrow><mo>(</mo><mi>h</mi><mi>k</mi><mi>l</mi><mo>)</mo></mrow></math></span>-specific bulk (residual) lattice strains are measured using X-ray Diffraction, while the local residual strains are measured using High Resolution Electron Back Scatter Diffraction. The residual strains are predicted using a dislocation density-based crystal plasticity model, with consideration for directional hardening due to backstress evolution. The work emphasizes on residual strain developments for four specific grain families: <span><math><mrow><mo>(</mo><mn>111</mn><mo>)</mo></mrow></math></span>, <span><math><mrow><mo>(</mo><mn>001</mn><mo>)</mo></mrow></math></span>, <span><math><mrow><mo>(</mo><mn>101</mn><mo>)</mo></mrow></math></span> and <span><math><mrow><mo>(</mo><mn>311</mn><mo>)</mo></mrow></math></span>, specifically in terms of their correlation with the underlying microstructure, studied using crystallographic orientation, misorientation, dislocation density and backstress evolution. Large intragranular orientation gradients, dislocation densities and backstress are observed during tensile deformation for the texturally dominant <span><math><mrow><mo>(</mo><mn>101</mn><mo>)</mo></mrow></math></span> grain family, indicating that these grains have higher plastic deformation as compared to the <span><math><mrow><mo>(</mo><mn>001</mn><mo>)</mo></mrow></math></span> and <span><math><mrow><mo>(</mo><mn>111</mn><mo>)</mo></mrow></math></span> grain families. This also contributes to the observed relaxation in lattice strains for the <span><math><mrow><mo>(</mo><mn>101</mn><mo>)</mo></mrow></math></span> grain family, with the resulting load shed being primarily accommodated by the <span><math><mrow><mo>(</mo><mn>001</mn><mo>)</mo></mrow></math></span> grain family. In contrast, no such orientation gradients or lattice strain relaxations are observed in the cyclically deformed material. The measured local residual strains, which are also qualitatively predicted by the crystal plasticity simulations, highlight the additional effect of spatial heterogeneity and neighboring grains on the development of residual strains. Finally, statistical analysis of the simulated residual strains reveals that the hierarchy in the development of lattice strains is in the following order for the different grain families: <span><math><mrow><mrow><mo>(</mo><mn>001</mn><mo>)</mo></mrow><mo>></mo><mrow><mo>(</mo><mn>311</mn><mo>)</mo></mrow><mo>></mo><mrow><mo>(</mo><mn>111</mn><mo>)</mo></mrow><mo>></mo><mrow><mo>(</mo><mn>101</mn><mo>)</mo></mrow></mrow></math></span> for tensile deformation, and <span><math><mrow><mrow><mo>(</mo><mn>001</mn><mo>)</mo></mrow><mo>></mo><mrow><mo>(</mo><mn>311</mn><mo>)</mo></mrow><mo>></
{"title":"Study of orientation-dependent residual strains during tensile and cyclic deformation of an austenitic stainless steel","authors":"Namit Pai, Indradev Samajdar, Anirban Patra","doi":"10.1016/j.ijplas.2024.104228","DOIUrl":"10.1016/j.ijplas.2024.104228","url":null,"abstract":"<div><div>This work presents a combined experimental and crystal plasticity finite element modeling study on the development of bulk and local residual strains during tensile and cyclic deformation of an austenitic stainless steel. The <span><math><mrow><mo>(</mo><mi>h</mi><mi>k</mi><mi>l</mi><mo>)</mo></mrow></math></span>-specific bulk (residual) lattice strains are measured using X-ray Diffraction, while the local residual strains are measured using High Resolution Electron Back Scatter Diffraction. The residual strains are predicted using a dislocation density-based crystal plasticity model, with consideration for directional hardening due to backstress evolution. The work emphasizes on residual strain developments for four specific grain families: <span><math><mrow><mo>(</mo><mn>111</mn><mo>)</mo></mrow></math></span>, <span><math><mrow><mo>(</mo><mn>001</mn><mo>)</mo></mrow></math></span>, <span><math><mrow><mo>(</mo><mn>101</mn><mo>)</mo></mrow></math></span> and <span><math><mrow><mo>(</mo><mn>311</mn><mo>)</mo></mrow></math></span>, specifically in terms of their correlation with the underlying microstructure, studied using crystallographic orientation, misorientation, dislocation density and backstress evolution. Large intragranular orientation gradients, dislocation densities and backstress are observed during tensile deformation for the texturally dominant <span><math><mrow><mo>(</mo><mn>101</mn><mo>)</mo></mrow></math></span> grain family, indicating that these grains have higher plastic deformation as compared to the <span><math><mrow><mo>(</mo><mn>001</mn><mo>)</mo></mrow></math></span> and <span><math><mrow><mo>(</mo><mn>111</mn><mo>)</mo></mrow></math></span> grain families. This also contributes to the observed relaxation in lattice strains for the <span><math><mrow><mo>(</mo><mn>101</mn><mo>)</mo></mrow></math></span> grain family, with the resulting load shed being primarily accommodated by the <span><math><mrow><mo>(</mo><mn>001</mn><mo>)</mo></mrow></math></span> grain family. In contrast, no such orientation gradients or lattice strain relaxations are observed in the cyclically deformed material. The measured local residual strains, which are also qualitatively predicted by the crystal plasticity simulations, highlight the additional effect of spatial heterogeneity and neighboring grains on the development of residual strains. Finally, statistical analysis of the simulated residual strains reveals that the hierarchy in the development of lattice strains is in the following order for the different grain families: <span><math><mrow><mrow><mo>(</mo><mn>001</mn><mo>)</mo></mrow><mo>></mo><mrow><mo>(</mo><mn>311</mn><mo>)</mo></mrow><mo>></mo><mrow><mo>(</mo><mn>111</mn><mo>)</mo></mrow><mo>></mo><mrow><mo>(</mo><mn>101</mn><mo>)</mo></mrow></mrow></math></span> for tensile deformation, and <span><math><mrow><mrow><mo>(</mo><mn>001</mn><mo>)</mo></mrow><mo>></mo><mrow><mo>(</mo><mn>311</mn><mo>)</mo></mrow><mo>></","PeriodicalId":340,"journal":{"name":"International Journal of Plasticity","volume":"185 ","pages":"Article 104228"},"PeriodicalIF":9.4,"publicationDate":"2025-02-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"142911523","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":1,"RegionCategory":"材料科学","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 2025-02-01DOI: 10.1016/j.ijplas.2024.104238
M.Y. Fei , P.F. Gao , Z.N. Lei , H.W. Li , M. Zhan , M.W. Fu
Trimodal microstructure, consisting of equiaxed α (αp), lamellar α (αl), and transformed β (βt), has become an ideal target microstructure of titanium alloys. However, the complex microstructure morphologies and the differences in mechanical property among the three constituent phases of the trimodal microstructure significantly influence its microscopic crack propagation behaviour and further affect its fracture toughness. To address this issue, a multiscale finite element (FE) model, including a microscopic crack propagation (micro-CP) model and a macroscopic fracture toughness (macro-FT) model, was established for analysis and prediction of the damage fracture behaviour and property of the trimodal microstructure. In this model, the deformation, damage and fracture behaviours of the trimodal microstructure at both micro and macro scales were described by bridging the constitutive laws of constituent phases and deformation responses. In tandem with this, the micro-CP model adopted a macro-micro nested structure, and the macro-FT model was developed based on a virtual fracture toughness test. Using the established multiscale FE model, the dependence of microscopic crack propagation and macroscopic fracture behaviours on the constituent phases of the trimodal microstructure was revealed. It is found that both αp and αl improved the path tortuosity and energy consumption of microscopic crack propagation, and αl decreased the microscopic crack propagation rate simultaneously. In addition, αp and αl contributed to the fracture toughness of the trimodal microstructure from both the intrinsic toughening mechanism (suppressing the heterogeneous deformation and damage and then decreasing the strength and increasing the plasticity) and the extrinsic toughening mechanism (increasing the tortuosity and energy consumption of crack propagation). The research provided an in-depth understanding of the damage and fracture behaviours of TA15 titanium alloy with the trimodal microstructure.
{"title":"Multiscale modeling of the damage and fracture behaviours of TA15 titanium alloy with trimodal microstructure","authors":"M.Y. Fei , P.F. Gao , Z.N. Lei , H.W. Li , M. Zhan , M.W. Fu","doi":"10.1016/j.ijplas.2024.104238","DOIUrl":"10.1016/j.ijplas.2024.104238","url":null,"abstract":"<div><div>Trimodal microstructure, consisting of equiaxed <em>α</em> (<em>α</em><sub>p</sub>), lamellar <em>α</em> (<em>α</em><sub>l</sub>), and transformed <em>β</em> (<em>β</em><sub>t</sub>), has become an ideal target microstructure of titanium alloys. However, the complex microstructure morphologies and the differences in mechanical property among the three constituent phases of the trimodal microstructure significantly influence its microscopic crack propagation behaviour and further affect its fracture toughness. To address this issue, a multiscale finite element (FE) model, including a microscopic crack propagation (micro-CP) model and a macroscopic fracture toughness (macro-FT) model, was established for analysis and prediction of the damage fracture behaviour and property of the trimodal microstructure. In this model, the deformation, damage and fracture behaviours of the trimodal microstructure at both micro and macro scales were described by bridging the constitutive laws of constituent phases and deformation responses. In tandem with this, the micro-CP model adopted a macro-micro nested structure, and the macro-FT model was developed based on a virtual fracture toughness test. Using the established multiscale FE model, the dependence of microscopic crack propagation and macroscopic fracture behaviours on the constituent phases of the trimodal microstructure was revealed. It is found that both <em>α</em><sub>p</sub> and <em>α</em><sub>l</sub> improved the path tortuosity and energy consumption of microscopic crack propagation, and <em>α</em><sub>l</sub> decreased the microscopic crack propagation rate simultaneously. In addition, <em>α</em><sub>p</sub> and <em>α</em><sub>l</sub> contributed to the fracture toughness of the trimodal microstructure from both the intrinsic toughening mechanism (suppressing the heterogeneous deformation and damage and then decreasing the strength and increasing the plasticity) and the extrinsic toughening mechanism (increasing the tortuosity and energy consumption of crack propagation). The research provided an in-depth understanding of the damage and fracture behaviours of TA15 titanium alloy with the trimodal microstructure.</div></div>","PeriodicalId":340,"journal":{"name":"International Journal of Plasticity","volume":"185 ","pages":"Article 104238"},"PeriodicalIF":9.4,"publicationDate":"2025-02-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"142908448","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":1,"RegionCategory":"材料科学","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 2025-02-01DOI: 10.1016/j.ijplas.2024.104220
Sijia Liu , Yunteng Wang
Frictional fracture phenomena in geological media are often closely related to fault instability in earthquakes and slip surface formation in geohazards. In this work, we propose a new phase-field model for capturing frictional fractures in pressure-sensitive geomaterials. Our model has three novel features: (i) a thermodynamically consistent energetic interface for contact and friction conditions; (ii) incorporation of a level set function to couple phase-field evolution and frictional-contact slips; and (iii) a transition from stored energy to yielding for describing different plastic-like frictional stick–slip fractures. Based on the energy conservation law and a variational inequality of virtual work, we formulate the governing equations for frictional fractures, including the dynamic equilibrium equation, phase-field evolution law, and most importantly, frictional interface plastic-like driving forces. We also present a robust numerical technique to handle the spatiotemporal formation and evolution of frictional fractures in rocks. We validate the model by simulating several benchmark examples. Our model is shown to reproduce both frictional stick and slip phenomena in rocks. We also apply this model to study the effect of confining pressure on frictional crack initiation and propagation in rocks, which helps us better understand the deep mechanisms of frictional fracture.
{"title":"A thermodynamically consistent phase-field model for frictional fracture in rocks","authors":"Sijia Liu , Yunteng Wang","doi":"10.1016/j.ijplas.2024.104220","DOIUrl":"10.1016/j.ijplas.2024.104220","url":null,"abstract":"<div><div>Frictional fracture phenomena in geological media are often closely related to fault instability in earthquakes and slip surface formation in geohazards. In this work, we propose a new phase-field model for capturing frictional fractures in pressure-sensitive geomaterials. Our model has three novel features: (i) a thermodynamically consistent energetic interface for contact and friction conditions; (ii) incorporation of a level set function to couple phase-field evolution and frictional-contact slips; and (iii) a transition from stored energy to yielding for describing different plastic-like frictional stick–slip fractures. Based on the energy conservation law and a variational inequality of virtual work, we formulate the governing equations for frictional fractures, including the dynamic equilibrium equation, phase-field evolution law, and most importantly, frictional interface plastic-like driving forces. We also present a robust numerical technique to handle the spatiotemporal formation and evolution of frictional fractures in rocks. We validate the model by simulating several benchmark examples. Our model is shown to reproduce both frictional stick and slip phenomena in rocks. We also apply this model to study the effect of confining pressure on frictional crack initiation and propagation in rocks, which helps us better understand the deep mechanisms of frictional fracture.</div></div>","PeriodicalId":340,"journal":{"name":"International Journal of Plasticity","volume":"185 ","pages":"Article 104220"},"PeriodicalIF":9.4,"publicationDate":"2025-02-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"142908450","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":1,"RegionCategory":"材料科学","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"OA","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Face-centered cubic (FCC) structured FeNiCoCr high-entropy alloys (HEAs) generally demonstrate good plasticity but exhibit relatively low strength. To tackle this challenge, we suggest the following approaches: (1) enhancing work-hardening ability through reducing the stacking fault energy of the alloy system. (2) adjusting the composition of alloying elements to control the formation of precipitation phase, thus fortifying the matrix. Based on the aforementioned perspectives, a series of alloys Fe2NiCoCr(VN)x (x = 0, 0.3, 0.5, 1.0) was designed by adjusting the Fe element content in FeNiCoCr HEAs, and then adding V and N alloying elements to the alloy. Experimental results show that Fe2NiCoCr(VN)0.5 HEAs exhibit high-quality work-hardening ability and strength. The yield strength enhanced from 150 MPa to 250 MPa, while the ultimate tensile strength was enhanced from 540 MPa to 800 MPa. This represents an increase of 66 % in yield strength and 48 % in ultimate tensile strength, respectively. And plasticity remained stable at 25 %, outperforming most as-cast FCC-structured HEAs. The changes in stacking fault energy and the dislocation slip behaviors around the precipitation phase were also calculated by the Molecular Dynamics simulation software Large-scale Atomic/Molecular Massively Parallel Simulator. This study not only reduces costs but also provides insights into the tunability of the mechanical properties of materials through alloying non-equiatomic HEAs.
{"title":"Improvement of work-hardening capability and strength of FeNiCoCr-based high-entropy alloys by modulation of stacking fault energy and precipitation phase","authors":"Lei Zhang , Zhiyu Feng , Zixian Xiong , Xinlong Zhang , Bingzhao Wu , Chunyu Zhao","doi":"10.1016/j.ijplas.2025.104242","DOIUrl":"10.1016/j.ijplas.2025.104242","url":null,"abstract":"<div><div>Face-centered cubic (FCC) structured FeNiCoCr high-entropy alloys (HEAs) generally demonstrate good plasticity but exhibit relatively low strength. To tackle this challenge, we suggest the following approaches: (1) enhancing work-hardening ability through reducing the stacking fault energy of the alloy system. (2) adjusting the composition of alloying elements to control the formation of precipitation phase, thus fortifying the matrix. Based on the aforementioned perspectives, a series of alloys Fe<sub>2</sub>NiCoCr(VN)<sub>x</sub> (<em>x</em> = 0, 0.3, 0.5, 1.0) was designed by adjusting the Fe element content in FeNiCoCr HEAs, and then adding V and N alloying elements to the alloy. Experimental results show that Fe<sub>2</sub>NiCoCr(VN)<sub>0.5</sub> HEAs exhibit high-quality work-hardening ability and strength. The yield strength enhanced from 150 MPa to 250 MPa, while the ultimate tensile strength was enhanced from 540 MPa to 800 MPa. This represents an increase of 66 % in yield strength and 48 % in ultimate tensile strength, respectively. And plasticity remained stable at 25 %, outperforming most as-cast FCC-structured HEAs. The changes in stacking fault energy and the dislocation slip behaviors around the precipitation phase were also calculated by the Molecular Dynamics simulation software Large-scale Atomic/Molecular Massively Parallel Simulator. This study not only reduces costs but also provides insights into the tunability of the mechanical properties of materials through alloying non-equiatomic HEAs.</div></div>","PeriodicalId":340,"journal":{"name":"International Journal of Plasticity","volume":"185 ","pages":"Article 104242"},"PeriodicalIF":9.4,"publicationDate":"2025-02-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"142937070","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":1,"RegionCategory":"材料科学","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 2025-02-01DOI: 10.1016/j.ijplas.2024.104219
Hao Hu , Tao Fu , Shiyi Wang , Chuanying Li , Shayuan Weng , Deqiang Yin , Xianghe Peng
Alloying is an economically efficient strategy to improve the thermal and mechanical stability of materials, which can also be applied to grain boundary (GB) in nanocrystalline materials to improve their mechanical properties. In this work, we investigated the mechanical properties and plastic deformation of bicrystal Ni samples with/without doping and segregation of multi-element (ME) atoms (including Co, Cr, Fe, and Mn atoms) using molecular dynamics (MD) simulations and Monte Carlo (MC) calculations at various temperatures. Each sample contains a Σ5 (210) [001] symmetric tilted GB. It was found that ME doping results in partial GB migration and softening, while ME segregation hinders GB migration, leading to strengthening. The softening and strengthening stem respectively from the distribution of ME atoms in the non-coincident site lattice (non-CSL) and in the coincident site lattice (CSL) sites. Furthermore, temperature affects the GB migration in ME-doped and ME-segregated samples through the compatibility of the ME atoms in GB. The results presented may contribute to understanding the mechanisms of strengthening and softening caused by ME doping and segregation at the atomic scale, and provide a perspective on the balance between strength and ductility.
{"title":"Multi-element segregation strengthening and doping softening of Σ5 (210) [001] symmetrically tilted grain boundary in Ni-based bicrystal","authors":"Hao Hu , Tao Fu , Shiyi Wang , Chuanying Li , Shayuan Weng , Deqiang Yin , Xianghe Peng","doi":"10.1016/j.ijplas.2024.104219","DOIUrl":"10.1016/j.ijplas.2024.104219","url":null,"abstract":"<div><div>Alloying is an economically efficient strategy to improve the thermal and mechanical stability of materials, which can also be applied to grain boundary (GB) in nanocrystalline materials to improve their mechanical properties. In this work, we investigated the mechanical properties and plastic deformation of bicrystal Ni samples with/without doping and segregation of multi-element (ME) atoms (including Co, Cr, Fe, and Mn atoms) using molecular dynamics (MD) simulations and Monte Carlo (MC) calculations at various temperatures. Each sample contains a Σ5 (210) [001] symmetric tilted GB. It was found that ME doping results in partial GB migration and softening, while ME segregation hinders GB migration, leading to strengthening. The softening and strengthening stem respectively from the distribution of ME atoms in the non-coincident site lattice (non-CSL) and in the coincident site lattice (CSL) sites. Furthermore, temperature affects the GB migration in ME-doped and ME-segregated samples through the compatibility of the ME atoms in GB. The results presented may contribute to understanding the mechanisms of strengthening and softening caused by ME doping and segregation at the atomic scale, and provide a perspective on the balance between strength and ductility.</div></div>","PeriodicalId":340,"journal":{"name":"International Journal of Plasticity","volume":"185 ","pages":"Article 104219"},"PeriodicalIF":9.4,"publicationDate":"2025-02-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"142867255","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":1,"RegionCategory":"材料科学","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 2025-02-01DOI: 10.1016/j.ijplas.2025.104240
Hongqing Zheng , Yuchen Yang , Jie Li , Xunwei Zuo , Jianfeng Wan , Yonghua Rong , Nailu Chen
A polycrystalline elastic-plastic phase field model is proposed to reveal the mechanisms of secondary crack initiation, propagation and closure during the water quenching process in medium-carbon martensitic steel. The formation of martensite variants during the quenching process is considered in our model. Moreover, this model can account for the influence of the elastic stress and plastic strain generated after the martensitic transformation during the quenching process on the fracture process. The simulation results show that secondary cracks initiate at the grain boundary region near the primary crack due to its induction. Additionally, they can also initiate at multiple locations in the high-angle grain boundary regions far from the primary crack. This occurs due to elastic stress concentration and plastic strain localization in these regions. Then secondary cracks mainly propagate along prior austenite grain boundary areas. The tensile stress on both sides of the crack tip is the main driving force for crack initiation and propagation. As the external loading increases, the stress at the crack tip gradually transitions into compressive stress, ultimately leading to the closure of the crack in the grain boundary regions. More importantly, these propagation paths of secondary cracks are consistent with the experimental results. Compared with intracrystalline defects, grain boundary defects are more likely to induce crack initiation and propagation. Therefore, this model can offer theoretical guidance for solving the issue of water quenching cracking in medium-carbon martensitic steel.
{"title":"Mechanisms of secondary crack initiation, propagation and closure during the water quenching process in medium-carbon martensitic steel","authors":"Hongqing Zheng , Yuchen Yang , Jie Li , Xunwei Zuo , Jianfeng Wan , Yonghua Rong , Nailu Chen","doi":"10.1016/j.ijplas.2025.104240","DOIUrl":"10.1016/j.ijplas.2025.104240","url":null,"abstract":"<div><div>A polycrystalline elastic-plastic phase field model is proposed to reveal the mechanisms of secondary crack initiation, propagation and closure during the water quenching process in medium-carbon martensitic steel. The formation of martensite variants during the quenching process is considered in our model. Moreover, this model can account for the influence of the elastic stress and plastic strain generated after the martensitic transformation during the quenching process on the fracture process. The simulation results show that secondary cracks initiate at the grain boundary region near the primary crack due to its induction. Additionally, they can also initiate at multiple locations in the high-angle grain boundary regions far from the primary crack. This occurs due to elastic stress concentration and plastic strain localization in these regions. Then secondary cracks mainly propagate along prior austenite grain boundary areas. The tensile stress on both sides of the crack tip is the main driving force for crack initiation and propagation. As the external loading increases, the stress at the crack tip gradually transitions into compressive stress, ultimately leading to the closure of the crack in the grain boundary regions. More importantly, these propagation paths of secondary cracks are consistent with the experimental results. Compared with intracrystalline defects, grain boundary defects are more likely to induce crack initiation and propagation. Therefore, this model can offer theoretical guidance for solving the issue of water quenching cracking in medium-carbon martensitic steel.</div></div>","PeriodicalId":340,"journal":{"name":"International Journal of Plasticity","volume":"185 ","pages":"Article 104240"},"PeriodicalIF":9.4,"publicationDate":"2025-02-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"142935215","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":1,"RegionCategory":"材料科学","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 2025-02-01DOI: 10.1016/j.ijplas.2024.104216
Yanzhi Peng , Caiju Li , Min Song , Zunyan Xu , Chenmaoyue Yang , Qiong Lu , Liang Liu , Xiaofeng Chen , Yichun Liu , Jianhong Yi
Heterogeneous microstructure design has been a prevalent strategy for breaking the strength-ductility dilemma in structural materials. However, it is still difficult to achieve customizable heterogeneous microstructures. Here, we employ a simple powder metallurgy method to construct "dual-metal" heterogeneous structure in aluminum matrix composite (AMC) by introducing hard high-entropy alloy particles into the soft aluminum matrix. By using mutual diffusion and self-organization strategies, reinforcements with special core-shell structures were synthesized in situ, forming multi-level heterogeneous structures within the composites. The results show that the heterogeneity of the microstructure plays an effective role in regulating the strain gradient and maintaining significant strain hardening ability during plastic deformation. In addition, the nanograin layer of the core-shell reinforcement outer shell possesses good toughness and stress-bearing capacity, enabling it to accommodate deformation and inhibit crack propagation effectively. This study provides a feasible method for designing AMCs with heterogeneous structures and contributes a conceptual framework for designing strong and ductile metal matrix composites.
{"title":"Breaking the strength-ductility trade-off in aluminum matrix composite through \"dual-metal\" heterogeneous structure and interface control","authors":"Yanzhi Peng , Caiju Li , Min Song , Zunyan Xu , Chenmaoyue Yang , Qiong Lu , Liang Liu , Xiaofeng Chen , Yichun Liu , Jianhong Yi","doi":"10.1016/j.ijplas.2024.104216","DOIUrl":"10.1016/j.ijplas.2024.104216","url":null,"abstract":"<div><div>Heterogeneous microstructure design has been a prevalent strategy for breaking the strength-ductility dilemma in structural materials. However, it is still difficult to achieve customizable heterogeneous microstructures. Here, we employ a simple powder metallurgy method to construct \"dual-metal\" heterogeneous structure in aluminum matrix composite (AMC) by introducing hard high-entropy alloy particles into the soft aluminum matrix. By using mutual diffusion and self-organization strategies, reinforcements with special core-shell structures were synthesized <em>in situ</em>, forming multi-level heterogeneous structures within the composites. The results show that the heterogeneity of the microstructure plays an effective role in regulating the strain gradient and maintaining significant strain hardening ability during plastic deformation. In addition, the nanograin layer of the core-shell reinforcement outer shell possesses good toughness and stress-bearing capacity, enabling it to accommodate deformation and inhibit crack propagation effectively. This study provides a feasible method for designing AMCs with heterogeneous structures and contributes a conceptual framework for designing strong and ductile metal matrix composites.</div></div>","PeriodicalId":340,"journal":{"name":"International Journal of Plasticity","volume":"185 ","pages":"Article 104216"},"PeriodicalIF":9.4,"publicationDate":"2025-02-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"142857912","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":1,"RegionCategory":"材料科学","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 2025-02-01DOI: 10.1016/j.ijplas.2025.104265
Junpeng Li , Yang Zhang , Weiguo Jiang , Junhua Luan , Zengbao Jiao , Chain Tsuan Liu , Zhongwu Zhang
The transformation-induced plasticity (TRIP) effect is one of the most powerful approaches to improve mechanical properties and work hardening capability of maraging stainless steels (MSSs). However, controlling the TRIP effect poses a great challenge due to the difficulties in manipulating the stability of reverted austenite (RA). In this work, through introducing nano-precipitates into the RA, we achieved a significant improvement in the work-hardening ability for MSSs. The role of the RA decorated and not decorated by nano-precipitates (RADP and RANDP, respectively) was carefully investigated. The precipitation of Ni3(Ti, Mo) and Mo-rich phases within RA causes a low stacking fault energy (SFE) in the RADP compared to the RANDP. In the initial stage of deformation, the RADP is susceptible to the TRIP effect due to the low SFE, which can effectively relieve stresses. Upon further deformation, the nano-precipitates within the RA can block the movement of the 1/6 < 112> Shockley partial dislocations and delay the transformation, thus improving the stability of the RA. This results in a sustainable absorption of stresses and delays the initiation and propagation of cracks. Moreover, the nano-precipitates in the matrix provide a significant increase in strength. Consequently, an excellent combination of high strength, ductility, and work-hardening ability was obtained in the MSSs. The newly developed MSS demonstrates a yield strength of 1790 ± 24 MPa, a tensile strength of 2140 ± 32 MPa, a uniform elongation of 9.5 ± 1.3 % and a total elongation of 16.4 ± 1.1 %. Exploiting the nano-precipitation within RA to tune the TRIP effect provides a new approach for developing high-performance MSSs.
{"title":"Enhancing work hardening through tuning TRIP by nano-precipitates in maraging stainless steels","authors":"Junpeng Li , Yang Zhang , Weiguo Jiang , Junhua Luan , Zengbao Jiao , Chain Tsuan Liu , Zhongwu Zhang","doi":"10.1016/j.ijplas.2025.104265","DOIUrl":"10.1016/j.ijplas.2025.104265","url":null,"abstract":"<div><div>The transformation-induced plasticity (TRIP) effect is one of the most powerful approaches to improve mechanical properties and work hardening capability of maraging stainless steels (MSSs). However, controlling the TRIP effect poses a great challenge due to the difficulties in manipulating the stability of reverted austenite (RA). In this work, through introducing nano-precipitates into the RA, we achieved a significant improvement in the work-hardening ability for MSSs. The role of the RA decorated and not decorated by nano-precipitates (RADP and RANDP, respectively) was carefully investigated. The precipitation of Ni<sub>3</sub>(Ti, Mo) and Mo-rich phases within RA causes a low stacking fault energy (SFE) in the RADP compared to the RANDP. In the initial stage of deformation, the RADP is susceptible to the TRIP effect due to the low SFE, which can effectively relieve stresses. Upon further deformation, the nano-precipitates within the RA can block the movement of the 1/6 < 112> Shockley partial dislocations and delay the transformation, thus improving the stability of the RA. This results in a sustainable absorption of stresses and delays the initiation and propagation of cracks. Moreover, the nano-precipitates in the matrix provide a significant increase in strength. Consequently, an excellent combination of high strength, ductility, and work-hardening ability was obtained in the MSSs. The newly developed MSS demonstrates a yield strength of 1790 ± 24 MPa, a tensile strength of 2140 ± 32 MPa, a uniform elongation of 9.5 ± 1.3 % and a total elongation of 16.4 ± 1.1 %. Exploiting the nano-precipitation within RA to tune the TRIP effect provides a new approach for developing high-performance MSSs.</div></div>","PeriodicalId":340,"journal":{"name":"International Journal of Plasticity","volume":"186 ","pages":"Article 104265"},"PeriodicalIF":9.4,"publicationDate":"2025-02-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"143072584","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":1,"RegionCategory":"材料科学","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 2025-02-01DOI: 10.1016/j.ijplas.2024.104226
Jie Huang , Mingyu Lei , Guochun Yang , Bin Wen
Twinning, a plastic deformation mode, is crucial in dictating material plasticity and significantly impacting their mechanical properties. In this work, we propose a new twinning mechanism based on the phenomenon of asymmetric shear response. By integrating transition state theory with this mechanism, we derive the twinning nucleation stress, and reveal the impact of temperature and strain rate on twin nucleation and growth processes. The model's efficacy is validated through a comparison of predicted results for face centered cubic (FCC), body centered cubic (BCC) and hexagonal close packed (HCP) crystals with experimental ones. This work provides a theoretical foundation for predicting the conditions under which twinning occurs, thereby guiding the design and fabrication of materials containing twin structures.
{"title":"Twinning induced by asymmetric shear response","authors":"Jie Huang , Mingyu Lei , Guochun Yang , Bin Wen","doi":"10.1016/j.ijplas.2024.104226","DOIUrl":"10.1016/j.ijplas.2024.104226","url":null,"abstract":"<div><div>Twinning, a plastic deformation mode, is crucial in dictating material plasticity and significantly impacting their mechanical properties. In this work, we propose a new twinning mechanism based on the phenomenon of asymmetric shear response. By integrating transition state theory with this mechanism, we derive the twinning nucleation stress, and reveal the impact of temperature and strain rate on twin nucleation and growth processes. The model's efficacy is validated through a comparison of predicted results for face centered cubic (FCC), body centered cubic (BCC) and hexagonal close packed (HCP) crystals with experimental ones. This work provides a theoretical foundation for predicting the conditions under which twinning occurs, thereby guiding the design and fabrication of materials containing twin structures.</div></div>","PeriodicalId":340,"journal":{"name":"International Journal of Plasticity","volume":"185 ","pages":"Article 104226"},"PeriodicalIF":9.4,"publicationDate":"2025-02-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"142887067","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":1,"RegionCategory":"材料科学","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
Pub Date : 2025-02-01DOI: 10.1016/j.ijplas.2025.104241
Zhide Li , Cheng Lu , Charlie Kong , M.W. Fu , Hailiang Yu
High strength and good ductility are essential for the engineering applications of structural materials, yet these two attributes often do not coexist. In the present study, a composite heterostructuring designed with multi-scale, lamellar, and bimodal was developed to deal with the trade-off between strength and ductility. This heterostructuring includes coarse-grain soft domains arranged in a lamellar structure within a matrix characterized by both fine and ultrafine grains arranged in a bimodal structure created through a straightforward thermo-mechanical process. The gradient in strength among various grain structures generates a gradient in strain during deformation. This promotes the generation of additional geometrically necessary dislocations (GNDs) in the soft domain, favouring strength enhancement. The ongoing and efficient accumulation and evolution of GNDs within the soft domains are further developed into the dislocation cells and subgrain boundaries, which, on the other hand, increase the strain hardening and, hence, the ductility.
{"title":"Enhancing the strength and ductility of pure metal via multi-scale and multitype composite heterostructuring","authors":"Zhide Li , Cheng Lu , Charlie Kong , M.W. Fu , Hailiang Yu","doi":"10.1016/j.ijplas.2025.104241","DOIUrl":"10.1016/j.ijplas.2025.104241","url":null,"abstract":"<div><div>High strength and good ductility are essential for the engineering applications of structural materials, yet these two attributes often do not coexist. In the present study, a composite heterostructuring designed with multi-scale, lamellar, and bimodal was developed to deal with the trade-off between strength and ductility. This heterostructuring includes coarse-grain soft domains arranged in a lamellar structure within a matrix characterized by both fine and ultrafine grains arranged in a bimodal structure created through a straightforward thermo-mechanical process. The gradient in strength among various grain structures generates a gradient in strain during deformation. This promotes the generation of additional geometrically necessary dislocations (GNDs) in the soft domain, favouring strength enhancement. The ongoing and efficient accumulation and evolution of GNDs within the soft domains are further developed into the dislocation cells and subgrain boundaries, which, on the other hand, increase the strain hardening and, hence, the ductility.</div></div>","PeriodicalId":340,"journal":{"name":"International Journal of Plasticity","volume":"185 ","pages":"Article 104241"},"PeriodicalIF":9.4,"publicationDate":"2025-02-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"142924679","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":1,"RegionCategory":"材料科学","ArticlePicture":[],"TitleCN":null,"AbstractTextCN":null,"PMCID":"","EPubDate":null,"PubModel":null,"JCR":null,"JCRName":null,"Score":null,"Total":0}
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