While the effects of pre-deformation on thermodynamically controlled transformation behaviors have been well established in traditional shape memory alloys, it remains unclear whether similar influences apply to kinetically controlled systems. In this letter, we investigate the thermally induced transformation behaviors of pre-deformed precursory NiTiNb alloy specimens, and compare them with those of equiatomic and near-equiatomic binary NiTi of different grain sizes and transformation paths. We show that Ms of NiTiNb increases monotonically with pre-deformation strain, in sharp contrast to the scenario in binary NiTi regardless of the grain size or transformation path. In comparison, Af of all NiTiNb and NiTi specimens are however insensitive to pre-deformation strain. We suggest that these discrepancies are likely attributed to the enhanced kinetic barrier of nucleation of the forward transformation.
{"title":"Abnormal impacts of pre-deformation on the martensitic transformation behaviors of precursory NiTiNb alloys","authors":"Youyi Yang, Qiuzhen Li, Pengfei Gao, Jingyuan Guo, Lishan Cui, Kaiyuan Yu","doi":"10.1016/j.scriptamat.2025.116693","DOIUrl":"10.1016/j.scriptamat.2025.116693","url":null,"abstract":"<div><div>While the effects of pre-deformation on thermodynamically controlled transformation behaviors have been well established in traditional shape memory alloys, it remains unclear whether similar influences apply to kinetically controlled systems. In this letter, we investigate the thermally induced transformation behaviors of pre-deformed precursory NiTiNb alloy specimens, and compare them with those of equiatomic and near-equiatomic binary NiTi of different grain sizes and transformation paths. We show that M<sub>s</sub> of NiTiNb increases monotonically with pre-deformation strain, in sharp contrast to the scenario in binary NiTi regardless of the grain size or transformation path. In comparison, A<sub>f</sub> of all NiTiNb and NiTi specimens are however insensitive to pre-deformation strain. We suggest that these discrepancies are likely attributed to the enhanced kinetic barrier of nucleation of the forward transformation.</div></div>","PeriodicalId":423,"journal":{"name":"Scripta Materialia","volume":"263 ","pages":"Article 116693"},"PeriodicalIF":5.3,"publicationDate":"2025-04-09","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"143800375","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":2,"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 : 2025-04-07DOI: 10.1016/j.scriptamat.2025.116692
Zengmeng Lin , Baoxi Liu , Kaisheng Ming , Pingguang Xu , Fuxing Yin , Shijian Zheng
Complementary layer thickness effects on strength and plasticity in Q235 and SUS304 steels provide a novel strategy to realize high strength and high plasticity of heterogeneous Q235/SUS304 multilayered steel. In this work, the tensile deformation behaviors and fracture characteristics of vacuum hot-rolled Q235/SUS304 multilayered steel with various layer thicknesses ranging from 223 μm to 5 μm were deeply investigated. The tensile strength improved with the reduction of layer thickness, and the uniform elongation was first increased and then decreased with decreasing layer thickness, and the peak value appeared at the layer thickness of 20 μm. Interestingly, the fracture elongation forms a high plateau value within the 10∼20 μm range. Further analysis reveals that the severe strain localization in the brittle SUS304 thin layers is delayed by the ductile Q235 layers, which is mainly attributed to the different texture evolution and dislocation configuration characteristics during tensile deformation.
{"title":"Complementary layer thickness effects of Q235 and SUS304 layers of multilayered steels for improving of tensile strength and plasticity simultaneously","authors":"Zengmeng Lin , Baoxi Liu , Kaisheng Ming , Pingguang Xu , Fuxing Yin , Shijian Zheng","doi":"10.1016/j.scriptamat.2025.116692","DOIUrl":"10.1016/j.scriptamat.2025.116692","url":null,"abstract":"<div><div>Complementary layer thickness effects on strength and plasticity in Q235 and SUS304 steels provide a novel strategy to realize high strength and high plasticity of heterogeneous Q235/SUS304 multilayered steel. In this work, the tensile deformation behaviors and fracture characteristics of vacuum hot-rolled Q235/SUS304 multilayered steel with various layer thicknesses ranging from 223 μm to 5 μm were deeply investigated. The tensile strength improved with the reduction of layer thickness, and the uniform elongation was first increased and then decreased with decreasing layer thickness, and the peak value appeared at the layer thickness of 20 μm. Interestingly, the fracture elongation forms a high plateau value within the 10∼20 μm range. Further analysis reveals that the severe strain localization in the brittle SUS304 thin layers is delayed by the ductile Q235 layers, which is mainly attributed to the different texture evolution and dislocation configuration characteristics during tensile deformation.</div></div>","PeriodicalId":423,"journal":{"name":"Scripta Materialia","volume":"263 ","pages":"Article 116692"},"PeriodicalIF":5.3,"publicationDate":"2025-04-07","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"143785222","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":2,"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 : 2025-04-07DOI: 10.1016/j.scriptamat.2025.116686
Han Wang , Xiang Fei , Shijie Sun , Naicheng Sheng , Guichen Hou , Jinguo Li , Yizhou Zhou , Xiaofeng Sun
The M23C6 phase is usually precipitated in high-Cr content Ni-based polycrystalline superalloys, which has significant effects on properties of the alloys. In this work, the role of Ti on the modification of M23C6 carbides was investigated. In the alloys without Ti (6.6Al-0Ti alloy), MC carbides decomposed and M23C6 carbides precipitated during primary aging treatment. In contrast, alloy containing Ti (3.8Al-3Ti alloy), MC carbides remained stable throughout aging process and M23C6 carbides precipitated during secondary aging treatment. Furthermore, M23C6 carbides distributed along grain boundaries in 6.6Al-0Ti alloy were larger and more regular. According to first-principle calculations, the formation energy of MC carbide in 3.8Al-3Ti alloy was lower, which indicated MC carbide was more stable, resulting in limited carbon available for M23C6 carbides precipitation. Therefore, the introduction of Ti would inhibit precipitation of M23C6 carbides due to more stable MC carbides in superalloy containing Ti.
{"title":"Modification of M23C6 carbides by Ti addition in Ni-based polycrystalline superalloy","authors":"Han Wang , Xiang Fei , Shijie Sun , Naicheng Sheng , Guichen Hou , Jinguo Li , Yizhou Zhou , Xiaofeng Sun","doi":"10.1016/j.scriptamat.2025.116686","DOIUrl":"10.1016/j.scriptamat.2025.116686","url":null,"abstract":"<div><div>The M<sub>23</sub>C<sub>6</sub> phase is usually precipitated in high-Cr content Ni-based polycrystalline superalloys, which has significant effects on properties of the alloys. In this work, the role of Ti on the modification of M<sub>23</sub>C<sub>6</sub> carbides was investigated. In the alloys without Ti (6.6Al-0Ti alloy), MC carbides decomposed and M<sub>23</sub>C<sub>6</sub> carbides precipitated during primary aging treatment. In contrast, alloy containing Ti (3.8Al-3Ti alloy), MC carbides remained stable throughout aging process and M<sub>23</sub>C<sub>6</sub> carbides precipitated during secondary aging treatment. Furthermore, M<sub>23</sub>C<sub>6</sub> carbides distributed along grain boundaries in 6.6Al-0Ti alloy were larger and more regular. According to first-principle calculations, the formation energy of MC carbide in 3.8Al-3Ti alloy was lower, which indicated MC carbide was more stable, resulting in limited carbon available for M<sub>23</sub>C<sub>6</sub> carbides precipitation. Therefore, the introduction of Ti would inhibit precipitation of M<sub>23</sub>C<sub>6</sub> carbides due to more stable MC carbides in superalloy containing Ti.</div></div>","PeriodicalId":423,"journal":{"name":"Scripta Materialia","volume":"263 ","pages":"Article 116686"},"PeriodicalIF":5.3,"publicationDate":"2025-04-07","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"143785221","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":2,"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 : 2025-04-07DOI: 10.1016/j.scriptamat.2025.116687
S.S. Nene, A. Dutta, G.R. Nandeshwar, A.R. Balpande
Conventional superalloys offer excellent high-temperature strength (HTS), oxidation resistance, and good room-temperature (RT) tensile ductility, however, at the expense of either increased density or high material costs. Here, we present a lightweight (7.53 g/cc) Ni30Co30Cr15V10Fe5Al5Ti2.5Si2.5 (at. %) high entropy superalloy (Ni-HESA) that achieves a remarkable strength-ductility synergy at RT (1296 MPa, 40 %), excellent HTS (600 MPa at 800 °C), and isothermal oxidation resistance at 900 °C for 96 h exposure (parabolic oxidation coefficient ∼3.693 × 10–4 mg2cm-4s-1) in its most microstructurally complex state. This microstructural complexity in Ni-HESA arises from the presence of γ′ (L12Ni3(Si, Ti) type) precipitate, annealing twins, and grain size modality within the γ-f.c.c. matrix. These features enhance RT work hardenability through back-stress strengthening while ensuring substantial microstructural stability at elevated temperatures, thereby improving both strength and oxidation resistance. The aforementioned property profile of Ni-HESA positions it as a promising superalloy for high-temperature applications, offering enhanced fuel efficiency.
{"title":"Towards light-weighting high entropy superalloy while retaining ambient strength-ductility synergy, high temperature strength and oxidation resistance","authors":"S.S. Nene, A. Dutta, G.R. Nandeshwar, A.R. Balpande","doi":"10.1016/j.scriptamat.2025.116687","DOIUrl":"10.1016/j.scriptamat.2025.116687","url":null,"abstract":"<div><div>Conventional superalloys offer excellent high-temperature strength (HTS), oxidation resistance, and good room-temperature (RT) tensile ductility, however, at the expense of either increased density or high material costs. Here, we present a lightweight (7.53 g/cc) Ni<sub>30</sub>Co<sub>30</sub>Cr<sub>15</sub>V<sub>10</sub>Fe<sub>5</sub>Al<sub>5</sub>Ti<sub>2.5</sub>Si<sub>2.5</sub> (at. %) high entropy superalloy (Ni-HESA) that achieves a remarkable strength-ductility synergy at RT (1296 MPa, 40 %), excellent HTS (600 MPa at 800 °C), and isothermal oxidation resistance at 900 °C for 96 h exposure (parabolic oxidation coefficient ∼3.693 × 10<sup>–4</sup> mg<sup>2</sup>cm<sup>-4</sup>s<sup>-1</sup>) in its most microstructurally complex state. This microstructural complexity in Ni-HESA arises from the presence of γ′ (L1<sub>2<img></sub>Ni<sub>3</sub>(Si, Ti) type) precipitate, annealing twins, and grain size modality within the γ-f.c.c. matrix. These features enhance RT work hardenability through back-stress strengthening while ensuring substantial microstructural stability at elevated temperatures, thereby improving both strength and oxidation resistance. The aforementioned property profile of Ni-HESA positions it as a promising superalloy for high-temperature applications, offering enhanced fuel efficiency.</div></div>","PeriodicalId":423,"journal":{"name":"Scripta Materialia","volume":"263 ","pages":"Article 116687"},"PeriodicalIF":5.3,"publicationDate":"2025-04-07","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"143785223","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":2,"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 : 2025-04-04DOI: 10.1016/j.scriptamat.2025.116685
Shangshu Wu , Yi Liu , Junbo Ding , Jiaxing Song , Quanwei Tian , Si Lan , Meng Wang , Yingqi Fan , Rong Huang , Shanyue Liang , Jin Tian , Zhen Chen , Ruoyu Liu , Jialin Chen , Xingwang Cheng
Alloys with high strength and competent ductility are highly demanded for modern engineering applications but difficult to design and prepare. In this study, we design a Co-rich Co35Cr20Fe20Ni20Al2Ti3 HEA that exhibits excellent tensile properties, facilitated by unique microstructures, namely pre-twins and nanolamellar L12 precipitates, which are introduced via multistep deformation and annealing. Comprehensive microstructural characterization, carried out through electron back scattering diffraction and transmission electron microscopy, demonstrates that interactions among lattice dislocations, pre-twins and nanolamellar L12 precipitates raise the dislocations slip stress barrier and dislocation storage rate, gifting the HEA a high strength and ductility mechanical properties. The present study provides insight into the fabrication of ultra-strong and ductile HEAs by tuning the substructures.
{"title":"Obtaining a strong and ductile Co-rich high entropy alloy via synergistic effect of pre-twinning and nanolamellar L12 precipitates","authors":"Shangshu Wu , Yi Liu , Junbo Ding , Jiaxing Song , Quanwei Tian , Si Lan , Meng Wang , Yingqi Fan , Rong Huang , Shanyue Liang , Jin Tian , Zhen Chen , Ruoyu Liu , Jialin Chen , Xingwang Cheng","doi":"10.1016/j.scriptamat.2025.116685","DOIUrl":"10.1016/j.scriptamat.2025.116685","url":null,"abstract":"<div><div>Alloys with high strength and competent ductility are highly demanded for modern engineering applications but difficult to design and prepare. In this study, we design a Co-rich Co<sub>35</sub>Cr<sub>20</sub>Fe<sub>20</sub>Ni<sub>20</sub>Al<sub>2</sub>Ti<sub>3</sub> HEA that exhibits excellent tensile properties, facilitated by unique microstructures, namely pre-twins and nanolamellar L1<sub>2</sub> precipitates, which are introduced via multistep deformation and annealing. Comprehensive microstructural characterization, carried out through electron back scattering diffraction and transmission electron microscopy, demonstrates that interactions among lattice dislocations, pre-twins and nanolamellar L1<sub>2</sub> precipitates raise the dislocations slip stress barrier and dislocation storage rate, gifting the HEA a high strength and ductility mechanical properties. The present study provides insight into the fabrication of ultra-strong and ductile HEAs by tuning the substructures.</div></div>","PeriodicalId":423,"journal":{"name":"Scripta Materialia","volume":"263 ","pages":"Article 116685"},"PeriodicalIF":5.3,"publicationDate":"2025-04-04","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"143767840","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":2,"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 : 2025-04-03DOI: 10.1016/j.scriptamat.2025.116684
Mingyu Gong , Haijian Chu , Yong Mao , Jian Wang
Intermetallic precipitates are strategically introduced to strengthen metallic alloys. Severe plastic deformation associated with dislocations interactions often causes destabilization of intermetallic precipitates in metallic alloys. Based on molecular dynamics simulations of non-coplanar dislocation dipole interactions, we reported anomalous reactions of forming vacancy-type defects (vacancy cluster, void and prismatic dislocation loop) in typical intermetallic compounds (i.e. L12-Ni3Al, L10-TiAl, and B2-NiAl). Compared with the reactions in metals, the formation of vacancy-type defects is attributed to the larger core energies and interaction forces of a dislocation dipole and the lowering formation energies of vacancies within the dislocation cores in intermetallic compounds. These vacancy-type defects are immobile and pin the motion of dislocations, locally disorder the crystal, and facilitate self-diffusion of alloying elements, consequently deteriorating structural stability of intermetallic precipitates.
{"title":"Anomalous interactions of non-coplanar dislocation dipole in intermetallic compounds","authors":"Mingyu Gong , Haijian Chu , Yong Mao , Jian Wang","doi":"10.1016/j.scriptamat.2025.116684","DOIUrl":"10.1016/j.scriptamat.2025.116684","url":null,"abstract":"<div><div>Intermetallic precipitates are strategically introduced to strengthen metallic alloys. Severe plastic deformation associated with dislocations interactions often causes destabilization of intermetallic precipitates in metallic alloys. Based on molecular dynamics simulations of non-coplanar dislocation dipole interactions, we reported anomalous reactions of forming vacancy-type defects (vacancy cluster, void and prismatic dislocation loop) in typical intermetallic compounds (i.e. L1<sub>2</sub>-Ni<sub>3</sub>Al, L1<sub>0</sub>-TiAl, and B2-NiAl). Compared with the reactions in metals, the formation of vacancy-type defects is attributed to the larger core energies and interaction forces of a dislocation dipole and the lowering formation energies of vacancies within the dislocation cores in intermetallic compounds. These vacancy-type defects are immobile and pin the motion of dislocations, locally disorder the crystal, and facilitate self-diffusion of alloying elements, consequently deteriorating structural stability of intermetallic precipitates.</div></div>","PeriodicalId":423,"journal":{"name":"Scripta Materialia","volume":"263 ","pages":"Article 116684"},"PeriodicalIF":5.3,"publicationDate":"2025-04-03","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"143761326","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":2,"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 : 2025-04-03DOI: 10.1016/j.scriptamat.2025.116683
Jinke Han , Ge Zhou , Haoyu Zhang , Siqian Zhang , Mingjiu Zhao , Chenyang Lu , Zhengxiong Su , Yuhan Peng , Xin Che , Lijia Chen , Peter K. Liaw
Metastable dual-phase HEAs with fine-grain structure exhibit the B-TRIP effect during room-temperature tensile testing, with a maximum elongation at a break of 77 %. This paper adopts three strategies: SFE calculation, fine grain structure preparation, and phase ratio control, to design and prepare a new Fe49Mn33.2Cr9.6Co8.2 HEA that can achieve multiple interconversion conditions between FCC and HCP phases thermodynamically in order to fully leverage the synergistic effect of SFE phase composition and stability grain size on room-temperature ductility. The results showed that the alloy did not fracture after undergoing the B-TRIP effect but underwent FCC phase to HCP phase transformation again at a deformation of 70 % until the fracture process. At the time of fracture, the HCP phase content remained at around 40 %, and the alloy exhibited a particular five-stage strain-hardening behavior. Under the Triple-TRIP effect, the highest post-fracture elongation at room temperature reported so far was obtained, which was 91 %.
{"title":"A strategy for Triple-TRIP-induced ultra-high room-temperature ductility of high-entropy alloys","authors":"Jinke Han , Ge Zhou , Haoyu Zhang , Siqian Zhang , Mingjiu Zhao , Chenyang Lu , Zhengxiong Su , Yuhan Peng , Xin Che , Lijia Chen , Peter K. Liaw","doi":"10.1016/j.scriptamat.2025.116683","DOIUrl":"10.1016/j.scriptamat.2025.116683","url":null,"abstract":"<div><div>Metastable dual-phase HEAs with fine-grain structure exhibit the B-TRIP effect during room-temperature tensile testing, with a maximum elongation at a break of 77 %. This paper adopts three strategies: SFE calculation, fine grain structure preparation, and phase ratio control, to design and prepare a new Fe<sub>49</sub>Mn<sub>33.2</sub>Cr<sub>9.6</sub>Co<sub>8.2</sub> HEA that can achieve multiple interconversion conditions between FCC and HCP phases thermodynamically in order to fully leverage the synergistic effect of SFE phase composition and stability grain size on room-temperature ductility. The results showed that the alloy did not fracture after undergoing the B-TRIP effect but underwent FCC phase to HCP phase transformation again at a deformation of 70 % until the fracture process. At the time of fracture, the HCP phase content remained at around 40 %, and the alloy exhibited a particular five-stage strain-hardening behavior. Under the Triple-TRIP effect, the highest post-fracture elongation at room temperature reported so far was obtained, which was 91 %.</div></div>","PeriodicalId":423,"journal":{"name":"Scripta Materialia","volume":"263 ","pages":"Article 116683"},"PeriodicalIF":5.3,"publicationDate":"2025-04-03","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"143761323","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":2,"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 : 2025-04-03DOI: 10.1016/j.scriptamat.2025.116680
Kohta Kasai, Toya Itano, Susumu Minami, Takahiro Shimada
Recent discoveries of polar skyrmions have garnered significant attention due to their unique properties beyond conventional polarization orders, requiring a comprehensive understanding of the stabilization mechanisms and topological transitions between other phases. However, the fundamental and critical question “How do polar skyrmions form?” still remains elusive. We provide the first detailed demonstration of the formation process of polar skyrmions and strain-dependent topological phase transitions in PbTiO3/SrTiO3 superlattices under various in-plane strain conditions. Our phase-field simulation revealed that in-plane strain stabilizes out-of-plane polarization, influencing the velocity of domain growth and the resulting topological phases. Under low in-plane strain, numerous polarization domains grow rapidly and connect to each other, forming a labyrinth phase. Conversely, under high in-plane strain, domains grow slowly and individually, forming a skyrmion bubble phase. Our results provide profound insights into the formation mechanism of skyrmions and the design principles of next-generation functional devices.
{"title":"Microscopic formation process of polar skyrmions and strain-dependent topological phase transitions in PbTiO3/SrTiO3 superlattices","authors":"Kohta Kasai, Toya Itano, Susumu Minami, Takahiro Shimada","doi":"10.1016/j.scriptamat.2025.116680","DOIUrl":"10.1016/j.scriptamat.2025.116680","url":null,"abstract":"<div><div>Recent discoveries of polar skyrmions have garnered significant attention due to their unique properties beyond conventional polarization orders, requiring a comprehensive understanding of the stabilization mechanisms and topological transitions between other phases. However, the fundamental and critical question “How do polar skyrmions form?” still remains elusive. We provide the first detailed demonstration of the formation process of polar skyrmions and strain-dependent topological phase transitions in PbTiO<sub>3</sub>/SrTiO<sub>3</sub> superlattices under various in-plane strain conditions. Our phase-field simulation revealed that in-plane strain stabilizes out-of-plane polarization, influencing the velocity of domain growth and the resulting topological phases. Under low in-plane strain, numerous polarization domains grow rapidly and connect to each other, forming a labyrinth phase. Conversely, under high in-plane strain, domains grow slowly and individually, forming a skyrmion bubble phase. Our results provide profound insights into the formation mechanism of skyrmions and the design principles of next-generation functional devices.</div></div>","PeriodicalId":423,"journal":{"name":"Scripta Materialia","volume":"263 ","pages":"Article 116680"},"PeriodicalIF":5.3,"publicationDate":"2025-04-03","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"143761325","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":2,"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 : 2025-04-01DOI: 10.1016/j.scriptamat.2025.116671
Y.Y. Hu , X.T. Wang , Y.J. Ma , J.L. Chen , X.J. Zhao , J. Cheng , T.R. Xu , W.L. Zhao , X.Y. Song , S. Wu , Z.H. Cao
Atomic size misfit is one of the origins of solid-solution strengthening in alloys. In this study, we reported a strong solid-solution strengthening via tuning the atomic size misfit in the single-phase body-centered cubic TiZrVNb-based refractory high-entropy alloys (HEAs). The results suggest that the yield strength of the cast samples significantly increased from 680 MPa to 998 MPa with increasing the largest atomic radius Zr content. Among them, the Ti35Zr15V25Nb25 HEA exhibits the best combination of high yield strength of 918 MPa and ductility of 16 %. The solid-solution strengthening causes the 318 MPa strength increment as the atomic size misfit increases from 3.43 % to 4.95 %, where the contribution of atomic size misfit reaches 77 %. Strong solid-solution strengthening mainly originates from the enhanced lattice distortion acting as a strong barrier to dislocation motion, where the resultant high-density dislocations and the activated multiple slip systems lead to the outstanding strain-hardening capacity of the HEAs.
{"title":"Strong solid solution strengthening caused by severe lattice distortion in body-centered cubic refractory high-entropy alloys","authors":"Y.Y. Hu , X.T. Wang , Y.J. Ma , J.L. Chen , X.J. Zhao , J. Cheng , T.R. Xu , W.L. Zhao , X.Y. Song , S. Wu , Z.H. Cao","doi":"10.1016/j.scriptamat.2025.116671","DOIUrl":"10.1016/j.scriptamat.2025.116671","url":null,"abstract":"<div><div>Atomic size misfit is one of the origins of solid-solution strengthening in alloys. In this study, we reported a strong solid-solution strengthening via tuning the atomic size misfit in the single-phase body-centered cubic TiZrVNb-based refractory high-entropy alloys (HEAs). The results suggest that the yield strength of the cast samples significantly increased from 680 MPa to 998 MPa with increasing the largest atomic radius Zr content. Among them, the Ti<sub>35</sub>Zr<sub>15</sub>V<sub>25</sub>Nb<sub>25</sub> HEA exhibits the best combination of high yield strength of 918 MPa and ductility of 16 %. The solid-solution strengthening causes the 318 MPa strength increment as the atomic size misfit increases from 3.43 % to 4.95 %, where the contribution of atomic size misfit reaches 77 %. Strong solid-solution strengthening mainly originates from the enhanced lattice distortion acting as a strong barrier to dislocation motion, where the resultant high-density dislocations and the activated multiple slip systems lead to the outstanding strain-hardening capacity of the HEAs.</div></div>","PeriodicalId":423,"journal":{"name":"Scripta Materialia","volume":"263 ","pages":"Article 116671"},"PeriodicalIF":5.3,"publicationDate":"2025-04-01","publicationTypes":"Journal Article","fieldsOfStudy":null,"isOpenAccess":false,"openAccessPdf":"","citationCount":null,"resultStr":null,"platform":"Semanticscholar","paperid":"143739100","PeriodicalName":null,"FirstCategoryId":null,"ListUrlMain":null,"RegionNum":2,"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 : 2025-03-30DOI: 10.1016/j.scriptamat.2025.116670
Jin Zhang , Zhigang Jiang , Jingchao Xu , Jipeng Duan , Haoyue Wang , Yuanhuai He , Wen Zhang , Peng Cao
Amorphous Si (a-Si) exhibits significant advantages as an anode material for lithium-ion batteries due to its excellent tolerance to intrinsic strain/stress and superior charge transfer kinetics. However, the successful implementation of a-Si requires scalable synthesis and rational design. In this study, we have successfully synthesized a self-supporting three-dimensional (3D) porous a-Si anode (3DporCu@a-Si@CNTs) using a simple process that avoids dangerous reagents or expensive equipment. The outstanding performance of the anode is attributed to its binder-free 3D porous structure, amorphous nature, and artificial surface modification. After 150 cycles at 0.1C, the 3DporCu@a-Si@CNTs anode delivers a high capacity of 2674 mAh g-1 while maintaining the 3D porous structure. Furthermore, it demonstrates a remarkable rate capability of 2281 mAh g-1 at 10C. The simplified synthesis process and the performance advantages highlight the potential of this anode in lithium-ion battery applications.
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