Adiabatic shear bands (ASBs), a form of dynamic plastic instability critical in ballistic penetration and armor perforation, are highly desirable in tungsten heavy alloys yet often hindered by their low susceptibility, leading to mushroom-headed deformation and reduced penetration performance. Here, we developed a series of novel W-containing high-entropy alloys (HEAs) with superior strength-plasticity synergy across a wide strain rates and high susceptibility to ASBs. These alloys exhibit a multi-phase microstructure consisting of a BCC and FCC matrix with coherent L12-γ', D022-γ" nanoparticles, and µ phase precipitates within the FCC phase. Under quasi-static conditions, this is evidenced by a high yield strength (σYS = 1253–1325 MPa) coupled with excellent plasticity (εf = 22%–48%). Remarkably, under dynamic loading, a significant strain rate hardening effect leads to a substantial increase in yield strength, reaching 1346–2338 MPa. Under dynamic loading, the FCC matrix fragments into a gradient structure composed of elongated lath-shaped and ultrafine equiaxed subgrains. Combined with dislocation rearrangement and thermal softening, dynamic recrystallization then drives microcrack propagation along the resulting ASBs. Numerical simulation and experimental results indicate that the alloy exhibits enhanced adiabatic shear susceptibility, which stems primarily from phase-mediated local softening combined with reduced thermal conductivity. These findings provide critical insights for guiding the rational design of W-containing HEAs with multiple integrated properties.

The effect of C content (0.02, 0.05, and 0.08 wt. %) on the microstructure, thermal stability, and mechanical properties of a high-strength Ni-Co-base wrought superalloy (Ni-38.0Co-2.7Al-3.3Ti-0.5Nb-0.9Ta-8.3Cr-2.9Mo-5.5W-0.02B-0.03Zr, wt. %) was systematically investigated. Raising the C level from 0.02 to 0.08 wt. % promotes the formation of blocky MC carbides along grain boundaries (GBs), which effectively refine the grain from 75 ± 16 μm to 21 ± 9 μm. All alloys retain a high volume fraction (∼50 %) of uniformly distributed γ′ nanoprecipitates and exhibit a γ/γ′ coherent microstructure with exceptional thermal stability during prolonged aging at 1123 K, as reflected by an ultralow coarsening rate constant (K = 0.44 ∼ 0.48 nm3/s). At 1073 K, the 0.02C alloy fails before yielding (El ∼ 0 %), whereas the 0.05C and 0.08C alloys show progressively increasing ductility (El = 1.1 ± 0.2 % and 3.0 ± 0.5 %, respectively) without sacrificing yield strength (σYS = 860 ∼ 871 MPa). This comparison identifies 0.05 wt %. C as a critical threshold for suppressing intermediate-temperature embrittlement. The improvement is attributed to the higher density of thermally stable MC carbides at GBs, which reinforce GBs against crack propagation. Moreover, the underlying strengthening mechanisms are further discussed. This study provides a quantitative framework for optimizing GB properties and matrix stability through precise C control in high-strength wrought superalloys.

Body-centered-cubic (BCC)-based multi-principal element alloys (MPEAs) are considered promising materials due to their excellent mechanical properties, particularly at elevated temperatures. However, their limited processability and high melting points impose significant challenges for the fabrication of load-bearing components by conventional casting. This work demonstrates the successful development of a novel BCC-based MPEA of Al2Ti4Zr4Nb3Ta3 through laser directed energy deposition (LDED). The additive manufactured cylindrical components exhibit excellent formability without cracks and distortion. The LDED processing promotes the in-situ microstructural optimization of the alloy, forming a homogeneous coherent BCC/B2 microstructure with cuboidal BCC nanoparticles precipitated in the B2 matrix, and achieving ultra-high yield strength of 2013 MPa at room temperature. The excellent strength is primarily attributed to the precipitation strengthening of cuboidal BCC nanoparticles and solid solution strengthening of alloying elements. Moreover, the LDED alloy exhibits a yield strength of 1380 MPa at 873 K and retains a yield strength of 290 MPa even at 1273 K. This work provides feasible avenue for additive manufacturing of BCC-based MPEAs, thereby facilitating their industrial applications.

To elucidate the intrinsic link between the body-centered cubic (BCC) structural stability and the deformation mechanisms of Ti-Mo alloys, first-principles (FP) calculations based on a cluster model are performed for Ti-xMo (x = 2.3, 4.7, 7.8, and 12.5 at. %) binary alloys. Structural models are constructed by embedding a cluster unit within a 4 × 4 × 4 BCC supercell. The formation energies (Ef) and binding energies (Eb) of the α and β phases indicate that BCC structural stability increases with higher Mo content, and that the Ti-12.5Mo alloy is energetically favored to form a single β phase. For the metastable Ti-4.7Mo alloy, the negative value of G(101)[101¯] indicates lattice softening, while the value of G(101)[010] = 3.9 GPa is lower than those of G(323)[13¯1] and G(110)[11¯1]. Both features facilitate the stress-induced α″ transformation. Conversely, in the stable Ti-12.5Mo alloy, G(011)[100] reaches 36 GPa, substantially exceeding G(123)[111¯], thereby suppressing α″-phase transformation and promoting dislocation slip. The present cluster model-embedded first-principles calculations demonstrate that the shear modulus serves as a valid descriptor linking BCC structural stability to deformation behavior in Ti-Mo alloys.

A novel high-strength Ni-Co-base wrought superalloy (Ni-38Co-2.7Al-3.3Ti-0.5Nb-0.9Ta-8.3Cr-2.9Mo-5.5W-0.02B-0.03Zr-0.08C, wt.%) with a high volume fraction (similar to 50%) of gamma' nanoprecipitates was developed for suppressing intermediate-temperature embrittlement (ITE). The coherent gamma/gamma' microstructure shows an exceptional thermal stability at 1123 K. The 0.08 wt.% C addition enhances the elongation from < 1 % (in C-free superalloy) to 3.5 similar to 9 % at ITs (973 similar to 1073 K) through the formation of MC carbides at grain boundaries, while achieving high yield strength (860 similar to 890 MPa). Moreover, this superalloy exhibits prominent creep resistance with the rupture lifetime of 129 h under 1073 K / 300 MPa, which is primarily governed by dislocation hindrance from stacking faults (SFs) and antiphase boundaries. It also possesses an excellent strain-hardening capacity at room-temperature due to the presence of abundant SFs and Lomer-Cottrell locks. This work proposes a novel strategy to overcome the ITE in high-strength superalloys for high-temperature applications.

Localized nano-scale phase transitions at line or planar faults inside the L12 - gamma ' phase have a substantial influence on the creep behaviors of superalloys. In this study, we observe a similar, yet micron-scale, FCC- gamma phase transition phenomenon at the grain boundaries (GBs) of a Ni3 Al-based alloy under intermediate temperature creep conditions. Both micro-/sub-structure observations and calculations reveal that the accumulation of superdislocations with Fe, Cr-rich disordered clusters provides necessary composition, structure, and energy conditions for the nucleation and growth of these intergranular gamma phases. This gamma transition consumes massive superdislocations, absorbing a quantity of defect energies, increasing the energy barrier for creep cavity nucleation, and providing extra gamma / gamma ' interfaces, thus significantly reducing the GB cracking tendency. The unveiled mechanisms could inspire the compositional design and GB engineering of similar alloys with intergranular superlattice structures. (c) 2026 Published by Elsevier Ltd on behalf of The editorial office of Journal of Materials Science & Technology.

Re-entrant structures are fundamental to achieving robust liquid repellency, especially for low-surface-tension liquids. However, existing fabrication techniques often face a trade-off among mechanical durability, substrate geometry compatibility, large-area processing, and rapid production. Metals, with their inherent robustness, offer a promising substrate, but direct and efficient machining of metallic re-entrant structures remains a significant challenge. Here, we present a one-step mechanical cutting strategy, termed confined shear-induced structure discretization (CSSD), to directly fabricate high-density re-entrant architectures on planar and curved metallic surfaces. By designing a cave-trapezoid composite tool, we achieve a controlled transition from continuous ridges to discrete re-entrant units during ultra-precision diamond turning. The resulting metallic surfaces sustain a super-repellent Cassie–Baxter state for a broad range of liquids, exhibiting a water contact angle of 161.7 ± 2.2°, indicating non-wetting behavior. Notably, this approach enables rapid, large-area manufacturing, with a material removal rate of 1.068 mm3 s−1 over areas up to 1.5 × 104 mm2. The re-entrant textures retain sufficient structural features after 1000 abrasion cycles to recover superhydrophobicity. This geometry-guided strategy reveals a mechanism for the scalable fabrication of discrete microstructures and offers useful guidance for extending the approach to other machining modalities. Researchers fabricate re-entrant microstructures on metals through a confined shear-induced structure discretization (CSSD) mechanism using a cave-trapezoid cutting tool, resulting in durable, liquid-repellent surfaces.

BCC-based high/medium-entropy alloys (H/MEAs) possess prominent high-temperature strength, low thermal expansion, and high thermal conductivity, making them a promising candidate for elevated-temperature applications. However, their limited deformability at room temperature (RT) hinders industrial implementation. Here, we report a novel cost-effective (FeCrNi)85(AlTi)15 MEA featuring a multiple-phase microstructure with BCC/L21, L21/BCC, and FCC/L12 coherent interfaces in the as-cast state. The strategic incorporation of L12strengthened FCC matrix phase within brittle BCC and L21 matrices can activate hetero-deformation-induced (HDI) hardening effect, achieving an attractive compressive plasticity of 35 % at room temperature. The wellcontrolled L21-Ni2AlTi, BCC, and L12-Ni3(Al, Ti) nanoparticles coherently precipitate in BCC, L21, and FCC matrix phases, respectively, resulting in a super-high yield strength of 1850 MPa, outperforming existing B2/L21strengthened BCC H/MEAs. The triple-coherent interface system demonstrates exceptional thermal stability, maintaining yield strengths of 850 MPa at 700 degrees C and 395 MPa at 800 degrees C. Moreover, this alloy exhibits a dynamic phase transformation-induced hardening effect during long-term aging due to the precipitation of sigma-FeCr phase. These results provide a new strategy for overcoming the drawback of inadequate deformability in BCC-based alloys and developing novel advanced as-cast materials for high-temperature applications under compressive loading.

The corrosion-resistance in lead-bismuth eutectic (LBE) coolant at elevated temperatures of traditional reducedactivation ferritic/martensitic (RAFM) steels does not meet the requirements for the application of fuel claddings. Here, we designed a novel Al-containing high-Si reduced-activation ferritic/martensitic (RAFM) alloy (Fe-0.22C10.5Cr-1.3W-0.26V-0.13Ta-1Si-0.2Al-0.4Mn) via the CALPHAD (Calculation of Phase Diagrams)-assisted clusterformula approach for the synergistic enhancement of creep and corrosion resistances. The microstructure of this alloy exhibits a fully martensitic matrix dispersed with short rod-shaped M23C6 (-133 nm) and near-spherical MC (-64 nm) carbides. This alloy demonstrates excellent thermal properties, endowing it high yield strength (585 MPa at room-temperature and 229 MPa at 923 K) and superior creep-rupture lifetime of 135 h under 923 K/ 120 MPa. Moreover, the alloy exhibits an extremely-thin oxide scales (-3 mu m) after being soaked in LBE liquid at 773 K/1000 h, which is much better than those of existing F/M steels. This is attributed to the collaborative addition of Cr, Al, and Si. The underlying mechanisms were further elucidated. The present work offers a promising strategy for developing novel RAFM alloys for nuclear applications.

Developing additively manufactured α + β Ti alloys for service at 600 °C remains a challenge due to the strength-ductility trade-off associated with coarse parent β grains and fully lamellar microstructures. Here we report an α + β Ti-6.5Al-2V-2Mo-1Nb-14Zr (wt%) alloy previously designed by the cluster formula approach. Its high Zr content enhances constitutional undercooling, promoting the formation of equiaxed parent β grains during 2 kW laser additive manufacturing. Subsequent solution treatment and aging yield a bi-lamellar microstructure comprising coarse primary α laths (1.37 μm in width) and fine secondary α precipitates (0.13 μm in width). This tailored microstructure delivers unprecedented tensile properties at both room temperature and 600 °C: ultimate tensile strength of 1249 MPa with 9.3% elongation at room temperature, and ∼769 MPa with 28.2% elongation at 600 °C, surpassing conventional high-temperature Ti alloys. The enhanced ductility originates from activated pyramidal slip in the primary α laths, while the excellent strength is attributed to the synergistic contributions of grain boundary strengthening, solid-solution strengthening, and aging-induced α₂ (Ti3Al) precipitation. This work demonstrates an effective strategy for designing advanced additively manufactured Ti alloys through simultaneous control of parent β grains and α phase.

Multi-component carbide ceramics have garnered significant attention as ultra-high-temperature structural materials due to their exceptionally high melting points and excellent mechanical properties. In this work, we systematically investigate the synergistic effects of C vacancies and Ti alloying on the thermodynamic stability and elastic behavior of (Zr, Ti)C-x carbides using first-principles calculations. Specific cluster structural models of [C-M-6](C,square)(5) (M = Zr/Ti, square = vacancy) were constructed by considering the local chemical short-range orders of elemental distribution and the ordering of vacancies on C sublattice, which were then employed as inputs for first-principles calculations. The results reveal that the introduction of C vacancies decreases the free energy at high temperatures and enhances the thermodynamic stability, whereas Ti substitution for Zr tends to reduce stability. Notably, the ternary carbide Zr5Ti1C5 ([C-Zr5Ti1](C,square)(5)) with an equimolar ratio of Ti-to-vacancy exhibits superior high-temperature thermodynamic stability. Analysis of entropy contributions indicates that both vacancies and Ti addition primarily alter the free energy by modifying the lattice vibration modes, an effect dominated by the vibrational entropy. These two types of defects weaken the M-C bond strength, resulting in reduced binding energy and Young's modulus. Furthermore, this synergistic effect considerably lowers the critical temperature required to stabilize the single-phase solid solution structure in multi-component carbides, which is attributed to a decrease in mixing enthalpy and an increase in configurational entropy caused by vacancies. The cluster-model-embedded first-principles approach offers valuable insight for designing high-performance carbides in complex ceramic systems.

This study investigates the influence of manganese (Mn) content on the dynamic recrystallization (DRX) behavior, precipitation evolution, and mechanical properties of a hot-extruded Mg-9.5Gd-3Y-1Zn alloy. A series of alloys with Mn additions of 0, 0.3, 0.5, and 0.7 wt. % were designed for comparative analysis. The results demonstrate that Mn addition effectively refines grain size after homogenization. During hot extrusion, the addition of Mn promotes the dynamic precipitation of long-period stacking ordered (LPSO) phases, which in turn stimulates the formation of kink bands (KBs) to accommodate plastic strain. These KBs hinder the dislocation movement, facilitating the continuous DRX process and leading to a significantly increased volume fraction of DRXed grains. Concurrently, alpha-Mn particles effectively pin grain boundary migration, resulting in finer DRXed grains. The segregation of Mn atoms along the KB structures promotes the static precipitation of gamma" and cluster-arranged layers during subsequent aging treatment, providing an additional strengthening increment. The Mg-9.5Gd-3Y-1Zn alloy with 0.7 wt. % Mn exhibits an excellent ultimate tensile strength of 514 MPa following hot extrusion and peak-aging treatment. This outstanding strength is attributed to the combined contributions of grain refinement, dynamic precipitation of LPSO phases during extrusion, static precipitation of beta' phases during aging, and the strengthening effect of KBs with solute atom segregation. (c) 2026 Published by Elsevier Ltd on behalf of The editorial office of Journal of Materials Science & Technology.

Dual-phase Ti alloys, recognized for excellent mechanical properties and processability, cannot withstand service temperatures above 500 degrees C. In this paper, a dual-phase alloy Ti-6.5Al-2V-2Mo-1Nb-14Zr-0.1Si (DT600) is developed, whose high-temperature performance is comparable to those of prevailing near-alpha 600 degrees C Ti alloys. The composition design follows the composition formula {Al2Ti14}(12)+beta-{Al1V2Ti15}(5) of popular dual-phase Ti-6Al-4V, via enhanced Al, partial replacement of V by stronger beta stabilizers Mo and Nb, and additional silicide formers Zr and Si, into alpha-{(Al,Si)(2)(Ti,Zr)(14)}(12)+beta-{Al-2(Mo,Nb,V)(2)(Ti,Zr)(14)}(5). 80 g ingots of DT600 and Ti-6Al-4V were prepared by arc melting and copper mold casting, followed by annealing at 700 degrees C for 2 h. Due to fine silicide precipitation (similar to 50 nm) and basket-weave alpha lamellar (similar to 260 nm) microstructure, its tensile properties at room temperature (R-m = 1321 MPa, R-p0.2 = 1242 MPa, and A = 5.2%) are superior to the reference Ti-6Al-4 V alloy (1004 MPa, 855 MPa, and 6.1%). Most importantly, this alloy achieves an unprecedented level of 600 degrees C tensile performance (739 MPa, 623 MPa, 46.2%), approaching the strength level of prevailing high-temperature near-alpha IMI834 grade, with much enhanced plasticity. The microstructure mechanism behind such superb performance is fully discussed. The development of DT600 demonstrates the usefulness of the cluster formula approach in accurate composition design of high-temperature Ti alloys.

Austenitic stainless steels (ASSs) with super-high corrosion resistance are critical for applications in extreme environments. However, the limited solubility of Cr and Mo in traditional ASSs often leads to the precipitation of unfavorable sigma-FeCr phase at elevated temperatures (ET). A new alloy design strategy for improved structural stability and corrosion resistance should therefore be explored. In this study, we systematically investigated the structural stability and precipitation behavior of a supersaturated FeCrNi super stainless medium-entropy alloy (SSMA) aged at 700 degrees C and 800 degrees C, as well as its influence on the mechanical and corrosion properties. It is found that the FeCrNi SSMA exhibits exceptionally high microstructural stability and well-suppressed precipitate coarsening at elevated temperatures, owing to the high mixing entropy and low mixing enthalpy. In samples aged at 700 degrees C and 800 degrees C for up to 100 h, brittle intermetallic compounds commonly found in high-Cr/Mo ASSs cannot be detected, and only a small number of alpha-Cr precipitates can be identified along grain boundaries. During annealing, the alpha-Cr grains can remain a fine average size of smaller than 2 mu m, and a low volume fraction of less than 1.5 %. The alloy exhibits excellent comprehensive properties after long-term aging. Its corrosion resistance is much better than that of conventional 304 ASS and typical FCC-based high-entropy alloys, and is parallel with that of high-Cr/Mo SASSs. The yield strength of our alloy is 180 MPa at 700 degrees C and 135 MPa at 800 degrees C, and it can maintain excellent ductility due to the dislocation slip, twinning, and dynamic precipitation strengthening of the alpha-Cr phase during deformation at ETs. The aging treatment at ETs does not degrade the ductility of recrystallized samples measured at room temperature (RT). These findings indicate that the FeCrNi SSMA is a promising candidate for application in elevated-temperature corrosive environments.

Conventional Ti alloys strictly limit the content of Al and Si to avoid ductility loss caused by the precipitation of intermediate phases, which in turn restricts the further enhancement of their ambient and high-temperature properties. This study proposes an innovative strategy based on precise composition design via the cluster formula approach, coupled with subsequent heat treatment to control intermediate phases. Starting from the cluster formula of Ti-6Al-4V, α-{Al2Ti14}12+β-{Al1V2Ti14}5, the composition was modified by increasing Al to promote α₂-Ti₃Al precipitation, adding Zr and trace Si to form silicides, and substituting V with a refractory-element (Mo₀.₅Nb₀.₅Ta₀.₅W₀.₅) to refine α lamellae. The prepared alloy, after solution treatment at 840 °C for 1 h and aging at 600 °C for 4 h, exhibits a multimodal microstructure consisting of equiaxed α (αe), lamellar α (αl), and secondary α (αs). A hierarchically distributed, multi-scale precipitate structure is observed: sub-micron silicides and nano-sized Ti3Al are preferentially located in the primary α phase, while secondary nano-silicides are uniformly dispersed within the βt matrix. The alloy achieves an ultra-high strength level at ambient temperature (Rm = 1496 MPa, Rp0.2 = 1446 MPa, A = 7.8 %) and retains a tensile strength of 695 MPa at 600 °C, comparable to that of typical near-α high-temperature Ti alloys such as IMI 834. This study successfully realizes the controlled precipitation of strengthening phases and microstructural refinement through cluster-formula based design, providing a novel pathway for developing Ti alloys with outstanding performance at both ambient and high temperatures.

Achieving high strength and ductility simultaneously in additive-manufactured body-centered-cubic (BCC) multi-principal-element alloys (MPEAs) remains a significant challenge, while utilizing the local chemical order is considered a possible pathway. Here, we report a novel Al2Ti7Zr2Nb5 MPEA fabricated by laser powder bed fusion (LPBF), which exhibits chemical medium-range order (CMRO) clusters embedded within a BCC matrix. Mechanical testing demonstrates that the CMRO enables a high strength-ductility synergy in the alloy (yield strength ∼ 1023 MPa, tensile ductility ∼ 32%, and fracture toughness ∼ 158 MPa·m1/2). Phase-field simulations indicate that CMRO formation is thermodynamically driven by strong interaction among Al, Ti, and Zr elements. Further analysis reveals that dislocations shear through CMRO, which decreases the glide resistance for the subsequent dislocations and facilitates the following dislocations to slip through the CMRO and form dislocation channels. The associated disruption of chemical ordering introduces lattice distortions that facilitate elastic strain accumulation and dislocation debris, thereby activating dynamic hardening and secondary planar slip and promoting the plastic deformation zone into the bulk specimen. Furthermore, the frequent intersection of dislocation channels sustains a sufficient strain-hardening rate to large strains. This work demonstrates CMRO as a promising pathway for developing high-performance MPEAs.

To achieve high strength in Ni−Co-based wrought superalloys, cold-rolling was introduced into the solution and aging treatments. The alloys were characterized and tested using EBSD, SEM, TEM, and tensile tester to analyze their microstructure and mechanical properties at different temperatures, revealing their strengthening and deformation mechanisms. Results indicated that after solution, cold-rolling, and double aging, the alloy contained high-density dislocations, stacking faults, Lomer−Cottrell locks, and nanotwins. The yield strengths of the alloy at room temperature, 923, and 1023 K were 1855, 1406, and 1086 MPa, respectively, which were significantly higher than those of typical Ni-based wrought superalloys. This enhancement was primarily attributed to the dislocations and nanotwins. Additionally, during the cold-rolling process, plastic deformation mainly occurred through dislocation slip. With the temperature increasing to 923 and 1023 K, the main deformation mechanisms of the alloy transformed to stacking faults and nanotwins, respectively.

Tin (Sn) metal usually exists in the tetragonal beta-Sn phase at room temperature. However, beta-Sn electrode often suffers from poor cycling stability due to large volume changes during cycles. Although beta-Sn phase tends to transform to cubic alpha-Sn phase at subzero temperatures, its electrochemical behavior toward Li storage has not yet been clearly reported because alpha-Sn is hard to obtain and keep stable at room temperature. In this work, we successfully obtained different amounts of alpha-Sn phase in the electrodes at room temperature just by adopting a strategy of slow-lithiation followed by fast-delithiation for pure beta-Sn. It is proposed that the internal stress and nucleating agent during fast delithiation process facilitates the transformation of beta-Sn to alpha-Sn. With the appearance of alpha-Sn, the cycling stability and high-rate capability of pure Sn electrodes can be significantly improved at both 30 degrees C and -30 degrees C. At -30 degrees C, the alpha-Sn electrode maintains stable capacities of 561 mAhg-1 at 0.5 Ag-1 and 429 mAhg-1 at 1 Ag-1 respectively, much superior to the typical commercial electrode materials. This study is the first to report the electrochemical behaviors of alpha-Sn at low temperatures, opening avenues for innovative Sn-based electrodes with promising prospects for Li-ion batteries in wide-temperature applications.

A novel strategy of introducing heterogeneous particles to promote dynamic precipitation is proposed for designing Mg-Bi alloys with high strength and excellent ductility. Through in-situ formation and extrusion, uniformly distributed trace Mg2Si particles are successfully obtained in the Mg-5Bi-3Al-0.4Si alloy. This significantly improves precipitation characteristics of nano Mg3Bi2 phases, as evidenced by reduced size and increased number density. Consequently, the Mg-5Bi-3Al-0.4Si alloy exhibits an increase in yield strength of 42 MPa, up to 371 MPa. Remarkably, introducing trace particles does not damage ductility, primarily due to the activation of non-basal slip and suppressed intergranular fracture tendency.

A novel Al 1.5 Ti 6.5 Zr 2 Nb 3 Ta 2 Mo 0.5 Cr 0.5 multiprincipal element alloy (MPEA) with a coherent BCC/B2 microstructure containing cuboidal BCC precipitates was designed. The microstructural evolution and corresponding mechanical properties under different heat‐treatment conditions were systematically investigated. After aging at 873 K, a coherent BCC/B2 microstructure is formed, exhibiting an excellent combination of high yield strength (~1200 MPa) and good compressive plasticity (~50%). This good mechanical performance is attributed to the cooperative deformation of kink bands and the BCC/B2 microstructure, where dislocation shearing of ordered B2 phase and the associated structure formation provide effective strengthening while maintaining plastic deformability. With increasing aging temperature to 973–1073 K, the B2 phase becomes thermodynamically unstable, leading to the precipitation of hexagonal Al 3 Zr 5 phases and subsequently (Al, Cr) 2 Zr Laves phases, accompanied by a degradation in both strength and ductility. High‐temperature compression tests reveal that the 873 K‐aged alloy retains a relatively high strength (~912 MPa) at 873 K, whereas a pronounced softening occurs at higher temperatures due to the transformation into a single BCC solid solution driven by enhanced elemental solubility. This work highlights the critical role of coherent BCC/B2 microstructures in governing both strengthening and deformation mechanisms in MPEAs.