The key to achieving synergistic optimization of the strength and electromagnetic interference shielding effectiveness (EMI SE) of magnesium (Mg) alloys depends on the precise control of the microstructure. However, the challenge remains how to design the morphology and spatial distribution of the second phase to simultaneously achieve effective enhancement of strength and multiple dissipation of electromagnetic waves (EMWs). This study prepared as-extruded and extruded-aged Mg-Gd-Zn-Zr alloys through casting, homogenization, hot extrusion, and aging. The extruded-aged Mg-13.1Gd-1.2Zn-0.6Zr (wt.%, VZ131K-EA) alloy achieves an ultimate tensile strength (UTS) of 372 MPa with EMI SE as high as 105.8 dB at 3000 MHz. The UTS and EMI SE of the VZ131K-EA alloy are significantly superior to those of previously reported Mg-Li, Mg-Zn, and other Mg-rare earth (RE) alloys, achieving a synergy between excellent strength and ultra-high EMI SE. The substantial presence of micron-sized blocky W phases, lamellar long-period stacking ordered (LPSO) phases, and dense nanoscale precipitates (β’ phase) in the VZ131K-EA alloy efficiently enhances the strength of the alloy. These second phases not only cause reflection and attenuation of EMWs due to impedance mismatch between themselves and the Mg matrix, but also, the multi-layered distribution of the W phase, along with the countless cage-like structures formed by lamellar LPSO and the β’ phase, can further enhance the multiple reflections and dissipation of EMWs within the alloy, thereby increasing absorption loss (SEA) and effectively preventing significant attenuation of EMI SE in the medium-low frequency range. Meanwhile, the high electrical conductivity and grain boundary density of the VZ131K-EA alloy improve reflection loss (SER) and SEA respectively, which together contribute to the ultra-high EMI SE.

Mg-based composites have been considered as promising structural materials for aerospace and automotive applications owing to their high specific strength and stiffness. However, their low room-temperature ductility and absolute strength have limited their wide application. To address the strength-ductility paradox, this study proposes an approach involving the in situ formation of fine, dispersed high-entropy phase (HEP) particles-Mg24(Y0.25Dy0.25Ho0.25Er0.25)5 (labeled as Mg24(4RE0.25)5), within the Mg matrix. The composition, morphology, distribution, and crystallographic orientation relationship between the HEP and the Mg matrix were investigated. The results demonstrate successful synthesis of the HEP, which exhibits obvious lattice distortion compared with the Mg24Y5 phase. In the as-cast state, the HEP is uniformly distributed in a network-like morphology throughout the matrix, transforming into dispersed particles after extrusion. Crucially, some in situ formed HEP particles exhibit coherent relationships with the Mg matrix. The resulting composites achieve an impressive tensile strength of 361.8 +/- 7.0 MPa, a high yield strength of 212.4 +/- 4.8 MPa, a high ductility of 10.6% +/- 1.0%, and a Vickers hardness of 107.4 +/- 3.0 HV. This simultaneous enhancement of strength and ductility is primarily attributed to the formation and uniform distribution of the HEP, coupled with the partially coherent interfaces. This work offers a novel strategy for designing high-performance Mg-based composites and provides new insights into the mechanisms underlying the strength-ductility synergy. (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic) , (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic) , (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic)(sic)-(sic)(sic)(sic)(sic)(sic) , (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)Mg(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic) ( HEP ) (sic)(sic)--Mg24(Y0.25Dy0.25Ho0.25Er0.25)5 ( (sic)(sic)(sic)Mg24(4RE0.25)5 ) (sic)(sic)(sic).(sic)(sic)(sic)HEP(sic)(sic)(sic),(sic)(sic),(sic)(sic)(sic)(sic)(sic)Mg(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic)HEP(sic)(sic)(sic)(sic)(sic) , (sic)(sic)Mg24Y5(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic) , HEP(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic) , (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic) , (sic)(sic)(sic)(sic)(sic)(sic)(sic)HEP(sic)(sic)(sic)Mg(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic) : (sic)(sic)(sic)(sic)(sic)361.8 +/- 7.0 MPa , (sic)(sic)(sic)(sic)(sic)(sic)212.4 +/- 4.8 MPa , (sic)(sic)(sic)(sic)10.6% +/- 1.0% , (sic)(sic)(sic)(sic)(sic)107.4 +/- 3.0 HV.(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic) HEP (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic) , (sic)(sic)(sic)Mg(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).

This work investigates the microstructure evolution of the as-extruded Mg-Gd-Y-Zn-Mn alloy during secondary hot deformation, aiming to provide a theoretical basis for determining the final forming conditions of the alloy. The results show that continuous dynamic recrystallization and discontinuous dynamic recrystallization co-exists at low temperature and high strain rate, and pyramidal slip is preferentially activated to align the grain c-axis along the compression direction. At moderate temperature and moderate strain rate, discontinuous dynamic recrystallization becomes dominant with the activation of prismatic slip, rotating the c-axis toward the transverse direction. Sufficient dynamic recrystallization is achieved at high temperature and low strain rate, leading to a dispersed texture distribution. Temperature lower than 400 degrees C coupled with high strain rate promotes the dynamic precipitation of beta phase, consumes solute atoms and weakens the subsequent aging strengthening effect. In contrast, temperatures above 440 degrees C inhibit beta phase dynamic precipitation and induce partial dissolution of grain-boundary beta phase, maintaining a high solute supersaturation and improving the aging hardening capacity. Based on microstructure and mechanical performance, the optimal final forming conditions of the alloy is determined to be around 440 degrees C/0.03 similar to 0.1 s(-1).

Achieving a synergistic enhancement of high strength and high electrical conductivity (EC) in magnesium (Mg) alloys represents a major challenge in current research due to their inherent trade-off between strength and EC. This study, based on the Mg-Zn-Zr system, successfully overcomes the traditional trade-off between strength and EC by introducing yttrium (Y) as a key alloying element and employing an over-aging process. The groundbreaking contribution for this study lies in reevaluating the value of over-aging processes: traditionally regarded as detrimental to strength, over-aging treatment actually serves as a key pathway to achieving high EC by promoting the complete precipitation of solute elements within the α-Mg matrix, thereby reducing lattice distortion and electron scattering. The addition of Y induces the target second phase with Zn, significantly reducing the solute concentration in the matrix to enhance EC. And more importantly, the negative vacancy binding energy of Y atoms effectively suppresses grain coarsening of the precipitated phase during over-aging. This allows the alloy to achieve high EC while maintaining high strength. The Mg-Zn-Y-Zr alloy ultimately developed exhibits outstanding comprehensive properties, with a tensile strength of 245.9±3.5MPa, elongation of 25.5±1.1%, and EC reaching 33.9% IACS. This study demonstrates that synergistic control of Y content and over-aging treatment can simultaneously achieve precipitation strengthening and matrix purification effects, providing an innovative strategy for designing next-generation high strength, high conductivity magnesium alloys.

Coordinating the strength and plasticity of magnesium matrix composites (MMCs) has always been a challenge. In this study, Ti particle-reinforced xTi/Mg-8Zn-0.5Zr (x = 0/3/6/9 wt%) MMCs were prepared by Melt-spinning (MS) technology. The objective is to refine the grain size through sub-rapid solidification (SRS) and form dispersed nanoscale beta-phase within the Mg matrix. The nano-scale beta phase can hinder dislocation movement during deformation and pin at twin boundaries, thereby helping to enhance the strength of MMCs. Microstructure analysis was performed using XRD, SEM, EBSD/in-situ EBSD, and TEM. In-situ SEM was used to analyze the crack propagation and fracture morphology of the Ti particle interface, diffusion layer, and Mg matrix during deformation. The experimental results revealed the twinning process and microstructure changes of xTi/Mg-8Zn-0.5Zr MMCs under different strains. The results show that 6Ti/Mg-8Zn-0.5Zr MMCs exhibit the best comprehensive mechanical properties during deformation, with a tensile strength of 361 MPa and a yield strength of 221 MPa, representing increases of 37.8% and 88.8%, respectively, compared to 0Ti/Mg-8Zn-0.5Zr. Analysis indicates that the superior mechanical properties of xTi/Mg-8Zn-0.5Zr MMCs are attributed to the synergistic effect of multiple factors, including grain refinement, the suppression of dislocation movement during the deformation of the MMCs by Ti particles, and the pinning of dislocations and twin boundary migration by the nanoscale second phase MgZn2. The synergistic effect of these mechanisms enables MMCs to possess a more comprehensive strength and plasticity.

The microstructural evolution and mechanical responses under multi-degree-of-freedom reciprocating torsion-compression deformations remain to be fully elucidated, particularly regarding the Swift and inverse Swift effects and their physical mechanisms, which constrain the design and formability of textured Mg alloys. Therefore, the multi-degree-of-freedom reciprocating pre-torsional-compressive loadings along extrusion direction (ED) were specifically designed. The twinning behaviours and the radial distribution of twin structures were systematically analysed. The driving mechanisms of the Swift and subsequent inverse Swift effects were discussed. Results demonstrated that free end torsion (FET) deformation induced radially linear-gradient twinning structure, while reverse FET (RFET) loading triggered FET twins detwinning and extensive {101(sic)2} tensile twin activation within the basal textures, driving the reverse FET twin texture further tend towards ED aggregation. FET twins inhibited the nucleation of RFET twins, resulting in the formation of a distinctive inverse-gradient twinning structure. 65% of the Swift-effect strain under low-strain FET (gamma < 0.12) was coordinated by dislocation slip, whereas the misfit strain induced by FET twins accommodated more than 85% of the axial shortening during gamma(FET) = 0.38. RFET-stage axial elongation was governed by detwinning, with subsequent axial shortening attributable to large-scale RFET twin activation. {102} tensile twins dominated initial free rotational compression (FRC) strain, the interactions between the release of residual shear stress and the reverse shear strain component induced by FRC twins results in the circumferential motionlessness during initial FRC. Proliferation of FRC twins promoted cumulative circumferential shear strain component, inducing further macroscopic reverse spontaneous rotation.

The worldu2019s first big data and intelligent design platform for magnesium materials, u201CMagNovau201D, jointly developed by Mingyue Lake Laboratory, Chongqing University, and the National Engineering Research Center for Magnesium Alloys, was officially launched.

Achieving a simultaneous enhancement of strength and ductility remains a critical bottleneck for the large-scale and cost-effective engineering application of magnesium alloys. In this work, guided by first-principles calculations, we tailored the tau-Mg32(Al,Zn)49 phase and optimised twin boundary, thereby designing and successfully synthesising a series of low-cost high-performance Mg-10Zn-4Al-0.4Mn-xSn (x = 0.0, 0.2, 0.4, 0.6; labelled as ZAM-xT) alloys. First-principles calculations demonstrated that the tau-Mg32(Al,Zn)49 phase reached optimal elastic properties at a Zn/Al ratio of 2:1, and that Sn was the most effective alloying element for Mg twin boundary strengthening. Moreover, experimental results showed that the main phases in the ZAM-xT alloys consisted of alpha-Mg, tau-Mg32(Al,Zn)49, AlMn and Al8Mn5, with the Zn/Al atomic ratio in the tau-Mg32(Al,Zn)49 phase maintaining a 2:1 proportion. The aged ZAM-0.6T alloy exhibited an ultimate tensile strength of 334 MPa, a yield strength of 191 MPa and an elongation of 11.8%, whereas the aged ZAM-0.4T alloy had the highest Young's modulus, reaching 48 GPa. In addition, Orowan and grain boundary strengthening were identified as the primary strengthening mechanisms, contributing 108 and 40 MPa, respectively, to the yield strength of the ZAM-0.6T alloy. This study demonstrated the use of first-principles calculations to design phase stability and interfacial strength, guiding alloying element selection to accelerate the development of high-strength ductile magnesium alloys, minimise experimental trial-and-error and advance lightweight cast alloy applications. (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)tau-Mg32(Al,Zn)49(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic), (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)Mg-10Zn-4Al-0.4Mn-xSn (x = 0.0, 0.2, 0.4, 0.6; (sic)(sic)(sic) ZAM-xT)(sic)(sic).(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic), tau-Mg32(Al,Zn)49(sic)(sic)(sic)Zn/Al(sic)(sic)2:1(sic), (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic), (sic)Sn(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic)(sic)(sic), ZAM-xT(sic)(sic)(sic)(sic)(sic)(sic)(sic)alpha-Mg, tau-Mg32(Al,Zn)49, AlMn (sic) Al8Mn5 (sic)(sic), tau-Mg32(Al,Zn)49(sic)(sic)(sic)Zn/Al(sic)(sic)(sic)(sic)(sic)(sic)2:1.(sic)(sic)(sic)(sic)(sic)(sic) ZAM-0.6T(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)334 MPa, (sic)(sic)(sic)(sic)(sic)191 MPa, (sic)(sic)(sic)(sic) 11.8%, (sic)(sic)(sic)(sic)(sic)(sic)(sic) ZAM-0.4T (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic), (sic)(sic) 48 GPa.(sic)(sic), ZAM-xT(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)Orowan(sic)(sic)(sic)(sic)(sic)(sic)(sic), (sic)(sic)(sic)ZAM-0.6T(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic) 108 MPa(sic) 40 MPa.(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic), (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic), (sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic), (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic), (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).

In this work, we successfully prepared a novel Mg-8Y-2Zn-1Sn-0.5Mn alloy with excellent hightemperature performance. The key is transforming the less thermally stable Mg2Y phase into the more thermally stable Sn3Y5 phase through elemental interactions. The Mg-8Y-2Zn-1Sn-0.5Mn alloy exhibits excellent mechanical properties at 250 degrees C, with ultimate tensile strength (UTS), yield strength (YS), and elongation of 368 MPa, 318 MPa, and 10.3%, respectively, which are much higher than most reported heat-resistant Mg alloys. An interesting observation is that the UTS of this alloy does not decrease when the temperature is increased from 250 to 300 degrees C. The outstanding high-temperature properties of Mg8Y-2Zn-1Sn-0.5Mn are attributed to the uniform distribution of multi-scale heat-resistant particles and the segregation of solute atoms. This work has obtained a new high-strength and heat-resistant Mg alloy by tailoring multi-scale precipitates and solute segregation, bringing new ideas for the development of heat-resistant Mg alloys. (c) 2025 Chinese Society of Rare Earths. Published by Elsevier B.V. All rights are reserved, including those for text and data mining, AI training, and similar technologies.

This work investigates the microstructure, mechanical properties, and thermal conductivity (TC) of Mg-9Gd-1Zn-0.5Zr (wt%) alloy in various states, focusing on revealing the effect of the form of alloying elements in the alloy on its mechanical properties and TC. The extruded Mg-9Gd-1Zn-0.5Zr (wt%) alloy achieved the exceptional combination of mechanical properties and TC after 120 h of aging treatment at 200 °C. The yield strength, ultimate tensile strength, elongation, and TC of the aged alloy are 315 MPa, 370 MPa, 12.4%, and 58.9 W/(m⋅K). The results indicate that the form of Gd and Zn elements significantly influences the TC, playing a dominant role. Meanwhile, the form of alloying elements exerts a stronger impact on TC than on the mechanical properties. During aging, the concentration of solute atoms, the density of the precipitates, and the size of the precipitates have a competitive relationship in terms of their influence on TC. Only when these factors achieve a balance can the alloy exhibit higher TC, corresponding to the peak aged state of TC. In contrast, for mechanical properties, the density and size of the precipitates play a more predominant role than the solute atom. This study provides theoretical guidance for developing novel magnesium alloys that combine excellent mechanical properties and TC.

With the aim of achieving outstanding thermal control and corrosion resistance properties, a white MAO thermal control coating sealed by a silicon-zirconium hybrid sol-gel layer was prepared in this work. The corrosion behavior of the coating was evaluated using potentiodynamic polarization and electrochemical impedance spectroscopy (EIS) in 3.5 wt.% NaCl solution. Microstructural and compositional characterizations were conducted using scanning electron microscopy (SEM), X-ray diffraction (XRD), and energy-dispersive spectroscopy (EDS). Results indicated that the sol-gel/MAO composite coating significantly outperformed the single-layer MAO coating in corrosion resistance, primarily due to effective sealing of micro-pores and cracks by the sol-gel layer, which prevented the penetration of corrosive agents. The post-immersion morphological observations were in good agreement with the EIS results. After immersion, the corrosion current density of the composite coating only increased from 10-6.4 to 10-5.1 A/cm2, while the corrosion potential decreased from -1.25 V to -1.35 V. The post-immersion morphological observations were consistent with EIS results. Meanwhile, the composite coating can effectively mitigate the thermal control performance degradation caused by corrosion. Compared with the MAO coating, the absolute increase in solar absorptance of the sol-gel/MAO coating is reduced by 60%. After 168 h of accelerated corrosion tests in a simulated marine environment, the solar absorptance (αS) of the sol-gel/MAO coating increased by only 0.05. This study demonstrates that the combination of MAO and sol-gel treatment provides a promising strategy for the development of lightweight, corrosion-resistant magnesium alloys for aerospace applications.

This paper investigates the effects of Ce on the microstructure, mechanical properties, and flame retardancy of the Mg-4Al-3Ca (AX43) alloy. Among all the experimental alloys, the extruded AX43-0.6Ce alloy exhibits the optimal comprehensive performance, with an ultimate tensile strength (UTS) of 318 MPa, a yield strength (YS) of 253 MPa, an elongation (EL) of 11.9%, and an ignition temperature of 1126 degrees C. With increasing Ce content, both the tensile properties and ignition temperature of the alloy first increase and then decrease, and the alloy with 0.6 wt% Ce shows the lowest recrystallization degree and the smallest grain size. The excellent tensile properties of this alloy are mainly attributed to the synergistic effect of the retained substructure and nano-sized Al2Ca phases; its outstanding flame retardancy benefits from the modification of the alloy's oxide film by Ce and the formation of the high-melting-point Al11Ce3 phase. The addition of Ce achieves the above-mentioned regulation of microstructure and properties by altering the recrystallization behavior of the alloy.

Bimodal grain structure (BGS) demonstrates significant potential in synergistically optimizing the strength and plasticity of magnesium alloys. Acquiring the desired BGS consequently became a critical challenge. This study took the Mg-9Gd-1Zn-0.5Zr (wt%, VZ91K) alloy as its subject. From the perspective of BGS formation mechanisms, it suggests an effective strategy for constructing BGS, revealing the associated microstructural evolution, as well as the strengthening and toughening mechanisms. Research indicates that fully dissolving the micron-sized blocky eutectic phase in the as-cast alloy can significantly suppress the particle-stimulated nucleation-induced dynamic recrystallization (PSN-DRX) that occurs during extrusion, thereby yielding a BGS in the VZ91K alloy. The VZ91K alloy with BGS exhibits a significant enhancement in yield strength compared to homogeneous alloys (194-268 MPa), accompanied by an acceptable decrease in elongation to fracture (24.5%-20.3%). Hetero-deformation-induced (HDI) hardening is the critical factor driving the synergistic strength-plasticity of the VZ91K alloy with BGS. During tensile deformation, the HDI stress and HDI hardening rate of the VZ91K alloy with BGS consistently exceed those of the homogeneous alloy. Additionally, dislocation strengthening, low-angle grain boundary strengthening, LPSO, and gamma ' phase strengthening are also responsible for the high strength of the VZ91K alloy with BGS. This study presents a novel approach to constructing BGS, which could facilitate its application in the regulation of the mechanical properties of magnesium alloys. (sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic)Mg-9Gd-1Zn-0.5Zr (wt%,VZ91K)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)VZ91K(sic)(sic).(sic)(sic)(sic)(sic)(sic)(sic)VZ91K(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(194 to 268 MPa),(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(24.5% to 20.3%).(sic)(sic)(sic)(sic)(sic)(sic)(sic)(HDI)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)VZ91K(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)VZ91K(sic)(sic)(sic)HDI(sic)(sic)(sic)HDI(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic),(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)(sic),LPSO(sic)gamma'(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)VZ91K(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic),(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic)(sic).

Magnesium-ion batteries show immense application potential in energy storage applications due to their outstanding advantages, which include high volumetric energy density, exceptional safety, environmental friendliness, abundant resources, and low cost. However, magnesium ions have a high charge density and strong polarization characteristics, leading to slow diffusion kinetics, limited reversible capacity, and poor cycling stability in cathode materials. These factors have severely constrained the further development of magnesium-ion battery systems. Therefore, developing high-performance cathode materials is a critical step in advancing the practical application of magnesium-ion batteries. In this review, the research progress on cathode materials for magnesium-ion batteries is systematically reviewed, the types and underlying mechanisms of cathode materials are elucidated, and the regulation strategies for different categories of cathode materials as well as the cathode-electrolyte interphase (CEI) are critically evaluated. Then, the latest applications of artificial intelligence (AI) technology in screening cathode materials for magnesium-ion batteries, predicting their performance, and analyzing their mechanisms are highlighted. Moreover, the potential value of AI in revealing magnesium storage reaction mechanisms, establishing structure-property relationships, and accelerating the discovery of new materials is discussed. Finally, this paper summarizes the industrialization progress and key technical challenges facing magnesium-ion battery cathode materials, and future development directions are outlined. This review aims to provide insights and references for the intelligent design, system construction, and industrialization of high-performance cathode materials for magnesium-ion batteries.

The strength-ductility trade-off remains a critical obstacle for particle-reinforced magnesium matrix composites (PMMCs), largely governed by the interfacial structure and matrix precipitation. Here, we systematically investigate the effect of Ag microalloying from 0 to 1.5 wt% on the microstructural evolution and mechanical behavior of hot-extruded 2Ti/Mg-6Zn-1.5Mn composites. Ag addition induced a reversible transition of the Ti/ Mg interfacial microstructure, wherein a continuous nanocrystalline Mn2Ti layer formed without Ag, coexists with intragranular Mn2Ti precipitates at 0.5 wt% Ag, disappears at 1.0 wt% Ag, and was fully reconstructed at 1.5 wt% Ag alongside dual-scale Mg-Zn phases. Meanwhile, Ag promoted the precipitation and aggregation of Mg7Zn3 phases, refines grains, and gradually reduced the dynamic recrystallization fraction. The optimal strength-ductility synergy was achieved at 0.5 wt% Ag, with yield strength (YS) of 254MPa, ultimate tensile strength (UTS) of 371 MPa and elongation of 19.9%. The enhanced strength is attributed to grain boundary strengthening, Orowan strengthening, solid solution strengthening and effective load transfer strengthening. The excellent toughness was mainly ascribed to the stable interfacial bonding, favorable work hardening behavior and suppressed strain localization inside Ti particles. Excessive Ag led to deteriorated interface, aggregated second phases and restricted deformability of Ti particles, resulting in rapid decline of plasticity. This work revealed the coupling regulation mechanism of Ag on interface and precipitation in Ti-reinforced Mg composites and provides a new strategy for developing high-performance Mg matrix composites with balanced strength and ductility.

To mitigate the long-standing trade-off in magnesium (Mg) alloys between low elastic modulus and strength-damping incompatibility, Mg-7Y-2.5Zn-xSi (x = 0.3, 0.6, 1.2 wt%) alloys were fabricated via Si alloying followed by hot extrusion. Increasing Si drives the second-phase evolution from Mg3Zn6Y/LPSO to thermally stable SiY, with additional Mg2Si forming at 1.2 wt% Si. Hot extrusion further fragments and refines these phases and modulates recrystallization (decreasing then increasing), accompanied by strengthening the texture. The introduction of high-modulus Si-containing phases increases the elastic modulus from 47 GPa to 50 GPa. The extruded WZ72–1.2Si alloy exhibits the highest tensile yield strength (TYS) of 210 MPa and ultimate tensile strength (UTS) of 303 MPa, which is mainly attributed to the synergistic contributions of dispersion strengthening by second-phase particles, dislocation strengthening and orientation hardening. In contrast, the extruded WZ72–0.6Si alloy shows superior room-temperature damping capacity (Q−1> 0.01 at a strain amplitude of ε = 0.1%), primarily due to the reduced solute-atom content and the high density of mobile dislocations induced by an appropriate number of Si-containing phases. With increasing temperature, the damping enhancement in both WZ72–0.6Si and WZ72–1.2Si alloys becomes more pronounced, indicating a higher high-temperature energy-dissipation capability than that of the low-Si alloy; this is closely related to the increased activity of dissipation mechanisms such as grain-boundary migration and interphase sliding at elevated temperatures.

1.Introduction As the lightest metallic structure material,magnesium(Mg)al-loy exhibits broad application prospects in aerospace,new energy vehicles and 3C electronic products[1-3].The large-scale appli-cation of Mg alloy is regarded as an essential breakthrough to achieve the goal of lightweight.However,the hexagonal close-packed(HCP)structure of Mg with low-symmetry results in lim-ited deformation modes that can be readily initiated at room tem-perature,mainly basal slip and extension twinning,thus causing inhomogeneous plastic deformation and poor plasticity[4,5].

This study clarifies the relationship between thermomechanical conditions in the final forging of Al-Mg-Sc alloys and their microstructure evolution, providing guidance for parameter optimization. Experiments reveal that dynamic recrystallization initiates at > 270 degrees C under slow strain rates (0.1/s), enhancing deformation uniformity. Macroscopic shear appears at 210 degrees C/1 s and it is mitigated by increasing temperature or reducing strain rate, vanishing at 300 degrees C. Even deformed at the condition near the instability threshold, the alloy maintains good strength, which is attributed to the large amount of substructures and fine Al-3(Sc,Zr) precipitates. Deformation at 0.1-0.01/s above 300 degrees C significantly alleviates the effects of flow localization and deformation band which are formed previously. By inducing recrystallization in the deformation bands, the material achieves both strength and elongation. These findings demonstrate that non-uniform deformation structures such as deformation bands can be mitigated by adjusting the strain conditions in the later stage, indicating that Al-Mg-Sc alloys with both strength and elongation can be obtained even under conditions close to instability (e.g., 330 degrees C-0.01/s).

This study reports a novel dual gradient-structured (GS) Mg–2Zn–0.8Gd (wt.%) alloy fabricated via surface sliding friction and followed by heat treatment. Excellent grain boundary (GB) stability is achieved through the co-segregation of Zn and Gd atoms. The segregated gradient structure produces an excellent strengthening and work hardening effect, which is attributed to the combined effects of prominent GB segregation within the GS layer and the recovery of dislocation storage capacity. Furthermore, a remarkable segregation hardening in the surface layer increases the hard–soft disparity, which arouses more geometrically necessary dislocations that further synergistically strengthen and toughen the alloy.

This study reveals the anisotropy of the tensile properties and the Portevin-Le Chatelier effect (PLC) of the spun Al-Mg-Sc alloy along three directions: the mandrel direction (MD), the direction at a 45° to the mandrel direction, and the transverse direction (TD). The TD exhibited a strong PLC and low strength, while the MD showed high strength and weak PLC. The 45° direction exhibited behavior between the two. Microstructure indicated that the differences in the Schmid factor dominated the accumulation of dislocations and strain localization. The different hindering effects of Al3(Sc, Zr) particles on dislocation motion exacerbated the anisotropy of the PLC effect.