High Dislocation Density Research Articles

Tailoring surface properties and corrosion resistance of laser shock peened Ti6Al4V alloy by low-temperature annealing

The present study examined the effects of laser shock peening (LSP) and low-temperature annealing after LSP (LSPA) on the corrosion resistance of the Ti6Al4V alloy. The high density of dislocations in the LSP samples contributes to the rapid formation of a TiO₂ passive film during the electrochemical corrosion process. In this study, low temperature annealing was employed to further improve the corrosion resistance. The results indicated that the corrosion resistance of the LSPA samples was significantly improved compared to that of the LSP-treated samples. The LSPA treatment facilitated the pre-generation of a dense TiO2 passive film on the alloy surface via oxidation, reduced corrosion rate, inhibited the penetration of dissolved oxygen and ions present in the sodium chloride solution into the alloy surface. Meanwhile, low-temperature annealing could rearrange and annihilate dislocations, creating subgrains and relaxing non-equilibrium grain boundaries induced by deformation. This process reduced active sites and grain boundary energy, ultimately improving the corrosion resistance of the Ti6Al4V alloy.

Deformation strengthening mechanism of laser remelted high manganese steel

In order to further improve the deformation hardening ability of high manganese steel (HMnS) under low stress or small deformation, a low speed laser remelting technology was proposed to process the HMnS surface. Through parameters optimization, microstructure characterization, wear testing, and deformation strengthening analysis, the deformation strengthening mechanism of laser remelted HMnS (LR-HMnS) was systematically studied, and excellent wear resistance properties was also achieved. Firstly, by optimizing the parameters of laser remelting, high-quality microstructures with large remelting depth and fewer porosities were obtained. Then, the sliding wear tests showed that although the surface hardness of LR-HMnS (252.83HV0.3) was only 2.56 % higher than that of continuous casting HMnS (CC-HMnS) (246.53HV0.3), its volume wear rate (1.87×10−5 mm3/N·m) was only 10 % of CC-HMnS (18.71×10−5 mm3/N·m), which exhibited excellent wear resistance properties. Finally, for quantitative evaluating its work hardening at high strain rates, Hopkinson compression test of LR-HMnS was conduced according to the operating conditions of HMnS parts. The microstructure after small compression deformation was analyzed using EBSD and TEM. It was found that the larger grain size of LR-HMnS was helpful of reducing the nucleation stress of twins, forming high-density nano-twins, high-density stacking faults, and high-density dislocations. The synergistic effect of stacking faults, dislocations, and twins which segmented the matrix and refined the grains, and achieved the dynamic Hall-Petch effect. The superior deformation strengthening and wear resistance exhibited by larger grain HMnS were called the inverse grain size effect. Additionally, the large number of C-Mn strong bond networks formed by element segregation could enhance the pinning effect of dislocations, promote deformation hardening rate and wear resistance properties under low stress or small deformation. The research results provided a new method for pre-hardening of HMnS, and will also expand the application potential of HMnS in combined conditions of high, medium, and low impact.

Study on the atomic scale deformation mechanism of the h-BN coating nickel matrix composites

In this paper, molecular dynamics (MD) simulations are applied to study the contact mechanical behavior of hexagonal boron nitride (h-BN) coating/Ni matrix composites during nanoindentation, revealing the material deformation mechanism. A systematic study is carried out on the load-depth curve, temperature response curve, defect morphology, and dislocation density in indentation. The results show that the presence of h-BN coating increases the actual loading area of the matrix, effectively reduces the contact stress between the tip of the indenter and the specimen, and also induces the generation of high-density Shockley dislocations, which increases the dislocation entanglement and leads to the localized hardening of the composites, thus reducing the matrix damage. During the loading process, the temperature of the specimen before the destruction of the h-BN coating is significantly lower than that after the destruction, indicating that the coating tends to block the transfer of temperature to the interior of the specimen, preventing the occurrence of temperature-induced tissue phase changes inside the specimen, and providing good protection for the interior of the specimen.

Formation process, microstructure characterization, and evolution mechanism of adiabatic shear bands in U-5.7Nb alloy under dynamic deformation

Uranium-niobium (U-Nb) alloys as structural materials play an important role in nuclear industry. During their utilizing, U-Nb alloys tend to dynamically fracture along the adiabatic shear bands, which affects their performances. In order to understand the formation process and mechanisms, we systematically investigate the adiabatic shear bands formed in U-5.7Nb alloys, where systematical characterization methods were applied, such as optical microscope, scanning electron microscope, and high-resolution transmission electron microscope. Using stopper rings, the U-5.7Nb alloy was impacted by a split Hopkinson pressure bar at a strain rate of 8 000 s-1 to perform seven strain levels. The formation process of adiabatic shear bands in U-5.7Nb alloys was characterized, and we found two types of adiabatic shear bands: the deformed ones together with the transformed ones. They are formed at different stage of severe shear localization. The deformed adiabatic shear bands mainly included highly deformed and elongated grains, and the transformed adiabatic shear bands were basically composed of ultrafine equiaxed grains with size of about 150 nm. High density of dislocations or dislocation cells were found in these ultrafine equiaxed grains. The occurrence of ultrafine equiaxed grains in the adiabatic shear bands of U-5.7Nb alloys was deduced to be rotational dynamic recrystallization mechanism.

Inhomogeneous deformation in the radial direction of the cold radial forged 30SiMn2MoVA steel tube

In this paper, the inhomogeneous deformation in the radial direction of the cold radial forged 30SiMn2MoVA steel tube was studied by finite element method, analyzing the microstructure and mechanical tests. The simulated result shows that the inhomogeneous deformation mainly distributed from the inner layer to the middle layer. In this region, the equivalent plastic strain rapidly decreases. The change from the middle to the outer is not significant. The distribution of microstructure and the results of mechanical properties also follow this pattern. The inner layer has the most refined grain size and the highest dislocation density. The strongest {110}<110> texture component has also been formed in the inner layer. The strength value of the inner layer is the highest, and the elongation is the lowest. There is not much difference in these indicators between the middle and outer regions. By calculating the strengthening contributions of solid solutions, dislocation density, and grain boundaries to yield strength, it was found that dislocation density is the main contributor. The calculated yield strength value is consistent with the experimental value.

Stress-induced martensite reorientation and its related performances in trained β-Ti based shape memory alloy

In the present study, the influence of training on the microstructural evolution, martensitic transformation behavior and mechanical/functional properties of Ti–V–Al–Zr shape memory alloy was investigated systematically. With the increasing of training cycling number, the degree of martensite reorientation became larger and larger. Moreover, higher density of dislocations appeared in the interior of martensite variants, upon the excessive training cycling number was applied. The international stress can be brought into the matrix, which not only promoted to the ω→αˊˊ transition, but also made the martensite phase stabilizer and even suppressed the αˊˊ→β martensitic transformation during training process. The superior mechanical properties including maximum fracture stress of 906 MPa and the higher fracture strain of 33.6% can be obtained in Ti–V–Al–Zr shape memory alloy subjected with the training cycles number of 5th, which can be attributed to the matrix strengthening stemmed from work hardening and suppression of ω precipitation. Meanwhile, the lower critical stress for the martensite variant reorientation and enhanced matrix strength synergistically contributed to the superior strain recovery characteristics with total completely recoverable strain of 6% in Ti–V–Al–Zr shape memory alloy by controlling training cycles number of 5th. Meanwhile, the higher micro-hardness can be obtained by training.

Insight into elongation and strength enhancement of heat-treated LPBF Ni-based superalloy 718 using in-situ SEM-EBSD

This study presents a detailed investigation into the deformation behaviour and the factors affecting the strength and ductility of laser powder bed fusion (LPBF) Ni-based superalloy 718 (Inconel 718) in both as-printed and heat-treated conditions using in-situ SEM + EBSD. The results show that following post-deposition high homogenization temperatures, the columnar grain structure of the as-printed Inconel 718 alloy successfully transformed to a nearly uniform grain size and the subsequent aging processes facilitated the precipitation of strengthening phases (γ′, γ''). The specimen subjected to heat treatment (HT1) exhibited higher strength but lower ductility, while the as-printed specimen shows higher tensile elongation due to high initial dislocation density. In contrast, the heat-treated (HT2) specimen presented a more optimal combination of strength and ductility. The underlying mechanism for the enhanced tensile properties in the HT2 specimen was nearly homogeneous deformation trend across the grains and ultrafine precipitation of hardening phases. In addition, the twin boundaries were stable in the early deformation stages and maintained their orientation. Multiple slip systems were activated at the high-deformation stage, resulting in a high proportion of geometric necessary dislocations. Further, the interaction of deformation-induced dislocation with twin boundaries transformed them into general boundaries such as high and low-angle grain boundaries, ultimately increasing ductility. On contrary, in the HT1 specimen, the deformation inhomogeneity in grains enabled the strain localization at grain boundaries, which ultimately caused the early formation of cracks.

Molecular Dynamics Simulation Study of Aluminum-Copper Alloys' Anisotropy under Different Loading Conditions and Different Crystal Orientations.

The commonly used aluminum-copper alloys in industry are mainly rolled plates and extruded or drawn bars. The aluminum-copper alloys' anisotropy generated in the manufacturing process is unfavorable for subsequent applications. Its underlying mechanism shall be interpreted from a microscopic perspective. This paper conducted the loading simulation on Al-4%Cu alloy crystals at the microscopic scale with molecular dynamics technology. Uniaxial tension and compression loading were carried out along three orientations: X-<1¯12>, Y-<11¯1>, and Z-<110>. It analyzes the micro-mechanisms that affect the performance changes of aluminum-copper alloys through the combination of stress-strain curves and different organizational analysis approaches. As shown by the results, the elastic modulus and yield strength are the highest under tension along the <11¯1> direction. Such is the case for the reasons below: The close-packed plane of atoms ensures large atomic binding forces. In addition, the Stair-rod dislocation forms a Lomer-Cottrell dislocation lock, which has a strengthening effect on the material. The elastic modulus and yield strength are the smallest under tension along the <110> direction, and the periodic arrangement of HCP atom stacking faults serves as the main deformation mechanism. This is because the atomic arrangement on the <110> plane is relatively loose, which tends to cause atomic misalignment. When compressed in different directions, the plastic deformation mechanism is mainly dominated by dislocations and stacking faults. When compressed along the <110> direction, it has a relatively high dislocation density and the maximum yield strength. That should be attributed to the facts below. As the atomic arrangement of the <110> plane itself was not dense originally, compression loading would cause an increasingly tighter arrangement. In such a case, the stress could only be released through dislocations. This research aims to provide a reference for optimizing the processing technology and preparation methods of aluminum-copper alloy materials.

On the plastic deformation mechanism of Al0.6CoCrFeNi high entropy alloy: In-situ EBSD study and crystal plasticity modeling

In this study, in-situ tensile tests with electron back-scattered diffraction (EBSD) were conducted to reveal the microstructural effects on the plastic deformation behavior of dual-phase Al0.6CoCrFeNi high entropy alloys (HEAs). The in-situ EBSD results demonstrated a uniform distribution of dislocation density in the fine grain (FG) samples, whereas high dislocation density was predominantly localized near body-centered cubic (BCC) phases in the coarse grain (CG) samples. The difference in mechanical properties between face-centered cubic (FCC) and BCC phases caused stress concentration and cracking at the boundaries during tension. The FCC phase within FG samples exhibited excellent plasticity, effectively impeding the propagation and coalescence of microcracks emanating from the BCC phase into longer cracks. For CG samples, brittle cracks formed in BCC phases are easy to merge, thus evolving into long cracks. Crystal plasticity finite element analysis revealed that as the strain increases, stress distribution in FG samples tended to become more homogeneous, whereas for CG samples high stress concentration consistently occurred within BCC phases. The deformation characteristics of FG were attributed to the synergistic effect generated by the FCC phase with heterogeneous grain size and the BCC phase characterized by small grain size.

Cryogenic tensile behavior of CoNiCrMo medium entropy alloy

The microstructure and mechanical properties of 35Co-34Cr-24Ni-7Mo medium entropy alloy, known as MP35N, were investigated at different cryogenic temperatures (77 K and 195 K) and compared with those at room temperature (295 K). The microstructural features at the mentioned three distinct temperatures were characterized by X-Ray diffraction, electron back skater diffraction analysis and transmission electron microscopy. It was found that, compared to room temperature, cryogenic temperatures significantly increased the yield strength and tensile strength from 330 MPa and 1300 MPa at 295 K to 711 MPa and 1890 MPa at 77 K, respectively, without a noticeable change in elongation. Microstructural investigation revealed that lower deformation temperatures resulted in higher dislocation density, higher stacking fault probability, more mechanical twins, and a more homogeneous dislocation structure. Up to a strain of 0.4, no sign of fcc to hcp phase transformation was observed in EBSD, TEM images, or SAED patterns, even at 77 K. The higher work hardening due to mechanical twinning, increased dislocation density, and lower stacking fault energy, in addition to a more homogeneous dislocation structure, postponed the formation of geometric instabilities and maintained a ductile fracture mechanism at cryogenic temperatures.

Induction mechanisms of high-density nano twins during solidification process: Reducing stacking fault energy of γ phase by Re and forming highly mismatched B2(Re)/α2 interface

It is extremely difficult to introduce high-density nano twins during the solidification process of TiAl alloy. In this study, high-density nanotwins are inducted in the as-cast Ti48Al2Cr alloyed by adding Re element. Phase transformation, morphology characteristics of nano twins, compressive and tensile properties, and the related mechanisms have been studied. Results show that B2 phase enriched with Re tends to precipitate along the α2/γ interface within lamellar colony. The stacking fault energy (SFE) of γ phase decreases from 43 mJ/m2 to 16 mJ/m2 as Re content increases from 0 at.% to 0.6 at.%, decreasing the critical shear stress for twin formation. Compared to the mismatch value of α2/γ interface (0.004), which of B2/α2 and B2/γ interfaces increase to 0.247 and 0.149, respectively. Driven by high interfacial stress, high-density dislocations are generated at the B2/α2 interface, providing the dislocation slip channel for the formation of stacking faults (SFs) and nanotwins at the B2/γ interface. Therefore, the mechanism of inducting high-density nanotwins is to reduce the stacking fault energy of γ phase by Re and form highly mismatched B2/α2 interface. Compressive strength and the strain increase from 1723 MPa to 2398 MPa and 29 % to 39 % as Re content increases from 0 at.% to 0.6 at.%, respectively. Tensile strength increases from 356 MPa to 452 MPa without sacrificing plasticity. The improvement in strength and plasticity are attributed to the nano-twinning strengthening and interfacial thermal mismatch strengthening. Forming nanotwins during solidification process serve as the nucleation sites for newly formed twins during deformation process, increasing the deformation tolerance of TiAl alloy.

Enhancing strength-ductility synergy in low-Mn lightweight steel by large-deformed warm rolling and flash annealing

The presence of δ-ferrite makes it challenging to achieve higher strength-ductility in low-Mn lightweight steels. In this study, a large deformation warm rolling process was used to construct a precursor enriched with Mn, nano-precipitations, ultra-fine grains, and high-density dislocations. The subsequent flash annealing process not only promotes the formation of multi-heterogeneous structures but also refines and reduces δ-ferrite while increasing the ultrafine-grained hard phase martensite. Additionally, this process enhances the retention of retained austenite, whose ultrafine grains contribute to improved mechanical stability. The synergistic effect of multiple strengthening mechanisms enables low-Mn lightweight steel to achieve outstanding comprehensive mechanical properties, with a tensile strength of 1423 MPa and a total elongation of 23.0 %.

Effect of the conventional shot peening and multiple shot peening on microstructure and residual stress of TC17 titanium alloy

This study examines the residual stress, microstructure, and stress-induced phase transformation of TC17 titanium alloy after different shot peening processes. A comprehensive analysis of the unique impact of shot peening on α-Ti and β-Ti was performed. The results indicate a substantial reduction in the grain size of the deformed layer and the creation of a high density of dislocations. Additionally, increased peening intensity results in decreased grain size, and multiple shot peening promotes further reduction in grain size. Compressive residual stresses were detected in the deformed layer, and multiple shot peening significantly augmented the residual stresses in the surface and near-surface regions. In particular, the highest compressive residual stresses after triple shot peening treatments were measured at −1079 MPa (at a depth of 10 μm for α-Ti) and −792 MPa (at a depth of 50 μm for β-Ti). In addition, multiple shot peening can significantly reduce surface roughness and enhance surface nanocrystallization when approximate surface residual stresses are obtained. Remarkably, the use of single shot peening revealed parallel stacking faults in certain α-Ti samples. However, under multiple shot peening, these stacking faults evolved into face-centered cubic Ti (FCC-Ti) with broader widths and a greater number. The stress-induced phase transition orientation relation was determined to be (0001)HCP//(11¯1)FCC and [21¯1¯0]HCP//[011]FCC, with α-Ti grains being interspersed with FCC-Ti, thus promoting additional grain refinement.

Promoting densification and strengthening effect of ultrasonic impact treatment on Haynes 230 alloy manufactured by laser powder bed fusion

Laser powder bed fusion (LPBF) has been extensively investigated owing to its high geometry formation accuracy and excellent mechanical properties. However, the LPBFed Haynes 230 parts typically display poor tensile and wear properties due to internal porosity. In this work, the ultrasonic impact treatment (UIT) was applied as a post-treatment to the LPBFed Haynes 230 alloy, porosity and microstructure modulation were performed to improve the strength properties and wear resistance. The pore closure and microstructure were studied by numerical simulations and experiments, and the mechanisms of increasing densification and strength were discussed. Results show that UIT can effectively close pores and reduce porosity, the internal porosity of the ultrasonic impacted layer for one, two, and three times decreases by 63.6 %, 70.9 %, and 81.8 %, respectively. Pore closure is attributed to the residual compressive stress and shear stress introduced by UIT. Besides, the UIT weakened texture strength and refined grains, especially promoting the formation of fine grains. Meanwhile, it also promotes the formation of a high dislocation density and improves the phase structure distribution. Furthermore, the ultimate tensile and yield strengths of the optimal impact process increased by 9.6 % and 34.6 %, respectively. The improvement in strength was attributed to dislocation, grain boundary, and promoting densification strengthening. The average friction coefficient reduces by 4.9 %–14.6 % by refining the surface grains and increasing dislocation density. This work has verified the feasibility of improving the mechanical properties and pore closure of the LPBFed Haynes 230 alloy by UIT.

Enhancing mechanical properties of medium Mn steel by warm rolling based on laminated elemental segregation

The hot-rolled microstructure of medium Mn steel has coarse grains and severe elemental segregation, resulting in low strength and plasticity. Constructing a multiphase structure, refining the microstructure, and regulating elemental segregation enhance the mechanical properties. In this study, liquid nitrogen treatment created a layered distribution of austenite and martensite. Warm rolling was then used to reduce layer thickness and refine grain structure. After liquid nitrogen and warm rolling treatments, the strength and plasticity of medium Mn steel increased to 1270 MPa and 23.3%, respectively, far exceeding the hot-rolled state (724 MPa, 12.8%). Warm rolling also triggers austenite reverted transformation (ART) and introduces high-density dislocations, further improving austenite stability. This strengthening effect is higher than that from intercritical annealing alone. Improved austenite stability delays the transformation induced plasticity (TRIP) effect, preventing brittle fracture and enhancing deformation coordination between layers, significantly increasing the plastic deformation capacity of medium Mn steel.

Dislocation structures and residual stresses in duplex stainless steel fabricated by laser powder bed fusion with 430 and 316L powders

The duplex stainless steel is fabricated using laser powder bed fusion (LPBF), with raw materials prepared by mechanically mixing 430 and 316 L powders in a 1:1 mass ratio. The as-built alloys exhibit good overall mechanical properties, and theoretical strength calculations are performed based on the flow strength model. Uniquely, the distribution of dislocations, residual stresses, and strain accommodation mechanisms are investigated using electron backscattered diffraction and transmission electron microscopy. The results show that the microstructure of the as-built alloys is predominantly ferritic phase, with an austenitic phase content of approximately 4 %. The ultimate tensile strength is 938 ± 4 MPa and the elongation is 19 ± 0.58 %. The as-built alloys possess high dislocation densities, with the dislocation density in the ferritic phases being higher than in the austenitic phases. In particular, austenitic phases present barely any local misorientation and minimal rotations within grains, stacking faults are introduced to accommodate the solidification strains. However, ferritic phases exhibit a high dislocations density, with dislocations present on the (101), (011‾) and (211) planes, accommodating solidification strains and cooling stresses through elastoplastic deformation, and building up geometrically necessary dislocations.

Effect of laser energy density on the phase transformation behavior and functional properties of NiTi shape memory alloy by selective laser melting

NiTi shape memory alloy (SMA) was prepared via selective laser melting (SLM). Orthogonal tests were conducted with varying laser power and scanning speeds to explore the influence of laser energy density on microstructure, phase transformation behavior, mechanical properties and functional properties (superelasticity and shape memory effect). As energy density increases from 24.3 to 106.3 J/mm³, microstructure transforms from fine to columnar grains. Ni consumption intensifies, boosting transformation temperature and B2 content at room temperature. Post cyclic stretching, B2 content in alloy escalates further at room temperature. Tensile strength peaked at 53.6 J/mm³, while the elongation rate significantly increases with increasing energy density. During cyclic stretching, low or high energy densities in SLM NiTi induce high-density dislocations and stable residual martensite, respectively, significantly inhibiting martensitic transformation and resulting in extremely poor functional properties. The alloy produced at 53.6 J/mm³ boasts exceptional superelasticity due to stress-induced martensitic transformation and phase inversion post-unloading. Following heating past the critical transition, it nearly fully recovers (97.78 % recovery rate). Despite multiple shape memory fatigue tests, it maintains a recovery rate above 90 %. This study provides crucial theoretical insights for optimizing NiTi SMA phase transformation behavior and enhancing the performance.

Multi-scale structural heterogeneity promoting hydrogen embrittlement in additively manufactured pure nickel

In this study, how physical differences in the microstructure of additively manufactured (AM) pure Ni affect its susceptibility to hydrogen embrittlement (HE) are investigated. The presence of high-density dislocation cells (DCs) and grain boundaries in AM Ni could absorb more hydrogen therein, with the DC boundaries serving as reversible hydrogen trapping sites. The DC boundaries overlapped with the grain boundaries might lead to an enhanced hydrogen diffusion therein for AM Ni. Consequently, an increased depth of hydrogen-affected region and accelerated failure process were observed in AM Ni during tensile testing due to intergranular cracking. Furthermore, the HE resistance can be slightly improved by a dislocation-cell elimination heat treatment for AM Ni-800, but it remains lower than that of traditionally manufactured Ni, primarily due to the residue of bi-modal grains with small grains along the molten pool boundaries. The underlying HE mechanism based on the structural heterogeneities at different scales for pure Ni is discussed.

Understanding process parameter-induced variability for tailoring precipitation behavior, grain structure, and mechanical properties of Al-Mg-Si-Mn alloy during solid-state additive manufacturing

Additive friction stir deposition (AFSD), a solid-state additive manufacturing technique, has excellent industrial application potential, particularly for Al alloys. However, in-depth process parameter-microstructure-property correlations are lacking, especially regarding precipitation behavior. In this work, AFSD of Al-Mg-Si-Mn alloy with various process parameter combinations was performed to understand the variation (by ∼ 70 %) in the nano/microhardness, concerning the precipitation behavior. The low nano/microhardness sample exhibited dissolution of the β” strengthening phase. However, higher nano/microhardness samples showed varying microstructural features with high dislocation density owing to fine-scale pre-β” precipitation and another sample possessed inhomogeneous β” phase distribution and β’ precipitation at the grain boundaries, thus exhibiting reprecipitation during AFSD. The variation in the grain structure was such that the high nano/microhardness samples exhibited large, elongated grains (∼11 to 13 µm) and low recrystallization fractions (∼16 –18 %) suggesting a predominantly non-recrystallized microstructure. Conversely, the lowest nano/microhardness sample exhibited the smallest grain size (∼5 µm) and, a higher recrystallization fraction (∼42 %). These findings demonstrate extensive variation in the precipitation behavior, grain structure, and mechanical properties due to the process parameters. Future applications can leverage this knowledge to tailor the microstructure and mechanical properties based on the identified process parameter combinations.

Effect of Al addition on microstructure and mechanical property of Mg-Mn-Ca-Ce based alloy

In this work, the effect of Al addition on the microstructure and mechanical properties of as-extruded Mg-0.6Mn-0.4Ca-0.2Ce-xAl (x=0, 0.1, 0.3 wt%; named as MXE, MXE01A, and MXE03A, respectively) alloys was investigated. The addition of the fifth group element Al changed the type and content of the second phase in the Mg-Mn-Ca-Ce alloys, and both Mg2Ca and Al-Mn nano-phases were precipitated in the Al-containing alloys, but more unfavorable micron-sized second phases were formed in the MXE03A alloy. In the MXE01A alloy, the high density of nanoscale second phases hindered recrystallized grain growth and contributed to the refinement of recrystallized grains to ∼0.94 μm. At the same time, the MXE01A alloy contains a high density of residual dislocations, which become obstacles to the movement of newly generated dislocations. As a result, the yield strength (YS) of the MXE01A alloy reached 330 MPa, and the elongation (EL) was maintained at 17.5 %. The present results can provide important theoretical guidance for the compositional optimization of low-cost and high-performance Mg wrought alloys.