Dual-phase Region Research Articles

Effect of rare earth yttrium and the deformation process on the thermal deformation behavior and microstructure of pure titanium for cathode rolls

This study explores the challenges associated with microstructural refinement and homogenization control for large titanium cathode rolls utilized in electrolytic copper foil production. An innovative deformation control strategy was developed by incorporating yttrium microalloying within the β→α dual-phase region to refine the hot-deformed microstructure of pure titanium. Gleeble thermal simulation tests were performed to assess the impact of rare earth Y, deformation temperatures (700–900 °C), and interpass cooling rates (5 °C/s, 25 °C/s, and 50 °C/s) on the hot deformation behavior and microstructural evolution of pure titanium. The results reveal that Y2O3 particles generated by the addition of rare earth Y enhance dynamic recrystallization through the particle-stimulated nucleation (PSN) mechanism, effectively pinning grain boundaries and impeding recrystallized grain growth. Increased interpass cooling rates lead to finer grains and higher stored energy. The mechanism for grain refinement during dual-phase deformation is described as follows: β-phase nonrecrystallization temperature deformation → rapid cooling control → α-phase recrystallization deformation control, energy storage, strain-induced dynamic phase transformation (SIDT, α→β), and dynamic recrystallization (DRX). Under experimental conditions of β-phase region deformation at 980 °C → inter-pass cooling rate of 50 °C/s → α-phase region deformation at 750 °C, the addition of rare earth yttrium achieved the most effective grain refinement, reducing the average grain size to 2.56 μm.

Microstructural Development, Deformation Behavior, and Texture Evolution Investigation during Hot Compression of a Dynamically Recrystallized Ti-5Cu Alloy in the Dual (α + β) Phase Region

Microstructural Development, Deformation Behavior, and Texture Evolution Investigation during Hot Compression of a Dynamically Recrystallized Ti-5Cu Alloy in the Dual (α + β) Phase Region

The effects of forging strategies on microstructures and mechanical properties of a Ti–5Al–5Mo–5V–1Cr–1Fe near β-titanium alloy

The present study systematically investigated the influence of forging strategies on the microstructures and deformation behaviors of a Ti–5Al–5Mo–5V–1Cr–1Fe (Ti-55511) near β-titanium alloy. Microstructure analysis revealed that the as-cast alloy exhibited a basket-weave structure predominantly comprised of lamellar α phase. Three different forging methods were used to adjust the morphology of the primary α phase during the final two forging steps: 1) dual-phase (825 °C) + dual-phase forging (DD sample), 2) dual-phase + β single-phase (900 °C) forging (DS sample), and 3) β single-phase + dual-phase forging (SD sample). After standard heat treatment, the DD samples exhibited equiaxed αp due to sufficient deformation in dual-phase region, while DS samples transformed into lamellar shape due to αp reforming during the cooling process of the final β single-phase forging. In contrast, the SD samples displayed short-rod αp due to reforming in the single-phase region and insufficient deformation in the dual-phase region. All these αp and βt phases can hinder dislocation motion to enhance the strength. The DS sample exhibited the best combination of strength, ductility, and impact toughness. During tensile deformation, planar dislocation slip and {101‾1} twinning were dominant in the αp, while wave slip occurred in the βt phase. The fracture behavior transitioned from brittle to ductile after forging and heat treatment. Overall, this study offers a practical and effective method for optimizing the mechanical properties of the Ti-55511 alloy.

Distinct Microstructure and Hardness of Zr-2.5Nb Alloy Annealed in Lower and Upper Dual-Phase Regions: the Role Played by Nb

Distinct Microstructure and Hardness of Zr-2.5Nb Alloy Annealed in Lower and Upper Dual-Phase Regions: the Role Played by Nb

Effect of primary α phase fraction on deformation mechanism of Ti-1023 alloy at room temperature

The fraction and morphology of α phase have important effects on the mechanical properties and deformation mechanism of Ti-1023 alloy. Here, the tensile stress-strain curves and deformation mechanisms with the fraction of α phase are discussed in detail. As α phase fraction decreases from 67.5 % to 12.6 %, there is a negative correlation coefficient between the yield strength and α phase volume fraction of Ti-1023 alloy, and its fitting equation is obtained. When the fraction of α phase is decreased to 12.6 %, the elongation and ultimate tensile strength of the alloy are 31.09 % and 845.52 MPa, as well as a transition from single to double yielding phenomenon, which is caused by stress-induced martensitic transformation (SIMT). When the fraction of α phase is high, the deformation mechanism is dominated by dislocation slip and mechanical twinning of the α phase. When the fraction of α phase is low, the deformation mechanism is dominated by mechanical twinning of the β matrix and stress-induced martensitic transformation (SIMT). The relationship between α phase fraction and deformation mechanism and mechanical properties of Ti-1023 in α+β dual phase region is studied, which provides a template to guide the development of comprehensive mechanical properties of metastable β titanium alloy in α+β dual phase region.

Deciphering the composition-microstructure correlation in low-density FeMnAlC steels with machine learning

FeMnAlC steels have been regarded as prospective candidates for the advanced high-strength steel with reduced density. However, the correlation between the complex steel composition and the resulting microstructure remains unclear. This study presents a robust and efficient approach for establishing the correlation between the composition and microstructure of low-density FeMnAlC steel using a machine learning algorithm. By employing classification and regression models, we successfully predicted four significant characteristics: the existence of the κ phase, a dual-phase region (γ + κ) at the aging temperature, a solitary γ phase region, and the volume fraction of the κ phase. Notably, the elements Al and C, with a particular emphasis on Al, exert significant influence on the phase structure. For example, when the Mn element content is 30 wt%, an estimated minimum Al content of around 4 wt% is required to guarantee the existence of the κ phase. Furthermore, the anticipated content range of Al and C required for the existence of the (γ + κ) duplex region at the aging temperature spans from 4.5 to 9.3 wt% and 0.4 to 1.1 wt%, respectively. Ultimately, the Fe-30Mn-8Al-1C steel was chosen for experimental validation, and the predicted characteristics exhibited excellent agreement with the experimental results. Our research offers a roadmap for the development of low-density steel, and the approach we devised holds promise for application in other metallic materials as well.

Microstructures and mechanical properties of Ti-55511 alloy subjected to rolling in the α+β dual-phase region

In this study, dual-phase region rolling was conducted on a Ti-55511 alloy with different initial rolling reductions in the single-phase region. The mechanical properties and microstructural characteristics of the alloy with different deformation conditions were investigated. Microstructure observations show the formation of a heterogeneous structure with a gradient size distribution of the α phase at the recrystallized grain boundaries, induced by the non-uniform stress distribution. The α phase and the β matrix exhibit the Burgers orientation relationship in the recrystallized region with the gradient structure. However, in the unrecrystallized region of the partially recrystallized specimens and in the grain interiors of the fully recrystallized specimens, the α phase and the β phase exhibit Pitsch-Schrader orientation relationship (P–S OR). A large number of the nano-sized α" martensite bands were observed after the dual-phase region rolling. These bands originated from the α/β interfaces and grew towards the interiors of the α phase. As the deformation increased, these nano-bands underwent a transformation into the {10 1‾ 1}α deformation twins, resulting in the fragmentation of the α phase. Mechanical testing results show that the mechanical properties of the alloy can be improved by the dislocation strengthening, the generation of profuse α phase and other microstructures including the heterogeneous distribution of the α phase, the nano-sized α" martensite and the {10 1‾ 1}α deformation twins.

Effect of warm rolling and heat treatment on heterogeneous austenite morphology and tensile property of 3Mn steel

Facing the current lack of clarity in temperature selection mechanisms for warm rolling in medium Mn steel, three warm rolling methods were conducted in 3Mn steel according to the rolling temperatures in the dual-phases region or ferrite region. Subsequently, the effect of heat treatment on the austenite morphologies and tensile properties of warm-rolling samples was studied. Rolling in dual-phase regions (750 °C) led to heterogeneous austenite morphology composed of equiaxed and lamellar grains while rolling in the ferrite region (600 °C) resulted in significant cementite precipitation and the absence of retained austenite. Warm rolling promoted the formation of dislocation cells in the lath-like grains, and they did not evolve into grain boundaries completely because low deformation temperature didn’t trigger the complete dynamic recrystallization. Tempering after rolling provided a significant enhancement in plasticity through the enrichment of C and Mn in austenite and the formation of multiple heterogeneous austenite morphologies with equiaxed, coarse lath-like and fine lamellar grains. In addition, superlattice structures in the matrix are formed through the formation of stacking fault networks and the spinodal decomposition. Ultimately, the exceptional properties were achieved in 3Mn steel, with an ultimate tensile strength of 1409 MPa and a total elongation of 27.3 %.

Synergistic control of plastic instability behavior by multi-heterogeneous austenite morphologies and stacking fault networks in 3Mn steel

A multi-heterogeneous austenite morphologies consisting of equiaxed + coarse lath-like + fine lamellar austenite grains is constructed in 3Mn steel through warm rolling in the dual-phase region and tempering. Lower tempering temperature induces a more uniform distribution of multi-heterogeneous austenite morphologies and effectively preserves the stacking fault network formed during warm rolling, which catches exceptional mechanical properties (ultimate tensile strength of 1591 MPa and total elongation of 24.5 %) as well as suppresses plastic instability behaviors including yield plateau and stress serrations in 3Mn steel.

Improvement of shape recovery by controlling the microstructure and mechanical properties in a thermomechanically-treated Fe-based alloy

In this research, the effects of thermomechanical treatment including heavy cold rolling and post-deformation annealing on the improvement of shape recovery in an Fe–9Ni–7Mn (at.%) martensitic alloy were investigated. Experimental results showed that the 80 % cold rolling produced a little fraction of strain-induced austenite phase in the martensitic matrix due to the strain concentration in the microstructure and the temperature rise under deformation. During post-deformation annealing at 590 °C in a dual phase (α+γ) region, a greater fraction of the austenite was introduced in the martensitic matrix such that its amount first increased by increasing the annealing time to 1.8 ks and then decreased at a more time of reversion. The microstructural evolution revealed that the austenite reversion under post-deformation annealing initially occurred by a shear nature at the early steps of reversion and then continued by diffusion. Tensile testing represented a good mixture of a relatively high ultimate tensile strength of ∼780 MPa and proper ductility of ∼8.5 % in the post-deformation annealed (PDA) sample for 0.9 ks. In addition, the shape memory properties were examined under the conditions of cold rolling and post-deformation annealing. The results showed a maximum shape recovery rate of ∼23 % for the cold rolled specimen which increased to ∼50 % after post-deformation annealing for 0.9 ks. The presence of a relatively high amount of retained austenite with proper stability and strength in the microstructure of the PDA sample for 0.9 ks was the reason for achieving the highest value of shape recovery.

Microstructure evolution and mechanical properties of Ti-1023 alloy during β slow cooling process

Microstructure evolution and mechanical properties of Ti-1023 alloy during cooling from single-phase region to dual-phase region with the cooling rate of 1 °C/min were systematically investigated. As the final cooling temperature decreased, grain boundary α′ martensite (α′GB), grain boundary α phase (αGB), Widmanstatten grain boundary α phase (αWGB), and Widmanstatten intragranular α phase (αWI) were sequentially precipitated. Correspondingly, mechanical properties and deformation mechanisms of Ti-1023 alloy changed significantly. When the final cooling temperature was higher than 700 °C, tensile curve showed an obvious double-yielding phenomenon with elongation >20%. Whereas the final cooling temperature was lower than 700 °C, and the double-yielding phenomenon disappeared. This was mainly attributed to the fact that β stability of Ti-1023 alloys was enhanced with the increase of α(α′) precipitated phases. And the room temperature deformation mechanism gradually changed from stress-induced α″ martensitic phase transformation to dislocation slip. Furthermore, strengthening mechanism of Ti-1023 alloy was analyzed in combination with grain size and precipitated phase effects.

Hot deformation behavior and dynamic recrystallization of dual-phase (CrCoNi)94Al3Ta3 medium entropy alloy

The microstructural evolution and dynamic recrystallization (DRX) behavior of a dual-phase (CrCoNi)94Al3Ta3 medium entropy alloy (MEA) was studied using thermal simulated test machine at temperature ranging from 1000 ℃ to 1150 ℃ under strain rate of 0.001–1 s−1. The initial dual-phase microstructures were equiaxed grains with face-centered cubic structure (γ) and L12 phase (γ') precipitated homogeneously in the grain, besides a certain amount pinned at boundary. The stress-strain curves exhibited a typical DRX softening behavior, in which the flow stress was sensitive to deformation temperature and strain rate. The deformation activation energy was calculated to be 612.04 kJ/mol (γ + γ' dual-phase region) and 391.02 kJ/mol (γ single-phase region) respectively. The appropriate hot deformation parameters of (CrCoNi)94Al3Ta3 MEA were 1100 ℃/0.001 s−1 and 1150 ℃/0.01 s−1 based on the hot processing map and deformation microstructure. The discontinuous DRX transformed to continuous DRX depended on deformation temperature, this was because that the interaction between precipitates and dislocation was weakened as the deformation temperature beyond the dissolution temperature of L12 phase.

Hot deformation behavior and flow stress modeling of coarse-grain nickel-base GH4151 superalloy ingot materials in cogging

Due to the high deformation resistance and poor thermal ductility of the new cast GH4151 alloy ingots, cracks are easy to occur during cogging process. For clarifying the effects of deformation parameters on microstructural evolution and dynamic recrystallization (DRX) nucleation mechanisms. In this work, the causes of crack formation and extension were first investigated using SEM and EBSD. The study revealed that the reasons for crack formation and propagation are the MC carbides at the original grain boundaries, large-size γ′ phase, residual eutectic phases, and tiny pores near the grain boundaries. Subsequently, a series of hot compression tests were performed using a Thermecamastor-Z thermo-mechanical simulator at temperatures ranging from 1080 °C to 1160 °C and a strain rate range of 0.01–10 s−1. The constitutive equation of the Arrhenius model and the hot working map was established, determining activation energy(Q) of 1086.58 kJ·mol−1. Large-size γ′ is coherent with the matrix. For the γ+γ′ dual-phase region, heterogeneous strain-induced dynamic recrystallization (HDRX) occurs, and discontinuous dynamic recrystallization (DDRX) is the main nucleation mechanism for DRX. However, for γ single-phase region, DDRX plays a more significant role. Furthermore, the MC phase (>1 μm) has different crystal orientations with the γ matrix and acts as sites for recrystallization through particle-stimulated nucleation (PSN). Finally, a fine and uniform grain structure can be obtained in the temperature range of 1120–1135 °C and the strain rate range of 0.1 s−1 to 1 s−1.

Unveiling the dynamic softening mechanism via micromechanical behavior for a near-β titanium alloy deformed at a high strain rate

For near-β high-strength titanium alloys, rheological softening is the key step during thermal deformation to determine the microstructure and mechanical properties. Nevertheless, the intrinsic softening mechanism during the rheological stage is still an open question due to the special complexity of the process. In this study, the deformation process of near-β titanium alloy TC18 (Ti–5Al–5Mo–5V–1Cr–1Fe, wt.%) in a dual-phase region at a high strain rate was investigated. The micromechanical behavior of TC18 alloy during thermal deformation at 785 °C and 0.1/s was revealed by using in-situ high-energy X-ray diffraction (HEXRD). The stress partitioning and microstructure evolution mechanism for this alloy were discussed in detail. It has been confirmed that the main softening mechanisms of TC18 alloy during thermal deformation are dynamic recovery (DR) and continuous dynamic recrystallization (cDRX). The stress partitioning between constituent phases featured by higher stress in the α phase than in the β phase induces an inhomogeneous strain field near α phase lamellae to promote the dislocation pile-up in subgrains. The cDRX process of β grains is composed of dislocation slipping, DR and subgrains formation, and transformation of recrystallized grains with high-angle grain boundaries (HAGB). Schmid factor and micro stress have a remarkable effect on dynamic recrystallization (DRX) behavior. The soft <200>β//LD oriented grains are more likely to undergo cDRX than the hard <111>β//LD oriented grains. This work may have implications for understanding the deformation mechanism and provide a fundamental basis for selecting appropriate processing technology for near-β titanium alloys.

Microstructure and creep properties of graded transition joints between nickel-based alloys and martensitic heat-resistant steels

Interfacial failure can significantly reduce creep lifetime of dissimilar metal welds (DMWs), bringing great economic losses and safety issues to power plants. The fundamental reason for interfacial failure is steep gradient of chemical compositions between different metals. Many researchers have made great efforts to develop graded transition joints (GTJs) aiming to eliminate the steep gradient, but the results of creep tests were rarely seen. The goal of the present work was to determine whether GTJs could effectively prolong creep life compared with conventional DMWs, and further to clarify the reason. In our study, a GTJ between creep-resistant steels and nickel-based alloys was fabricated by a dual-wire TIG method. It was shown that the gradients of chemical compositions and hardness were significantly reduced over a longer distance of ∼17 mm than that of ∼100 μm in conventional DMWs, and microstructures varied from full martensite to mixed martensite + austenite, and finally to full austenite. The formation of dual-phase region composed of martensite and austenite was due to the segregation behavior of Cr, Ni, and Mo to inter-dendritic regions during solidification. Creep tests showed that creep life of the GTJ was much shorter than conventional DMWs, and two different failure modes were found, one of which failed in COST E HAZ (creep life 790 h), and the other in the nickel-rich martensite zone of transition region (creep life 435 h). The failure in COST E HAZ was the combined results of creep, plastic deformation and oxidation, and the failure in nickel-rich martensite zone was due to localized austenization induced shrinkage during creep tests. Nickel-rich martensite was not observed after post weld heat treatment (PWHT) due to the sluggish kinetics of nickel atoms diffusion, while creep tests provided enough time for nickel atoms to diffuse into austenite, which transformed into martensite with nickel enriched after creep tests. Based on the results, it is concluded that the GTJ might not be a feasible solution to extend creep life of DMWs at least in the current situation, due to the inevitable occurrence of nickel-rich martensite.

Effect of Mn and Mo on the microstructure and electrical resistivity of Ti-Al alloy prepared by mechanical alloying and spark plasma sintering

High electrical resistivity titanium alloys can effectively reduce the attenuation of eddy current shielding to magnetic field, and have a good application prospect in magnetic compression devices. The Ti-Al alloys alloyed with Mn and Mo were prepared by mechanical alloying and spark plasma sintering in this study. The effect of alloying elements Mn and Mo on microstructure characteristics, electrical resistivity and micro-hardness of Ti-Al alloy, as well as the effect of annealing on Ti-Al-Mn-Mo quaternary alloy were investigated. The results show that the microstructure of Ti-9Al-xMn (x = 0, 1, 2, 4, 6 wt%) alloys was transformed from a single-phase α of Ti-9Al alloy to multiphase consisting of α + β + α2 phases. With the increase of Mn content, the number of α phase decreased, and (β + α2) dual phase region increased. The electrical resistivity of Ti-9Al-xMn alloys increased with the increase of Mn content and decreased as Mn content was more than 4 wt%. The Ti-9Al-4Mn alloy had the electrical resistivity of 2.176 μΩ‧m. The α phase grains in Ti-8Al-4Mn-1Mo and Ti-7Al-4Mn-2Mo were refined by Mo alloying, the content of α2 phase reduced, and β phase increased compared with Ti-9Al-4Mn alloy. The electrical resistivity of the quaternary alloys increased and the micro-hardness decreased. The Ti-8Al-4Mn-1Mo alloy had the higher electrical resistivity (2.252 μΩ‧m) and micro-hardness (627 HV). Annealing slightly decreased the micro-hardness of Ti-8Al-4Mn-1Mo alloy, but the electrical resistivity remained at the level of as-sintered alloy.

Optimal tensile properties of laser powder bed fusion hereditary basket-weave microstructure in additive manufactured Ti6Al4V

Post-heat treatments applied to laser powder bed fusion ( L -PBF) additive manufactured (AM) Ti6Al4V components aim to achieve good strength-ductility matching through tailoring microstructures, including microstructural features that span across length scales, such as prior β phase grains, laths and precipitates. The effects of initial prior β microstructure and subsequent solution treatment and aging (STA) on mechanical properties have been investigated. In all cases, the increase of solution temperature and aging treatment improve the strength due to solution-strengthening and precipitation-strengthening. It is confirmed that the L -PBF hereditary basket-weave microstructure possesses better tensile properties than other microstructures, with an ultimate tensile strength of 1185 ± 6 MPa and an elongation of 15.3 ± 0.3%. The optimal tensile properties stem from the fine structured primary α and transformed β phases in the retained L -PBF prior β grains, which are both beneficial to improving the work-hardening capacity, as well as enhancing the resistance to crack initiation and propagation. This finding can guide the optimization of mechanical properties for the L -PBF additive manufactured Ti6Al4V components. • Multi-heat treatments in single-phase region and dual-phase region are performed. • Retained L -PBF characteristics possess optimal tensile properties. • Fine structures contribute to good performance in the work hardening. • Fine structures enhance the resistance to crack initiation and propagation.

Crystallographic texture and structure formed in rolled sheets of zirconium alloys during annealing

This paper examines the processes of recrystallization in sheets of Zr &ndash; 2.5% Nb alloy rolled down to a 50&ndash;90% deformation and annealed at 610 oC for 1, 3 and 5 hours. The heating rate varied from 10 to 100 oC/min. With the help of X-ray structure and texture analysis, the authors looked at optimizing the crystal structure of the deformed alloy while examining changes in the crystallographic texture. It was established that annealing of Zr &ndash; 2.5% Nb alloy sheets performed at the temperature that corresponds to the dual phase region&nbsp;&alpha; +&nbsp;&beta; of an equilibrium phase diagram also leads to recrystallization, as it happens when applying the annealing temperature of 580 oC. However, an 11% increase in the concentration of the additional phase suppresses changes in the crystallographic texture, which may be due to the predominant precipitation of &beta;-zirconium at grain boundaries. At the same time, the growth of recrystallized grains still follows the main regularities of orientation: the orientation of growing grains corresponds to the texture maximum slopes of the direct pole figure (0001); an increased pole density was observed on the difference charts of the direct pole figure {10.0}, which is indicative of the presence of grains that are disoriented to the deformed matrix at 30o around the base normals. It is shown that the contribution of the above mentioned processes is determined by the type of initial texture, the annealing temperature, the heating rate and the amount of &beta;-phase. An extended annealing time (from 1 to 5 hours) at the temperature of the dual phase region does not cause any significant change in the crystallographic texture.This research was funded by the Ministry of Science and Higher Education of&nbsp;the Russian Federation; Agreement No. 075-15-2021-1352.

Size disorder: A descriptor for predicting the single- or dual-phase formation in multi-component rare earth zirconates

Eighteen different 5-component equimolar rare earth zirconates were successfully synthesized by solid state reaction method. Among them, 5 of them exhibit a high-entropy fluorite structure, 8 have a high-entropy pyrochlore structure, and the remaining 5 have dual-phase structures of both pyrochlore and fluorite. For high-entropy rare earth zirconates with single-phase structure, the lattice parameter is almost linearly correlated with the average cation radius ratio. In combination with a large number of previous reports, a summary is made to study the synergistic effects of the average cation radius ratio, configuration entropy and size disorder on the single-phase formation ability of multi-component rare earth zirconates. The conclusion verifies that the size disorder of about 5% is the boundary for the multi-component rare earth zirconates to form a single-phase or dual-phase region, while the average cation radius ratio of 1.467 is the demarcation between a pyrochlore and a defective fluorite structure in the single-phase zone, and the configuration entropy had less effect. Excessive size disorder leads to the enrichment or barrenness of certain components, which is the main reason for the formation of dual phase ceramics. • 18 Different equimolar 5-component rare earth zirconates have been prepared. • The size disorder ( δ *) can predict the single-phase formation ability of zirconates. • δ * = 5% is the boundary between the single- and dual-phase rare earth zirconates. • The single-phase forming ability of rare-earth zirconates is independent of entropy.

Investigation of High-Temperature Constitutive Behavior of Ti555211 Titanium Alloy Subjected to Plastic Deformation in the Different Phase Regions

Ti555211 titanium alloy is subjected to plastic deformation in the dual-phase (α + β phase) zone and single-phase (β phase) zone at various deformation temperatures and strain rates. High-temperature constitutive equations of the alloy in the dual-phase zone and single-phase zone are established in order to describe deformation behavior of the alloy in the different phase zones. By comparing the constitutive equation of the alloy in the dual-phase zone with that of the alloy in the single-phase zone, the deformation activation energy of the former was found to be higher than that of the latter. It is obvious that the deformation activation energy of α phase is obviously greater than that of β phase. Furthermore, the microstructural evolution of the alloy is different in the dual-phase zone and single-phase zone. When the alloy was subjected to plastic deformation in the dual-phase zone, the size of the grains in the β phase increased with the decreasing strain rate. When the alloy was subjected to plastic deformation in the single-phase zone, the size of the grains in the β phase considerably increased with the increasing deformation temperature. In particular, in the microstructures of the alloy subjected to plastic deformation in the single-phase region, the elongated grains can be observed at higher strain rates. Furthermore, it is more difficult for the alloy to induce plastic deformation in the dual-phase region than in the single-phase region.