Solution-treated Alloy Research Articles

Degradation Kinetics of As-Cast and Solution-Treated (T4) Magnesium-Based Alloys for Biodegradable Orthopedic Implants

Degradation Kinetics of As-Cast and Solution-Treated (T4) Magnesium-Based Alloys for Biodegradable Orthopedic Implants

Tailoring Deformation Homogeneity of WE43 Alloy through Strain Rate Sensitivity and Back Pressure during Equal Channel Angular Pressing

AbstractEqual channel angular pressing (ECAP) of the magnesium alloys at room temperature owing to their limited workability is challenging. Successful ECAP processing of WE43 magnesium faces two main difficulties, heterogeneous distribution of the strain rate and also tensile strain accommodation on the top surface of the workpiece, leading to catastrophic segmentation of the alloy. In this paper, strain rate sensitivity (SRS) was studied to adopt a proper preprocessing of the material before ECAP processing. The SRS exponents, obtained from compression tests, revealed that solution treatment reduced the SRS of the alloy. To mitigate strain accommodation, an ECAP core-sheath configuration was used to induce back pressure for the sake of deformation homogeneity improvement. A combination of experimental processing and 3D finite element method simulations was applied to the solution-treated WE43 alloy with different core sizes and sheath materials. By finding the optimized core sizes and sheath materials with higher strengths, the differences in microhardness and equivalent plastic strain were reduced. Besides, the adequate magnitude of back pressure and the imposed fully compressive stress prevent fragmentation of the WE43 core during ECAP. After stepwise modifications, the plastic strain inhomogeneity index decreased from 1.340 to 0.671.

Microstructure evolution and aging behavior of surface-nanocrystallized WE43 Mg alloy by ultrasonic shot peening at a cryogenic temperature

In this study, the microstructure evolution and aging behavior of surface-nanocrystallized WE43 Mg alloy induced by ultrasonic shot peening at a cryogenic temperature were examined. The results reveal that the original coarse grains with an average grain size of 46.7 μm were refined to nanocrystalline grains with 31.5 nm in the nanocrystalline region, demonstrating a marked grain refinement effect. After aging treatment, the nanocrystalline region experienced two aging stages. During Stage Ⅰ, there was a rapid increase in hardness, and in Stage Ⅱ, it reached a maximum of 154.2 HV, representing a 105.6% improvement over the solution-treated alloy. Further microstructural characterization indicates that solute segregation initially occurred along the grain boundaries, leading to a rapid increase in hardness during Stage Ⅰ. Subsequently, two types of precipitates were observed both at the grain boundaries and within the grains during Stage Ⅱ, with the combined effects of solute segregation and precipitation contributing to a further increase in hardness.

Effect of heat treatment on the microstructure and mechanical properties of Mg-Gd-Y-Zr alloys fabricated by wire arc additive manufacturing

ABSTRACT Wire arc additive manufacturing (WAAM) technology is expected to be used for the fabrication of large and complex magnesium alloy components. In this work, Mg-9.54Gd-1.82Y-0.44Zr (wt.%, GW92) alloy thin-walled components were fabricated by cold metal transfer (CMT) arc in CMT-Advance mode. The microstructure of the WAAMed GW92 alloy consists of fine equiaxed ɑ-Mg grains with an average size of ∼17 μm, eutectic phases, β" phase, cubic phases, and Zr particles. The short-term high-temperature solution treatment at 525 ℃ for 25 minutes significantly reduced the content of the eutectic phase, resulting in a significant increase in elongation (EL) (13.5 ± 0.3%). The peak aging time of the solution-treated GW92 alloy at 225 ℃ for 12 h. The WAAM-T6 sample showed a significant increase in strength while maintaining good ductility, with a yield strength (YS) of 235 ± 3 MPa, ultimate tensile strength (UTS) of 360 ± 7 MPa, and elongation of 10.8 ± 1.7%. The synergistic strength and ductility properties of Mg-Gd-Y-Zr alloys fabricated by the WAAM process were significantly impacted by the short-term high-temperature solution + aging treatments to preserve the fine grain and high-density.

Deformation behavior and failure mechanism of AA7075 alloy during the cryogenic temperature-assisted incremental sheet forming process

High-strength aluminum alloys are potential structural materials for thin-walled aerospace and automotive components. However, the limited formability at room temperature (RT) hinders their wide industrial application. In this study, a cryogenic temperature-assisted incremental sheet forming (CT-ISF) process for manufacturing 3D curved thin-walled structures was proposed. An experimental platform for CT-ISF was established to form AA7075 alloys. We found that the formability of the solution-treated AA7075 alloy sheet was greatly improved under the cryogenic environment without sacrificing its strength. In combination with double pass forming process, the formability of the sheet can be further improved. The stable deformation of the sheet is promoted due to the suppression of the Portevin-Le Chatelier (PLC) effect at CT, which reduces axial force fluctuations during the forming process. The line roughness value of the meridional direction was reduced by 36.8% at CT due to the enhanced work-hardening and the utilization of MoS2 lubricant. In terms of microstructural evolution, we found that the fracture morphology of the formed parts changed from tensile fracture at RT to shear fracture at CT. The improved formability was attributed to increased Goss and E texture contents, delay in dislocation evolution, and suppression of the PLC effect. This work introduces a novel CT-ISF process that significantly enhances the formability of high-strength Al alloy. In particular, it unravels the enhancement mechanism of formability in the CT-ISF process, providing theoretical support for further research.

Development of highly corrosion-resistant Mg-Al-Y extruded alloy via regulating the Mg17Al12 phase

A highly corrosion-resistant AW90 extruded alloy (Mg-9Al-0.2Y wt %) was developed via alloying and solution-aging treatment (PW = 0.14 mm/y). The solution-treated AW90 alloy exhibits the most severe localized corrosion due to the strong micro-galvanic acceleration effects. The finely dispersed Mg17Al12 phase promotes the strong quasi-passive behavior and uniform corrosion of the aged AW90 alloy due to the formation of a dense and uniform corrosion product film. The high corrosion resistance of the aged AW90 alloy is attributed to the formation of a Mg-Al layered double hydroxide film, which has stronger resistance to chloride ions.

Solute clustering and its role in a titanium alloy made by laser powder bed fusion

In recent years, atomic clusters and composition undulation have been observed in a number of concentrated solid-solution alloys and were found to be beneficial for strength-ductility synergy. Some reports are also available on the observation of atomic clusters in body-centred cubic metastable β titanium alloys but the role of these atomic clusters in mechanical property development is unclear. In this study, we report the formation of solute atomic clusters in an additively manufactured and solution-treated metastable titanium alloy and investigate their role in deformation and strengthening mechanisms. It was found that the atomic clusters together with ultrafine ω precipitates present in the material effectively pin dislocation motion and contribute to an ultrahigh yield strength. The interaction between dislocations and solute atomic clusters leads to an increased shear stress necessary for dislocation motion. The atomic clusters and the resulting chemical undulation generate pronounced atomic strain fluctuations and distortions with alternating tensile and compressive strain fields, which lead to large local internal stresses and thus resistance to dislocation glide. Cross slip has also been frequently observed in the additively manufactured and solution-treated metastable titanium alloys, which is beneficial for strain hardening and ductility. We also reveal that thermal cycling in the alloy can lead to a significant influence on the microstructural evolution. During solidification and cooling upon laser powder bed fusion, only β and athermal ω precipitates form. With repetitive thermal cycling, the microstructure transforms into α + β grains together with isothermal ω particles. The present findings suggest that solute atom clustering can be introduced through proper selection of solute elements, providing a new strengthening mechanism for titanium alloys.

Effect of solid-solution treatment on high-temperature properties and creep fracture mechanism of laser powder bed fused Inconel 625 alloy

Laser powder bed fusion (LPBF) has been widely used for fabricating Inconel 625 (IN625) alloy, and it is widely regarded as a promising manufacturing technology. However, during high-temperature service, the γ″ strengthening phase of LPBFed IN625 gradually transforms into the detrimental δ phase. Controlling the morphology and distribution of precipitates is necessary for optimizing high-temperature performance. This study compared the as-built and 1090 °C solution-treated LPBFed IN625 alloy and investigated the microstructure evolution, tensile properties, and creep fracture behavior at a high temperature of 815 °C. The results show that the solid-solution treatment improves the creep ductility of LPBFed IN625 alloys at 815 °C by forming a high percentage of twinned boundaries and eliminating dislocations. The formation of coarsened needle-like δ phases and carbides during creep reduces the strength of the grain boundaries and is responsible for creep fracture failure. During creep of the as-built samples, the irregular Laves phase between the columnar dendrites gradually transforms into plate-like δ phases and M6C carbides uniformly and densely distributed within the columnar grains. The precipitation-strengthening effect of these fine precipitates, combined with the initial high density of dislocations and strong texturing effect, brings favorable high-temperature strength and creep fracture life but consequently leads to low creep ductility.

A comparative study on cryogenic formability and paint baking property of AA7075 alloy sheets tempered at fast retrogressed and pre-aged conditions

Forming at cryogenic temperatures provides a new approach to the formability improvement of 7000-series high-strength aluminum alloys. However, the cryogenic forming process based on solution-treated (W) or peak artificial aged (T6) alloys cannot meet the demands of autobody manufacturing for good formability, high post-formed strength and high efficiency simultaneously. The fast retrogression (FR) treatment of AA7075-T6 and pre-aging (PA) treatment of AA7075-W are elaborately designed to tailor a pre-hardened AA7075 alloy, which has good cryogenic formability and relatively high initial strength, and can be further strengthened by paint baking in high efficiency. The results show the optimum fast retrogression temperature for AA7075-FR is 400 °C, at which the sample can acquire a cryogenic elongation of 29.2% and obtain 90% of initial T6 sheet tensile strength by the combined effect of cryogenic pre-deformation and subsequent paint baking treatment. The optimum pre-aging temperature for AA7075-PA is 120 °C, at which the sample can acquire a cryogenic elongation of 31.0% and exceed 96% of tensile strength of AA7075-T6 after paint baking treatment. The comparative study demonstrates that the supersaturated solid solution matrix with an appropriate proportion of GP zones and η′ phases, but few Cr-containing dispersoids and precipitate free zones, is an ideal pre-hardened microstructure to get a good combination of cryogenic formability and final strength. The precipitation of GP zones and η′ phases is prior to the formation of precipitate free zones during pre-aging of AA7075-W, making the pre-aged hardening cryogenic forming process more suitable for automobile industry.

Microstructures, transformation temperatures and superelastic properties of the rapidly solidified (TiZrHf)50Ni25Co10Cu15 HESMAs

In this study, the effects of the rapid solidification process on microstructures, transformation behaviors and superelastic properties of the multi-component (TiZrHf)50Ni25Co10Cu15 (at%) high-entropy shape memory alloy (HESMA) were investigated. The as-spun (TiZrHf)50Ni25Co10Cu15 fibers were prepared by a rapid solidification process. The solution-treated (TiZrHf)50Ni25Co10Cu15 alloy bulk specimen consisted of a (NiCoCu)-rich matrix, (TiZrHf)2(NiCoCu)-type phase and carbide, while the as-spun fiber specimen consisted of (TiZrHf)-rich matrix and carbide. The (TiZrHf)2(NiCoCu)-type phase is dissolved in the matrix of as-spun fibers due to the rapid solidification process. The martensitic transformation start temperature of the (TiZrHf)50Ni25Co10Cu15 alloy increased from 53.5 °C to 91.5 °C after the rapid solidification process. Both the (TiZrHf)50Ni25Co10Cu15 alloy bulk and fiber specimens showed clear superelasticity and the total superelastic recovery strain increased from 4.6 % to 5.7% after the rapid solidification process.

Assessing fatigue crack growth thresholds for a Ti-6Al-4V (STOA) alloy using two experimental methods

Fatigue crack growth rate behavior in the threshold and near-threshold regimes for a Ti-6Al-4V solution-treated and over-aged (STOA) alloy was investigated using two test procedures: i) accelerated load reduction (ALR) utilizing faster load-shed rates than recommended in the ASTM standard E647 load-reduction (LR) test procedure, and ii) compression pre-cracking constant-amplitude (CPCA) or load-increasing (CPLI) and load-reduction (CPLR). Fatigue crack growth tests were conducted on compact, C(T), specimens (B = 6.35 mm) with two different widths (W = 51 and 76 mm) at two stress ratios (R = 0.1 and 0.7). The crack-growth-rate test data were compared to previous test data produced from the same batch of material using the ASTM LR and CPCA test procedures that were tested on C(T) specimens (W = 25, 51 and 76 mm) over a wide range in stress ratios (R = 0.1, 0.4, and 0.7).Although none of the load-reduction test procedures provided a good representation of the threshold value (ΔKth) at low R, the CPCA test procedure was the most promising. The LR, ALR, and CPLR test procedures were influenced by prior loading history, leading to higher ΔKth values and slower crack growth rates in the threshold regime due to a rise in the crack-opening loads. The LR and ALR tests at R = 0.1 and shed rates of −0.08, −0.32, and −0.95 mm−1 yielded ΔKth values that were 15 to 38 % higher than the estimated threshold stress-intensity factor range (ΔK*th)R=0.1 based on the crack-closure model (FASTRAN). The compression pre–cracking test procedures are more accurate alternatives for developing threshold and near-threshold fatigue crack growth rates. Specifically, the CPLR test procedure produced a ΔKth value that was 8–18 % higher than (ΔK*th)R=0.1. Additionally, LR and ALR tests produced different ΔKth values as a function of the specimen width for a given load ratio, which violates classical fracture mechanics principles. In addition, the spread in the ΔK-rate data in the low-rate regime was larger than the spread in the mid-rate regime as a function of R, a term referred to as “fanning”. In contrast, the CPCA test procedure produced consistent crack growth rates over the same range of ΔK values examined, independent of the specimen width and these data did not exhibit “fanning” with R. Further research is necessary to develop standard test procedures capable of providing a more definitive representation of the ΔKth value in the threshold regime. However, FASTRAN can serve as a crucial tool in aligning the actual ΔKth values with those obtained through CP testing, thereby bridging the gap and enhancing the reliability of the results.

Post-processing ageing treatment of friction surfaced Al-16Si alloy: experimental and theoretical studies

In this study, we investigated the impact of ageing heat treatment following friction surfacing of a solid solution-treated Al-16Si alloy on coating geometry, microstructure, and wear resistance. We employed a simulation using the smoothed-particle hydrodynamics (SPH) method alongside experimental analysis. The simulation results revealed that as the rotational speed increased from 600 to 1000 rpm, the coating efficiency decreased significantly from 31.2 to 13.1%. When comparing the coating to the substrate and the consumable rod, it was seen that after ageing heat treatment, the wear rate of the coating made at a rotational speed of 600 rpm dropped by a lot, by 70% compared to the substrate and by 53% compared to the consumable rod.

Enhanced strength in Pt–25Au–25Cu–25Ni medium-entropy alloy by a combination of cold working and aging

Precious metals and alloys are widely used in the aerospace industry and microelectronic devices due to their excellent chemical stability and electrical properties. However, the expensive price limits their broad use. The multi-principal element approach shows the ability to reduce the cost and retain desirable properties. Therefore, a precious metal medium entropy alloy, Pt–25Au–25Cu–25Ni, was designed and prepared, and the effect of annealing temperature on the microstructure and mechanical and electric properties of Pt–25Au–25Cu–25Ni alloy was studied. The alloy is a face-centered cubic phase after annealing at temperatures above 850 °C. The decomposition along the grain boundaries occurs after annealing at temperatures 400–750 °C. After annealing at low temperatures, the cold-deformed alloy shows a significant age-strengthening effect, whereas the solution-treated alloy does not. The hardness of the solution-treated alloy stabilized around 225 HV. But aging of cold-deformed samples at 400 °C for 1 h showed the maximum ultimate tensile strength and hardness of 1497 MPa and 454 HV, 179 MPa and 56 HV increased compared with the cold-deformed alloy. The TEM results show that the nanosized L12 ordered phase formed during aging at low temperatures, and acts as an aging strengthening phase. And the cold deformation promotes the L12 phase formation during aging. Meanwhile, the electric resistivity of cold-deformed samples after aging at low temperatures decreases in a large stage. The lowest value appeared as 53.36 μΩ cm.

Larger recovery strains in a CoNiSi alloy due to enhanced reversibility of FCC⇌HCP martensitic transformation

It is not clear how coherent ordered nanoparticles affect characteristics of FCC⇌HCP martensitic transformation in disordered alloys. In this paper, the precipitations of coherent ordered nanoparticles and their effects on the FCC⇌HCP martensitic transformation were systematically investigated in a solution-treated Co24Ni6Si shape memory alloy. The results showed that both the coherent ordered L12 structured and L11 structured nanoparticles could precipitate even in the solution-treated Co24Ni6Si alloy followed by water quenching. The L12 structured nanoparticles strongly hindered the occurrence of stress-induced HCP martensitic transformation and its reverse transformation, but their hindrance dramatically reduced with the decrease of size when below 1.5 nm. The coherent ordered nanoparticles did not convert the non-thermoelastic FCC⇌HCP martensitic transformation to the thermoelastic ones owing to the absence of group-subgroup relation between the parent phase and martensite. A maximal recovery strain of 6.7 % was obtained after only aging at 1073 K for 1 min. This value was 1∼2 % higher than the reported maximal ones in conventional FeMnSi-based alloys subjected to complicated thermomechanical treatments. The enhanced reversibility of HCP martensitic transformation could account for this larger recovery strain by the ultrafine coherent ordered L12 structured nanoparticles.

Effect of single roll drive rolling on microstructure, texture, and mechanical property anisotropy of Al−5.6Zn−2.5Mg−1.4Cu aluminum alloy

The current research aimed to study the microstructure and texture development of the Al−5.6Zn−2.5Mg−1.4Cu alloy during single roll drive rolling process (SRDR). The relationship between mechanical property anisotropy and microstructure and texture was investigated in detail. The SRDR process was immediately performed on the solution-treated sample with four different thickness reductions of 10%, 20%, 40%, and 60%, respectively. Microstructural examination by optical and scanning electron microscopes, texture evaluation by X-ray diffraction, and mechanical properties evaluation by tensile tests were conducted. The results showed that the value of in-plane anisotropy was significantly reduced from 11.6% in solution-treated alloy to 2.4% and 3.1% in 40% and 60% reduction rolled samples, respectively. This was due to the formation of the Rotated Cube component, decreasing the overall texture intensity, and the formation of new grains through dynamic recrystallization. The yield strength in the rolling direction (RD) was higher than that in the transverse direction (TD), which was due to grain morphology and texture in these samples. The severity of Portevin−Le Chatelier (PLC) along the RD (0°) was much lower than that along the HD (45°) and TD (90°) owing to the presence of several strong orientations along the RD. By increasing the thickness reduction, the difference between strain hardening rates of RD, HD, and TD decreased due to the decrement of texture intensity. There was no difference between the fracture surfaces of 60% samples in the RD, HD, and TD, revealing nearly isotropic fracture behavior.

Mechanical behaviour and microstructural evolution of Ti–6Al–1Mo–1V–2Zr–2Cr–1Fe alloy subjected to hot compression deformation

A new titanium alloy with chemical composition of Ti–6Al–1Mo–1V–2Zr–2Cr–1Fe (wt.%) is designed and produced. The hot deformation behavior, microstructural evolution and texture evolution of the alloy after solution treatment are investigated in this paper. Firstly, the constitutive equation of solution-treated Ti–6Al–1Mo–1V–2Zr–2Cr–1Fe alloy with the consideration of strain compensation is obtained based on compressive test at the temperatures of 950–1100 °C and the strain rates of 0.01–10 s−1, which can be used to describe the flow behaviour at elevated temperatures. According to the corresponding constitutive equation, the flow stress of solution-treated alloy is accurately predicted, which is further verified by the experimental data. Furthermore, discontinuous dynamic recrystallization (DDRX) and continuous dynamic recrystallization (CDRX) are observed in the microstructures of the deformed alloys, where deformation temperature and strain rate have a significant effect on DDRX and CDRX processes of solution-treated Ti–6Al–1Mo–1V–2Zr–2Cr–1Fe alloy. Moreover, plastic deformation and dynamic recrystallization have a comprehensive influence on the texture evolution of solution-treated Ti–6Al–1Mo–1V–2Zr–2Cr–1Fe alloy. ηbcc-fiber textures of {100}<001> and {110}<001>, εbcc-fiber texture of {112}<111> and ξbcc-fiber texture of {110}<112> are the main texture compositions of the deformed samples, where all of the deformed samples exhibit a strong {100}<001> texture.

The Effect of IMCs and Segregation on the Microstructure and Mechanical Properties of β-Type Titanium Alloys

Two new β-type titanium (β-Ti) alloys of Ti-10.5Cr-5.4Mn-2.4Zr-0.9Al and Ti-15.6Cr-12Mn-3.3Zr were designed with the same bond order value 2.79 and different d-orbital energy level values of 2.28 and 2.16, respectively. The effect of intermetallic compounds (IMCs) and the segregation behaviors of β-Ti alloys were discussed by adding excessive and normal alloying elements to alloys under both as-cast and solution-treated conditions. The mono-β phase in the Ti-10.5Cr-5.4Mn-2.4Zr-0.9Al alloy and β+intermetallic compounds (IMCs) in the Ti-15.6Cr-12Mn-3.3Zr alloy were identified and observed. The as-cast and solution-treated alloys showed their ultimate tensile strength and fracture strain; these were 982 and 1002 MPa, with 9.82 and 9.89% for Ti-10.5Cr-5.4Mn-2.4Zr-0.9Al, and 448 and 296 MPa, with 0.12 and 0.11% for Ti-15.6Cr-12Mn-3.3Zr, respectively. Moreover, the Vickers hardness values of the as-cast and solution-treated alloys were 345 and 355 for Ti-10.5Cr-5.4Mn-2.4Zr-0.9Al, and 422 and 466 for Ti-15.6Cr-12Mn-3.3Zr, respectively.

A scalable method for preparing Al–Mg–Si–Cu alloy profile with varies heterogeneous structures and their relationship with mechanical properties

This work reports a simple method for manufacturing heterogeneous structured Al–Mg–Si–Cu alloy profile modified by TiB2–TiC particles using conventional hot extrusion and solution heat treatment. The heterogeneous structures containing different proportions of coarse grains and fine grains can be regulated by the solution treatment time, and their relationships with the mechanical properties are studied. The results show that the formation of the heterogeneous structure in the alloy is attributed to the non-uniform distribution of the TiB2–TiC particles, which have strong inhibition effects on the recrystallization in the particle-rich zone. When the proportion of coarse/fine grains in the heterostructure is about 2:1, the mechanical properties of the solution-treated alloy profile achieved a high level: tensile strength and yield strength are 345 MPa and 227 MPa, respectively, which are 35% and 53% higher than those of the as-extruded alloy with almost no loss of elongation. This work provides a strategy to advance the scalable manufacturing of heterogeneous structured Al alloy profile for various applications.

Post-heat treatment of laser powder bed fusion fabricated Al–La–Mg–Mn alloy: On intermetallic morphology control and strength-ductility balance

In this study, a newly developed Al–La–Mg–Mn alloy was subjected to solution heat treatment for the first time. During the solution heat treatment at 500 ℃, the continuous network Al11La3 intermetallics were transformed into a discontinuous granular form. Ultrafine intermetallics (∼0.20 µm) were achieved via multi-point spheroidization with the aid of endogenous nanoprecipitates. Of note, the intragranular intermetallics were inert to coarsening, while the intergranular intermetallics grew gradually to ∼0.58 µm within 6 h. Compared to the as-printed alloy (UTS ∼588 MPa, Elongation ∼6.4%), the solution-treated alloy at 500 ℃ for 1 h (UTS ∼477 MPa, Elongation ∼14.3%) demonstrated a remarkable improvement in ductility, with a 123% increase, despite a modest decrease of 19% in strength, thereby balancing the strength-ductility. The limited decline in strength is primarily attributed to the high-content solute Mg atoms and thermally stable intragranular intermetallics. Interestingly, the mechanical properties were independent of the holding times at 500 ℃, despite the coarsening of intergranular intermetallics. This is mainly due to the optimization of intermetallics’ scale distribution, which tailors and equalizes the stress distribution between the grain boundary and interior, as well as between the melt pool boundary and interior during deformation. These findings provide the first insight into the effect of post-heat treatment on the intermetallic evolution and mechanical properties of LPBF Al–(La, Ce) alloys.

Mechanical Property and Microstructure of Rolled 7075 Alloy under Hot Compression with Different Original Grains

The hot compression of rolled 7075 alloys with different heat treatments was performed. The temperature ranged from 200 to 400 °C, and the strain rate was 0.01 s−1. The stress level decreases with the increasing temperature during compression, and the strength of the alloy in the original condition is higher than that of solution-treated (ST) alloy at the same deformation condition. The alloys with different heat treatments exhibit different anisotropic behaviors at 200 °C; the anisotropy for the alloys in both conditions becomes weaker with increasing temperature. Then, the corresponding microstructure was studied. The alloy’s microstructure in its original condition consists of fiber grains; however, many equiaxed grains are found after solution treatment due to the recrystallization. The grains with different shapes lead to different anisotropic mechanical properties. For the alloys in both conditions, the density of the dislocation decreases with increasing temperature during compression, and a certain number of subgrains were found when deformed at 400 °C due to the higher driving force and a higher rate of atomic migration. Meanwhile, it is observed that the precipitates of the alloy become coarser during higher-temperature deformation. Dynamic softening is dominant in high-temperature deformation, decreasing stress during hot deformation.