Fraction Of Boundaries Research Articles

Effect of laser shock peening on tribological properties of 55SiMoVA bearing steel

Wear is an important factor limiting the service life of 55SiMoVA bearing steel. In this work, laser shock peening (LSP) technology is used to improve the tribological properties of 55SiMoVA bearing steel, and the corresponding underlying mechanism is systematically discussed. After LSP, the kurtosis (Sku) of surface roughness asperities reduced from 10.355 to 5.488, and no new phase was generated. Electron backscatter diffraction (EBSD) and transmission electron microscopy (TEM) analysis suggested LSP induced the generation of dislocation structures and deformation twins, leading to a decrease in the average grain size and an increase in the fraction of high-angle grain boundaries. Due to the work-hardening and fine-grain strengthening, the microhardness increased by 16.6 %, the maximum residual compressive stress amounted to −793.1 MPa, and the coefficient of friction (COF) and wear volume were significantly reduced. Scanning electron microscopy (SEM) results indicated that the wear mechanism of 55SiMoVA bearing steel before and after LSP was not transformed. However, the abrasive wear and delamination wear of the LSPed specimens were significantly improved, which was mainly attributed to grain refinement, increasing microhardness and constructing a residual compressive stress layer in the subsurface layer of 55SiMoVA bearing steel. During the sliding process, the increase in microhardness limits micro-plowing on the wear surface, and the residual compressive stress inhibits the crack formation and expansion, improving the wear resistance of 55SiMoVA bearing steel.

Physical mechanism for nanocrystalline NiTi alloy with ultrasmall-sized grains exhibiting one-way shape memory effect without temperature-induced phase transformation

In the present work, a novel finding is that nanocrystalline NiTi alloy with ultrasmall-sized grains (where the diameter of grains is less than or equal to 10 nm) presents one-way shape memory effect (OWSME) without temperature-induced phase transformation, where the involved physical mechanism is revealed by combining experiments with molecular dynamics simulation (MD). The results show that fraction of grain boundaries (GBs) is so much that temperature-induced martensitic transformation is suppressed, but it leads to a certain unrecoverable strain. The following loading results in increase of strain and decrease of Gibbs free energy, which leads to stress-induced martensitic transition. After unloading, Gibbs free energy is increased by the release of elastic strain, which leads to partial reverse martensitic transition. Consequently, OWSME in nanocrystalline NiTi alloy with ultrasmall-sized grains is aroused by retained stress-induced martensitic transition followed by its reverse phase transition rather than temperature-induced one followed by its reverse phase transition.

Effect of heat treatment on microstructure and mechanical properties of oscillating laser-arc hybrid welded 12Cr13 thick plate

Heat treatment of oscillating laser-arc hybrid welded 12Cr13 martensitic stainless steel was carried out, the microstructure and mechanical properties were studied. The results showed that sound formation was obtained without crack, pores and lack of fusion. The microstructure of the weld was mainly columnar austenite with strong texture. After heat treatment, the microstructure was coarsened but the homogeneity was improved with the grain sizes in the weld center of about 250 μm. The fractions of the high angle grain boundaries decreased while the fractions of CSL boundaries increased. After heat treatment, the strength and hardness of the weld decreased. However, the elongation and section shrinkage rate are increased by 25 % and 20 %, respectively, and the impact energy of the heat affected zone is increased from 62 J to 88 J. Finally, the effect of the oscillating laser beam on the energy distribution and molten pool flow was discussed, the effect mechanism of heat treatment on microstructure and properties of weld was illustrated, and the relationship between the microstructure and properties of the weld was established.

The Influence of Microstructure Evolution on the Mechanical and Electrochemical Properties of Dissimilar Welds from Aluminum Alloys Manufactured Via Friction Stir Welding

The present study investigated a new configuration of friction stir welded joints from two aluminum alloys. Dissimilar welds AA6082/AA1350 were examined, whereas, for AA1350, two states were investigated—coarse-grained (CG) and ultrafine-grained (UFG). Changes in the mechanical and electrochemical properties regarding the microstructure evolution across the welds were discussed. The average grain size in the stir zone (SZ) for all materials equaled 4 to 5 µm with a fraction of high-angle grain boundaries of about 77 pct, indicating the occurrence of continuous dynamic recrystallization. Changes in the microhardness across the welds were connected with differences in grain size (AA1350) and dissolution of β″ precipitates in the SZ of AA6082. As a result, the tensile strength of the welds decreased compared to base materials AA6082 and AA1350 UFG; however, there was an increase when compared to the base material AA1350 CG. Electrochemical experiments revealed that pitting corrosion occurred for AA1350, while for AA6082, it was a combination of pitting and intergranular corrosion. The depth of corrosion attack was higher for AA1350, with a maximum value of ~ 70 µm for base materials, while in the SZ, a depth decreased to 50 µm. For the AA6082, the maximum depth was measured in the SZ and did not exceed 30 µm.

Effect of hold-type on cyclic life and microstructural evolution of an austenitic stainless steel

The present work investigates the effect of different type of hold on the change in microstructure and cyclic life. i.e., number of cycles to failure of the 304LN grade austenitic stainless steel at an elevated temperature. The strain-controlled low cycle fatigue and creep-fatigue interaction tests were carried out in air at 540 °C for constant total strain amplitude levels of ± 0.5 % and ± 0.7 %. The duration of hold-time was maintained at a constant level of 600 s at peak tensile, compressive and both peak tensile-compressive strain during different creep-fatigue interaction tests. Due to incorporation of creep damage, the cyclic life of the creep-fatigue interaction-tested samples has been found to be lower than that of the low cycle fatigue-tested samples. The tensile-hold appears to have maximum impact on reduction in cyclic life during creep-fatigue interaction tests followed by tension-compression hold and compressive hold. The scanning electron microscopy and electron back scattered diffraction analyses of creep-fatigue interaction-tested samples have revealed that the grain size coarsening, reduction in twin boundary fraction and increase in average Kernel Average Misorientation are the key factors in reduction of cyclic life.

Optimizing Tempering Parameters to Enhance Precipitation Behavior and Impact Toughness in High-Nickel Steel

This study explores the effects of tempering on the precipitation behavior and impact toughness of high-nickel steel. The specimens underwent double quenching at 870 °C and 770 °C, followed by tempering at various temperatures. Advanced characterization techniques including optical microscopy (OM), scanning electron microscopy (SEM), and transmission electron microscopy (TEM) were used to elucidate precipitation phenomena. Additionally, electron backscatter diffraction (EBSD) was employed to assess the misorientation distribution after tempering. Charpy impact tests were performed on specimens tempered at different temperatures to evaluate their toughness. The findings reveal that with increasing tempering temperature, the fraction of low-angle grain boundaries decreases, which correlates positively with enhanced impact toughness. The results demonstrate that tempering at 580 °C optimizes the material’s microstructure, achieving an impact toughness value of approximately 163 J.

Investigating the influence of post-deposition heat treatment (PDHT) on the characteristic changes in wire arc additively manufactured 410 martensitic stainless steel thin-wall structure

Obtaining the desired material characteristics of an as-deposited martensitic stainless steel (MSS) structure fabricated by wire arc additive manufacturing (WAAM) is challenging due to several factors like inhomogeneity, precipitation, phase transition, etc. This investigation elucidates the impact of post-deposition heat treatment (PDHT) on the microstructural and mechanical properties of the WAAM-processed 410 MSS thin-wall structure and compares it with the as-deposited 410 thin-wall structure. The MSS thin-wall structure consists of retained austenite (γ), delta (δ) ferrite, martensite laths and Cr-rich M23C6 type carbide. The M23C6 volume fraction increases by up to 18 %, and the γ-phase fraction reduces by up to 40 % by applying PDHT. The PDHT process significantly changed the texture from {110}<011> to {001}<110>. The PDHT process increases the dislocation density (1.974 × 10−15 m−2) than the as-deposited condition (0.924 × 10−15 m−2). The total low energy boundary (LAGB+CSL) contribution of the as-deposited sample is 19.5 %, whereas the PDHT sample demonstrated a higher fraction of low energy boundaries of 32.4 %. The PDHT sample showed a much smaller distribution of grains with an average grain size of 11 μm compared to the as-deposited condition. The overall hardness increases from 468 HV to 487 HV after PDHT compared to the as-deposited condition with lower inhomogeneity across the build direction. The mean 0.2 % proof stress, ultimate tensile stress, and elongation of the PDHT sample increased by 17 %, 5 %, and 60 %, respectively, compared to the as-deposited sample.

Advancing piezoelectric properties of barium titanate ceramic through AC + DC field poling over Curie temperature

The significance of increased domain nucleation sites from smaller grain size (GS) of barium titanate (BT) ceramics on piezoelectric properties was analyzed for different types of poling, including conventional DC poling, modified DC poling, and AC plus DC poling, conducted at different poling temperatures. The AC plus DC poling conducted at 1.5 °C above the Curie temperature (T C) showed the highest piezoelectric constant (d 33) of 528 pC/N, with an average domain size of 100 nm observed after poling. The d 33 improvement was attributed to smaller domain size formation from field-induced phase transitions and homogenous distribution of point defects achieved by the AC field. Comparative analysis with larger grain BT ceramics under AC plus DC poling suggests that defects and volume fraction of grain boundaries in BT ceramics could have an effect on domain sizes.

Understanding the isothermal compression behavior of Al-Mg-Si alloy based on hot deformation parameters and instability criteria

This work comprehensively studied the microstructure evolution and thermodynamic behavior of homogenized cast Al-Mg-Si alloy by using the dynamic materials model (DMM) of hot deformation activation energy (Q) and power dissipation efficiency (η), which were influenced by Zener-Holomon (Z) parameters of temperature-compensated strain rate. The Q varies with the material constitutive parameters n(T) and sε̇ and leads to a non-monotonic trend in the Z parameter. These coupling relationships have profound significance for revealing plastic deformation. The microstructure and microtexture evolution under four representatively Z parameters had been characterized, and it was found that the deformation mechanism under higher lnZ was mainly dynamic recovery (DRV) and a typical <101>//TD texture with a maximum strength of 14.41 was exhibited. As lnZ decreased, the volume fraction of high angle grain boundaries (HAGBs) and recrystallized grains increased from 20.89 % and 1.5 % to 49.47 % and 40.9 %, the geometrically necessary dislocation (GNDs) density dropped from 1.55 × 1014/m2 to 0.40 × 1014/m2, and the softening mechanism gradually shifted to dynamic recrystallization (DRX), with the volume fraction of Cube texture {001} <100> increasing and Goss texture {011} <110> decreasing. Hot processing maps were established based on the Prasad and Murty instability criterion. The results showed that the instable and stable zones had a strong correlation with η. Lower η often implies microcracks, deformation bands and flow localization, as well as extremely uneven grain distribution and a low recrystallization volume fraction, and the stable zone mainly exhibited the phenomenon of DRX dominated recrystallization behavior improving microstructure homogenization. By comparing the specific hot processing map and microstructure evolution, the prediction ability for determining Murty instability criterion is stronger than Prasad for homogenized cast Al-Mg-Si alloy.

EBSD analysis and mechanical properties of low-carbon steel during drawing with shear deformation

In the current study, the effect of shear deformation combined with conventional drawing processes on the evolution of the microstructure, texture and mechanical properties of low-carbon steel was investigated using electron backscatter diffraction, Vickers microhardness and tensile test. For that, two samples were drawn with a shear die to 8 (ShD8–23 sample) and 23 % (ShD23–23 sample) of diameter reduction and followed by conventional drawing for a diameter reduction of 23 %, respectively. The results show that the overall grain size reduction was about 9.2 and 12.8 % and a significant increase in low-angle grain boundary fraction of 77.8 and 85.9 % for ShD8–23 and ShD23–23 samples, respectively. A typical <110>//DD fiber containing A {110}<001>, B {110}<111> and C {110}<110> components was formed in both samples. In contrast to the B and C components, the stored energy in the A component, estimated by the Kernel Average Misorientation (KAM) approach, was found to be low and stable with increasing deformation. The ultimate tensile strength of the ShD8–23 and ShD23–23 samples was improved by 49 and 52 %, respectively. The yield strength was increased by 95 and 108 % for ShD8–23 and ShD23–23 samples, respectively. The mechanical properties improvement was related to the deformation and initial microstructure. The contribution of dislocation strengthening, originated from geometrically necessary dislocations, is found to be dominant for the increase of yield strength rather than grain refinement strengthening.

Effect of individual and synergistic alloying of In and Ni on microstructure, phase stability and thermal properties of lead-free Sn-0.7Cu solder

ABSTRACT The study explores the individual and synergistic effect of alloying indium (In) and nickel (Ni) with Sn-0.7 wt.% Cu solder on microstructure and thermal properties. Solders consist of β-Sn phase matrix and Cu6Sn5 intermetallic phase. In dissolves within β-Sn, while Ni substitutes Cu atoms of Cu6Sn5 forming (Cu,Ni)6Sn5. Alloying either In or Ni with Sn-0.7Cu lowers solidus and liquidus temperatures of the alloys, with a greater reduction in the case of In. Synergistic alloying of In and Ni with Sn-0.7Cu leads to a widening of 93%. Smaller fraction and localised presence of Cu6Sn5 in In-containing alloys resulted in dual-peaked grain size distribution. In the case of Ni, a fraction of (Cu,Ni)6Sn5 increased, generating more interfaces for nucleating β-Sn grains and eventually causing grain refinement. An increment in the fraction of low-angle grain boundaries (LAGBs) was observed in both alloying cases. The synergistic effect of In and Ni yields a more uniform grain size and lesser LAGBs.

New insights on microstructural parameters controlling mechanical properties of rolled molybdenum

The aim of this paper is to understand microstructural evolution and their key effects on mechanical properties of rolled molybdenum (Mo) from as-received sintered sheet. A batch of pure Mo sheets with various thickness reductions have been characterized in detail. The results reveal that the microstructure evolves by three stages including grain refinement, dynamic recrystallization (DRX) and grain elongation. For the rolled Mo, the fractions of low angle grain boundaries (LAGBs) are much higher than that of as-sintered Mo but do not increase monotonically with increasing thickness reductions. The occurrence of DRX results in the decrease of LAGBs at the intermediate stage while a larger rolling reduction results in grain boundaries bursting with high angle characters at the later stage. All rolled sheets are textured with dominant orientation locating at γ-fiber and θ-fiber line. Room-temperature tensile tests demonstrate that all rolled Mo sheets are much stronger and more ductile (ultimate tensile strength, UTS = ∼650–1000 MPa and total elongation, TE = ∼10–35%) than as-sintered Mo (UTS = ∼400 MPa and TE = 0), but a larger thickness reduction unexpectedly results in the deteriorated ductility which can be attributed to the increased number of HAGBs. The elongated microstructure with refined grains and the high fraction of LAGBs induced by rolling are considered to be the dominant parameters responsible to the improved mechanical properties of Mo. We suggest that rolling parameters should be optimized carefully to avoid the detrimental effect of crack initiation from the increase in high angle grain boundaries (HAGBs).

Effect of HIP Treatment on the Evolution of Texture and Microstructure of LBPF Fabricated Pure Ni

Microstructure and texture analysis were conducted employing electron backscatter diffraction (EBSD) technique on laser powder bed fusion (LPBF) fabricated pure Ni. The texture analysis of the hot isostatic pressed (HIP) and as-printed (AP) samples were done utilizing orientation distribution function (ODF) maps. The AP sample comprises mostly of &amp;lt;110&amp;gt;||BD fiber texture with insignificant presence of twins. In contrast, the HIP sample has &amp;lt;111&amp;gt;||BD grains. It was found that the development of the texture &amp;lt;111&amp;gt;||BD was due to the deformation linked to the HIP process. In addition, HIP generated a substantial fraction of Σ3 coincident site lattice boundaries (CSL) because of pure Ni which is a medium stacking fault energy (SFE) element.

Through glass via (TGV) copper metallization and its microstructure modification

The microstructure and uniformity of Cu metallization in the through glass via (TGV) structure were investigated through electron backscatter diffraction (EBSD) analysis system and finite element analysis (FEA) method. Two different direct current (DC) electroplating methods were employed for the TGV metallization, including single- and multiple-step electroplating methods. We found that the multiple-step electroplating process with appropriate current density (j)/plating time (t) can efficiently enhance the throwing power (TP) value (uniformity) of electroplated Cu in the TGV metallization. Moreover, the Cu electrodeposition via the multiple-step electroplating process possessed larger grain sizes and high fraction of high angle grain boundaries (HAGBs), including twin boundaries (TBs), which are very beneficial to the mechanical and electrical properties of Cu interconnects. Detailed analyses of the uniformity (i.e., TP), crystallographic microstructure (e.g., grain size), and mechanical characteristics (e.g., ductility) of electroplated Cu derived from single- and multiple-step electroplating process were discussed in this paper.

Synergistic interplay between residual stress, hardness, and microstructural evolution in laser peened stainless steel 347

This study investigates the correlation between the properties of stainless steel 347 samples processed using Laser Shock Peening without Coating (LSPwC). While optimizing the process under different surface confinement conditions, the primary focus is on exploring the synergistic interplay between residual stress, hardness, and microstructural evolution for the selected condition. LSPwC with a water confinement layer at 6 GW cm−2 power density, showed significant Compressive Residual Stress (CRS) of −447.50 ± 48.71 MPa at 60 μm, reaching approximately 76 % of the yield stress and the dislocation density at 60 μm depth is 9.830 × 1014 m−2. Additionally, hardness increased to 256.50 ± 14.15 HV0.1 (∼+53 %) at 50 μm depth. Moreover, there was an increase in the grain boundary fraction to 0.3766 (∼+81 %), along with a rise in the twin boundary fraction to 0.1480. At 6 GW cm−2, correlation analysis revealed a strong relationship between compressive residual stress and hardness (correlation coefficient of 0.972), and between hardness and dislocation density (correlation coefficient of 0.968). Consequently, the 6 GW cm−2 condition emerges as the most practical and effective choice, offering substantial compressive stresses, improved hardness, and efficient grain refinement, and thus favours the 6 GW cm−2 power density condition as the optimal choice for LSPwC of stainless steel 347.

Driving force for enhancing the cold silver sinter joining using time domain-dependent Ag–Au epitaxy and interfacial stress

We reveal the mechanism of the cold silver sinter joining process using time-dependent characteristics of Ag–Au interactions grown in the highly (111) orientation. In the initial (∼15 min) state at 175 °C, the Ag–Au inter-diffusion layers developed strongly in the (001) direction, and with increasing time (∼60 min), they switched epitaxial growth in the (111) orientation. The die-bonding strength was significantly improved from 14.9 MPa to 37.8 MPa when the sintering time increased from 15 min to 60 min. The gradual Ag–Au epitaxial growth behavior with a higher stacking-fault energy (SFE) at 175 °C was the dominant factor linearly increasing the cold silver sinter joining strength and ultimately maximizing energy absorption leading to fracture. The surface finish of Au, which can contribute to the time-dependent growth of Ag–Au inter-diffusion layers, underwent a dramatic transformation from a Cube texture to a γ-fiber texture over time. This change was attributed to the micro/nanoscale shear deformation, and reduction of the twin boundary fraction. This study unveiled the in-depth fundamental mechanism for strengthening and pressureless cold sinter joining of Ag–Au epitaxial layers by comprehensively considering this texture behavior, changes in X-ray residual stress, and mechanical properties.

Intercritically Annealed Medium-Manganese Steel: Insights into Microstructural and Microtextural Evolution, Strain Distribution, and Grain Boundary Characteristics.

Aluminum-incorporated medium-manganese steel (MMnS) has potential for lightweight transport applications owing to its impressive mechanical properties. Increasing the austenite volume fraction and making microstructural changes are key to manufacturing MMnS. However, the grain boundary character and strain distribution of intercritically annealed low-density MMnS have not been extensively scrutinized, and the effects of crystallographic texture orientation on tensile properties remain ambiguous. Therefore, in this study, the microstructure, microtexture, strain distribution, and grain boundary characteristics of a hot-rolled medium-Mn steel (Fe-0.2 C-4.3 Al-9.4 Mn (wt%)) were investigated after intercritical annealing (IA) at 750, 800, or 850 °C for 1 h. The results show that the 800 °C annealed sample exhibited the highest austenite volume fraction among the specimens (60%). The duplex microstructure comprised lath-type γ-austenite, fine α-ferrite, and coarse δ-ferrite. As the IA temperature increased, the body-centered cubic phase orientation shifted from <001> to <111>. At higher temperatures, the face-centered cubic phase was oriented in directions ranging from <101> to <111>, and the sums of the fractions of high-angle grain boundaries and coincidence-site-lattice special boundaries were significantly increased. The 800 °C annealed sample with a high austenite content and strong γ-fiber {111}//RD orientation demonstrated a noteworthy tensile strength (1095 MPa) and tensile elongation (30%).

Optimization of the grain boundary network and tensile properties of powder metallurgy-hot isostatic pressed Ni-based alloy Inconel 625

Powder metallurgy-hot isostatic pressing (PM-HIPing) is an advanced manufacturing technology for large-sized and complex-shaped components for nuclear applications. In the present study, a novel PM-HIPing strategy was proposed to optimize the grain boundary network and tensile properties of Ni-based alloy Inconel 625, and it was verified by a series of experiments. Samples with 69 % and 74 % of coincidence site lattice (CSL) grain boundaries were obtained when the narrow-size ranged powder was consolidated at 1140 °C and 1180 °C, respectively. The fraction of CSL grain boundaries was further increased to ∼78.5 % after a high temperature solution treatment. Room temperature yield strength and ultimate tensile strength of PM-HIPed alloy 625 were comparable to that of the wrought specimens, elongation of the specimens was ∼56–60 %, the samples all featured with dimple ductile dominant fracture mode.

Grain refinement and strain delocalization in TRIP high-entropy alloys during hot deformation

Transformation-induced plasticity (TRIP) high-entropy alloy (HEAs) have shown promising mechanical properties, making them potential candidates for various applications. The preparation of structures with fine grains and heterogeneous orientation is important to improve the strength and ductility of TRIP-HEAs. However, the evolution and mechanism of grain refinement with heterogeneously oriented structures of TRIP-HEAs during thermal deformation and its effect on strain delocalization are not clear. In this paper, the microstructure evolution and strain delocalization of a TRIP-HEA, Co35Cr25Ni15Mn15Fe10 (atomic percent, at %) was examined through hot compression tests conducted at temperatures ranging from 900 ℃ to 1000 ℃, and strain rates ranging from 0.001 s−1 to 0.1 s−1. The results revealed that the average grain size of the alloy decreases with increasing deformation temperature and reducing strain rate due to the appearance of dynamic recrystallization (DRX) and annealed twins. After deformation at 1000 °C-0.001 s−1, the average grain size of the alloy decreases from 169.85 μm (initial sample) to 21.5 μm, and the volume fraction of DRX and twin boundaries (TBs) increases to 81.9 % and 37.6 %, respectively. The DRX mechanism of the TRIP-HEA transformed from discontinuous dynamic recrystallization (DDRX) at 900 °C-0.1 s−1/0.01 s−1 to geometric dynamic recrystallization (GDRX) at 900 °C-0.001 s−1 and then to continuous dynamic recrystallization (CDRX) at 950 °C/1000 °C-0.001 s−1. Furthermore, the occurrence of DRX promotes the formation of annealed twins, resulting high volume fraction of high angle boundaries (HAGBs) and twin-matrix pairs, and contributing to grain refinement. Encouragingly, these HAGBs and twin-matrix pairs not only contributes to grain refinement, but also facilitates strain delocalization via dispersing strain and forming strain gradient, thus leading to coordinated deformation. This result is of great significance for understanding and improving the mechanical properties of TRIP-HEAs, and it can help in the design of high-performance TRIP-HEAs for various applications.

Substructure and texture evolution of a novel near-α titanium alloy with bimodal microstructure during hot compression in α+β phase region

Ti65 alloy has extensive potential applications in manufacturing high-temperature components in the aerospace industry. During thermomechanical processing in the α+β phase region, complicated microstructure and texture evolution occurs. In this work, isothermal hot compression experiments were conducted to comprehensively investigate the substructure and texture evolution of Ti65 alloy with bimodal microstructure via the electron backscatter diffraction (EBSD) technique, and the influence of processing parameters on the evolution of substructure and texture was systematically analyzed. The experimental results showed that the distribution of grain boundaries and the transformation of low-angle boundaries (LABs) to high-angle boundaries (HABs) exhibited sensitivity to temperature and strain rate. The fraction of sub-grain boundaries decreased, while the fraction of HABs increased with the increasing of strain rate or temperature due to the spheroidization of the lamellar α phase accompanied by the wedging of the β phase during deformation and the relative misorientation angle distribution between different α variants precipitated from β phase. Temperature rising at a high strain rate resulting from adiabatic heat promoted atomic activity, caused dislocations to be absorbed by sub-grain boundaries or HABs, and finally reduced the dislocation density in both αp and αs phases. Dynamic spheroidization was the main mechanism with increasing temperature, and coarsening of the lamellar α phase was the main mechanism with increasing strain rate. With the increase of temperature or decrease of strain rate, the texture of the αp phase became stronger and the basal and pyramidal slip could be activated. For the αs phase, spheroidization and variant selection together influence the orientation distribution. As a result, the texture evolution showed a complicated tendency.