Dynamic Recrystallization Behavior Research Articles

Optimization in strength-ductility of Mg-Gd-Y-Zn-Zr alloy processed by upsetting-extrusion combined with intermediate thermo-mechanical treatment (ITMT)

In this work, the effects of intermediate annealing and intermediate annealing subsequent aging treatment on the second phase precipitation, dynamic recrystallization (DRX) behavior, and mechanical properties of Mg-9Gd-4Y–2Zn-0.5Zr (wt.%) alloy were comparatively studied. The results showed that the one-pass upsetting-extrusion (UE) deformation intermediate annealing treatment sample (UAE) exhibited the highest dynamic recrystallized (DRXed) grains number fraction and the largest average DRXed grain size, which was mainly attributed to the precipitation of a large number of β-Mg5RE phases (>1 μm) at the grain boundaries (GBs) and within unDRXed grains after annealing treatment. These β-Mg5RE phases promoted DRX through particle-stimulated nucleation (PSN) mechanism during subsequent extrusion process. However, the lack of the pinning effect of the fine second phase precipitations led to the growth of DRXed grains. The DRXed grains of the deformation intermediate annealing subsequent peak-aging treatment sample (UAAE) were significantly smaller than the UAE sample. This is mainly due to the fact that the densely distributed prismatic β′ phases precipitated by the peak-aging treatment were rapidly transformed into nano-scale β-Mg5RE phases and pinned at the DRXed grain boundaries to inhibit the growth of the DRXed grains during the subsequent extrusion process. The ultimate tensile strength (UTS) and failure elongation (EL) of the UAAE sample were 274 MPa and 14.3%, respectively, 4.2% and 85.7% higher than those of the UE sample, showing excellent strength-ductility synergy. The randomly oriented fine DRXed grains, coarse unDRXed grains with high-density dislocations and substructures, and nano-scale β-Mg5RE particles were co-contribute to the strength-ductility synergy.

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.

Comparison of Thermal Deformation Behavior and Characteristics of Mg-Gd-Y-Zn Alloys with and without Bulk LPSO Phase.

Alloys Mg-8Gd-4Y-0.6Zn-0.5Zr (referred to as 0.6Zn) without the bulk long-period stacking ordered (LPSO) phase and Mg-8Gd-4Y-1.1Zn-0.5Zr (referred to as 1.1Zn) containing the bulk LPSO phase were prepared and a series of hot compression tests were conducted to examine and evaluate the influence of the bulk LPSO phase on the thermal deformation behavior and characteristics of the Mg-Gd-Y-Zn-Zr alloy. The bulk LPSO phase affects the dynamic recrystallization behavior, resulting in differences in flow stress between two alloys under different conditions. Specifically, in the temperature range of 380~460 °C, compression at lower strain rates is beneficial for the LPSO phase to promote dynamic recrystallization, while compression at a high strain rate inhibits the dynamic recrystallization due to the severe deformation of the bulk LPSO phase to release the stress concentration instead. The increase in temperature helps the LPSO promote dynamic recrystallization. As a result, the LPSO phase promotes dynamic recrystallization at all experimental strain rates at 500 °C. Furthermore, the thermal processing maps of the 0.6Zn and 1.1Zn alloys are established, and their optimal processing windows are located at 500 °C/0.001~0.01 s-1 and 500 °C/0.01 s-1, respectively. In addition, the instability zones for the 1.1Zn alloy are much larger than that for the 0.6Zn alloy, which corresponds to the microcracks generated at the interfaces between α-Mg and bulk LPSO phases.

Flow stress and dynamic recrystallization behavior and modeling of GH4738 superalloy during hot compression

GH4738 superalloy is a key material for gas turbine engines, yet its relatively poor thermoplasticity and narrow temperature range for hot working deteriorate grain structure uniformity and thereafter service performance. Employing hot compression experiments and finite element analysis (FEA), the present study examined the thermoplasticity of the GH4738 alloy and proposed a fast approach to establishing its dynamic recrystallization (DRX) model. The hot working conditions were considered in the 1000–1160 °C temperature range under strain rates of 2–26 s−1 up to a true compressive strain of 0.69. Friction- and temperature-corrected stress-strain curves were obtained, based on which the efficiency of power dissipation and constitutive equations were constructed. It reveals that DRX is the dominant softening mechanism in the GH4738 alloy, where the sensitivity of flow softening positively correlates with lower temperatures and higher strain rates. The appropriate hot working condition for the alloy is temperatures around 1040–1080 °C and a strain rate larger than 8 s−1. The final grain sizes (d) and fractions of DRX (Xdyn) were minimized using the stochastic gradient descent algorithm based on 120 sets of data within the framework of the Avrami equation. It is shown that the formulated model and its integration into the FEA not only yield satisfactory agreement with the experiment but effectively avoid the complexity involved in the traditional method. The study provides key inputs for predicting the flow behavior and grain structure of the GH4738 superalloy, which shall be critical for process development and optimization of industrial manufacturing processes.

Effect of pre-aging on microstructure, activation energy, texture evolution of Mg–9Gd–4Y–2Zn–0.5Zr alloy during compression deformation

This paper illustrated the effects of pre-aging on the microstructure, texture evolution, and deformation behavior of Mg–9Gd–4Y–2Zn–0.5Zr alloy during hot compression. Dynamic recrystallization (DRX) behavior, texture evolution, stress-strain curve, and activation energy of the solid solution and pre-aged alloy were evaluated. The results showed that the second-phase particles of the pre-aged samples exhibit combination of two types particles structure, which is composed of coarse dynamic precipitation particles and fine nanoparticles. The combination of these two types particles showed the best grain refinement effect by accelerating the DRX process, as the coarse dynamic precipitation particles promoted DRX through the PSN mechanism and the fine granular phase pinned dislocations and inhibited grain growth. As a result, the pre-aged samples had a higher DRX grain volume fractions and smaller average grain sizes than the solid solution alloys. In addition, the pre-aged sample had higher deformation activation energy (Q = 294.8 kJ/mol) than solid solution sample (Q = 223 kJ/mol) because β-phase pin dislocations formed during deformation restrained the movement of grain boundaries. The pre-aged alloys also showed a more concentrated texture than the solid solution alloys, with the c-axis of the coarse grains distributed from the compression direction (CD) at 30° inclination to the normal direction (ND). The c-axis distribution of the coarse grains was more scattered in the solid solution alloys. A hot processing map was constructed for the pre-aged alloy and used for evaluation. The optimal deformation parameters for the pre-aged Mg–9Gd–4Y–2Zn–0.5Zr alloy were between 0.001 and 0.1 s−1 at 400 °C–480 °C. These significant observations not only provide theoretical guidance but also practical application for setting plastic forming deformation parameters in industrial production.

Achieving high strength near 400 MPa in an ultra-fine grained Mg–Bi–Ca ternary alloy via low-temperature extrusion

Significantly enhancing the mechanical properties of Mg–Bi base series alloys is of great significance for their wider application prospects. Here, a new Mg–3Bi–1Ca (BX31, wt.%) alloy showing high tensile yield strength of ∼397.1 MPa, high ultimate tensile strength of ∼416.2 MPa and acceptable elongation of ∼8% was fabricated by low-temperature extrusion. The analysis of microstructure showed that the enhanced yield strength was attributed to the ultra-fine grain structure (∼0.84 μm), nano-scale second phases including Mg2Bi2Ca and Mg2Ca, and Ca segregation at grain boundaries. In addition, a weak basal fiber texture to some extent provided more basal slip activities, guaranteeing the suitable ductility. The dynamic recrystallization and dislocation behavior of the BX31 billet during extrusion were also systematically observed and discussed to reveal the formation mechanisms of the ultra-fine grain structure with the weak basal fiber texture in the as-extruded BX31 alloy. As mentioned above, this work offers a new insight to obtain high-performance Mg–Bi base series alloys.

A new cellular automata model for hot deformation behavior of AZ80A magnesium alloy considering topological technique

In this paper, the CA model of grain topological deformation technique (T-CA) and the physical constitutive model considering strain are introduced to study the hot deformation behavior of extruded AZ80A magnesium alloy. The isothermal compression test of extruded AZ80A magnesium alloy was carried out on the Gleeble-3800 thermal simulator. The deformation temperature and strain rate were 598 K∼723 K and 0.001 s−1∼1 s−1, respectively. According to the experimental results, a phenomenological constitutive model of flow stress considering strain was constructed. The reliability of the model was verified by comparing the experimental and predicted flow stress. The influence of thermal deformation parameters, i.e., deformation temperature, strain rate, and strain, on the DRX kinetic curve and grain size evolution was studied based on the CA model with the introduction of grain topological (T-CA) deformation technology. Meanwhile, the influence of initial grain size on dynamic recrystallization was studied using the conventional CA model (C-CA) and the CA model with topological deformation (T-CA) technology. Finally, the accuracy of the T-CA model was verified by combining physical experiments and electron backscatter diffraction (EBSD) technology. At the temperature of 598 K, the strain rate of 0.1 s−1, and the strain of 0.91, the error between the average grain size simulated by the topological CA (T-CA) model and the experimental results is 7.6 %, which is consistent with the experimental results. When the initial grain size is 43 µm, compared with the conventional CA simulation method (C-CA), the CA simulation method with the introduction of grain topological deformation can promote the occurrence of recrystallization, improving the simulation speed and accuracy. The error between the percentage of recrystallization and the experiment is 4.5 % and 3.2 %, respectively, indicating that the simulation method with the introduction of grain topological deformation (T-CA) can accurately predict the dynamic recrystallization behavior of AZ80A magnesium alloy.

Unveiling the effect of Gd content on the dynamic recrystallization behavior and resultant mechanical property of magnesium

The dependence of dynamic recrystallization (DRX) behavior of Mg on the Gd content was studied using Mg-3wt %Gd and Mg-13 wt%Gd alloys in this work. After solution treatment, the two alloys labeled as the AS-3Gd and AS-13Gd samples, were hot-compressed at 480 °C to the true strain of ε = 1.3. As a comparison, the AS-13Gd sample was peak-aged and labeled as the AA-13Gd sample, which was also subjected to hot-compression under the same condition. The results showed that adding Gd content significantly delayed the DRX progress and affected the dominant DRX mechanism. Specifically, continuous DRX dominated the AS-3Gd sample while discontinuous DRX controlled the AS-13Gd sample. For the AA-13Gd sample, continuous DRX started easily during low straining but discontinuous DRX become dominant during high straining. Consequently, the DRX fractions were 91%, 61%, and 67% for the AS-3Gd, AS-13Gd, and AA-13Gd samples, respectively. Besides, the AS-13Gd sample achieved the best combination of strength and ductility, due to the successful collaboration of strong solution strengthening and obvious texture weakening. On the other hand, the insufficient solution strengthening failed in improving the strength of AS-3Gd sample, and the strong texture hardening deteriorated the ductility of AA-13Gd sample.

Texture tailoring and microstructure refinement induced by {11−21} and {10−12} twinning in an extruded Mg-Gd alloy

An extruded Mg-17Gd (wt%) alloy with < 0001 > fiber texture was compressed along different directions at room temperature. Electron backscatter diffraction characterization was used to investigate the texture tailoring, twinning and dynamic recrystallization (DRX) behaviors. The results indicate that {10−12} and {11−21} twinning activated. The [0001] pole tilted to compression direction with the strain increasing and twinning dominated the texture transition. Activation of {10−12} twinning can be governed by Schmid law, while it is more appropriate to explain the activation of {11−21} twinning by the basal slip transfer condition in the twinned grains according to the slip trace analysis. In addition, operation of {11−21} twinning can facilitate the nucleation of {10−12} twin in the same grain by changing Schmid factor (SF) in the vicinities of {11−21} twin. Grain refinement occurred in the specimens with large strain and the average grain size decrease from ∼27 µm to ∼12 µm. The mechanism of grain refinement can be summarized as follows: the mobility of twin boundaries will be restricted because of the twin-twin and dislocation-twin interaction and converted to random high angle grain boundaries (HAGBs). The random HAGBs offer the nucleation sites and the strain accumulation within twins offer the driving force which facilitate the formation of DRXed grains at random HAGBs. Additionally, the SF difference within parent grain may result in the formation of HAGBs, and these HAGBs can connected the random HAGBs that result from the dislocation-twin interaction which result in the formation of new grains.

Formation mechanism of Cube texture components ({001}) associated with dynamic recrystallization during compression in the single BCC phase region of Ti-22Al-25Nb alloy

The present study, employing EBSD as the primary method, investigates the formation mechanism of Cube texture components in Ti-22Al-25Nb alloy during uniaxial compression at high-temperature single-phase field. The research reveals that the formation of Cube components is closely related to texture evolution and dynamic recrystallization (DRX) behavior. Firstly, the formation of <001> and <111> dual fiber texture structures is a prerequisite for the development of Cube component, which mainly forms under large strains. Subsequently, continuous dynamic recrystallization (CDRX) and discontinuous dynamic recrystallization (DDRX) play distinct roles in the formation of Cube component. CDRX and DDRX occur in grains belonging to <001> and <111> fiber textures, respectively, exhibiting significant orientation dependence. <001> grains, characterized by a lower Taylor factor, undergo CDRX, causing sub-grains near the grain boundaries in <001> grains to rotate towards the Cube orientation. In contrast, <111> grains with a higher Taylor factor undergo DDRX, leading to the accumulation of high stored energy near the grain boundaries in <111> grains. When the two types of grains are adjacent, the significant orientation difference between them facilitates the rapid growth of Cube-oriented sub-grains through grain boundary migration. This results in a conspicuous Cube texture component on a macroscopic scale.

Significantly improvement in formability and ductility of AZ31 Mg alloy by differential temperature rolling

The implementation of asymmetric deformation proves to be an effective approach towards optimizing the basal texture of wrought Mg alloys, ultimately leading to improved plasticity and formability. This work performs differential temperature rolling (DTR) on AZ31 Mg alloy to achieve asymmetric deformation. After the DTR process, the ductility and formability of the RT-200 sample are comparable to the traditional cold rolling and annealing combination process. Combined with the annealing treatment (AT), the fracture elongation and Erichsen value of the RT-200/AT sample are reached 32.4% and 4.49 mm, respectively. The improvement of the ductility and formability is mainly attributed to the texture weakening, which originates from the temperature gradient formed in the DTR process. The gradient temperature field modifies the dynamic recrystallization behavior during the rolling deformation process, as well as the static recrystallization behavior during annealing. The microstructure evolution and the texture weakening mechanism are discussed in detail. The findings can serve as a theoretical reference for the development of high-ductility Mg alloys and for optimizing the continuous hot-rolling process of Mg alloys.

Achieving outstanding heat-resistant Mg-Gd-Y-Zn-Mn alloy via introducing RE/Zn segregation on α-Mn nanoparticles

A novel Mg-8Gd-2Y-1.5Zn-1Mn (GYZ-1Mn, wt.%) alloy with extraordinary high-temperature mechanical properties was developed by introducing RE/Zn segregation on α-Mn nanoparticles. Its ultimate tensile stress (UTS) and yield stress (YS) are 312 MPa and 248 MPa at 300 ℃, which are 87 MPa and 52 MPa higher than the highest strengths of other Mg-Gd-Y-Zn alloys reported in the previous literature. The outstanding performance of GYZ-1Mn alloy was associated with the segregation of RE/Zn atoms on the α-Mn nanoparticles, which facilitated the formation of fine lamellar long period stacking ordered (LPSO) phase and impeded the coarsening of α-Mn. Consequently, retarded dynamic recrystallization behavior occurred in the GYZ-1Mn, resulting in fine grain size, high density of geometrically necessary dislocations and strong fiber texture intensity to strengthen the high-temperature mechanical properties. Hence, this work paved a novel path for the development of heat-resistant Mg alloys by introducing elemental segregation on nanoparticles.

Finite element and experimental analysis of grain refinement caused by dynamic recrystallization during high-speed cutting of nickel-based superalloys

Nickel-based superalloys are subjected to complex mechanical and thermal loads during high-speed cutting, resulting in dynamic recrystallization behavior. The microstructure state is closely related to fatigue performance. In this paper, the Johnson-Mehl-Avrami-Kolmogorov model is used to predict the microstructure evolution of during high-speed cutting of superalloy GH4169. The finite element model of microstructure evolution considering dynamic recrystallization is established by user-defined subroutine on simulation platform. The error of cutting force obtained by experiment and simulation is within 12%. Serrated chips are obtained in high-speed cutting of superalloy GH4169. The typical characteristics of serrated chips such as peak, valley and peak-to-peak distance obtained by simulation are used to compare with the experimental results, and the error is within 20%. The dynamic recrystallization grain size increases as cutting speed increases. The promoting effect of increasing temperature on grain growth is greater than that inhibition effect of increasing strain rate, which leads to the increase of average grain size of machined surface.

The evolution of microstructure and texture induced by grinding and subsequent thermal exposure of single crystal alloy

The dynamic recrystallization (DRX) behavior during grinding and static recrystallization (SRX) behavior during thermal exposure of Ni-based single crystal alloy were compared in this work. The microstructure changes after DRX and SRX were characterized by field emission scanning electron microscopy (FE-SEM) and scanning transmission electron microscopy (STEM). The grain orientation and dislocation density distribution were analyzed by transmission Kikuchi diffraction (TKD) and electron backscatter diffraction (EBSD). The results show that SRX is affected by DRX process on the ground subsurface of single crystal alloy. The nucleation sites of SRX at high temperature are derived from significant number of high-density dislocation structures generated by DRX that induced by grinding process. Compared with the equiaxed nanograins produced by DRX, micron-scale cellular and equiaxed grains are formed on the surface, and dislocation density decreases sharply after SRX. The original cube texture of single crystal superalloy changes into shear texture due to plastic deformation during grinding, and then into strong recrystallization texture at high temperature. The microstructure changes under deformation and high temperature directly affect the final properties of single crystal blades. It is of great practical significance to understand the microstructure evolution and grain orientation changes during DRX and SRX processes, so as to reveal the mechanism of single crystal transforming into polycrystal from machining process to service stage of single crystal blades.

Dynamic recrystallization behavior and microstructure evolution of high-strength low-alloy steel during hot deformation

The dynamic recrystallization (DRX) behavior and microstructure evolution of the high-strength low-alloy (HSLA) steel were studied by isothermal compression experiments at temperatures ranging from 850 to 1150 °C and strain rates ranging from 0.01 to 10 s−1 with a true strain of 0.8. The true stress-strain curves show that the flow stress increases with increasing strain rate and decreasing deformation temperature. The constitutive equation of the HSLA steel was established based on the peak stress, and the deformation activation energy was calculated to be 414.263 kJ/mol. Processing maps corresponding to different true strains were constructed based on the dynamic material model. High strain rates and low deformation temperatures are more likely to lead to flow instability. The microstructure deformed at low temperatures and high strain rates mainly consists of elongated initial grains. The DRX nucleation mechanism of the HSLA steel was explained. Many fine grains nucleate at the initial grain boundaries, forming a necklace structure. The serrated or bulged grain boundaries are the beginning of DRX. In addition, the DRX volume fraction model was established, and the DRX grain size was analyzed. High temperatures and low strain rates promote the nucleation and growth of the DRX.

Enhanced strength-ductility synergy of homogeneous isomeric Al–Cu–Mg sheet prepared by powder metallurgy

In this study, a new type of homogeneous isomeric mixed-crystal billet were prepared by hot pressing sintering first and then the isomeric Al–Cu–Mg alloy sheets with a good balance of strength and ductility were successfully prepared by extruding. The microstructure shows that a typical ‘shell core’ structure in which coarse grains coated with fine grains is formed in the sheet, and the ratio of coarse grains to fine grains in the sheet can be precisely controlled by adjusting the particle size of the powder. And the formation and modification mechanism of the homogeneous isomeric are thoroughly discussed in the present study. The results show that the coordinated deformation of coarse grains and the generation of dynamic recrystallization behavior during extrusion deformation of mixed-crystal billet are the main reasons for the formation of the ‘shell core’ structure in the sheets. When the proportion of coarse grains reaches 50%, the isomeric structure can be better preserved in the alloy sheet and the comprehensive properties of the homogeneous isomeric are better than those of the traditional sintered and extruded alloy sheet. The above study provides a new reference idea for the preparation and application of high-performance Al–Cu–Mg alloy sheets.

Effects of trace Ag on the dynamic recrystallization and mechanical properties of Mg-Gd-Y-Zr alloy

In this paper, the role of trace Ag in the dynamic recrystallization (DRX) behaviors and mechanical properties of Mg-7.5Gd-1.5Y-0.4Zr (wt.%) alloy are illustrated, aided by hot deformation with advanced characterization techniques. Results show that dynamic precipitates cannot occur at temperatures of 420 °C and 470 °C. Adding 0.5 wt% Ag causes sluggish DRX in Mg-Gd-Y-Zr alloys, and grain boundaries are more stable due to Gd and Ag co-segregation, which improves the flow stress during hot compression. To better illustrate the relationship between Ag micro-alloying and mechanical properties, based on the hot compression test, Mg-Gd-Y-Zr extrusion bars with and without Ag are fabricated at 470 °C and at an extrusion ratio of 9. The Mg-7.5Gd-1.5Y-0.4Zr-0.5Ag (wt.%) extrusion bar exhibits excellent strength in the synergistic strengthening effects of the strong texture, high density dislocation, and segregation of Gd and Ag at grain boundaries. Therefore, this work lays the foundation for the subsequent fabrication of large-scale components in Ag-free and Ag-containing Mg-Gd-based alloys.

The dynamic recrystallization behavior of the Ti-5.5Mo-7.2Al-4.5Zr-2.6Sn-2.1Cr titanium alloy during hot rolling based on macro-meso multiscale crystal plasticity finite element approach

The understanding of dynamic recrystallization under complex thermo-mechanical coupling is still a technical challenge. Therefore, in this work, combining the Johnson-Mehl-Avrami-Kolmogorov recrystallization grain model, a macro-meso multiscale crystal plasticity finite element approach was innovatively proposed. The isothermal hot compression test was performed to obtain the true stress-strain curves of Ti-5.5Mo-7.2Al-4.5Zr-2.6Sn-2.1Cr titanium alloy (strain rates: 0.001 s−1, 0.01 s−1, 0.1 s−1, 1 s−1, and 10 s−1; temperatures: 650 ℃, 700 ℃, 750 ℃, 800 ℃, and 850 ℃). Afterward, corresponding fitted parameters can be used to update the volume fraction and size of recrystallized grains of each sub-step. The macro simulation results showed that the surface layer had prominent strain partitioning and lower equivalent stress after hot rolling (thickness reduction: 60 %). For the region of interest, the calculated volume fraction and equivalent circle diameter of recrystallized grains were 2.45% and ∼1 µm, respectively, which were in good agreement with the experimental results.

Thermo-mechanics Driven Dynamic Recrystallization Behavior and Mechanism in High Strength Martensitic Stainless Steel

Thermo-mechanics Driven Dynamic Recrystallization Behavior and Mechanism in High Strength Martensitic Stainless Steel

Dynamic and Postdynamic Recrystallization Behavior of GWZ Magnesium Alloy Under Double‐Hit Hot Compression

Herein, dynamic and postdynamic recrystallization behaviors of GWZ magnesium are investigated. Toward this end, the single‐hit and double‐hit hot compression tests are conducted under strain rate of 0.001 s−1 at 400 °C. The prestrains of 0.1 and 0.5 are considered to investigate the effect of interpass time (5–300 s) on the compressive strength level. At the low strain level of 0.1, the contribution of Hall–Petch effect is considerable due to the occurrence of static recrystallization. In addition, the rare earth texture component is eliminated during interpass annealing. This causes increasing the strength of the material during second pass of hot compression. In contrast, at higher imposed strain, the strength level decreases with increasing the interpass time of annealing. The high amount of strain is completely consumed and the remaining stored energy is not high enough to trigger the occurrence of static recrystallization. The occurrence of metadynamic recrystallization and subsequent growth are characterized. In addition, the texture does not change in respect of the intensity or numbers/types of components. Accordingly, the observed decreasing trend of the strength is justified relying on the occurrence grain growth.