Microstructure Evolution and a Unified Constitutive Model of Ti-55511 Alloy Compressed at Stepped Strain Rates

Su, Gang; Zhong, Yun; Lin, Y.C.; He, Dao‐Guang; Zhang, Song; Chen, Zijian

doi:10.3390/ma14226750

Cited by 30 publications

(5 citation statements)

References 61 publications

Supporting

Mentioning

Contrasting

Order By: Relevance

“…Furthermore, the hot-forming process is usually accompanied by complicated deformation mechanisms such as dynamic recrystallization (DRX), dynamic recovery (DRV), etc. These deformation mechanisms are greatly influenced by the forming parameters [ 4 , 5 , 6 ]. Therefore, to precisely tailor the microstructures and optimize the final properties of alloy parts, it is necessary to research the sensitivity of microstructures and properties to deformation parameters.…”

Section: Introductionmentioning

confidence: 99%

Modeling Dynamic Recrystallization Behavior in a Novel HIPed P/M Superalloy during High-Temperature Deformation

et al. 2022

Self Cite

View full text Add to dashboard Cite

The dynamic recrystallization (DRX) features and the evolution of the microstructure of a new hot isostatic pressed (HIPed) powder metallurgy (P/M) superalloy are investigated by hot-compression tests. The sensitivity of grain dimension and DRX behavior to deformation parameters is analyzed. The results reveal that the DRX features and grain-growth behavior are significantly affected by deformation conditions. The DRX process is promoted with a raised temperature/true strain or a reduced strain rate. However, the grains grow up rapidly at relatively high temperatures. At strain rates of o.1 s−1 and 1 s−1, a uniform microstructure and small grains are obtained. Due to the obvious differences in the DRX rate at various temperatures, the piecewise DRX kinetics equations are proposed to predict the DRX behavior. At the same time, a mathematical model for predicting the grain dimension and the grain growth behavior is established. To further analyze the DRX behavior and the changes in grain dimension, the hot deformation process is simulated. The developed grain-growth equation as well as the piecewise DRX kinetics equations are integrated into DEFORM software. The simulated DRX features are consistent with the test results, indicating that the proposed DRX kinetics equations and the established grain-growth model can be well used for describing the microstructure evolution. So, they are very useful for the practical hot forming of P/M superalloy parts.

show abstract

Section: Introductionmentioning

confidence: 99%

Modeling Dynamic Recrystallization Behavior in a Novel HIPed P/M Superalloy during High-Temperature Deformation

et al. 2022

Self Cite

View full text Add to dashboard Cite

show abstract

“…In general, grain boundaries bulging is related to strain-induced grain boundaries migration, and the bulging grain boundaries will become the DRX nucleation site [ 49 ]. The initiation of DRX is, firstly, the appearance of serrated grain boundaries and then the grain boundaries migrate and transform into convex grain boundaries during the strain induction process [ 50 ] and become the core of DRX initiation. Figure 9 shows the different stages of DRX.…”

Section: Resultsmentioning

confidence: 99%

Effect of Ultrasonic-Assisted Casting on Hot Deformation Mechanism and Microstructure of 35CrMo Steel Ingot

et al. 2021

View full text Add to dashboard Cite

Hot compression tests were performed with strain rates (0.01–10 s−1) and temperatures (850–1150 °C). The power law relationship between the critical stress and critical strain and Zener–Hollomon parameters was determined by θ-σ curves. Microstructure was investigated by electron backscattered diffraction. The results showed that the flow behavior and microstructure of 35CrMo steel was affected by ultrasonic-assisted casting. The activation energy of non-ultrasonic and ultrasonic-assisted 35CrMo steel were 410 ± 9.9 and 386 ± 9.4 kJ/mol, respectively, and the activation energy of ultrasonic-assisted specimens was reduced by 6%. In addition, the ultrasonic-assisted treatment refines the grains to some extent and makes the softening process of ultrasonic-assisted samples progress faster, which promoted the development of dynamic recrystallization and the production of Σ3 boundaries. The discontinuous dynamic recrystallization was the main DRX nucleation mechanism of the 35CrMo steel.

show abstract

“…In the (TiC + TiB+(TiZr)5Si3)/TA15 composite, after oxidation, the β-Ti phase forms the layers wetting the α/α GBs (Figure 19) [99]. GB wetting by the second solid phase was observed in a βsolidifying γ-TiAl alloy during β-α transformation [93], α-β phase transformation in a metastable TiZr based alloy [95], single-pass laser welding of 304 stainless steel and TC4 Ti alloy with V interlayer and Cu/V bilayer [97], in the TiAl2 and TiAl aluminum-rich intermetallics [100], Ti6Al4V/TiC composite coatings [102], in titanium aluminide materials manufactured by combustion and high-temperature shear deformation [103], in Ti-30.46 wt%Zr-0.73 wt%Hf-5.29 wt%Al-3.04 wt%V α + β alloy [104], in α + β Ti-4V-6Al titanium alloy [105], in Ti-80 at% W alloys [106], in 4J36/Ni/Cu/V/TC4 diffusion-bonded joints [107], the welded CP-Ti/304 stainless steel and CP-Ti/T2 bimetallic sheets [108], in the near-β Ti-5Mo-5Al-5V-1Fe-1Cr (Ti-55511) alloy [109], the hot isostatic pressed TA15 titanium alloy after solution and aging treatment [110]. By changing the Mo content in the Ti-44Al-(0-7)Mo (at%) alloys, the different variants of mutual complete and incomplete GB wetting by the α2, γ, and β o phases were observed (see Figure 20) [111].…”

Section: Influence Of Gb Wetting By the Second Solid Phase On The Pro...mentioning

confidence: 99%

Grain Boundary Wetting by the Second Solid Phase: 20 Years of History

Straumal

Lepkova

Korneva

et al. 2023

Metals

View full text Add to dashboard Cite

Grain boundaries (GBs) can be wetted by a second phase. This phase can be not only liquid (or melted), but it can also be solid. GB wetting can be incomplete (partial) or complete. In the case of incomplete (partial) wetting, the liquid forms in the GB droplets, and the second solid phase forms a chain of (usually lenticular) precipitates. Droplets or precipitates have a non-zero contact angle with the GB. In the case of complete GB wetting, the second phase (liquid or solid) forms in the GB continuous layers between matrix grains. These GB layers completely separate the matrix crystallites from each other. GB wetting by a second solid phase has some important differences from GB wetting by the melt phase. In the latter case, the contact angle always decreases with increasing temperature. If the wetting phase is solid, the contact angle can also increase with increasing temperature. Moreover, the transition from partial to complete wetting can be followed by the opposite transition from complete to partial GB wetting. The GB triple junctions are completely wetted in the broader temperature interval than GBs. Since Phase 2 is also solid, it contains GBs as well. This means that not only can Phase 2 wet the GBs in Phase 1, but the opposite can also occur when Phase 1 can wet the GBs in Phase 2. GB wetting by the second solid phase was observed in the Al-, Mg-, Co-, Ni-, Fe-, Cu-, Zr-, and Ti-based alloys as well as in multicomponent alloys, including high-entropy ones. It can seriously influence various properties of materials.

show abstract

Microstructure Evolution and a Unified Constitutive Model of Ti-55511 Alloy Compressed at Stepped Strain Rates

Cited by 30 publications

References 61 publications

Modeling Dynamic Recrystallization Behavior in a Novel HIPed P/M Superalloy during High-Temperature Deformation

Modeling Dynamic Recrystallization Behavior in a Novel HIPed P/M Superalloy during High-Temperature Deformation

Effect of Ultrasonic-Assisted Casting on Hot Deformation Mechanism and Microstructure of 35CrMo Steel Ingot

Grain Boundary Wetting by the Second Solid Phase: 20 Years of History

Contact Info

Product

Resources

About