Coarsening of (αTi) + (βTi) Microstructure in the Ti–Al–V Alloy at Constant Temperature

Горнакова, А. С.; Straumal, Boris B.; Prokofiev, S. I.

doi:10.1002/adem.201800510

Cited by 24 publications

(9 citation statements)

References 24 publications

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“…Some TiFe particles were ordered in chains along the boundaries of the α-Ti grains (see, for example, Figure 1a). This phenomenon is called incomplete or complete grain boundary wetting by a second solid phase and it has been previously observed in various Ti-based alloys [23,[33][34][35][36][37]. In the corresponding SEM/BSE micrographs, the TiFe grains appear to be bright due to a higher Fe content and, thus, a higher mean atomic number of TiFe as compared to α-Ti.…”

Section: Characterization Of the Initial State Of The Samplesmentioning

confidence: 73%

Formation and Thermal Stability of ω-Ti(Fe) in α-Phase-Based Ti(Fe) Alloys

Kriegel

Rudolph

Kilmametov

et al. 2020

Metals

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In this work, the formation and thermal stability of the ω-Ti(Fe) phase that were produced by the high-pressure torsion (HPT) were studied in two-phase α-Ti + TiFe alloys containing 2 wt.%, 4 wt.% and 10 wt.% iron. The two-phase microstructure was achieved by annealing the alloys at 470 °C for 4000 h and then quenching them in water. Scanning electron microscopy (SEM) and X-ray diffraction (XRD) were utilized to characterize the samples. The thermal stability of the ω-Ti(Fe) phase was investigated using differential scanning calorimetry (DSC) and in situ high-temperature XRD. In the HPT process, the high-pressure ω-Ti(Fe) phase mainly formed from α-Ti. It started to decompose by a cascade of exothermic reactions already at temperatures of 130 °C. The decomposition was finished above ~320 °C. Upon further heating, the phase transformation proceeded via the formation of a supersaturated α-Ti(Fe) phase. Finally, the equilibrium phase assemblage was established at high temperatures. The eutectoid temperature and the phase transition temperatures measured in deformed and heat-treated samples are compared for the samples with different iron concentrations and for samples with different phase compositions prior to the HPT process. Thermodynamic calculations were carried out to predict stable and metastable phase assemblages after heat-treatments at low (α-Ti + TiFe) and high temperatures (α-Ti + β-(Ti,Fe), β-(Ti,Fe)).

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Section: Characterization Of the Initial State Of The Samplesmentioning

confidence: 73%

Formation and Thermal Stability of ω-Ti(Fe) in α-Phase-Based Ti(Fe) Alloys

Kriegel

Rudolph

Kilmametov

et al. 2020

Metals

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“…Particularly, GB wetting can control the distribution of minor phases among the grains of the matrix phase. Previously, such phenomena have been extensively studied in binary metallic alloys [71][72][73][74][75]83,84,97,98,108]. These data can also be used for the description of multicomponent alloys.…”

Section: Discussionmentioning

confidence: 99%

“…In this case, this is the complete wetting of α/α GB by the interlayer of a β-phase, as in inset (d) in Figure 1. The GB wetting transitions by the second solid phase have been directly observed in numerous binary metallic systems such as Ti-Fe [72,73], Ti-Co [74], Ti-Al-V [75], Zr-Nb [76], Al-Mg [77], Cu-Co [78], Al-Zn [79,80], Fe-Au [81], Cu-In [82,83] and Mg-RE alloys [84]. An example for the Al-Zn system is shown in Figure 2 (unpublished results from the work partially described in [82]).…”

Section: Grain Boundary Wetting Phenomenamentioning

confidence: 99%

Grain Boundary Wetting Phenomena in High Entropy Alloys Containing Nitrides, Carbides, Borides, Silicides, and Hydrogen: A Review

et al. 2021

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In this review, we analyze the structure of multicomponent alloys without principal components (they are also called high entropy alloys—HEAs), containing not only metals but also hydrogen, nitrogen, carbon, boron, or silicon. In particular, we discuss the phenomenon of grain boundary (GB) wetting by the melt or solid phase. The GB wetting can be complete or incomplete (partial). In the former case, the grains of the matrix are completely separated by the continuous layer of the second phase (solid or liquid). In the latter case of partial GB wetting, the second solid phase forms, between the matrix grains, a chain of (usually lenticular) precipitates or droplets with a non-zero value of the contact angle. To deal with the morphology of GBs, the new GB tie-lines are used, which can be constructed in the two- or multiphase areas of the multidimensional HEAs phase diagrams. The GBs in HEAs in the case of complete or partial wetting can also contain hydrides, nitrides, carbides, borides, or silicides. Thus, GB wetting by the hydrides, nitrides, carbides, borides, or silicides can be used in the so-called grain boundary chemical engineering in order to improve the properties of respective HEAs.

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“…In Figure 1, there are some thick lamellar α phases (α L ) at the boundaries between subgrains/grains of the β matrix. Such behavior is related to the so-called complete and incomplete wetting of grain boundaries by the second solid phase in the β→α transformation process [36,37], but those continuous grain boundary α L are deleterious to the material ductility [38]. In the subsequent hot deformation process, those α L can be spheroidized and the material ductility can be improved.…”

Section: Methodsmentioning

confidence: 99%

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

Zhong

Lin

et al. 2021

Materials

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The flow behavior and microstructure change of the Ti-55511 alloy are investigated by thermal compression experiments with stepped strain rates. The phase transformation features, the dynamic recrystallization (DRX) behavior of the β matrix, the dynamic spheroidization mechanism of the lamellar α phase and the evolution of the β sub-grain size are quantitatively analyzed. A unified constitutive model is constructed to characterize the hot deformation features of the Ti-55511 alloy. In the established model, the work hardening effect is taken into account by involving the coupled effects of the equiaxed and lamellar α phases, as well as β substructures. The dynamic softening mechanisms including the dynamic recovery (DRV), DRX and dynamic spheroidization mechanisms are also considered. The material parameters are optimized by the multi-objective algorithm in the MATLAB toolbox. The consistency between the predicted and experimental data indicates that the developed unified model can accurately describe the flow features and microstructure evolution of the hot compressed Ti-55511 at stepped strain rates.

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Coarsening of (αTi) + (βTi) Microstructure in the Ti–Al–V Alloy at Constant Temperature

Cited by 24 publications

References 24 publications

Formation and Thermal Stability of ω-Ti(Fe) in α-Phase-Based Ti(Fe) Alloys

Formation and Thermal Stability of ω-Ti(Fe) in α-Phase-Based Ti(Fe) Alloys

Grain Boundary Wetting Phenomena in High Entropy Alloys Containing Nitrides, Carbides, Borides, Silicides, and Hydrogen: A Review

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

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