J. Mater. Sci. Technol. ›› 2020, Vol. 39: 56-73.DOI: 10.1016/j.jmst.2019.07.052
• Invited Review • Previous Articles Next Articles
Pengfei Gaoab*(
), Mingwang Fub, Mei Zhana*(), Zhenni Leia, Yanxi Lia
Received:2019-06-11
Revised:2019-07-13
Accepted:2019-07-28
Published:2020-02-15
Online:2020-03-11
Contact:
Gao Pengfei,Zhan Mei
Pengfei Gao, Mingwang Fu, Mei Zhan, Zhenni Lei, Yanxi Li. Deformation behavior and microstructure evolution of titanium alloys with lamellar microstructure in hot working process: A review[J]. J. Mater. Sci. Technol., 2020, 39: 56-73.
Fig. 1. The typical lamellar microstructure after primary hot working in β-phase region (The microstructure of TA15 alloy after heating to 1020 ℃, hold 5 min then air cooled).
Fig. 2. Schematic of formation process (a) [14] and Burgers relationship between α and β phase (b) [16] of lamellar microstructure.
Fig. 3. Typical orientation map (a) and orientation relationship between α and β phase (b) of lamellar microstructure [17].
| Misorientation types | Rotation axis/angle | Prandom (%) |
|---|---|---|
| A | I (identity) | 8.3 |
| B | [1 1 2¯ 0]/60° | 16.6 |
| C | [10 7¯ 17 3]/60.83° | 33.3 |
| D | [ | 16.6 |
| E | [ | 16.6 |
| F | [ | 8.3 |
Table 1 Misorientations between α variants (expressed in axis/angle pairs) inherited from the same parent β grain and the corresponding probabilities without variant selection [21].
| Misorientation types | Rotation axis/angle | Prandom (%) |
|---|---|---|
| A | I (identity) | 8.3 |
| B | [1 1 2¯ 0]/60° | 16.6 |
| C | [10 7¯ 17 3]/60.83° | 33.3 |
| D | [ | 16.6 |
| E | [ | 16.6 |
| F | [ | 8.3 |
Fig. 4. Important parameters of β processing, influencing mechanisms and resulting microstructure features of lamellar microstructure.
Fig. 5. General influence law of cooling rate on the microstructure features of lamellar microstructure.
Fig. 6. The typical evolution of lamellar α during hot deformation of Ti-6Al-4 V alloy with lamellar microstructure at 600 ℃ and 0.001 s-1: (a) prior to deformation, and after height reductions of (b) 25%, (c) 50% and (d) 70% [11].
Fig. 7. Orientation distribution of lamellar α traces relative to the compression axis for Ti-6Al-4 V with lamellar microstructure deformed at 900 ℃, 0.1 s-1 to different strains [12].
Fig. 8. The typical crystallographic texture evolution of lamellar α during hot deformation of Ti-6Al-4 V alloy with lamellar microstructure at 950 ℃ and 0.1 s-1: (a) ε = 0, (b) ε = 0.2, (c) ε = 0.7, (d) ε = 1.0 [42].
Fig. 9. The kinking of lamellar colonies during hot compression (a) and tension (b) of Ti-6Al-4 V at 900 ℃, 0.1 s-1. The compression/tension axis is vertical in both micrographs. [46].
Fig. 10. The SEM image (a) and corresponding inverse pole figure (b) of a region containing kinking of lamellar α in the hot deformation of TA15 alloy with lamellar microstructure [17]. (In the inverse pole figure, β phase is indicated by gray areas, the black lines correspond to HABs, and the silver lines represent LABs).
Fig. 11. The schematic of globularization mechanism of lamellar α.
Fig. 12. The globularization heterogeneity after hot deformation of ELI grade Ti-6Al-4 V alloy with lamellar microstructure [51].
Fig. 13. The semi-quantitative relationship between globularization efficiency and c-axis tilt from compression direction (Taylor factor) of lamellar α [45].
Fig. 14. The texture heterogeneity after subtransus processing of TIMETAL 834 alloy with lamellar microstructure [63].
Fig. 15. Schematic representation of two-stage compression with parallel (Sample P) or vertical (Sample V) directions in the second compression stage and the corresponding results of globularization kinetics [68].
Fig. 16. Schematic representation of globularization process of lamellar α during the interrupted compression [70].
Fig. 17. Shear band and flow localization in the hot working of titanium alloy with lamellar microstructure: (a) Ti17 alloy deformed at 780 ℃, 10 s-1 and 30% [71]; (b) Ti-5Al-2Sn-2Zr-4Mo-4Cr alloy deformed at 770 ℃, 5 s-1 and 60% [72]; (c) Ti-6Al-4 V alloy deformed at 850 ℃, 10 s-1 and 50% [73].
Fig. 18. Typical flow curve of titanium alloy with lamellar microstructure and equiaxed microstructure during subtransus processing.
| Temperature (℃) | Strain rate (s-1) | Δσ/σp at ε¯=0.50 | ||
|---|---|---|---|---|
| Heating related softening | Microstructure related softening | Total softening | ||
| 815 | 10-3 | 0.00 | 0.26 | 0.26 |
| 815 | 10-1 | 0.09 | 0.29 | 0.38 |
| 815 | 101 | 0.16 | 0.12 | 0.28 |
| 900 | 10-3 | 0.00 | 0.23 | 0.23 |
| 900 | 10-1 | 0.09 | 0.31 | 0.40 |
| 900 | 101 | 0.15 | 0.13 | 0.28 |
| 955 | 10-3 | 0.00 | 0.16 | 0.16 |
| 955 | 10-1 | 0.10 | 0.23 | 0.33 |
| 955 | 101 | 0.17 | 0.05 | 0.22 |
Table 2 Comparisons between the softening extents related to deformation heating and microstructure changes at different conditions for a Ti-6Al-4 V alloy with lamellar microstructure [12].
| Temperature (℃) | Strain rate (s-1) | Δσ/σp at ε¯=0.50 | ||
|---|---|---|---|---|
| Heating related softening | Microstructure related softening | Total softening | ||
| 815 | 10-3 | 0.00 | 0.26 | 0.26 |
| 815 | 10-1 | 0.09 | 0.29 | 0.38 |
| 815 | 101 | 0.16 | 0.12 | 0.28 |
| 900 | 10-3 | 0.00 | 0.23 | 0.23 |
| 900 | 10-1 | 0.09 | 0.31 | 0.40 |
| 900 | 101 | 0.15 | 0.13 | 0.28 |
| 955 | 10-3 | 0.00 | 0.16 | 0.16 |
| 955 | 10-1 | 0.10 | 0.23 | 0.33 |
| 955 | 101 | 0.17 | 0.05 | 0.22 |
Fig. 19. The dislocation substructure and subgrain structure (LAB) within the lamellar α and β phases: (a) Ti-6Al-4 V alloy deformed at 600 ℃ to 25% height reduction (LAB is depicted as red line) [11]; (b) Ti-5Al-2Sn-2Zr-4Mo-4Cr alloy deformed at 800 ℃ to the strain of 0.11 (LAB is depicted as yellow line) [82];(c) Ti-6Al-4 V alloy deformed at 800 ℃ to the strain of 0.29 [83].
Fig. 20. Schematic of the relation between α morphology characteristic and flow softening extent [85].
Fig. 21. Fraction of lamellar α presenting different orientations with a bin size of 10° and Taylor factor for α lattice (solid line) [87].
Fig. 22. The variation of average Taylor factor with strain [87].
Fig. 23. The contribution of friction stress and Hall-Petch stress to the total stress [87].
Fig. 24. The peak flow stress vs. the inverse square root of the average lamellar α thickness for.
| Temperature(℃) | ks(MPam)at$\dot{\varepsilon}$(s-1)= | ks'MPamat$\dot{\varepsilon}$s-1= | ||||
|---|---|---|---|---|---|---|
| 0.1 | 1.0 | 10.0 | 0.1 | 1.0 | 10.0 | |
| Based on σp v.s. l-1/2 | Based on (σp-σss) v.s. l-1/2 | |||||
| 815 | 0.0296 | 0.0526 | 0.0547 | 0.0286 | 0.0518 | 0.0537 |
| 900 | 0.0242 | 0.0322 | 0.0424 | 0.0193 | 0.0283 | 0.0442 |
Table 3 The Hall-Petch constants based on σp v.s. l-1/2 and (σp-σss) vs. l-1/2 at different conditions [39].
| Temperature(℃) | ks(MPam)at$\dot{\varepsilon}$(s-1)= | ks'MPamat$\dot{\varepsilon}$s-1= | ||||
|---|---|---|---|---|---|---|
| 0.1 | 1.0 | 10.0 | 0.1 | 1.0 | 10.0 | |
| Based on σp v.s. l-1/2 | Based on (σp-σss) v.s. l-1/2 | |||||
| 815 | 0.0296 | 0.0526 | 0.0547 | 0.0286 | 0.0518 | 0.0537 |
| 900 | 0.0242 | 0.0322 | 0.0424 | 0.0193 | 0.0283 | 0.0442 |
Fig. 25. Bright field micrographs of Ti-5-5-5-3 deformed at 785 ℃ to strain of 0.1: (a) regions of high disloaction density in lamellar α, (b) slip transmission across α/β interfaces.
| Flow softening source | Main influencing factors | General influencing laws on flow softening |
|---|---|---|
| Deformation heating | •Temperature •Strain rate | Lower temperature and higher strain rate promote the deformation heating and flow softening |
| Evolution of dislocation substructure and dynamic recovery (DRV) | Higher temperature and lower strain rate facilitate the evolution of dislocation substructure, DRV and flow softening | |
| Dynamic globularization of lamellar α | -- | -- |
| Kinking of lamellar α | •Temperature •Strain rate | Lower temperature and higher strain rate promote lamellar α kinking and flow softening |
| Evolution of mechanical texture and crystallographic texture | •Mechanical texture and crystallographic texture of the initial microstructure •Compression direction | -- |
| Loss of Hall-Petch strengthening associated with α/β interfaces | •Temperature •Strain rate •Lamellar α thickness | Lower temperature, higher strain rate and smaller lamellar α thickness are beneficial to the Hall-Petch strengthening loss and flow softening |
| Adiabatic shear band and flow localization | •Temperature •Strain rate | Lower temperature and higher strain rate would increase the tendency to produce adiabatic shear band, flow localization and flow softening |
Table 4 Main influencing factors and laws for the flow softening of lamellar microstructure during hot deformation.
| Flow softening source | Main influencing factors | General influencing laws on flow softening |
|---|---|---|
| Deformation heating | •Temperature •Strain rate | Lower temperature and higher strain rate promote the deformation heating and flow softening |
| Evolution of dislocation substructure and dynamic recovery (DRV) | Higher temperature and lower strain rate facilitate the evolution of dislocation substructure, DRV and flow softening | |
| Dynamic globularization of lamellar α | -- | -- |
| Kinking of lamellar α | •Temperature •Strain rate | Lower temperature and higher strain rate promote lamellar α kinking and flow softening |
| Evolution of mechanical texture and crystallographic texture | •Mechanical texture and crystallographic texture of the initial microstructure •Compression direction | -- |
| Loss of Hall-Petch strengthening associated with α/β interfaces | •Temperature •Strain rate •Lamellar α thickness | Lower temperature, higher strain rate and smaller lamellar α thickness are beneficial to the Hall-Petch strengthening loss and flow softening |
| Adiabatic shear band and flow localization | •Temperature •Strain rate | Lower temperature and higher strain rate would increase the tendency to produce adiabatic shear band, flow localization and flow softening |
Fig. 26. The comparison of globularization fraction of Ti-17 sample deformed to 45% reduction at 840 ℃ between experimental and predicted results by integrated model [90]. (‘E’ and ‘S’ represent experiment data and simulation results, respectively).
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