Effects of strain state and slip mode on the texture evolution of a near-α TA15 titanium alloy during hot deformation based on crystal plasticity method

doi:10.1016/j.jmst.2019.07.051

Abstract

Abstract:

A thorough understanding of the texture evolution of near-α titanium alloys during the hot metal forming can help obtain an optimal crystallographic texture and material performance. The strain state has an obvious effect on the texture evolution of near-α titanium alloys during the hot metal forming. In this paper, the texture evolution of a near-α TA15 titanium alloy during the hot metal forming under different strain states were discussed based on the crystal plasticity finite element method. It is found that the basal and prismatic slip systems are regarded as the dominant slip modes due to the similar low critical resolved shear stress during the hot metal forming of the TA15 sheet rotating the lattice around the [10$\bar{1}$0] and 〈0001〉 axis, respectively. Once both of them cannot be activated, the pyramidal-2 slipping occurs rotating the lattice around the [10$\bar{1}$0] axis. The relationship between the texture evolution and strain state is established. All the (0001) orientations form a band perpendicular to the direction of the first principal strain. The width of the band along the direction of the second principal strain depends on the ratio of the compressive effect to the tensile effect of the second principal strain. This relationship can help control the crystallographic texture and mechanical properties of the titanium alloys component during the hot metal forming.

Key words: Texture evolution, Strain states, Crystal plasticity method, Near-α, TA15 sheets;, Hot deformation

Zhao Jie, Lv Liangxing, Wang Kehuan, Liu Gang. Effects of strain state and slip mode on the texture evolution of a near-α TA15 titanium alloy during hot deformation based on crystal plasticity method[J]. J. Mater. Sci. Technol., 2020, 38: 125-134.

Figures/Tables 10

Fig. 1. Microstructure characterization of the undeformed TA15 sheet. (a) IPFs; (b) PFs.

Table 1 Parameters of CPFEM during the hot deformation of the TA15 sample.

Symbol	Meaning	Value
$\dot{γ}_0^α$	Reference shear strain rate (s^-1)	0.001
F₀	Helmholtz free energy (kJ mol^-1)	413
$τ_{cr}^α$	CRSS of prismatic slip systems (MPa)	140
p/q	Exponent	1.5 / 0.5
λ	Coefficient	0.024
μ	Shear modulus (GPa)	4.3
b	Burgers vector (m)	2.95×10^-10
h	Hardening parameter	0.3
$ρ_{Se}^β=ρ_{Ssw}^β$	Initial edge or screw dislocation density for each slip system (m^-2)	1.0×10¹³
C_e=C_Ssw	Coefficient	0.5
K_Se=K_Ssw	Parameters related to the mean free path	1×10^-5
d_Se=d_Ssw	Critical annihilation distance (m)	5×10^-7Table 1 Parameters of CPFEM during the hot deformation of the TA15 sample

Fig. 2. Polycrystal model and the simulated and experimental results of samples with the true strain of 0.3. (a) finite element model in ABAQUS; (b) comparison of orientations in simulation and experiment; simulated results during RD- (c) and TD-tension (d); (e) experimental results of undeformed and deformed samples; (f) fitting curves of true stress-strain; (g) simulated prismatic SF and dislocation density.

Fig. 3. Simulated and experimental (0001) and (10$\bar{1}$0) PFs during RD- and TD-tension. (a) (0001) PFs; (b) (10$\bar{1}$0) PFs.

Fig. 4. Simulated texture evolutions and shear strains induced by the dominant slip modes of grains with four initial orientations during RD- and TD-tension. evolution of (0001) PFs during RD- (a) and TD-tension (d); evolution of (10$\bar{1}$0) PFs during RD- (b) and TD-tension (e); shear strains induced by the dominant slip mode during RD- (c) and TD-tension (f).

Fig. 5. Schematics of lattice rotation of (0001) and {10\bar{1}0} planes during the hot uniaxial tension. (a) definition of angles α and β; (b) relationship between the SFs of basal and pyramidal-2 slipping and angle α; (c) relationship between the SFs of prismatic slipping and angle β; (d) lattice rotation of (0001) plane; (e) lattice rotation of {10\bar{1}0} planes.

Fig. 6. Simulated (0001) and (10$\bar{1}$0) PFs and the schematic of lattice rotation of (0001) plane of TA15 samples with initial random orientations during the hot uniaxial compression. (a) imposed stress; simulated (0001) and (10$\bar{1}$0) PFs with the effective strain of 0.25 (b) and 0.5 (c); (d) lattice rotation of (0001) plane.

Fig. 7. Simulated (0001) and (10$\bar{1}$0) PFs of TA15 samples with initial random orientations with an effective strain of 0.5 during the hot uniaxial and equi-biaxial compression. imposed stress during the hot equi-biaxial (a) and uniaxial compression (d); PFs of Y-Z plane (b) and X-Y plane (c) during the hot equi-biaxial compression; PFs of X-Z plane (e) and X-Y plane (f) during the hot uniaxial compression.

Fig. 8. Simulated (0001) and (10$\bar{1}$0) PFs of TA15 samples with initial random orientations during hot deformation under different strain states with an effective strain of 0.5. (a) equi-biaxial tension; (b) nonequi-biaxial tension; (c) plane strain; (d) nonequi-biaxial compression; (e) equi-biaxial compression. (X, Y and Z axes represent the directions of the first, second and third principal strain/stress, respectively.).

Fig. 9. Schematics of lattice rotation of (0001) and {10$\bar{1}$0} planes under different strain states. (a) lattice rotation of (0001) plane; (b) lattice rotation of {10$\bar{1}$0} planes; (c) comparison of the calculated and experimental values of the tilt angle θ.

References

[1]	K. Wang, G. Liu, J. Zhao, J. Wang, S. Yuan, Mater. Des. 91 (2016) 269-277.
[2]	G. Liu, K. Wang, B. He, M. Huang, S. Yuan, Mater. Des. 86 (2015) 146-151.
[3]	Y. Wu, G. Liu, K. Wang, Z. Liu, S. Yuan, Int. J. Adv. Manuf. Technol. 88 (5-8) (2016) 2143-2152.
[4]	K. Wang, G. Liu, K. Huang, D.J. Politis, L. Wang, Mater. Sci. Eng. A 708 (2017) 149-158.
[5]	Z. Zeng, Y. Zhang, S. Jonsson, Mater. Sci. Eng. A 513-514 (2009) 83-90.
[6]	P. Lin, A. Feng, S. Yuan, G. Li, J. Shen, Mater. Sci. Eng. A 563 (2013) 16-20.
[7]	J. Kawałko, P. Bobrowski, P. Koprowski, A. Jarz˛ebska, M. Bieda, M. Łagoda, K. Sztwiertnia, J. Alloys. Compd. 707 (2017) 298-303.
[8]	X.X. Wang, M. Zhan, M.W. Fu, P.F. Gao, J. Guo, F. Ma, J. Mater. Process. Technol. 261 (2018) 86-97.
[9]	N. Srinivasan, R. Velmurugan, R. Kumar, S.K. Singh, B. Pant, Mater. Sci. Eng. A 674 (2016) 540-551.
[10]	S.K. Sahoo, R.K. Sabat, S. Sahni, S. Suwas, Mater. Des. 91 (2016) 58-71.
[11]	H. Li, H.Q. Zhang, H. Yang, M.W. Fu, H. Yang, Int. J. Plast. 90 (2017) 177-211.
[12]	T. Mayama, M. Noda, R. Chiba, M. Kuroda, Int. J. Plast. 27 (12) (2011) 1916-1935.
[13]	G. Zhou, M.K. Jain, P. Wu, Y. Shao, D. Li, Y. Peng, Int. J. Plast. 79 (2016) 19-47.
[14]	L.S. Tóth, Y. Estrin, R. Lapovok, C. Gu, Acta Mater. 58 (5) (2010) 1782-1794.
[15]	F. Roters, P. Eisenlohr, L. Hantcherli, D.D. Tjahjanto, T.R. Bieler, D. Raabe, Acta Mater. 58 (4) (2010) 1152-1211.
[16]	E. Popova, Y. Staraselski, A. Brahme, R.K. Mishra, K. Inal, Int. J. Plast. 66 (2015) 85-102.
[17]	H. Li, X. Sun, H. Yang, Int. J. Plast. 87 (2016) 154-180.
[18]	J. Zhao, L. Lv, G. Liu, K. Wang, Mater. Sci. Eng. A 707 (2017) 30-39.
[19]	Y.B. Chun, M. Battaini, C.H.J. Davies, S.K. Hwang, Metall. Mater. Trans. A 41 (13) (2010) 3473-3487.
[20]	K. Wang, G. Liu, J. Zhao, K. Huang, L. Wang, J. Mater. Process. Technol. 259 (2018) 387-396.
[21]	G.I. Taylor, Analysis of Plastic Strain in a Cubic Crystal, in: Stephen Timoshenko 60th Anniversary Volume, 1938, pp. 218-224.
[22]	E.P. Busso, F.T. Meissonnier, N.P. O’Dowd, J. Mech. Phys. Solids 48 (11) (2000) 2333-2361.
[23]	K.-S. Cheong, E.P. Busso, Acta Mater. 52 (19) (2004) 5665-5675.
[24]	T.R. Bieler, S.L. Semiatin, Int. J. Plast. 18 (9) (2002) 1165-1189.
[25]	H. Li, D.E. Mason, T.R. Bieler, C.J. Boehlert, M.A. Crimp, Acta Mater. 61 (20) (2013) 7555-7567.
[26]	L.X. Lv, L. Zhen, Mater. Sci. Eng. A 528 (22) (2011) 6673-6679.
[27]	S. Balasubramanian, L. Anand, Acta Mater. 50 (1) (2002) 133-148.
[28]	H. Wu, W. Xu, D. Shan, B.C. Jin, J. Mater. Process. Technol. 263 (2019) 112-128.
[29]	X.G. Fan, H. Yang, P.F. Gao, J. Mater. Process. Technol. 214 (2) (2014) 253-266.
[30]	H. Li, X. Hu, H. Yang, L. Li, Int. J. Plast. 82 (2016) 127-158.
[31]	Z.J. Wang, H. Song, J. Alloys. Compd. 470 (1-2) (2009) 522-530.