Process design and microstructure-property evolution during shear spinning of Ti2AlNb-based alloy

doi:10.1016/j.jmst.2021.05.065

Abstract

Abstract:

Rotationally symmetric workpieces of Ti₂AlNb-based alloys have great potential for high-temperature service condition in aviation industry, while the poor workability limits their application until now. In this study, shear spinning and heat treatment were first conducted to investigate the corresponding microstructure evolution and mechanical properties of Ti₂AlNb conical workpieces. The microstructure of the 1^st and 2^nd pass spun workpieces (SP1 and SP2) mainly consisted of B2 + retained α₂ phases. After two passes spinning, the B2 phase texture changed from <111>//ND of as-received alloy to be <001>//ND. The ultimate tensile stress (UTS) of SP1 and SP2 was increased to 1163 MPa and 932 MPa, respectively, compared with 782 MPa of as-received alloy at 650 °C. Also, the yield stress anomaly (YSA) occurred in SP1 and SP2 because {110}<111> and {112}<111> cross slip systems of B2 phase were difficult to slip at or below room temperature (RT), but they became active at 650 °C and above. As an essential step for increasing the spinnability of multi-pass spinning process of the Ti₂AlNb alloy, the H3 heat treatment scheme, i.e. 960°C/2 h+ 850°C/12 h, was carried out between two successive passes to increase the hot workability, by which the ductility of the heat treated as-spun workpieces with the microstructure of B2 + primary O + acicular secondary O + high amount spheroidized α₂ phases reached 72.1% at 900°C. After being subject to the H1 heat treatment scheme, i.e. 960 °C-2 h, the spun workpieces with the microstructure of B2 + primary O + intergranular primary α₂ phases achieved an optimized comprehensive mechanical properties both at room temperature and 650°C, which should be chosen as the post-spinning heat treatment process for the service requirement.

Key words: Ti₂AlNb-based alloy, Shear spinning, Conical workpiece, Microstructural evolution, Mechanical property

Sibing Wang, Wenchen Xu, Bin Shao, Guoping Yang, Yingying Zong, Wanting Sun, Zhongze Yang, Debin Shan. Process design and microstructure-property evolution during shear spinning of Ti₂AlNb-based alloy[J]. J. Mater. Sci. Technol., 2022, 101: 1-17.

Figures/Tables 22

Fig. 1. (a) Illustration of shear spinning, (b) schematic diagram of 2 passes shear spinning experimental procedure, (c) shear spinning of Ti2AlNb alloy by gas torches, (d) illustrations of sampling location in spun workpieces.

Table 1 The applied heat treatment schemes and the corresponding phase constitutes for the Ti2AlNb alloy and in this study.

Scheme	Heat treatment parameters	Microstructure
H1	960 °C/2 h AC	B2 + primary O + primary α₂
H2	960 °C/2 h AC+820 °C/12 h FC	B2 + primary O + acicular secondary O+ high amount spheroidized α₂
H3	960 °C/2 h AC+850 °C/12 h FC	B2 + primary O + acicular secondary O + high amount spheroidized α₂

Fig. 2. Initial microstructure of the as-received Ti2AlNb sheet: (a) metallographic image, (b, c) BSE images, (d) TEM bright field image and selected area electron diffraction (SAED) patterns.

Fig. 3. Tensile strain-stress curves and fracture morphologies of as-received alloy at different temperatures: (a) tensile strain-stress curves, (b-d) fracture morphologies at room temperature, 650 °C and 900 °C, respectively.

Table 2 Mechanical property of as-received (AR), SP1, SP2, HTSP1 and HTSP2 at room temperature (RT), 650 °C and 900 °C with a strain rate of 0.001 s-1.

Material	UTS (MPa)	YS (MPa)	ε_f (%)	UTS (MPa)	YS (MPa)	ε_f (%)	UTS (MPa)	YS (MPa)	ε_f (%)
	RT			650 °C			900 °C
AR	1136±56	935±45	9.5±0.5	782±39	675±33	18.3±0.9	200±10	145±7	75.6±3.8
SP1	1069±53	956±47	1.1±0.1	1163±58	1075±53	8.9±0.4	297±14	277±10	42.7±2.1
SP1-H1	1174±57	1010±48	10.5±0.5	1020±51	834±41	12.9±0.6	248±12	231±11	56.6±2.8
SP1-H2	1087±54	960±47	6.0±0.3	792±39	703±35	14.9±0.7	237±11	215±10	61.7±3.1
SP1-H3	1045±52	880±44	5.6±0.3	733±35	678±33	17.3±0.9	232±12	207±10	72.1±3.6
SP2	902±45	824±41	0.6±0.1	932±45	856±42	12.5±0.6	210±10	189±9	78.7±3.9
SP2-H1	968±33	901±44	6.5±0.3	934±46	691±34	15.1±0.8	172±8	162±8	91.6±4.6
SP2-H2	815±40	785±39	1.2±0.1	747±37	674±33	16.4±0.8	170±8	158±7	94.8±4.7
SP2-H3	804±40	764±38	1.1±0.1	615±31	467±23	21.9±1.1	179±9	155±7	116.9±5.8

Fig. 4. Photos of the as-received circular plate and spun workpieces: (a) as-received circular plate, (b) successful 1st pass pun workpiece, (c) failed 2nd pass spun workpiece processed by continuous spinning without inter-pass heat treatment, (d) successful 2nd pass spun workpiece made by the optimized process with inter-pass heat treatment.

Fig. 5. Tensile strain-stress curves and fracture morphologies of SP1 at different temperatures: (a) tensile strain-stress curves, (b-d) fracture morphology at room temperature, 650 °C and 900 °C, respectively.

Fig. 6. Microstructure of SP1: (a) OM, (b) BSE, (c) Bright field image of TEM, (d) diffraction pattern of B2 and α2 phase in (c).

Fig. 7. Strain-stress curves of HTSP1 at different temperatures and fracture morphologies of HTSP1 at 900 °C: (a, b, c) strain-stress curves of HTSP1 at room temperature, 650 °C and 900 °C, respectively; (d, e, f) typical fracture morphologies of SP1-H1, SP1-H2 and SP1-H3 specimens at 900 °C, respectively.

Fig. 8. Micrographs of HTSP1: (a, b) BSE images of SP1-H1 specimen; (c) bright field image of TEM result of SP1-H1 specimen; (d) diffraction patterns of B2, α2 and O phases in (c); (e, f) BSE images of SP1-H2 specimen; (g, h) BSE images of SP1-H3 specimen.

Fig. 9. Strain-stress curves and fracture morphologies of SP2 at different temperatures: (a) strain-stress curves, (b-d) typical fracture morphologies at room temperature, 650 °C and 900 °C, respectively.

Fig. 10. Microstructure of SP2: (a) OM, (b) BSE, (c) bright field image of TEM, (d) diffraction patterns of B2 and α2 phases in (c).

Fig. 11. Strain-stress curves of HTSP2 at different temperatures and fracture morphologies of HTSP1 at room temperature: (a-c) strain-stress curves of HTSP2 at room temperature, 650 °C and 900 °C, respectively; (d-f) typical fracture morphologies of SP2-H1, SP2-H2 and SP2-H3 at room temperature, respectively.

Fig. 12. BSE micrographs of HTSP2 samples: (a, b) BSE of SP2-H1; (c, d) BSE of SP2-H2; (e, f) BSE of SP2-H3.

Fig. 13. Phase map and inverse pole figure (IPF) of the as-received sheet and spun workpieces: (a, b) AR, (c, d) SP1, (e, f) SP2.

Fig. 14. B2 phase invers pole figure (IPF), pole figure (PF) and ODF in RD-TD plane of the as-received sheet and spun workpieces: (a-c) AR, (d-f) SP1, (g-i) SP2, (j) standard stereographic projection of some key orientations.

Fig. 15. Schematic diagram of texture evolution mechanism of B2 phase during two passes spinning: (a) <111>//ND texture of as-received alloy, (b) <111>//ND and <001>//ND texture of 1st pass spun workpiece, (c) <001>//ND texture of 2nd pass spun workpiece.

Fig. 16. Schmid factors of B2 phase in RD under different slip systems including {110}<001>, {110}<111> and{112}<111>: (a-c) AR, (d-f) SP1, (g-i) SP2.

Fig. 17. Schmid factors of B2 phase in ND under different slip systems including {110}<001>, {110}<111> and{112}<111>: (a-c) AR, (d-f) SP1, (g-i) SP2.

Table 3 Mean Schmid factors of three different slip systems in RD

Slip system	AR	SP1	SP2
{110}<001>	0.41	0.31	0.24
{110}<111>	0.44	0.47	0.48
{112}<111>	0.46	0.47	0.48

Table 4 Mean Schmid factors of three different slip systems in ND

Slip system	AR	SP1	SP2
{110}<001>	0.45	0.32	0.11
{110}<111>	0.36	0.42	0.44
{112}<111>	0.39	0.45	0.48

Fig. 18. (a, c, e) Mechanical property comparison between AR, SP1 and HTSP1; (b, d, f) mechanical property comparison between AR, SP2 and HTSP2.

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Process design and microstructure-property evolution during shear spinning of Ti₂AlNb-based alloy

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