Effect of Heat Treatment on Mechanical Properties of a Novel Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr Alloy

doi:10.11901/1005.3093.2023.532

Chinese Journal of Materials Research

2024, Vol. 38

Issue (7): 519-528 DOI: 10.11901/1005.3093.2023.532

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Effect of Heat Treatment on Mechanical Properties of a Novel Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr Alloy

PENG Wenfei¹^,²^,³, HUANG Qiaodong¹^,², Moliar Oleksandr¹^,², DONG Chaoqi¹^,², WANG Xiaofeng¹^,³(

)

^1.Faculty of Mechanical Engineering and Mechanics, Ningbo University, Ningbo 315211, China
^2.Key Laboratory of Part Rolling Technology, Ningbo University, Ningbo 315211, China
^3.Key Laboratory of Impact and Safety Engineering, Ministry of Education, Ningbo University, Ningbo 315211, China

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PENG Wenfei, HUANG Qiaodong, Moliar Oleksandr, DONG Chaoqi, WANG Xiaofeng. Effect of Heat Treatment on Mechanical Properties of a Novel Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr Alloy. Chinese Journal of Materials Research, 2024, 38(7): 519-528.

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Abstract

Herein, the effect of heat treatments (solution, solution+single aging and solution+double aging) on the microstructure and mechanical properties of a novel Ti-based alloy Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr was investigated through microstructure characterization and tensile testing. The microstructure observations indicate that the alloy prior to heat treatment possesses a bimodal microstructure consisted of primary α_p phase, secondary α_s phase, and β phase, and the volume fraction of the primary α_p phase and secondary α_s phase is 22% and 21%, respectively. After solution treated in the dual phase zone, a portion of the original α_p and α_s phases was replaced by β phase and the alloy microstructure is comprised of metastable β phase, equiaxed primary α_p phase, and coarse lamellar secondary α_s phase. After single aging, a large number of evenly distributed needle-like nano secondary α_s phases are precipitated within the β phase; After double aging, the volume fraction of α phase increases significantly, while the grain size of primary α_p phase and secondary α_s phase increases with the increasing aging time. Quasi-static tensile test results reveal that alloys subjected to solution treatment in the dual phase zone exhibit significant enhancements in elongation compared to the as hot-rolled ones, but yielding at lower stress levels. Single aging results in significant increase of strength, thereby presenting an improved strength-ductility balance of the alloy. In comparison with the hot rolling process, the double aging process is unfavored to the ductility, moreover, with the increasing aging time, the strength decreases and elongation increases gradually. Finally, the variation in the work hardening rate of the alloy subjected to different heat treatments may be explained by work hardening rate-strain curves. Based on the experimental data, the modified Hall-Petch constitutive model is fitted, whilst the results predicted by this constitutive model have high coincidence with the experimental data.

Key words: metallic materials α + β titanium alloy heat treatment microstructure mechanical property

Received: 31 October 2023

ZTFLH:

TG146.2

Fund: Major Project of Ningbo Science and Technology Innovation 2025(2021Z099);National Natural Science Foundation of China(52075272);State Key laboratory for Advanced Metal and Materials

Corresponding Authors: WANG Xiaofeng, Tel: 17858883615, E-mail: wangxiaofeng@nbu.edu.cn

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	PENG Wenfei
	HUANG Qiaodong
	Moliar Oleksandr
	DONG Chaoqi
	WANG Xiaofeng

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https://www.cjmr.org/EN/10.11901/1005.3093.2023.532 OR https://www.cjmr.org/EN/Y2024/V38/I7/519

Table 1 Main chemical compositions of Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr alloy (mass fraction, %)

Fig.1 Hot rolled rod microstructure of Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr alloy

Table 2 Heat treatment process schedule

Fig.2 Schematic diagram of the tensile sample

Fig.3 X-ray diffraction of specimens with different states

Fig.4 Microstructure of Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr alloy after solution treatment at 850^oC

Fig.5 Microstructure of Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr alloy after 850^oC solution+aging treatment (a) SA1; (b) SA2; (c) SA3; (d) SA4

Heat treatment	α_p phase volume fraction $V α p$ / %	α_p phase equivalent diameter λ / μm	α_s phase volume fraction $V α s$ / %	α_s phase interval λ / μm
Hot rolled	22	1.0	21	0.08
ST1	36	1.1	15	0.3
SA1	33	1.2	19	0.03
SA2	42	1.8	27	0.08
SA3	42	1.8	29	0.08
SA4	43	1.9	30	0.1

Table 3 Microstructure changes of titanium alloy after different heat treatment

Fig.6 Tensile engineering stress-strain curve of titanium alloy under different heat treatment conditions

Heat treatment	Mechanical property
Heat treatment	UTS / MPa	YS / MPa	EL / %
Hot rolled	1120 $- 6 + 15$	1054 $- 8 + 11$	14.4 $- 1.3 + 1.7$
ST1	973 $- 4 + 21$	916 $- 4 + 14$	15.4 $- 1.8 + 2.1$
SA1	1149 $- 21 + 9$	1111 $- 13 + 9$	14.3 $- 0 + 2.7$
SA2	1118 $- 13 + 3$	1106 $- 4 + 5$	8.2 $- 2 + 0.3$
SA3	1109 $- 7 + 4$	1090 $- 1 + 8$	11.3 $- 1.2 + 1.8$
SA4	1085 $- 8 + 21$	1070 $- 4 + 11$	11.4 $- 0.3 + 0$
Common titanium alloys
TC4	933	894	8.7
TC11	1030	910	9
TC16	1087	920	16
TC18	1101	1049	12
SP700	-	1192	5.5

Table 4 Mechanical properties of Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr alloy

Fig.7 Fracture morphology of specimens with different states (a、d) ST1; (b、e) SA1; (c、f) SA2

Fig.8 Work hardening rate-strain curves of the Ti-6Al-2Mo-2V-3 Nb-2Fe-1Zr alloy (a) Tensile hardening curve; (b) Change pattern of the hardening curve

Fig.9 Microstructures of Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr alloy after solution at 910^oC

Fig.10 Tensile engineering stress-strain curve of Ti-6Al-2Mo-2V-3Nb-2Fe-1Zr alloy after 910^oC solution

Fig.11 Schematic illustration of dislocation movement in α_s spacing

Fig.12 Fitting and actual value comparison of different microscopic tissue intensity assignments

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