Effect of hydrogen charging on microstructural evolution and corrosion behavior of Ti-4Al-2V-1Mo-1Fe alloy

doi:10.1016/j.jmst.2020.06.010

Abstract

Abstract:

The effect of hydrogen charging on microstructural evolution and corrosion behavior of a Ti-4Al-2V-1Mo-1Fe alloy in a 3.5 wt.% NaCl solution was investigated. The results showed that the hydrogen charging induced the formation and growth of γ-TiH and δ-TiH₂ phases, leading to the initiation and propagation of hydrogen-induced cracks. It was also found that hydrogen charging can change the passivity of this alloy and increase its pitting corrosion susceptibility. The main reason for these was attributed to the formation of hydrides in α phase in the Ti-4Al-2V-1Mo-1Fe alloy, leading to the preferential dissolution of the α phase and thus the deterioration in the protective ability of passive film.

Key words: Titanium alloy, Hydrogen, Microstructure, Corrosion, Electrochemical

Yanxin Qiao, Daokui Xu, Shuo Wang, Yingjie Ma, Jian Chen, Yuxin Wang, Huiling Zhou. Effect of hydrogen charging on microstructural evolution and corrosion behavior of Ti-4Al-2V-1Mo-1Fe alloy[J]. J. Mater. Sci. Technol., 2021, 60: 168-176.

Figures/Tables 13

Fig. 1. SEM image of the etched Ti4211 alloy (a), EDS analysis of the α phase in the Ti4211 alloy (b), and EDS analysis of the β phase in the Ti4211 alloy (c).

Table 1 Chemical compositions of the α and β phases (wt.%) analyzed using EDS in Fig.1.

	Ti	Al	V	Mo	Fe
α	93.3	4.4	2.3	-	-
β	78.7	2.5	7.8	6.0	5.0

Fig. 2. (a) XRD patterns of the uncharged and hydrogen-charged Ti4211 alloy at different charging times, (b) section of XRD plots in (a) ranging from 33° to 43°.

Fig. 3. DSC curves of the charged and uncharged Ti4211 alloy.

Fig. 4. Surface morphologies of the Ti4211 alloy after hydrogen charging for 4 h (a), 8 h (b), 12 h (c), and 24 h (d).

Fig. 5. Nyquist (a) and Bode plots (b) of the charged and uncharged Ti4211 alloys in 3.5 wt.% NaCl solution. The data at 0 h were reproduced from the Ref. [5].

Table 2 Parameters of equivalent circuit obtained by fitting the EIS spectra.

t (h)	R_s (Ω cm²)	R_p (Ω cm²)	Q (Ω^-1 Sⁿ cm^-2)	n
0	8.71 ± 0.87	6.50 ± 0.35 × 10⁵	2.56 ± 0.26 × 10^-5	0.95 ± 0.01
1	11.69 ± 1.17	6.44 ± 0.14 × 10⁵	4.37 ± 0.15 × 10^-5	0.93 ± 0.01
4	12.49 ± 0.24	3.58 ± 0.52 × 10⁵	3.25 ± 0.47 × 10^-5	0.93 ± 0.02
24	7.32 ± 0.71	6.18 ± 0.76 × 10⁴	1.44 ± 0.36 × 10^-4	0.83 ± 0.03

Table 3 Corrosion parameters derived from the potentiodynamic polarization curves in Fig. 7.

t (h)	E_corr (V_SCE)	i_corr (A /cm²)	i_p (A /cm²)	E_p (V_SCE)
0	-0.36	4.91 × 10^-8	4.75 × 10^-6	-
1	-0.51	6.97 × 10^-8	5.15 × 10^-6	-
4	-0.34	1.82 × 10^-7	6.73 × 10^-6	1.4
24	-0.25	7.75 × 10^-7	2.01 × 10^-5	1.2

Fig. 8. Morphologies of the Ti4211 sample hydrogen charged for 24 h after potentiodynamic polarization test: (a) corrosion morphology, (b) high magnification of the area marked by the red square in Fig. 8(a), and (c) three-dimensional (3D) optical micrographs.

Fig. 9. Cross-sectional images of the Ti4211 sample after hydrogen charging for 24 h.

Fig. 10. Schematics showing the hydride formation process in the Ti4211 alloy during hydrogen charging [79].

Fig. 6. Equivalent circuit used for quantitative evaluation of the EIS spectra in Fig. 5.

Fig. 7. Potentiodynamic polarization curves of the charged and uncharged Ti4211 alloy in 3.5 wt.% NaCl solution.

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