Effect of sulfate-reducing bacteria on hydrogen permeation and stress corrosion cracking behavior of 980 high-strength steel in seawater

doi:10.1016/j.jmst.2021.02.039

Abstract

Abstract:

980 high-strength steel has been widely used in marine engineering structures due to its high strength and toughness. However, it is easily affected by the harsh environmental conditions (such as the presence of sulfate-reducing bacteria, SRB), leading to the risk of stress corrosion cracking (SCC). In this paper, the effects of SRB and its metabolites on hydrogen permeation and SCC mechanism of 980 steel in seawater solution were investigated by slow strain rate tensile test, scanning electron microscope, X-ray energy spectroscopy, Raman spectroscopy and Devanathan-Stachurski double electrolytic cell. Results demonstrated that the SCC susceptibility of 980 steel was promoted in the presence of SRB, which was related to the cultivation time of the bacteria. When SRB were cultivated for 3d and 6d, the SCC mechanism was controlled by hydrogen-induced cracking (HIC); while the cultivation time extended to 11d, the SCC of 980 steel was under the combined effect of the anodic dissolution (AD) and HIC mechanism. When cultivated for 16d, the SCC of 980 steel was caused by the dominant AD. Both the SRB accelerated hydrogen permeation under cathodic depolarization process and SRB assisted AD (pitting corrosion) played an enhancing role in promoting SCC susceptibility of 980 steel.

Key words: Stress corrosion cracking, Sulfate-reducing bacteria, Microbiologically influenced corrosion, 980 High-strength steel, Seawater

Meiying Lv, Xuchao Chen, Zhenxin Li, Min Du. Effect of sulfate-reducing bacteria on hydrogen permeation and stress corrosion cracking behavior of 980 high-strength steel in seawater[J]. J. Mater. Sci. Technol., 2021, 92: 109-119.

Figures/Tables 14

Fig. 1. Schematic diagram of the hydrogen permeation device.

Fig. 2. Dimension of the specimen used in SSRT test (unit: mm).

Fig. 3. Stress-strain curves of 980 steel in different solutions.

Fig. 4. The SCC susceptibilities of 980 steel in different environments expressed as (a) the ratio of elongation-loss and (b) the ratio of reduction-in-area.

Fig. 5. Fracture morphologies of 980 steel (a, a1 and a2) in air and inoculated SRB solutions cultivated for (b, b1 and b2) 3d, (c, c1 and c2) 6d, (d, d1 and d2) 11d and (e, e1 and e2) 16d. (The yellow and blue arrows indicate secondary cracks and corrosion pits, respectively).

Fig. 6. Side morphologies of 980 steel (a) in air and inoculated SRB solutions cultivated for (b) 3d, (c) 6d, (d) 11d and (e) 16d. (The yellow and blue arrows indicate secondary cracks and corrosion pits, respectively).

Fig. 7. Polarization curve of the nickel-plated 980 steel in 0.1mol/L NaOH solution.

Fig. 8. Hydrogen permeation curves of 980 steel in different solutions.

Fig. 9. Hydrogen permeation parameters of 980 steel in different solutions: (a) the diffusion coefficient, (b) the diffusion flux of hydrogen and (c) the apparent hydrogen concentration.

Fig. 10. SEM images of 980 steel after immersing in different media for 24h (a) sterile, (b) 3D- SRB, (c) 6d-SRB, (d) 11d-SRB and (e) 16d-SRB.

Table 1 EDS results of the element contents (at%) in the corrosion products marked in Fig. 10.

Element	C	O	Fe	S
Sterile	29.44	40.26	29.97	0.33
3D- SRB	7.45	67.29	22.70	2.55
6d-SRB	9.00	72.88	17.55	0.57
11d-SRB	16.72	50.40	21.18	11.70
16d-SRB	17.66	41.15	22.41	18.78

Fig. 11. Raman spectrum of corrosion products of 980 steel immersed in different media for 24 h.

Fig. 12. Schematic diagrams of the effect of SRB on hydrogen permeation (a) 3D- SRB, (b) 6d-SRB, (c) 11d-SRB and (d) 16d-SRB.

Fig. 13. Schematic diagram of the SCC process controlled by the HIC and AD mechanisms for 980 steel in different solutions. (It represents only the relative contributions of these two factors, rather than the real values.).

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