Effect of Inherent Films Resulted from Manufacturing Process on Corrosion of B30 Cu-Ni Alloy

doi:10.11902/1005.4537.2025.037

Journal of Chinese Society for Corrosion and protection

2025, Vol. 45

Issue (6): 1575-1588 DOI: 10.11902/1005.4537.2025.037

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Effect of Inherent Films Resulted from Manufacturing Process on Corrosion of B30 Cu-Ni Alloy

WANG Lifang, SHANG Mengchao, GAO Xiyu, LIU Guichang(

), SUN Wen

School of Chemical Engineering, Dalian University of Technology, Dalian 116024, China

Cite this article:

WANG Lifang, SHANG Mengchao, GAO Xiyu, LIU Guichang, SUN Wen. Effect of Inherent Films Resulted from Manufacturing Process on Corrosion of B30 Cu-Ni Alloy. Journal of Chinese Society for Corrosion and protection, 2025, 45(6): 1575-1588.

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Abstract

The inherent surface film resulted from the manufacturing process on the as received B30 Cu-Ni alloy may affect its corrosion behavior, especially the initial stage of corrosion, but there is a lack of methods to quickly evaluate such influence. In this paper, the initial corrosion behavior in seawater of two B30 Cu-Ni alloys of more or less the same chemical composition but with different inherent films resulted by different manufacturing process were studied via immersion test with EIS and Mott-Schottky measurement, as well as SEM and XPS etc. The results show that the presence of Ni oxide and carbon film in the inherent film leads to a higher initial corrosion potential and higher impedance of B30 Cu-Ni alloy with the inherent film rather than that has the film removed, which is not conducive to the rapid formation of a corrosion products film on B30 Cu-Ni alloy in seawater. In particular, when elemental carbon exists in the inherent film, the potential difference between the surface film and the substrate can be maintained for a long time, thus a "large cathode and small anode" will be formed between the surface film and the substrate. This condition leads to localized corrosion of the substrate, significantly reducing the corrosion resistance of B30 Cu-Ni alloy. When the free corrosion potential of the B30 Cu-Ni alloy withinherent film is negative or can be reduced within 1 h and maintained below -0.1 V during corrosion process, a passive film with good corrosion resistance may form on the B30 Cu-Ni alloy surface. When the free corrosion potential of the B30 Cu-Ni alloy with inherent film is positive and maintained for a long time, pitting is easy to occur, which is not conducive to the corrosion resistance of B30 Cu-Ni alloy. It follows that the characteristics of free corrosion potential and its evolution of B30 Cu-Ni alloy with inherent films can be used as an index to evaluate the influence of the inherent films on the corrosion resistance of B30 Cu-Ni alloy.

Key words: B30 Cu-Ni alloy original film potential corrosion resistance localized corrosion

Received: 26 January 2025 32134.14.1005.4537.2025.037

ZTFLH:

TG174

Corresponding Authors: LIU Guichang, E-mail: gchliu@dlut.edu.cn

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	WANG Lifang
	SHANG Mengchao
	GAO Xiyu
	LIU Guichang
	SUN Wen

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https://www.jcscp.org/EN/10.11902/1005.4537.2025.037 OR https://www.jcscp.org/EN/Y2025/V45/I6/1575

Table 1 Compositions of B30 Cu-Ni alloy pipe sample (mass fraction/ %)

Fig.1 Surface morphologies of A sample (a, b), B sample (c, d) and C sample (e, f) after immersion in seawater for 10 d (a, c, e) and 60 d (b, d, f)

Table 2 EDS results of the marked points in Fig.1 for A, B and C samples immersed in seawater for 60 d (mass fraction / %)

Fig.2 Surface morphologies of A sample (a), B sample (b) and C sample (c) immersed in seawater for 60 d after removal of the corrosion product films

Fig.3 XPS fine peaks of Cu 2p (a-c), Ni 2p_3/2 (d-f) and Fe 2p_3/2 (g-i) on the surfaces of A sample (a, d, g), B sample (b, e, h) and C sample (c, f, i) after immersion in seawater for 60 d

Fig.4 XPS determined contents of Cu (a), Ni (b) and Fe (c) compounds in corrosion product films formed on A, B and C samples

Fig.5 Open-circuit potential vs. time curves of A sample (a), B sample (b) and C sample (c) immersed in seawater for 60 d

Fig.6 Nyquist (a, c) and Bode (b, d) plots EIS of A sample immersed in seawater for 60 d

Fig.7 Nyquist (a, c) and Bode (b, d) plots of B sample immersed in seawater for 60 d

Fig.8 Nyquist (a, c) and Bode (b, d) plots of C sample immersed in seawater for 60 d

Fig.9 Equivalent circuit models for fitting EIS data: (a) C sample, no corrosion, (b) initial stage of corrosion, (c) medium and late stages of corrosion

Table 3 Fitting parameters of EIS of A sample immersed in seawater for 60 d

Table 4 Fitting parameters of EIS of B sample immersed in seawater for 60 d

Table 5 Fitting parameters of EIS of C sample immersed in seawater for 60 d

Fig.10 Variations of R_ct (a) and R_f (b) of A, B and C samples in seawater with immersion time

Fig.11 Polarization curves of A, B and C samples after 60 d immersion in seawater

Table 6 Fitting parameters of polarization curves of A, B and C samples immersed in seawater for 60 d

Fig.12 Mott-Schottky curves of A sample (a), B sample (b) and C sample (c) after immersion in seawater for 60 d

Table 7 Fitting results of Mott-Schottky curves in Fig.12

Fig.13 Surface morphologies of A sample (a) and B sample (b) with original corrosion films

Table 8 EDS results of the compositions of the marked regions in Fig.13

Fig.14 XPS survey spectra of the original corrosion films of A sample and B sample (a), and fine peaks of C 1s (b), Cu 2p (c), and Ni 2p_3/2 (d)

Fig.15 Open circuit potentials (a) and lg |Z|_{0.01 Hz} values (b) of A and B samples with and without the original corrosion films after immersion in seawater for 30 min

Fig.16 Open-circuit potentials of A and B samples as a function of time

Fig.17 Schematic illustrations of effects of the original corrosion films on the subsequent corrosion processes of A sample (a, b) and B sample (c, d)

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