Microstructure and Corrosion Resistance of Low-Carbon Martensitic Stainless Steel 0Cr13Ni4Mo with 3%Cu Addition

doi:10.11900/0412.1961.2022.00541

Acta Metall Sin

2024, Vol. 60

Issue (12): 1656-1666 DOI: 10.11900/0412.1961.2022.00541

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Microstructure and Corrosion Resistance of Low-Carbon Martensitic Stainless Steel 0Cr13Ni4Mo with 3%Cu Addition

YANG Binbin¹^,², SONG Yuanyuan¹(

), HAO Long¹, JIANG Haichang¹, RONG Lijian¹

1 CAS Key Laboratory of Nuclear Materials and Safety Assessment, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
2 School of Materials Science and Engineering, Taiyuan University of Science and Technology, Taiyuan 030024, China

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YANG Binbin, SONG Yuanyuan, HAO Long, JIANG Haichang, RONG Lijian. Microstructure and Corrosion Resistance of Low-Carbon Martensitic Stainless Steel 0Cr13Ni4Mo with 3%Cu Addition. Acta Metall Sin, 2024, 60(12): 1656-1666.

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Abstract

Low-carbon martensitic stainless steel 0Cr13Ni4Mo is widely used in hydraulic turbine runners, oil and gas storage, high-pressure pipes in power generation, and other fields owing to its high strength, good corrosion resistance, and good welding properties. However, to enhance its performance under different environments, there is a need to improve its strength and corrosion resistance. Previous studies have found that adding Cu to 0Cr13Ni4Mo steel enhances its strength through the formation of Cu-rich precipitation. However, the impact of Cu on the corrosion behavior of the 0Cr13Ni4Mo steel is not yet well understood. This study aims to investigate the effect of adding 3%Cu (mass fraction) on the microstructure and corrosion resistance of low-carbon martensitic stainless steel 0Cr13Ni4Mo using various techniques such as SEM, XRD, TEM, APT, and electrochemical testing. The results show that after solution treatment at 1050^oC, Cu is uniformly distributed on the lath martensite matrix. After tempering at 400^oC, Cu forms minute nanoclusters with a large number of Fe atoms segregated. On the other hand, tempering at 500^oC leads to the growth of Cu-rich precipitates with a size of 5-10 nm, where Cu atoms are mainly segregated at the core of the precipitates and are in a coherent relationship with the martensitic matrix. Carbides grow from Fe-rich nanoclusters to Cr-rich precipitates during the tempering process. The addition of 3%Cu to low-carbon martensitic stainless steel shows excellent corrosion resistance after tempering at 500^oC. This may be due to the emission of Cr atoms to the surrounding matrix during the growth of Cu-rich precipitates, which reduces the Cr-depleted zone caused by Cr-rich carbides in the matrix, thus reducing the corrosion sensitivity of 0Cr13Ni4Mo martensitic stainless steel with 3%Cu addition. These findings provide a better understanding of the role of Cu-rich precipitates on the corrosion performance of low-carbon martensitic stainless steels and provide guidance for the design of corrosion resistant steels.

Key words: 0Cr13Ni4Mo Cu-rich precipitation corrosion resistance atomic probe tomography

Received: 24 October 2022

ZTFLH:

TG142

Fund: Industrialized Science and Technology Cooperation Between Jilin Province and CAS(2024SYHZ0004);Natural Science Foundation of Liaoning Province(2020-MS-08)

Corresponding Authors: SONG Yuanyuan, assistant professor, Tel: (024)23971976, E-mail: songyuanyuan@imr.ac.cn

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	YANG Binbin
	SONG Yuanyuan
	HAO Long
	JIANG Haichang
	RONG Lijian

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https://www.ams.org.cn/EN/10.11900/0412.1961.2022.00541 OR https://www.ams.org.cn/EN/Y2024/V60/I12/1656

Table 1 Chemical compositions of two low-carbon martensitic stainless steels

Fig.1 SEM images of 0Cu (a-c) and 3Cu (d-f) steels after different heat treatments (a, d) solution treated at 1050^oC (b, e) tempered at 400^oC (c, f) tempered at 500^oC

Fig.2 XRD spectra of 0Cu and 3Cu steels after different heat treatments

Fig.3 TEM analyses of the 3Cu steel tempered at 500^oC for 2 h
(a) bright field TEM image
(b) corresponding EDS mapping of square area in Fig.3a of Cu
(c) HRTEM image of the matrix and Cu-rich precipitate
(d, f) enlarged HRTEM images of the matrix (d) and Cu-rich precipitate (f) in Fig.3c, respectively
(e, g) corresponding fast Fourier transformation (FFT) patterns of Figs.3d (e) and f (g), respectively

Fig.4 Potentiodynamic polarization curves of 0Cu and 3Cu steels after different heat treatments in 3.5%NaCl solution (E—potential, i—current density)

Table 2 Electrochemical parameters of potentiodynamic polarization curves of 0Cu and 3Cu steels after different heat treatments in 3.5%NaCl solution

Fig.5 Nyquist (a) and Bode (b) plots of 0Cu and 3Cu steels after different heat treatments in 3.5%NaCl solution (Z—impedance, Z'—real part of impedance, Z''—imaginary part of impedance, f—frequency)

Fig.6 Equivalent circuit diagram of 0Cu and 3Cu stainless steels in 3.5%NaCl solution (R_s—solution resistance, R_f—surface passivation film resistance, Q_f—surface passivation film capacitance, R_ct—double layer charge transfer resistance, C_dl—double layer capacitance)

Table 3 Equivalent circuit fitting parameters of 0Cu and 3Cu steels after different heat treatments in 3.5%NaCl solution

Fig.7 Atom distribution maps of Fe, Cr, Ni, Mn, Mo, C, and Cu in 3Cu steel solution treated at 1050^oC for 2 h (a) and the nearest neighbor count distributions of Cu (b) (d-pair—distance between two atoms)

Fig.8 Atom distribution maps of Fe, Cr, Ni, Mn, Mo, C, and Cu in 3Cu steel 400^oC tempered for 2 h (a), isoconcentration surface distribution of 1.3%C (atomic fraction) and corresponding C clusters distribution (b), and isoconcentration surface distribution of 4%Cu (atomic fraction) and corresponding Cu cluster distribution (c)

Fig.9 Atom distribution maps of Fe, Cr, Ni, Mn, Mo, C, and Cu in 3Cu stainless steel 500^oC tempered for 2 h (a), isoconcentration surface distribution of 3%C (atomic fraction) and corresponding C clusters distribution (b), and isoconcentration surface distribution of 15%Cu (atomic fraction) and corresponding Cu cluster distribution (c)

Fig.10 Schematics of the corrosion mechanism of 0Cu (a) and 3Cu (b) steels tempered at 500^oC

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