Effect of Ce on Cleanliness, Microstructure, and Pitting Corrosion Resistance of 75Cr1 Steel

doi:10.11900/0412.1961.2022.00359

Acta Metall Sin

2024, Vol. 60

Issue (9): 1229-1238 DOI: 10.11900/0412.1961.2022.00359

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Effect of Ce on Cleanliness, Microstructure, and Pitting Corrosion Resistance of 75Cr1 Steel

MENG Ze¹, LI Guangqiang¹^,², LI Tengfei³, ZHENG Qing⁴, ZENG Bin⁴, LIU Yu¹(

)

^1.State Key Laboratory of Refractories and Metallurgy, Wuhan University of Science and Technology, Wuhan 430081, China
^2.Key Laboratory for Ferrous Metallurgy and Resources Utilization of Ministry of Education, Wuhan University of Science and Technology, Wuhan 430081, China
^3.Hubei Provincial Key Laboratory for New Processes of Ironmaking and Steelmaking, Wuhan University of Science and Technology, Wuhan 430081, China
^4.Lianyuan Iron and Steel Co. Ltd., Loudi 417009, China

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MENG Ze, LI Guangqiang, LI Tengfei, ZHENG Qing, ZENG Bin, LIU Yu. Effect of Ce on Cleanliness, Microstructure, and Pitting Corrosion Resistance of 75Cr1 Steel. Acta Metall Sin, 2024, 60(9): 1229-1238.

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Abstract

Saw blades are always running under a high resonance, large lateral pressure, large tensile stress, and corrosive environment. Nonmetallic inclusions in steel break the continuity of the matrix and easily cause stress concentration and crack formation. Furthermore, the inclusions, especially MnS/CaS, cause the initiation of pitting corrosion. Rare-earth elements in steel can play the role in liquid steel purification, inclusion modification, and solid solution alloying. Rare-earth inclusions can act as the nucleation sites for the formation of the δ-Fe/γ-Fe phase during the solidification of molten steel, thus refining the solidification structure, and have relatively lower pitting sensitivity. In this study, the effect of Ce treatment on the cleanliness, microstructure, and corrosion resistance of 75Cr1 steel was investigated via inclusion characterization and in situ observation of the microstructure evolution as well as electrochemical polarization experiments. Results showed that Ce can effectively remove O, S, and other impurity elements in steel. With the increase in Ce content, the typical inclusions in 75Cr1 steel changed from the initial Ca-Mg-Al-O + MnS + CaS + TiN inclusions to Ce₂O₂S and Ce₂O₂S-CeAlO₃ inclusions and then to rare-earth sulfide inclusions. After the oxygen and sulfur contents were reduced to a certain extent, Ce started to combine with residual elements such as P and As to form rare-earth phosphide and arsenide inclusions. The size and number of inclusions firstly decreased and then increased. Meanwhile, the morphology of the inclusions firstly changed from irregular to spherical and then changed to irregular again when excessive Ce was added. The addition of appropriate Ce can refine the austenite grains and inhibit their growth; moreover, the corrosion potential and pitting corrosion resistance of steel are improved and the self-corrosion currents decrease. The 0.0195%Ce-containing 75Cr1 steel showed the highest cleanliness, a refined microstructure, and enhanced pitting corrosion resistance.

Key words: Ce treatment inclusions characteristics oxygen content sulfur content grain refinement pitting corrosion resistance

Received: 27 July 2022

ZTFLH:

TF769.9

Fund: National Natural Science Foundation of China(52004189);Key Research and Development Pro-jects of Hubei Province(2022BAA021)

Corresponding Authors: LIU Yu, associate professor, Tel: 18007135350, E-mail: liuyu629@wust.edu.cn

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	MENG Ze
	LI Guangqiang
	LI Tengfei
	ZHENG Qing
	ZENG Bin
	LIU Yu

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https://www.ams.org.cn/EN/10.11900/0412.1961.2022.00359 OR https://www.ams.org.cn/EN/Y2024/V60/I9/1229

Fig.1 Schematic of high frequency induction furnace

Fig.2 Heat treatment pattern for in situ observations

Fig.3 Variation of total oxygen and sulfur content in steel with Ce content

Fig.4 Sizes (a) and number distributions (b) of inclusions in steels (C1: 0%Ce, C2: 0.0074%Ce, C3: 0.0195%Ce, C4: 0.0260%Ce, C5: 0.0416%Ce)

Fig.5 Morphology and element distributions of typical inclusions in C1 steel

Fig.6 Morphologies and element distributions of typical inclusions in C2 steel
(a) Ce₂O₂S (b) Ce₂O₂S-CeAlO₃

$E q u a t i o n$	ΔG^θ / (J·mol^-1)	No.
$[C e] + [O] + 1 / 2 [S] = 1 / 2 C e 2 O 2 S (s)$	$- 675700 + 165.50 T$	(1)
$[C e] + 3 / 2 [O] = 1 / 2 C e 2 O 3 (s)$	$- 714380 + 179.74 T$	(2)
$[C e] + A l 2 O 3 (s) = C e A l O 3 (s) + [A l]$	$- 423900 + 247.30 T$	(3)
$[C e] + [S] = C e S (s)$	$- 422100 + 120.38 T$	(4)
$[C e] + 3 / 2 [S] = 1 / 2 C e 2 S 3 (s)$	$- 536420 + 163.86 T$	(5)
$[C e] + 4 / 3 [S] = 1 / 3 C e 3 S 4 (s)$	$- 497670 + 146.30 T$	(6)

Table 1 Standard Gibbs free energies of rare earth inclusions^[34]

Fig.7 O-S equilibrium curve (a) and Ce-Al equilibrium curve (b) in molten steel at 1600^oC (w[M]—mass fraction of dissolved element M in liquid steel)

Fig.8 Morphology and element distributions of typical inclusions in C3 steel

Fig.9 Ce-S equilibrium curves in molten steel at 1600^oC

Fig.10 Morphologies and element distributions of typical inclusions in C4 (a) and C5 (b) steels

Fig.11 In situ CLSM images of tested steels after 30 min holding at 1150^oC (a-c) and corresponding processed diagrams of grain boundary (d-f)
(a, d) C1 (b, e) C3 (c, f) C5

Fig.12 Phase distributions in 75Cr1 steel at different temperatures

Fig.13 Average austenite grain sizes of steels after different holding time at 1150^oC

Fig.14 Polarization curves of the C1, C3, and C5 steels (Insets show the corresponding local magnified curves)

Table 2 Electrochemical parameters of the C1, C3, and C5 steels in 3.5%NaCl corrosion solution

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