稀土<strong>Ce</strong>对薄带连铸无取向<strong>6.5%Si</strong>钢组织、高温拉伸性能和断裂模式的影响

doi:10.11900/0412.1961.2021.00115

金属学报

2022, Vol. 58

Issue (5): 637-648 DOI: 10.11900/0412.1961.2021.00115

研究论文

本期目录 | 过刊浏览

稀土Ce对薄带连铸无取向6.5%Si钢组织、高温拉伸性能和断裂模式的影响

李民¹^,², 李昊泽¹(

), 王继杰², 马颖澈¹, 刘奎¹

^1.中国科学院金属研究所师昌绪先进材料创新中心沈阳 110016
^2.沈阳航空航天大学材料科学与工程学院沈阳 110136

Effect of Ce on the Microstructure, High-Temperature Tensile Properties, and Fracture Mode of Strip Casting Non-Oriented 6.5%Si Electrical Steel

LI Min¹^,², LI Haoze¹(

), WANG Jijie², MA Yingche¹, LIU Kui¹

^1.Shi -changxu Innovation Center for Advanced Materials, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
^2.College of Materials Science and Engineering, Shenyang Areospace University, Shenyang 110136, China

引用本文:

李民, 李昊泽, 王继杰, 马颖澈, 刘奎. 稀土Ce对薄带连铸无取向6.5%Si钢组织、高温拉伸性能和断裂模式的影响[J]. 金属学报, 2022, 58(5): 637-648.
Min LI, Haoze LI, Jijie WANG, Yingche MA, Kui LIU. Effect of Ce on the Microstructure, High-Temperature Tensile Properties, and Fracture Mode of Strip Casting Non-Oriented 6.5%Si Electrical Steel[J]. Acta Metall Sin, 2022, 58(5): 637-648.

全文: PDF(5672 KB) HTML

摘要:

研究了Ce元素对薄带连铸无取向6.5%Si钢凝固组织、有序相、高温拉伸性能和断裂模式的影响。结果表明,添加Ce可以在薄带连铸过程中形成高熔点Ce₂O_2.5S和Ce₄O₄S₃,促进钢液异质形核,细化铸带凝固组织。Ce对有序相变无明显影响,铸带有序度由高至低所对应的拉伸温度分别为650、400和800℃。随拉伸温度提高,铸带的屈服强度与抗拉强度降低,断后延伸率提高。当拉伸温度高于500℃,Ce元素的钢液净化和凝固组织细化作用有助于提高晶界强度,避免沿晶断裂。铸带在拉伸过程中发生动态回复和再结晶,最终发生韧性断裂,断后延伸率得到显著提高。研究结果证实,稀土处理可以作为薄带连铸无取向6.5%Si钢增塑的一种有效途径。

关键词 ：无取向6.5%Si钢, 薄带连铸, 稀土, 塑性, 断口形貌

Abstract：

Non-oriented 6.5%Si electrical steel exhibits excellent high-frequency magnetic properties, such as low iron loss and near-zero magnetostriction. Moreover, the high Si content causes poor deformability due to the solution strengthening effect of Si and the resulting ordering transformations, delaying the commercial application. Strip casting is a near-net forming technology that directly produces thin strips from the melt and reduces the required rolling deformation for the fabrication of thin sheets. This technology could be a viable option for industrializing the production of non-oriented 6.5%Si electrical steel. Despite this, even in the strip casting process, this brittle material is prone to edge cracks. Thus, improving the intrinsic plasticity of strip casting non-oriented 6.5%Si electrical steel is necessary through chemical modification to eliminate the deforming defects. The effect of Ce on the ordered phase of the solidification microstructure, high-temperature tensile properties, and fracture mode of strip casting non-oriented 6.5%Si electrical steel was investigated in this work. The results showed that the addition of Ce introduced high-melting Ce₂O_2.5S and Ce₄O₄S₃ during strip casting, which promoted heterogeneous nucleation and refined the solidification microstructure of the as-cast strip. The presence of Ce did not affect the ordering condition of the as-cast strip. In decreasing order, the tensile temperatures corresponding to the ordered degree of the as-cast strip were 650, 400, and 800^oC. With the tensile temperature increasing, the yield and tensile strengths of the as-cast strip decreased, whereas the elongation gradually increased. When the tensile temperature exceeded 500^oC, the purification and microstructure refining effects of Ce improved grain-boundary cohesion and prevented intergranular cracking. Moreover, the occurrences of dynamic recovery and recrystallization eventually made the as-cast strip doped with Ce fractured by dimples, leading to a considerably enhanced tensile ductility. According to the findings, the rare-earth treatment should be considered as an effective method for increasing the ductility of strip casting non-oriented 6.5%Si electrical steel.

Key words： non-oriented 6.5%Si electrical steel strip casting rare earth ductility fracture morphology

收稿日期: 2021-03-23

ZTFLH:

TG11

基金资助:国家自然科学基金项目(51801221)

作者简介: 李民,男,1996年生,硕士生

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https://www.ams.org.cn/CN/10.11900/0412.1961.2021.00115 或 https://www.ams.org.cn/CN/Y2022/V58/I5/637

表1 无取向6.5%Si钢铸带的化学成分 (mass fraction / %)

图1 薄带连铸流程及其凝固过程示意图

图2 CS1和CS2铸带显微组织的OM像

图3 CS1和CS2铸带SEM像和EPMA元素分布图

表2 图3c中CS2铸带颗粒状第二相EPMA分析结果 (atomic fraction / %)

Case	[uvw]_s	[uvw]_n	d[uvw]_s / nm	d[uvw]_n / nm	d[uvw]_s·cosθ / nm	δ / %
$(0001) C e 2 O 2.5 S / / (111)$ _δ-_Fe	[ $2110$ ] $C e 2 O 2.5 S$	[ $1 ¯ 10$ ] _δ-_Fe	0.3967	0.4146	0.3967	3.9
	[ $10 1 ¯ 0$ ] $C e 2 O 2.5 S$	[ $2 ¯ 11$ ] _δ-_Fe	0.6871	0.7128	0.6871
	[ $1100$ ] $C e 2 O 2.5 S$	[ $1 ¯ 01$ ] _δ-_Fe	0.3967	0.4146	0.3967
$(010) C e 4 O 4 S 3 / / (111)$ _δ-_Fe	[ $001$ ] $C e 4 O 4 S 3$	[ $1 ¯ 10$ ] _δ-_Fe	0.3958	0.4146	0.3958	4.6
	[ $1 ¯ 02$ ] $C e 4 O 4 S 3$	[ $3 ¯ 12$ ] _δ-_Fe	1.0457	1.0970	1.0457
	[ $100$ ] $C e 4 O 4 S 3$	[ $1 ¯ 1 ¯ 2$ ] _δ-_Fe	0.6851	0.7182	0.6851

表3 晶格错配度计算结果

图4 CS1和CS2铸带300~900℃的工程应力-应变曲线

图5 CS1和CS2铸带的高温拉伸性能对比

图6 CS1和CS2铸带的TEM暗场像及对应的[001]晶带轴选区电子衍射(SAED)花样

图7 CS1和CS2铸带300和400℃拉伸断口形貌的SEM像

图8 CS1和CS2铸带300和400℃拉伸断口纵剖面的OM像

图9 CS1和CS2铸带500和650℃拉伸断口形貌的SEM像

图10 CS1和CS2铸带500和650℃拉伸断口纵剖面的OM像

图11 CS1和CS2铸带700、800和900℃拉伸断口形貌的SEM像

图12 CS1和CS2铸带700、800和900℃拉伸断口纵剖面的OM像

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