1.钢铁研究总院有限公司先进特殊钢全国重点实验室,北京 100081
2.北京科技大学钢铁共性技术协同创新 中心,北京 100083
3.江苏申源集团有限公司,泰州 225722
4.东北特殊钢集团股份有限公司,大连 116000
邸英南(1996—),男,博士,工程师; E-mail:diyingnan0615@163.com
收稿:2026-06-23,
修回:2026-07-06,
录用:2026-07-07,
纸质出版:2026-09-30
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邸英南,付博,刘亚鹏等.新能源汽车一体化压铸用模具钢GY-DCK20组织及性能[J].特殊钢,2026,47(05):25-32.
Di Yingnan,Fu Bo,Liu Yapeng,et al.Microstructure and Properties of Die Steel GY-DCK20 for Integrated Die Casting of New Energy Vehicles[J].Special Steel,2026,47(05):25-32.
邸英南,付博,刘亚鹏等.新能源汽车一体化压铸用模具钢GY-DCK20组织及性能[J].特殊钢,2026,47(05):25-32. DOI:10.20057/j.1003-8620.N260095.
Di Yingnan,Fu Bo,Liu Yapeng,et al.Microstructure and Properties of Die Steel GY-DCK20 for Integrated Die Casting of New Energy Vehicles[J].Special Steel,2026,47(05):25-32. DOI:10.20057/j.1003-8620.N260095.
在新能源汽车一体化压铸成型技术背景下,开发并生产了一种特大型高均匀、高韧性、高等向压铸模具钢GY-DCK20,结合金相分析、SEM分析、ASPEX夹杂物分析等表征方法,开展了不同位置取样组织均匀性及室温力学性能研究,结果表明,采用{电弧炉(EAF)+氩氧精炼炉(AOD)}→真空精炼(RH)→连铸→保护气氛电渣重熔(PESR)的高纯净冶炼工艺,可有效控制有害元素及气体含量,尺寸为2~5 μm的细小夹杂物占比可达到73.4%以上,夹杂物类型主要为氧化物。不同位置取样未见明显带状偏析,球化组织良好,碳化物细小且弥散分布。1 030 ℃对比1 010 ℃淬火后的热处理硬度高出1HRC左右,且具备更好的冲击性能。回火阶段二次硬化峰在540 ℃附近,主要原因为细小颗粒状合金碳化物析出;650 ℃回火马氏体开始发生回复和再结晶,形成等轴状铁素体晶粒;700 ℃回火马氏体板条结构消失,碳化物沿晶聚集,再结晶晶粒严重粗化。GY-DCK20钢在44~46HRC的使用硬度下,不同位置横、纵V型缺口冲击吸收功均在35 J以上,心部等向性可达0.97,具备优异的综合力学性能。
In the context of integrated die-casting forming technology for new energy vehicles, a new type of extra-large, highly uniform, high-toughness, and high- isotropy die-casting mold steel GY-DCK20 was developed and produced. The microstructural uniformity of samples taken from different locations and their room-temperature mechanical properties were investigated by characterization methods such as metallographic analysis, SEM analysis, and ASPEX inclusion analysis. The results indicate that the high-cleanliness smelting process (EAF +AOD) → RH → Continuous Casting → PESR effectively controls the content of harmful and gaseous elements. Fine inclusions measuring 2-5 μm account for over 73.4% of the total, with oxides being the primary type. No significant banding segregation was observed in samples taken from different locations; the spheroidized microstructure was well-developed, and carbides were fine and uniformly distributed. The heat-treated hardness after quenching at 1 030 ℃ was approximately 1HRC higher than that at 1 010 ℃, and the steel exhibited better impact performance. During the tempering stage, the secondary hardening peak occurred near 540 °C, primarily due to the precipitation of fine, granular alloy carbides; at 650 ℃, martensite began to undergo recovery and recrystallization, forming equiaxed ferrite grains; at 700 ℃, the lath structure of the martensite disappeared, carbides aggregated along the grain boundaries, and recrystallized grains coarsened significantly. At a service hardness of 44-46HRC, the test steel exhibits a transverse and longitudinal V-notch impact absorbed energy of over 35 J at various locations, with an isotropy ratio of up to 0.97 in the core, demonstrating excellent comprehensive mechanical properties.
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