CN105714190B - 一种耐冲击载荷轴承用钢及其热处理方法 - Google Patents
一种耐冲击载荷轴承用钢及其热处理方法 Download PDFInfo
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Abstract
一种耐冲击载荷轴承用钢,它的化学成分重量百分比为:C:0.18~0.30、Si:1.50~1.80、Mn:0.20~1.00、Cr:1.50~2.00、Ni:0.10~0.30、Al:0.05~0.80、Mo:0.20~0.40、W:0.20~0.50、N:0.0065~0.01,S:≦0.010、P:≦0.015、O:≦0.0008、Ti:≦0.003、H:≦0.00015,其制备方法主要是首先对渗碳钢进行表面渗碳处理,渗碳后表面碳含量0.80‑1.10wt.%,然后进行球化退火处理,再进行最终热处理:加热到840‑880℃保温1~3h,然后将其冷却至Ms表层‑(10~30)℃,保温2~5分钟,随后放到Ms表层+(10~30)℃炉中等温3~5h,继续升温至Ms表层+(50~70)℃保温1~2h,最后空冷至室温。本发明能够大幅度降低轴承钢中的Ni含量、节约能源、降低成本,还可以保证心部的高韧性。
Description
技术领域
本发明属于材料科学与工程领域,特别涉及一种轴承用钢及其制备方法。
背景技术
轴承是在机械设备中的关键基础零部件,其服役条件十分复杂,要求轴承不仅要具有优良耐磨性,同时还要具有高的抗滚动接触疲劳性能。而对于一些在服役过程中还受到较大载荷冲击的轴承,如轧机轴承、矿山机械轴承、风电轴承等,除要求轴承具有高耐磨性、抗接触疲劳性能外,还要求轴承内部具有高的韧性,可以抵抗冲击载荷。因此这类轴承通常选用渗碳轴承钢制造。
传统最常用的渗碳轴承钢为G20Cr2Ni4A钢,经过马氏体淬、回火处理后为马氏体轴承钢,具有高硬度、优异的耐磨性和滚动接触疲劳性能,因此在世界范围内获得最为广泛的应用。然而,G20Cr2Ni4A钢中Ni含量高达3.25~3.75wt%,轴承钢的原材料成本非常高,降低轴承钢的成本,一直是轴承行业的需求。因此,我国也开发了一些低Ni含量或无Ni的渗碳轴承钢,如G20CrMo,G20CrNiMo,G20CrNi2Mo,G10CrNi3Mo,G20Cr2Mn2Mo等钢种,这些渗碳轴承经最终热处理工艺处理后均为马氏体轴承。
近年来,新型渗碳轴承钢不断发展。专利ZL201110156392.7公开了一种化学成分为C:0.16~0.24、Si≦0.1、Mn≦0.1、Cr:0.3~1.5、Ni:1.50~4.50、Mo:0.3~1.5、Nb:0.02~0.10、V:0.3%~0.9,的轴承钢,最终的热处理工艺为油淬加低温回火处理。专利ZL201110156409.9公开了一种高速铁路用渗碳轴承钢及其制备方法,其所研发轴承钢的成分为C:0.18~0.24、Si≦0.1、Mn≦0.1、Cr:0.5~2.0、Ni:1.50~4.50、Mo:0.3~1.5、Nb:0.02~0.10、V:0.3%~0.9,热处理工艺为淬火+深冷处理+低温回火处理。公开号为CN102653843A的专利公开了一种渗碳轴承钢,其主要化学成分为C:0.10~0.16、Si:0.15~0.40、Mn:0.40~0.90、Cr:1.3~1.8、Ni:3.10~3.80、Mo:0.02~0.09、Al:0.015~0.04。专利CN104694847A公开了一种含Ni渗碳轴承钢,其最终热处理工艺为淬火温度800-900℃,回火温度150-170℃。这些渗碳轴承钢热处理后组织均为马氏体组织。同时为了保证马氏体轴承钢具有足够的韧性,在这些轴承钢组织中均加入了不少于1.5wt.%的Ni元素。
发明内容
本发明的目的在于提供一种能够大幅度降低Ni的含量、节约能源、降低成本的耐冲击载荷轴承用钢及其热处理方法。本发明主要通过在轴承钢原材料中加入Si合金元素抑制碳化物析出,加入Al合金元素,既保证形成足够的AlN细化晶粒,又起到加快贝氏体转变、抑制碳化物析出,减少了残余奥氏体的含量,同时保证轴承的表面硬度和心部的韧性。
本发明的技术方案如下:
一种耐冲击载荷轴承用钢,它是一种表面为以纳米尺寸为主的多尺度贝氏体、结合少量马氏体、少量残余奥氏体和保留的未溶碳化物组成的混合组织,心部为低碳马氏体与下贝氏体组成的混合组织的轴承用钢;它的化学成分质量百分比为C:0.18~0.30、Si:1.50~1.80、Mn:0.20~1.00、Cr:1.50~2.00、Ni:0.10~0.30、Al:0.05~0.80、Mo:0.20~0.40、W:0.20~0.50、N:0.0065~0.01,S:≦0.010、P:≦0.015、O:≦0.0008、Ti:≦0.003、H:≦0.00015,其余为Fe和正常杂质。
上述轴承钢的热处理方法:
(1)对上述成分的轴承用钢加工成轴承后,对其表面进行常规渗碳处理,渗碳后表面碳含量为0.80-1.10wt.%,有效渗碳硬化层深度1.0~8.0mm,硬度不低于HRC58渗碳层深度0.6~3.2mm,随后进行常规球化退火处理;
(2)对步骤(1)的轴承进行最终热处理,加热到840-880℃保温1~3h,然后将其冷却至Ms表层-(10~30)℃,保温时间2~5min,随后放到Ms表层+(10~30)℃等温3~5h,继续升温至Ms表层+(50~70)℃保温1~2h,最后空冷至室温。
本发明与现有技术相比具有如下优点:
(1)原材料中高的(Si+Al)含量可以有效地抑制贝氏体相变过程中碳化物析出,获得高强韧性的贝氏体组织,同时高的Si含量还可以提高材料的淬透性,使得该轴承钢适合于制造大壁厚轴承;
(2)原材料中加入合金元素Al元素加快贝氏体相变,同时通过三阶段等温处理,第一阶段的短时等温,缩短贝氏体转变孕育期,促进贝氏体形核,第三阶段的短时等温,加快剩余奥氏体向贝氏体转变,减少残余奥氏体含量,缩短转变时间。另外不需要最后进行回火处理,节省热处理成本。
(3)原材料中大幅度降低Ni的含量至≤0.3wt.%,降低成本,同时结合等温处理还可以进一步保证心部的高韧性。
附图说明
图1为本发明实施例1获得轴承钢表层的扫描电镜图。
图2为本发明实施例1获得轴承钢心部的金相图。
图3为本发明实施例2获得轴承钢表层的透射电镜图。
图4为本发明实施例3获得轴承钢心部的透射电镜图。
具体实施方式
实施例1
采用轴承用钢的化学成分(wt.%)为:C 0.18,Mn 0.35,Si 1.54,Cr 1.72,Mo0.38,W 0.21,Ni 0.12,Al 0.68,O 0.00075,P 0.011,S 0.005,H 0.00002、其余为Fe和正常杂质。对上述轴承钢进行渗碳处理,渗碳后轴承表面的碳含量为0.85wt.%,Ms表层为190℃,有效渗碳硬化层深度1.3mm,硬度不低于HRC58渗碳层深度0.6mm。将轴承钢进行球化退火处理后,加热至850℃保温2h,后放入175℃盐浴中进行等温,等温时间2分钟后,随后放入到205℃的盐浴中继续等温5h,最后转入250℃炉中等温1.5h后空冷。得到表层的组织如附图1所示,可见表层的碳化物尺寸细小,且分布均匀,贝氏体尺寸跨度较大;心部组织以低碳马氏体组织为主如附图2所示。处理后轴承表面硬度HRC58.5,表层的残余奥氏体含量8.5%,心部冲击韧性aku为115J/cm2,心部硬度为HRC38。
实施例2
采用轴承用钢的化学成分(wt.%)为:C 0.23,Mn 0.60,Si 1.60,Cr 1.59,Mo0.31,W 0.32,Ni 0.12,Al 0.08,O 0.00068,P 0.011,S 0.008,H 0.00005、其余为Fe和正常杂质。对上述轴承钢进行渗碳处理,渗碳后轴承表面的碳含量为0.96wt.%,Ms表层为193℃,有效渗碳硬化层深度4.1mm,硬度不低于HRC58渗碳层深度1.7mm。将轴承钢进行球化退火处理后,加热至840℃保温2.5h,放入180℃盐浴中进行等温,等温时间3分钟后,随后放入到215℃的盐浴中继续等温3h,最后转入245℃炉中等温2h后空冷。得到表层的组织如附图3所示,可以看到少量的孪晶马氏体组织,大部分贝氏体板条厚度小于100nm。处理后轴承表面硬度HRC60.5,表层的残余奥氏体含量9.3%,心部冲击韧性aku为125J/cm2,心部硬度为HRC40。
实施例3
采用轴承用钢的化学成分(wt.%)为:C 0.29,Mn 0.95,Si 1.66,Cr 1.43,Mo0.23,W 0.46,Ni 0.25,Al 0.40,O 0.00063,P 0.009,S 0.007,H 0.00003、其余为Fe和正常杂质。对上述轴承钢进行渗碳处理,渗碳后轴承表面的碳含量为1.08wt.%,Ms表层为180℃,有效渗碳硬化层深度7.5mm,硬度不低于HRC58渗碳层深度3.1mm。将轴承钢进行球化退火处理后,加热至870℃保温1h,放入170℃盐浴中进行等温,等温时间4分钟后,随后放入到210℃的盐浴中继续等温4h,最后转入250℃炉中等温1h后空冷。得到心部的组织为以低碳马氏体组织为主和少量贝氏体的混合组织,如附图4所示。处理后轴承表面硬度HRC61,表层的残余奥氏体含量7.8%,心部冲击韧性aku为139J/cm2,心部硬度为HRC41。
表1实施例与G20Cr2Ni4A钢力学性能对比
性能指标 | G20Cr2Ni4A | 实施例1 | 实施例2 | 实施例3 |
表面硬度HRC | 61 | 58.5 | 60.5 | 61 |
心部韧性J/cm2 | 113 | 115 | 125 | 139 |
心部硬度HRC | 45.5 | 38 | 40 | 41 |
对于渗碳轴承,要求经过热处理后表层的硬度不低于HRC58,心部硬度不低于HRC32。表1给出了本发明实施例与G20Cr2Ni4A钢的性能对比。可以看出,本发明实施例中的性能完全满足渗碳轴承的要求,同时心部在满足硬度的同时,冲击韧性比G20Cr2Ni4A钢还有进一步的提高,说明本发明轴承钢及其热处理方法适合于制造耐冲击载荷的轴承。
Claims (2)
1.一种耐冲击载荷轴承用钢,其特征在于:它是一种表面为以纳米尺寸为主的多尺度贝氏体、结合少量马氏体、少量残余奥氏体和保留的未溶碳化物组成的混合组织,心部为低碳马氏体与下贝氏体组成的混合组织的轴承用钢;它的化学成分质量百分比为:C 0.18~0.30、Si 1.50~1.80、Mn 0.20~1.00、Cr 1.50~2.00、Ni 0.10~0.30、Al 0.08~0.80、Mo0.20~0.40、W 0.20~0.50、N 0.0065~0.01,S≦0.010、P≦0.015、O≦0.0008、Ti≦0.003、H≦0.00015,其余为Fe和正常杂质。
2.权利要求1所述的耐冲击载荷轴承用钢的热处理方法,其特征在于:
(1)对上述成分的轴承用钢加工成轴承后,对其表面进行常规渗碳处理,渗碳后表面碳含量为0.80-1.10wt.%,有效渗碳硬化层深度1.0~8.0mm,硬度不低于HRC58渗碳层深度0.6~3.2mm,随后进行常规球化退火处理;
(2)对步骤(1)的轴承进行最终热处理,加热到840-880℃保温1~3h,然后将其冷却至Ms表层-(10~30)℃,保温时间2~5min,随后放到Ms表层+(10~30)℃炉中等温3~5h,继续升温至Ms表层+(50~70)℃保温1~2h,最后空冷至室温。
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