CN104593573B - 一种高效提升非调质钢强韧性的复合形变热处理强化方法 - Google Patents
一种高效提升非调质钢强韧性的复合形变热处理强化方法 Download PDFInfo
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- CN104593573B CN104593573B CN201510091645.5A CN201510091645A CN104593573B CN 104593573 B CN104593573 B CN 104593573B CN 201510091645 A CN201510091645 A CN 201510091645A CN 104593573 B CN104593573 B CN 104593573B
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- 229910052799 carbon Inorganic materials 0.000 description 6
- 238000009826 distribution Methods 0.000 description 3
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- 229910001563 bainite Inorganic materials 0.000 description 2
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- 230000032683 aging Effects 0.000 description 1
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- OKTJSMMVPCPJKN-UHFFFAOYSA-N carbon Chemical compound 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- 238000005496 tempering Methods 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N tin hydride Chemical compound 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[Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 238000002604 ultrasonography Methods 0.000 description 1
Abstract
本发明公开了一种高效提升非调质钢强韧性的复合形变热处理强化方法，首先将非调质钢棒材加热至1050～1200℃使其充分奥氏体化，然后进行第一次高温形变热处理，使奥氏体晶粒发生变形并细化、部分动态再结晶、固态相变及形变诱导弥散析出强化，再待高温形变处理后样品冷至动态再结晶温度以下30～50℃时再进行第二次温变形处理。该方法操作简单、易于实现、节能环保，可实现细晶强化、沉淀强化和形变强化的协同，显著改善非调质钢的力学性能，经检测，复合形变热处理强化后非调质钢的抗拉强度可达920～1050MPa，屈服强度为845～891MPa，伸长率为17％～21％，断面收缩率为45％～58％。
Description
技术领域
[0001] 本发明涉及一种材料处理方法，具体涉及一种高效提升非调质钢强韧性的复合形 变热处理强化方法;属于金属材料改性及塑性成形领域。
背景技术
[0002] 非调质钢作为一种节约资源能源的经济型材料，是在钢中加入微量元素 V、Ti、Nb 和N等，通过形变强化或控乳控冷工艺，使合金元素以C、N等化合物弥散析出，使其性能达到 或超过调质钢的强度韧性。相对调质处理结构钢而言，非调质钢结构件制造过程中省去了 淬火加高温回火工艺过程，有利于减少淬火变形、开裂、硬度分布不均，降低氧化和脱碳倾 向，具有材料利用率高、产品合格率高、制造流程短、能源资源消耗少等优点，在装备关键零 部件的制造领域具有广阔的应用前景。
[0003] 自1972年德国THYSEN公司开发第一种非调质锻钢49MnVS3(铁素体-珠光体，抗拉 强度850MPa)并取代调质CK45钢用于制造汽车曲轴以来，美国、日本等国家先后开发了铁素 体-珠光体型、低碳贝氏体型和低碳马氏体型多种非调质钢，并成功应用于汽车发动机曲 轴、连杆等零部件的生产制造。
[0004] 近年来，我国已开始逐步重视非调质钢的开发和应用研究：由公布号为CN 104264040A的专利文献可知，目前国内通过传统的热锻控冷工艺得到的非调质钢的抗拉强 度只能达到800MPa级，屈服强度仅为500MPa级。因此，如何保证非调质钢优异的强度和韧性 配合仍是决定非调质钢能否在机械装备领域规模应用的关键技术难题之一。
[0005] 目前，针对非调质钢的强韧性改善与提升，研究者们主要从材料成分设计、形变强 化技术和热处理控制技术等方面进行了深入的探索。其中，形变强化与热处理控制技术作 为提升非调质钢的一种有效的途径，已受到国内外的广泛关注。如日本新日铁公司开发了 氧化物冶金技术，通过控制先共析铁素体及MnS的析出，改善VN、TiN等强化相的数量及分 布，从而提高非调钢的强度和韧性;宝钢公司通过在非调钢中添加 B、V及微量的Mo等元素， 设计研制出12Mn2VB贝氏体型非调钢，具有优异的综合力学性能;王志明等研究发现锻造温 度及冷却方式对非调质钢38MnVS5的组织及力学性能影响显著（机械制造，2009,47(543): 43-45);赵秀明等研究发现锻后快冷结合缓冷技术可提高38MnVS非调质钢晶内铁素体的数 量及分布，在保证强度的同时仍具有良好的韧性（材料热处理学报，2013,34(11): 114-118);蔡璐等采用冷拔的方法研究了非调质钢螺栓的强化效应(材料工程，2010,4:69-71); Mao X Y等研究了时效强化对非调钢丝材冲击韧性具有显著的影响（Philosophical magazine letters,2014,94(3):135-140)〇
[0006] 迄今为止，尽管上述方法在非调质钢的力学性能提升方面均具有一定的效果，但 增幅不甚明显。其主要原因为：（1)仅施以高温锻压形变处理时，由于微量元素的不均匀扩 散和动态再结晶过程的发生，导致材料组织分布不均，形变强化效应难以恒久保留；（2)由 于材料高温形变与再结晶过程的影响，导致控制冷却时固态相变、晶粒细化和析出强化行 为更接近平衡状态，强化效果不明显；（3)冷变形处理时尽管形变强化效应能够较好的保 持，但常会随着形变抗力的逐步增加，在材料内部形成少许微裂纹等缺陷，生产质量控制难 度增大，材料强化效果降低。以上诸多因素表明，革新非调质钢的强韧化手段，对于其强度 和韧性的改善和提升仍有较大的空间。
发明内容
[0007] 为解决现有技术的不足，本发明的目的在于提供一种高效提升非调质钢强韧性的 复合形变热处理强化方法。
[0008] 为了实现上述目标，本发明采用如下的技术方案：
[0009] -种高效提升非调质钢强韧性的复合形变热处理强化方法，包括如下步骤：
[0010] S1、将非调质钢棒材加热至1050~1200°C，使其充分奥氏体化，保证V、Ti、Nb等微 量强化合金元素能够充分固溶并均匀分布于母相中，有效阻止奥氏体晶粒粗化，使其在冷 却的过程中获得细小的组织；
[0011] S2、将奥氏体化的棒材自奥氏体化温度开始第一次高温形变，快速冷却，使奥氏体 晶粒发生变形并细化、部分动态再结晶、固态相变及形变诱导第二相在初生相内部均匀弥 散析出；
[0012] S3、待高温形变样品冷至动态再结晶温度以下30~50°C时再进行第二次温变形， 控制冷却，抑制再结晶过程发生，并在材料内部产生大量的位错、亚结构等晶体缺陷和形变 诱导析出大量弥散分布的第二相。
[0013] 在完成对材料的复合形变热处理强化后，还可以包括如下检测步骤：
[0014] S4、采用磁粉和超声波复合探伤技术对复合形变强化处理的非调质钢样品进行微 裂纹等加工缺陷检测；根据国标GB/T 2975-1998和GB/T 228.1-2010取样并测试其室温拉 伸力学性能。
[0015] 优选地，前述步骤S1中，采用中频感应加热的方式，如中频感应炉对非调质钢棒材 进行加热，具有加热速度快、热量分布均匀、生产效率高、氧化损失少、表面质量好、无污染 等优点，此种加热方式能够进一步提尚广品的生广效率和材料利用率。同时，利用尚精度红 外测温仪进行温度测量，以检测材料的温度，选择合适的塑性变形时机。
[0016] 优选地，前述步骤S2和S3中，利用空冷或风冷的方式进行快速冷却，且冷却速度可 调节，无需其它特殊的冷却介质或装置，降低了生产成本和设备要求。
[0017] 优选地，前述步骤S2中，第一次高温形变时，形变终了温度在900~950 °C，形变量 为5~95%。
[0018] 更优选地，前述步骤S3中，第二次温变形时，形变起始温度控制在550~750°C，形 变量为5 %~40 %。
[0019] 具体地，前述步骤S2和S3中，形变方式为为拉拔、压缩、自由锻或模锻中的一种或 两种以上方式的结合。
[0020] 本发明的有益之处在于：本发明的热处理强化方法首先将非调质钢棒材加热至 1050~1200Γ使其充分奥氏体化，然后进行第一次高温形变，使奥氏体晶粒发生变形并细 化、部分动态再结晶、固态相变及形变诱导弥散析出强化;然后，待高温形变处理的样品冷 至动态再结晶温度以下30~50°C时再进行第二次温变形，以风冷或空冷的方式控制冷却， 抑制再结晶，产生大量的位错、亚结构和形变诱导析出第二相。该方法操作简单、易于实现、 节能环保，可实现细晶强化、沉淀强化和形变强化的协同，显著改善非调质钢的力学性能， 如强度和韧性，经检测，复合形变热处理强化后非调质钢的抗拉强度可达920~1050MPa，屈 服强度为845~891MPa，伸长率为17 %~21 %，断面收缩率为45 %~58 %。该方法可有效提 尚非调质钢广品的成材率和合格率，实现其尚性能、短流程、低成本尚效制造，广生良好的 经济和社会效益。
具体实施方式
[0021]以下结合具体实施例对本发明作具体的介绍。
[0022] 实施例1
[0023] 本实施例以热乳态的38MnVS圆形钢棒（试样标记为A0)为实施对象，钢棒直径为 80mm，处理步骤为：
[0024] S1、将钢棒锯成80mm厚的试样，置于中频感应炉中加热至1150~1200°C，使试样完 全奥氏体化，合金元素充分溶于奥氏体中；
[0025] S2、用红外测温仪检测温度，使试样在950~1150 °C范围内进行第一次高温形变， 锻压方式为自由锻，锻造形变量控制为20%，以风冷的方式进行控制冷却，V、Ti等合金元素 主要以C、N化合物的方式在晶界晶内弥散析出，抑制晶粒长大获得细小的组织结构；
[0026] S3、使用红外测温仪检测温度，当步骤S2中的第一次高温形变试样冷却至550~ 650°C范围内进行第二次温变形，形变量控制在10%，锻压方式为自由锻，锻压变形后采用 空冷的方式控制冷却，试样标记为A1。
[0027] 实施例2
[0028] 本实施例与实施例1步骤完全相同，区别之处在于第一次高温形变热处理的变形 量为25%，第二次温变形的起始温度为550~600°C，形变量为5%，试样标记为A2。
[0029] 实施例3
[0030]本实施例以热乳态的35MnVN圆形非调质钢(试样标记为B0)为实施对象，钢棒直径 为160mm，处理步骤为：
[0031] S1、将钢棒锯成80mm厚的试样，将其置于中频感应炉中加热至1050~1100 °C，使试 样完全奥氏体化，合金元素充分溶于奥氏体中；
[0032] S2、用红外测温仪检测温度，使试样在900~1100 °C范围内进行第一次高温形变， 锻压方式为模锻，锻压形变量控制为25%，以风冷的方式进行控制冷却，合金元素主要以C、 N化合物的方式在晶界析出，抑制晶粒长大获得细小的组织结构；
[0033] S3、使用红外测温仪检测温度，当步骤S2中的第一次高温形变试样冷却至550~ 600°C范围内进行第二次温形变，形变量控制在5%，锻造变形后采用空冷的方式进行控制 冷却，试样标记为B1。
[0034] 实施例4
[0035]本实施例以热乳态的12Mn2VB贝氏体型非调质钢(试样记为C0)为实施对象，钢棒 直径为100mm，锻造步骤为：
[0036] S1、将钢棒锯成80mm厚的试样，将其置于中频感应炉中加热至1150~1200°C，使试 样完全奥氏体化，Mn、V、Ti、B等合金元素充分溶于奥氏体中；
[0037] S2、用红外测温仪检测温度，使试样在950~1150 °C范围内进行第一次高温形变， 锻造方式为自由锻，锻造形变量控制为15%，以风冷的方式进行控制冷却，合金元素主要以 C、N化合物的方式在晶界析出，抑制晶粒长大，从而获得细小的组织结构；
[0038] S3、用红外测温仪检测温度，当步骤S2中的第一次高温形变试样冷却至650~750 °C范围内进行第二次温变形，形变量控制在15%，锻造方式为模锻，锻造变形后采用风冷的 方式进行控制冷却，试样标记为C1。
[0039] 性能测试
[0040] 根据国标GB/T 2975-1998和GB/T 228.1-2010取样测试其力学性能，测试结果如 表1所示。
[0043] 表1本发明方法制得试样与各热乳态试样的力学性能比较
[0044] 从表1中可以看出，试样经本发明的复合形变(第一次高温形变+第二次温变形)强 化方法处理后，其屈服强度提高43~64%左右，抗拉强度提高22~29 %，且仍保持了良好的 塑性，表明本发明的复合形变热处理强化方法能够明显提高非调质钢强韧性，扩大非调质 钢的应用领域，具有良好的推广应用前景。
[0045]以上显示和描述了本发明的基本原理、主要特征和优点。本行业的技术人员应该 了解，上述实施例不以任何形式限制本发明，凡采用等同替换或等效变换的方式所获得的 技术方案，均落在本发明的保护范围内。
Claims (4)
1. 一种高效提升非调质钢强韧性的复合形变热处理强化方法，其特征在于，包括如下 步骤： 51、 将非调质钢棒材加热至1050~1200°C，使其充分奥氏体化，保证V、Ti、Nb微量强化 合金元素能够充分固溶并均匀分布于母相中，有效阻止奥氏体晶粒粗化，在冷却的过程中 获得细小的组织； 52、 将奥氏体化的棒材自奥氏体化温度开始第一次高温形变热处理，然后快速冷却，使 奥氏体晶粒发生变形并细化、部分动态再结晶、固态相变及形变诱导第二相在初生相内部 均匀弥散析出；所述第一次高温形变时，形变终了温度在900~950°C，形变量为5~95% ; 53、 待高温形变热处理样品冷至动态再结晶温度以下30~50°C时再进行第二次温变形 处理，控制冷却，抑制再结晶过程发生，并在材料内部产生大量的位错、亚结构晶体缺陷和 形变诱导析出大量弥散分布的第二相;所述第二次温变形时，形变起始温度控制在550~ 750 °C，形变量为5 %~40 %。
2. 根据权利要求1所述的一种高效提升非调质钢强韧性的复合形变热处理强化方法， 其特征在于，所述步骤S1中，采用中频感应加热的方式对非调质钢棒材进行加热，并利用高 精度红外测温仪进行温度测量。
3. 根据权利要求1所述的一种高效提升非调质钢强韧性的复合形变热处理强化方法， 其特征在于，所述步骤S2和S3中，利用空冷或风冷的方式进行冷却，且冷却速度是能够调节 的。
4. 根据权利要求1~3任一项所述的一种高效提升非调质钢强韧性的复合形变热处理 强化方法，其特征在于，所述步骤S2和S3中，形变方式为拉拔、压缩、自由锻或模锻中的一种 或两种以上方式的结合。
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