CN102560023A - Thermal treatment method for low-carbon chrome-silicon manganese low alloy steel - Google Patents
Thermal treatment method for low-carbon chrome-silicon manganese low alloy steel Download PDFInfo
- Publication number
- CN102560023A CN102560023A CN2012100515901A CN201210051590A CN102560023A CN 102560023 A CN102560023 A CN 102560023A CN 2012100515901 A CN2012100515901 A CN 2012100515901A CN 201210051590 A CN201210051590 A CN 201210051590A CN 102560023 A CN102560023 A CN 102560023A
- Authority
- CN
- China
- Prior art keywords
- low
- silicon
- alloy steel
- carbon chromium
- manganese
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Images
Landscapes
- Heat Treatment Of Articles (AREA)
Abstract
低碳铬硅锰低合金钢的热处理方法，低碳铬硅锰低合金钢的高强韧淬火-配分热处理方法。是要解决现有传统的热处理工艺处理得到低碳铬硅锰低合金钢不能兼顾高强度与良好塑韧性的要求的问题。方法：将低碳铬硅锰低合金钢奥氏体化处理后，然后在低碳铬硅锰低合金钢的上马氏体点Ms以下170-10℃的温度下进行等温淬火或者不完全淬火，保温6s～5400s，再淬火至室温，即完成。经本发明的低碳铬硅锰低合金钢的高强韧淬火-配分热处理方法处理后的低碳铬硅锰低合金钢的拉伸强度达1665MPa～2085MPa，塑性为9％～15％。在保证该系列钢种保持高强度的同时兼具一定的塑性，且综合力学性能比传统热处理工艺显著提高。
Heat treatment method for low-carbon chromium-silicon-manganese low-alloy steel, high-strength quenching-partition heat treatment method for low-carbon chromium-silicon-manganese low-alloy steel. It is to solve the problem that the low-carbon chromium-silicon-manganese low-alloy steel obtained by the existing traditional heat treatment process cannot meet the requirements of high strength and good plasticity and toughness. Method: After austenitizing the low-carbon chromium-silicon-manganese low-alloy steel, austempering or incomplete quenching is carried out at a temperature of 170-10°C below the upper martensitic point M s of the low-carbon chromium-silicon-manganese low-alloy steel , keep warm for 6s ~ 5400s, and then quench to room temperature, that is to say, it is completed. The tensile strength of the low-carbon chromium-silicon-manganese low-alloy steel treated by the high-strength and toughness quenching-partition heat treatment method of the present invention reaches 1665MPa-2085MPa, and the plasticity is 9%-15%. While ensuring the high strength of this series of steels, it also has a certain degree of plasticity, and its comprehensive mechanical properties are significantly improved compared with traditional heat treatment processes.
Description
技术领域 technical field
本发明涉及低碳铬硅锰低合金钢的高强韧淬火-配分热处理方法。The invention relates to a high-strength and toughness quenching-partitioning heat treatment method for low-carbon chromium-silicon-manganese low-alloy steel.
背景技术 Background technique
低碳铬硅锰低合金钢主要应用于航空飞机轴、梁和起落架等以及航天火箭、原子能工业等关键承力构件，是最早商品化的一类低合金超高强度钢。低合金超高强度钢是在调质结构钢的基础上发展起来的，通过添加少量的合金元素，达到固溶强化并提高钢的淬透性和马氏体回火稳定性的目的。这类钢的合金元素总含量一般不高于5％，碳含量在0.25-0.50％之间，热处理工艺一般为淬火后再进行回火处理。但是传统的热处理工艺不能兼顾高强度与良好塑韧性的要求：若降低回火温度保持其抗拉强度1500-1600MPa左右，则塑性较低(延伸率仅3％-6％左右)、裂纹敏感性很高易发生低应力脆断；若提高回火温度可改善塑性(延伸率＞10％)，但强度大幅下降至1000-1100MPa。为此，需要开发简便易行的不完全淬火-等温配分热处理新工艺，在保证适当塑性的前提下大幅提高该系列钢的拉伸强度，或者在保证高强度的同时显著改善塑性和韧性，从而实现高强度、高塑韧性的不同配合，同时改善该系列钢的氢脆敏感性和应力腐蚀抗力，适应海洋性气候等恶劣环境日益增长的高强度重要构件的性能需求。Low-carbon chromium-silicon-manganese low-alloy steels are mainly used in key load-bearing components such as aviation aircraft shafts, beams, and landing gears, as well as space rockets and atomic energy industries. They are the earliest commercialized low-alloy ultra-high-strength steels. Low-alloy ultra-high-strength steel is developed on the basis of quenched and tempered structural steel. By adding a small amount of alloying elements, it achieves solid solution strengthening and improves the hardenability and martensitic tempering stability of the steel. The total content of alloy elements in this type of steel is generally not higher than 5%, and the carbon content is between 0.25-0.50%. The heat treatment process is generally quenched and then tempered. However, the traditional heat treatment process cannot take into account the requirements of high strength and good plasticity and toughness: if the tempering temperature is lowered to maintain its tensile strength of about 1500-1600MPa, the plasticity is low (elongation is only about 3%-6%), crack sensitivity It is very prone to low stress brittle fracture; if the tempering temperature is increased, the plasticity can be improved (elongation > 10%), but the strength is greatly reduced to 1000-1100MPa. To this end, it is necessary to develop a new process of incomplete quenching-isothermal partition heat treatment that is simple and easy to greatly increase the tensile strength of this series of steels under the premise of ensuring proper plasticity, or significantly improve plasticity and toughness while ensuring high strength, so that Realize the different combinations of high strength, high plasticity and toughness, improve the hydrogen embrittlement sensitivity and stress corrosion resistance of this series of steels at the same time, and adapt to the increasing performance requirements of high-strength important components in harsh environments such as marine climates.
发明内容 Contents of the invention
本发明是要解决现有传统的热处理工艺处理得到低碳铬硅锰低合金钢不能兼顾高强度与良好塑韧性的要求的问题，提供了低碳铬硅锰低合金钢的热处理方法，处理得到同时具备良好强度和较好的塑性的低碳铬硅锰低合金钢，达到较好的综合力学性能。The present invention aims to solve the problem that the low-carbon chromium-silicon-manganese low-alloy steel obtained by the existing traditional heat treatment process cannot meet the requirements of high strength and good plastic toughness, and provides a heat treatment method for the low-carbon chromium-silicon-manganese low-alloy steel, which can be processed to obtain Low-carbon chromium-silicon-manganese low-alloy steel with good strength and good plasticity at the same time, achieving better comprehensive mechanical properties.
本发明的第一种低碳铬硅锰低合金钢的热处理方法是通过以下步骤实现的：将低碳铬硅锰低合金钢奥氏体化处理后，然后在低碳铬硅锰低合金钢的上马氏体点Ms以下170-10℃的温度下进行等温淬火或者不完全淬火，保温6s～5400s，再淬火至室温，即完成低碳铬硅锰低合金钢的热处理方法。The heat treatment method of the first low-carbon chromium-silicon-manganese low-alloy steel of the present invention is realized through the following steps: after the low-carbon chromium-silicon-manganese low-alloy steel is austenitized, then the low-carbon chromium-silicon-manganese low-alloy steel Austempering or incomplete quenching at a temperature of 170-10°C below the upper martensitic point M s , holding for 6s to 5400s, and then quenching to room temperature completes the heat treatment method for low-carbon chromium-silicon-manganese low-alloy steel.
本发明的第二种低碳铬硅锰低合金钢的热处理方法是通过以下步骤实现的：一、将低碳铬硅锰低合金钢奥氏体化处理后，然后在低碳铬硅锰低合金钢的上马氏体点Ms以下170-10℃的温度下进行等温淬火或者不完全淬火，保温6s～5400s；二、将经步骤一处理后的低碳铬硅锰低合金钢在Ms+100℃至Ms-100℃的温度区间内，等温配分热处理6s～5400s，然后再淬火至室温，即完成低碳铬硅锰低合金钢的热处理方法。The heat treatment method of the second low-carbon chromium-silicon-manganese low-alloy steel of the present invention is realized through the following steps: 1. After austenitizing the low-carbon chromium-silicon-manganese low-alloy steel, Austempering or incomplete quenching at a temperature of 170-10°C below the upper martensitic point M s of the alloy steel, and heat preservation for 6s to 5400s; 2. The low-carbon chromium-silicon-manganese low-alloy steel treated in
本发明所述的低碳铬硅锰低合金钢包括但并不仅限于30CrMnSi、30CrMnSiNi2、30CrMnSiNi2A钢和其他低碳SiMn钢。The low-carbon chromium-silicon-manganese low-alloy steel described in the present invention includes but is not limited to 30CrMnSi, 30CrMnSiNi2, 30CrMnSiNi2A steel and other low-carbon SiMn steels.
本发明的低碳铬硅锰低合金钢奥氏体化处理中的奥氏体化温度为低碳铬硅锰低合金钢的AC3以上30℃～50℃，保温时间为10s～1800s，其中AC3为加热时铁素体全部转变为奥氏体终了温度。The austenitizing temperature of the low-carbon chromium-silicon-manganese low-alloy steel in the austenitization treatment of the present invention is 30°C to 50°C above A C3 of the low-carbon chromium-silicon-manganese low-alloy steel, and the holding time is 10s to 1800s, wherein A C3 is the temperature at which all ferrite transforms into austenite when heated.
本发明的低碳铬硅锰低合金钢的上马氏体点Ms，针对某一特定的低碳铬硅锰低合金钢的上马氏体点Ms，是固定值的，且本领域技术人员根据公知常识很简单的就能够获得某低碳铬硅锰低合金钢的上马氏体点Ms。The upper martensitic point M s of the low-carbon chromium-silicon-manganese low-alloy steel of the present invention is a fixed value for the upper martensitic point M s of a specific low-carbon chromium-silicon-manganese low-alloy steel, and those skilled in the art According to common knowledge, the upper martensitic point M s of a certain low-carbon chromium-silicon-manganese low-alloy steel can be easily obtained.
本发明针对商品化低碳铬锰硅系低合金钢提出的淬火-配分(Quenching andPartitioning，简称Q&P)工艺与传统淬火回火工艺不同，本发明的淬火-配分热处理工艺将低碳铬锰硅低合金钢奥氏体化后，先在低碳铬硅锰低合金钢的马氏体转变温度区间内进行等温淬火或者不完全淬火得到部分马氏体和未转变奥氏体，然后在(Ms+100℃，Ms-100℃)的温度区间内保温，使碳从先形成马氏体向未转变奥氏体中扩散并使之稳定化，最后淬火到室温，得到由低碳马氏体和富碳奥氏体组成的复相组织。相对于传统淬火回火工艺，本发明的淬火-配分热处理工艺能使马氏体钢在保持强度水平的前提下明显改善塑韧性。The quenching and partitioning (Quenching and Partitioning, Q&P) process proposed by the present invention for commercialized low-carbon chromium-manganese-silicon low-alloy steel is different from the traditional quenching and tempering process. After the alloy steel is austenitized, austempering or incomplete quenching is carried out in the martensitic transformation temperature range of the low-carbon chromium-silicon-manganese low-alloy steel to obtain partial martensite and untransformed austenite, and then in (M s +100°C, M s -100°C) to keep warm in the temperature range, so that carbon diffuses from the first formed martensite to the untransformed austenite and stabilizes it, and finally quenched to room temperature to obtain low carbon martensite and carbon-rich austenite. Compared with the traditional quenching and tempering process, the quenching-partitioning heat treatment process of the present invention can significantly improve the plasticity and toughness of the martensitic steel under the premise of maintaining the strength level.
经本发明的低碳铬硅锰低合金钢的高强韧淬火-配分热处理方法处理后的低碳铬硅锰低合金钢的拉伸强度达1665MPa～2085MPa，塑性为9％～15％。在保证该系列钢种保持高强度的同时兼具一定的塑性，且综合力学性能比传统热处理工艺(淬火回火工艺)显著提高，同时根据该系列钢种不同的含碳量和目标性能设计和优化的第一种热处理方法或者第二种热处理方法，获得不同的高强度、高塑韧性和优良的应力腐蚀抗力的配合，满足不同的性能需求。The tensile strength of the low-carbon chromium-silicon-manganese low-alloy steel treated by the high-strength and toughness quenching-partition heat treatment method of the present invention reaches 1665MPa-2085MPa, and the plasticity is 9%-15%. While ensuring the high strength of this series of steels, it has a certain degree of plasticity, and the comprehensive mechanical properties are significantly improved compared with the traditional heat treatment process (quenching and tempering process). At the same time, according to the different carbon content and target performance of this series of steels The first heat treatment method or the second heat treatment method is optimized to obtain different combinations of high strength, high plastic toughness and excellent stress corrosion resistance to meet different performance requirements.
附图说明 Description of drawings
图1为具体实施方式四的热处理方法的工艺示意图；图2为具体实施方式四中处理后的30CrMnSi钢的透射电镜明场像图片；图3为具体实施方式四中处理后的30CrMnSi钢的透射电镜暗场像图片；图4为具体实施方式四中处理后的30CrMnSi钢的衍射斑点图；图5为具体实施方式九的热处理方法的工艺示意图。Fig. 1 is the technological schematic diagram of the heat treatment method of specific embodiment four; Fig. 2 is the transmission electron microscope bright field image picture of the 30CrMnSi steel after processing in specific embodiment four; Fig. 3 is the transmission electron microscope image picture of the 30CrMnSi steel after processing in specific embodiment four Electron microscope dark field images; FIG. 4 is a diffraction spot diagram of 30CrMnSi steel treated in Embodiment 4; FIG. 5 is a process schematic diagram of the heat treatment method in Embodiment 9.
具体实施方式 Detailed ways
本发明技术方案不局限于以下所列举具体实施方式，还包括各具体实施方式间的任意组合。The technical solution of the present invention is not limited to the specific embodiments listed below, but also includes any combination of the specific embodiments.
具体实施方式一：本实施方式第一种低碳铬硅锰低合金钢的热处理方法是通过以下步骤实现的：将低碳铬硅锰低合金钢奥氏体化处理后，然后在低碳铬硅锰低合金钢的上马氏体点Ms以下170-10℃的温度下进行等温淬火或者不完全淬火，保温6s～5400s，再淬火至室温，即完成低碳铬硅锰低合金钢的热处理方法。Specific embodiment one: the heat treatment method of the first low-carbon chromium-silicon-manganese low-alloy steel in this embodiment is realized through the following steps: After the low-carbon chromium-silicon-manganese low-alloy steel is austenitized, then the low-carbon chromium Austempering or incomplete quenching at a temperature of 170-10°C below the upper martensitic point M s of silicon-manganese low-alloy steel, heat preservation for 6s-5400s, and then quenching to room temperature, that is, the heat treatment of low-carbon chromium-silicon-manganese low-alloy steel is completed method.
本实施方式的低碳铬硅锰低合金钢的上马氏体点Ms，针对某一特定的低碳铬硅锰低合金钢的上马氏体点Ms，是固定值的，且本领域技术人员根据公知常识很简单的就能够获得某低碳铬硅锰低合金钢的上马氏体点Ms。The upper martensitic point M s of the low-carbon chromium-silicon-manganese low-alloy steel in this embodiment is a fixed value for the upper martensitic point M s of a specific low-carbon chromium-silicon-manganese low-alloy steel, and the technology in the art Personnel can easily obtain the upper martensitic point M s of a certain low-carbon chromium-silicon-manganese low-alloy steel based on common knowledge.
本实施方式适用于30CrMnSi系列低碳铬锰硅系低合金超高强度钢的热处理。使用的钢种成分如下：This embodiment is suitable for heat treatment of 30CrMnSi series low-carbon chromium-manganese-silicon-based low-alloy ultra-high-strength steel. The steel composition used is as follows:
本实施方式的热处理工艺适用于30CrMnSi系列低碳铬锰硅系低合金超高强度钢的热处理。其中凡是满足下述表1中所列的成分的钢种均适用于本实施方式的热处理工艺：The heat treatment process of this embodiment is applicable to the heat treatment of 30CrMnSi series low-carbon chromium-manganese-silicon-based low-alloy ultra-high-strength steel. Wherein, all steel types that satisfy the composition listed in the following Table 1 are applicable to the heat treatment process of this embodiment:
表1具体实施方式一中热处理方法适用钢种的成分(Wt.％)The composition (Wt.%) of heat treatment method applicable steel type in table 1 specific embodiment one
具体实施方式二：本实施方式与具体实施方式一不同的是：所述的低碳铬硅锰低合金钢为30CrMnSi钢、30CrMnSiNi2钢或者30CrMnSiNi2A钢。其它与具体实施方式一相同。Embodiment 2: This embodiment differs from
本实施方式中所述的低碳铬硅锰低合金钢包括但并不仅限于30CrMnSi钢、30CrMnSiNi2钢和30CrMnSiNi2A钢，还包括其他低碳SiMn钢。The low-carbon chromium-silicon-manganese low-alloy steel described in this embodiment includes but is not limited to 30CrMnSi steel, 30CrMnSiNi2 steel and 30CrMnSiNi2A steel, and also includes other low-carbon SiMn steels.
具体实施方式三：本实施方式与具体实施方式一不同的是：所述低碳铬硅锰低合金钢奥氏体化处理中的奥氏体化温度为低碳铬硅锰低合金钢的AC3以上30℃～50℃，保温时间为10s～1800s，其中AC3为加热时铁素体全部转变为奥氏体终了温度。其它与具体实施方式一相同。Specific embodiment three: The difference between this embodiment and specific embodiment one is: the austenitizing temperature in the austenitizing treatment of the low-carbon chromium-silicon-manganese low-alloy steel is A of the low-carbon chromium-silicon-manganese low-alloy steel The temperature above C3 is 30°C-50°C, and the holding time is 10s-1800s, where A C3 is the final temperature at which all ferrite transforms into austenite when heated. Others are the same as in the first embodiment.
具体实施方式四：本实施方式30CrMnSi钢的热处理方法是通过以下步骤实现的：将30CrMnSi钢在810℃～890℃下保温600s完成奥氏体化处理后，然后在170～320℃的温度下进行等温淬火或者不完全淬火，保温30s～600s，再淬火至室温，即完成30CrMnSi钢的热处理方法。Specific Embodiment 4: The heat treatment method of 30CrMnSi steel in this embodiment is realized through the following steps: After the 30CrMnSi steel is kept at 810°C-890°C for 600s to complete the austenitization treatment, then it is carried out at a temperature of 170-320°C Austempering or incomplete quenching, heat preservation for 30s ~ 600s, and then quenching to room temperature, the heat treatment method of 30CrMnSi steel is completed.
本实施方式的热处理方法的工艺示意图如图1所示，图中AT表示奥氏体化温度，QT表示淬火温度，PT表示配分温度。The process schematic diagram of the heat treatment method of this embodiment is shown in Figure 1, in which AT represents the austenitizing temperature, QT represents the quenching temperature, and PT represents the partition temperature.
经本实施方式的热处理工艺处理后的30CrMnSi钢的抗拉强度达到1740MPa～2085MPa，塑性达到10.5％～15％，断面收缩率达21.5％～35％。在保证30CrMnSi钢的强度的同时，获得了很好的塑性，实现了30CrMnSi钢的强塑性配合。The tensile strength of the 30CrMnSi steel treated by the heat treatment process of this embodiment reaches 1740MPa-2085MPa, the plasticity reaches 10.5%-15%, and the reduction of area reaches 21.5%-35%. While ensuring the strength of 30CrMnSi steel, it obtains good plasticity and realizes the strong-plastic fit of 30CrMnSi steel.
通过下述试验验证本实施方式的30CrMnSi钢的热处理方法的有益效果：The beneficial effect of the heat treatment method of the 30CrMnSi steel of the present embodiment is verified by following tests:
试验1：30CrMnSi钢的热处理方法是通过以下步骤实现的：将30CrMnSi钢在850℃下保温600s完成奥氏体化处理后，然后在250℃的温度下进行等温淬火，保温300s，再淬火至室温，即完成30CrMnSi钢的热处理方法。处理后的30CrMnSi钢的抗拉强度为2085MPa，并且塑性达到10.5％，断面收缩率为21.5％，获得较高的抗拉强度和一定的塑性。具有很好的强塑性配合。Test 1: The heat treatment method of 30CrMnSi steel is realized through the following steps: After the 30CrMnSi steel is held at 850°C for 600s to complete the austenitization treatment, it is then austenitized at 250°C, held for 300s, and then quenched to room temperature , That is to complete the heat treatment method of 30CrMnSi steel. The treated 30CrMnSi steel has a tensile strength of 2085MPa, a plasticity of 10.5%, a reduction of area of 21.5%, and a higher tensile strength and certain plasticity. Has a very good strong plastic fit.
试验2：30CrMnSi钢的热处理方法是通过以下步骤实现的：将30CrMnSi钢在850℃下保温600s完成奥氏体化处理后，然后在220℃的温度下进行等温淬火，保温300s，再淬火至室温，即完成30CrMnSi钢的热处理方法。处理后的30CrMnSi钢的抗拉强度为1740MPa，并且塑性达到15％，断面收缩率为35％，获得较高的抗拉强度和一定的塑性。具有很好的强塑性配合。Test 2: The heat treatment method of 30CrMnSi steel is realized through the following steps: After the 30CrMnSi steel is held at 850°C for 600s to complete the austenitization treatment, it is then austenitized at 220°C, held for 300s, and then quenched to room temperature , That is to complete the heat treatment method of 30CrMnSi steel. The tensile strength of the treated 30CrMnSi steel is 1740MPa, and the plasticity reaches 15%, and the reduction of area is 35%, so that higher tensile strength and certain plasticity are obtained. Has a very good strong plastic fit.
本试验处理后是30CrMnSi钢的透射电镜明场像图片如图2所示，可以观察到马氏体板条和介于板条之间的残余奥氏体；透射电镜暗场像图片如图3所示；衍射斑点图如图4所示。The TEM bright-field image of 30CrMnSi steel after treatment in this test is shown in Figure 2, and martensite laths and retained austenite between the laths can be observed; the TEM dark-field image is shown in Figure 3 Shown; Diffraction spot diagram is shown in Fig. 4.
具体实施方式五：本实施方式30CrMnSiNi2钢或者30CrMnSiNi2A钢的热处理方法是通过以下步骤实现的：将30CrMnSiNi2钢或者30CrMnSiNi2A钢在AC3以上30℃～50℃下保温10s～3600s完成奥氏体化处理后，然后在马氏体转变起始点Ms以下170～10℃的温度下进行等温淬火或者不完全淬火，保温6s～5400s，再淬火至室温，即完成30CrMnSiNi2钢或者30CrMnSiNi2A钢的热处理方法。Specific embodiment five: The heat treatment method of 30CrMnSiNi2 steel or 30CrMnSiNi2A steel in this embodiment is realized through the following steps: After the austenitization treatment is completed, the 30CrMnSiNi2 steel or 30CrMnSiNi2A steel is kept at 30°C-50°C above A C3 for 10s-3600s , and then carry out austempering or incomplete quenching at a temperature of 170-10°C below the starting point of martensitic transformation M s , keep warm for 6s-5400s, and then quench to room temperature, that is, complete the heat treatment method of 30CrMnSiNi2 steel or 30CrMnSiNi2A steel.
具体实施方式六：本实施方式第二种低碳铬硅锰低合金钢的热处理方法是通过以下步骤实现的：一、将低碳铬硅锰低合金钢奥氏体化处理后，然后在低碳铬硅锰低合金钢的上马氏体点Ms以下170-10℃的温度下进行等温淬火或者不完全淬火，保温6s～5400s；二、将经步骤一处理后的低碳铬硅锰低合金钢在Ms+100℃至Ms-100℃的温度区间内，等温配分热处理6s～5400s，然后再淬火至室温，即完成低碳铬硅锰低合金钢的热处理方法。Specific embodiment six: the heat treatment method of the second low-carbon chromium-silicon-manganese low-alloy steel in this embodiment is realized through the following steps: 1. After austenitizing the low-carbon chromium-silicon-manganese low-alloy steel, and then Carry out austempering or incomplete quenching at a temperature of 170-10°C below the upper martensitic point M s of carbon-chromium-silicon-manganese low-alloy steel, and keep warm for 6s to 5400s; The alloy steel is subjected to an isothermal partition heat treatment for 6s to 5400s in the temperature range from M s +100°C to M s -100°C, and then quenched to room temperature to complete the heat treatment method for low-carbon chromium-silicon-manganese low-alloy steel.
本实施方式的低碳铬硅锰低合金钢的上马氏体点Ms，针对某一特定的低碳铬硅锰低合金钢的上马氏体点Ms，是固定值的，且本领域技术人员根据公知常识很简单的就能够获得某低碳铬硅锰低合金钢的上马氏体点Ms。The upper martensitic point M s of the low-carbon chromium-silicon-manganese low-alloy steel in this embodiment is a fixed value for the upper martensitic point M s of a specific low-carbon chromium-silicon-manganese low-alloy steel, and the technology in the art Personnel can easily obtain the upper martensitic point M s of a certain low-carbon chromium-silicon-manganese low-alloy steel based on common knowledge.
具体实施方式七：本实施方式与具体实施方式六不同的是：所述的低碳铬硅锰低合金钢为30CrMnSi钢、30CrMnSiNi2钢或者30CrMnSiNi2A钢。其它与具体实施方式六相同。Embodiment 7: This embodiment differs from Embodiment 6 in that the low-carbon chromium-silicon-manganese low-alloy steel is 30CrMnSi steel, 30CrMnSiNi2 steel or 30CrMnSiNi2A steel. Others are the same as in the sixth embodiment.
本实施方式中所述的低碳铬硅锰低合金钢包括但并不仅限于30CrMnSi钢、30CrMnSiNi2钢和30CrMnSiNi2A钢，还包括其他低碳SiMn钢。The low-carbon chromium-silicon-manganese low-alloy steel described in this embodiment includes but is not limited to 30CrMnSi steel, 30CrMnSiNi2 steel and 30CrMnSiNi2A steel, and also includes other low-carbon SiMn steels.
具体实施方式八：本实施方式与具体实施方式六不同的是：所述低碳铬硅锰低合金钢奥氏体化处理中的奥氏体化温度为低碳铬硅锰低合金钢的AC3以上30℃～50℃，保温时间为10s～1800s，其中AC3为加热时铁素体全部转变为奥氏体终了温度。其它与具体实施方式六相同。Embodiment 8: The difference between this embodiment and Embodiment 6 is that the austenitization temperature of the low-carbon chromium-silicon-manganese low-alloy steel in the austenitization treatment is A of the low-carbon chromium-silicon-manganese low-alloy steel. The temperature above C3 is 30°C-50°C, and the holding time is 10s-1800s, where A C3 is the final temperature at which all ferrite transforms into austenite when heated. Others are the same as the sixth embodiment.
具体实施方式九：本实施方式30CrMnSi钢的热处理方法，其是通过以下步骤实现的：一、将30CrMnSi钢在810℃～880℃下保温600s完成奥氏体化处理后，然后在170～250℃的温度下进行等温淬火或者不完全淬火，保温60s～300s；二、将经步骤一处理后的30CrMnSi钢在330℃～440℃的温度区间内，等温配分热处理120s～900s，然后再淬火至室温，即完成30CrMnSi钢的热处理方法。Ninth specific embodiment: The heat treatment method of 30CrMnSi steel in this embodiment is realized through the following steps: 1. After austenitizing the 30CrMnSi steel at 810°C to 880°C for 600s to complete the austenitization treatment, Carry out isothermal quenching or incomplete quenching at a certain temperature, and keep warm for 60s~300s; 2. The 30CrMnSi steel treated in
本实施方式的热处理方法的工艺示意图如图5所示，图中AT表示奥氏体化温度，QT表示淬火温度，PT表示配分温度。The process schematic diagram of the heat treatment method of this embodiment is shown in FIG. 5 , in which AT represents the austenitizing temperature, QT represents the quenching temperature, and PT represents the partition temperature.
经本实施方式的热处理工艺处理后的30CrMnSi钢的抗拉强度达到1665MPa～1740MPa，塑性达到9％～13％。在保证30CrMnSi钢的强度的同时，获得了很好的塑性，实现了30CrMnSi钢的强塑性配合。The tensile strength of the 30CrMnSi steel treated by the heat treatment process of this embodiment reaches 1665MPa-1740MPa, and the plasticity reaches 9%-13%. While ensuring the strength of 30CrMnSi steel, it obtains good plasticity and realizes the strong-plastic fit of 30CrMnSi steel.
通过下述试验验证本实施方式的30CrMnSi钢的热处理方法的有益效果：The beneficial effect of the heat treatment method of the 30CrMnSi steel of the present embodiment is verified by following tests:
试验3：30CrMnSi钢的热处理方法，其是通过以下步骤实现的：一、将30CrMnSi钢在850℃下保温600s完成奥氏体化处理后，然后在220℃的温度下进行等温淬火，保温120s；二、将经步骤一处理后的30CrMnSi钢在350℃的温度下，等温配分热处理120s，然后再淬火至室温，即完成30CrMnSi钢的热处理方法。处理后的30CrMnSi钢的抗拉强度为1740MPa，并且塑性达到9.0％，获得较高的抗拉强度和一定的塑性。具有很好的强塑性配合。Test 3: The heat treatment method of 30CrMnSi steel is realized through the following steps: 1. After austenitizing the 30CrMnSi steel at 850°C for 600s, it is then austempered at 220°C for 120s; 2. The 30CrMnSi steel treated in
试验4：30CrMnSi钢的热处理方法，其是通过以下步骤实现的：一、将30CrMnSi钢在850℃下保温600s完成奥氏体化处理后，然后在240℃的温度下进行等温淬火，保温120s；二、将经步骤一处理后的30CrMnSi钢在410℃的温度下，等温配分热处理600s，然后再淬火至室温，即完成30CrMnSi钢的热处理方法。处理后的30CrMnSi钢的抗拉强度为1665MPa，塑性达到13％，强度较传统热处理最佳值略微降低，但是塑性较好。具有很好的强塑性配合。Test 4: The heat treatment method of 30CrMnSi steel is realized through the following steps: 1. After austenitizing the 30CrMnSi steel at 850°C for 600s, it is then austenitized at 240°C for 120s; 2. The 30CrMnSi steel treated in
试验5：30CrMnSi钢的热处理方法，其是通过以下步骤实现的：一、将30CrMnSi钢在850℃下保温600s完成奥氏体化处理后，然后在180℃的温度下进行等温淬火，保温120s；二、将经步骤一处理后的30CrMnSi钢在430℃的区间内的温度下，等温配分热处理900s，然后再淬火至室温，即完成30CrMnSi钢的热处理方法。处理后的30CrMnSi钢的抗拉强度为1735MPa，塑性达到12.5％，强塑积为21520MPa％。获得较高的抗拉强度和一定的塑性。具有很好的强塑性配合。Experiment 5: The heat treatment method of 30CrMnSi steel is realized through the following steps: 1. After austenitizing the 30CrMnSi steel at 850°C for 600s, it is then austempered at 180°C for 120s; 2. The 30CrMnSi steel treated in
具体实施方式十：本实施方式30CrMnSiNi2钢或者30CrMnSiNi2A钢的热处理方法，其是通过以下步骤实现的：一、将30CrMnSiNi2钢或者30CrMnSiNi2A钢在AC3以上30℃～50℃下保温10s～1800s完成奥氏体化处理后，然后在马氏体转变起始点Ms以下170-10℃的温度下进行等温淬火或者不完全淬火，保温6s～5400s；二、将经步骤一处理后的30CrMnSiNi2钢或者30CrMnSiNi2A钢在Ms+100℃至Ms-100℃的温度区间内，等温配分热处理6s～5400s，然后再冷却至室温，即完成30CrMnSiNi2钢或者30CrMnSiNi2A钢的热处理方法。Specific Embodiment Ten: The heat treatment method of 30CrMnSiNi2 steel or 30CrMnSiNi2A steel in this embodiment is realized through the following steps: 1. The 30CrMnSiNi2 steel or 30CrMnSiNi2A steel is kept at 30°C-50°C above A C3 for 10s-1800s to complete the austenitic After the tempering treatment, austempering or incomplete quenching is carried out at a temperature of 170-10°C below the starting point of martensitic transformation M s , and the temperature is kept for 6s to 5400s; 2. The 30CrMnSiNi2 steel or 30CrMnSiNi2A steel treated in
Claims (6)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2012100515901A CN102560023A (en) | 2012-03-01 | 2012-03-01 | Thermal treatment method for low-carbon chrome-silicon manganese low alloy steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2012100515901A CN102560023A (en) | 2012-03-01 | 2012-03-01 | Thermal treatment method for low-carbon chrome-silicon manganese low alloy steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN102560023A true CN102560023A (en) | 2012-07-11 |
Family
ID=46406622
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2012100515901A Pending CN102560023A (en) | 2012-03-01 | 2012-03-01 | Thermal treatment method for low-carbon chrome-silicon manganese low alloy steel |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN102560023A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102876981A (en) * | 2012-10-17 | 2013-01-16 | 夏雨 | Method for preparing medium and low carbon chrome-silicon-manganese martensite cast steel with hardening surface layer |
| CN103215417A (en) * | 2013-05-14 | 2013-07-24 | 哈尔滨工业大学 | Method for ultra-high enhanced heat treatment for medium carbon silicon-manganese-chromium-nickel low-alloy steel |
| CN103243204A (en) * | 2013-05-13 | 2013-08-14 | 哈尔滨工业大学 | Strengthening and toughening heat treatment method of medium carbon manganese-vanadium low alloy steel |
| CN103276164A (en) * | 2013-05-15 | 2013-09-04 | 哈尔滨工业大学 | High-strength and high-toughness heat treatment method of medium-carbon silicon-manganese-chromium-nickel series low alloy steel |
| CN112575256A (en) * | 2020-11-26 | 2021-03-30 | 博耀能源科技有限公司 | High-strength and high-toughness large-diameter wind power bolt with shell/horse complex phase structure and preparation method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2004022794A1 (en) * | 2002-09-04 | 2004-03-18 | Colorado School Of Mines | Method for producing steel with retained austenite |
| CN101487096A (en) * | 2009-02-19 | 2009-07-22 | 北京科技大学 | Low-alloy high-strength C-Mn-Al Q & P steel and method of manufacturing the same |
| CN101705345A (en) * | 2009-09-02 | 2010-05-12 | 北京科技大学 | Process method for improving ductility and toughness of Cr-containing high-strength steel by utilizing carbon distribution |
| CN101903539A (en) * | 2007-12-20 | 2010-12-01 | Posco公司 | Steel wire rod for bearing steel, manufacturing method of steel wire rod for bearing steel, heat treatment method of steel bearing, steel bearing and soaking method of bearing steel |
-
2012
- 2012-03-01 CN CN2012100515901A patent/CN102560023A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2004022794A1 (en) * | 2002-09-04 | 2004-03-18 | Colorado School Of Mines | Method for producing steel with retained austenite |
| CN101903539A (en) * | 2007-12-20 | 2010-12-01 | Posco公司 | Steel wire rod for bearing steel, manufacturing method of steel wire rod for bearing steel, heat treatment method of steel bearing, steel bearing and soaking method of bearing steel |
| CN101487096A (en) * | 2009-02-19 | 2009-07-22 | 北京科技大学 | Low-alloy high-strength C-Mn-Al Q & P steel and method of manufacturing the same |
| CN101705345A (en) * | 2009-09-02 | 2010-05-12 | 北京科技大学 | Process method for improving ductility and toughness of Cr-containing high-strength steel by utilizing carbon distribution |
Non-Patent Citations (8)
| Title |
|---|
| 《Materials Research》 20051231 John G.Speer等 The"Quenching and Partitioning"Process:Background and Recent Progress 417-423 1-6 第8卷, 第4期 * |
| DONG H.KIM,JOHN G.SPEER,HAN S.KIM,AND BRUNO C.DE COOMAN: "Observation of an Isothermal Transformation during Quenching and Partitioning Processing", 《METALLURGICAL AND MATERIALS TRANSACTIONS A》 * |
| H.Y.LI等: "Microstructure and Mechanical Properties of an Ultrahigh-Strength 40SiMnNiCr Steel during the One-Step Quenching and Partitioning Process", 《METALLURGICAL AND MATERIALS TRANSACTIONS A》 * |
| J.SPEER，D.K.MATLOCK，B.C.DE COOMAN，J.G.SCHROTH: "Carbon partitioning into austenite after martensite transformation", 《ACTA MATERIALIA》 * |
| JOHN G.SPEER等: "The"Quenching and Partitioning"Process:Background and Recent Progress", 《MATERIALS RESEARCH》 * |
| 庄宝潼，唐荻，江海涛，刘智: "Q&P工艺对0.3C-1.35Mn-1.30Si钢力学性能的影响", 《材料热处理学报》 * |
| 纪云航，冯伟骏，王利，薛小怀: "新一代高强度淬火分配钢的研究和应用", 《钢铁研究学报》 * |
| 赵才，江海涛，唐荻，赵松山，李辉: "低碳硅-锰Q&P钢工艺优化及残余奥氏体的定量研究", 《2007中国钢铁年会论文集》 * |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102876981A (en) * | 2012-10-17 | 2013-01-16 | 夏雨 | Method for preparing medium and low carbon chrome-silicon-manganese martensite cast steel with hardening surface layer |
| CN103243204A (en) * | 2013-05-13 | 2013-08-14 | 哈尔滨工业大学 | Strengthening and toughening heat treatment method of medium carbon manganese-vanadium low alloy steel |
| CN103215417A (en) * | 2013-05-14 | 2013-07-24 | 哈尔滨工业大学 | Method for ultra-high enhanced heat treatment for medium carbon silicon-manganese-chromium-nickel low-alloy steel |
| CN103276164A (en) * | 2013-05-15 | 2013-09-04 | 哈尔滨工业大学 | High-strength and high-toughness heat treatment method of medium-carbon silicon-manganese-chromium-nickel series low alloy steel |
| CN103276164B (en) * | 2013-05-15 | 2014-12-31 | 哈尔滨工业大学 | High-strength and high-toughness heat treatment method of medium-carbon silicon-manganese-chromium-nickel series low alloy steel |
| CN112575256A (en) * | 2020-11-26 | 2021-03-30 | 博耀能源科技有限公司 | High-strength and high-toughness large-diameter wind power bolt with shell/horse complex phase structure and preparation method thereof |
| CN112575256B (en) * | 2020-11-26 | 2021-12-31 | 博耀能源科技有限公司 | High-strength and high-toughness large-diameter wind power bolt with shell/horse complex phase structure and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103131962B (en) | High-tenacity low-alloy high-strength steel and quenched-tempered heat treatment method thereof | |
| CN103305673B (en) | Method for manufacturing fine-grain 35CrNi3MoV steel large forging stock | |
| US9624559B2 (en) | Bearing steel excellent in rolling-contact fatigue properties and method for producing same | |
| CN101509056B (en) | Thermal treatment method for precipitation hardening of martensitic stainless steel FV520B | |
| US11401566B2 (en) | High strength and high toughness stainless steel and processing method thereof | |
| CN105385835B (en) | A kind of heat treatment method for improving the high-strength steel part obdurability of cut deal | |
| CN102534132A (en) | Quenching-partitioning thermal treatment method for high strength and toughness of medium carbon silicon-manganese low alloy steel | |
| CN105463307B (en) | A kind of Q&P steel with gradient structure and preparation method thereof | |
| CN104451408B (en) | Strong bainitic steel of carbon superelevation and preparation method thereof in one | |
| CN106222544B (en) | Annular forging piece and its heat treatment method | |
| Giordani et al. | Mechanical and metallurgical evaluation of carburized, conventionally and intensively quenched steels | |
| CN102560023A (en) | Thermal treatment method for low-carbon chrome-silicon manganese low alloy steel | |
| CN104164548B (en) | A Heat Treatment Process for Thick and Large Section Low Carbon and Low Alloy Steel Casting and Forging | |
| CN109207693A (en) | A method of improving quenched and tempered state low-alloy nodular bainite steel impact flexibility | |
| CN109930082A (en) | A kind of high-intensity and high-tenacity upper bainite steel and preparation method thereof | |
| CN103184319A (en) | Heat treatment method for improving low-temperature impact energy of 35CrMoA steel | |
| CN102021479B (en) | Si-containing medium carbon steel and thermal treatment method for Si-containing medium carbon steel to obtain high strength and elasticity | |
| CN103469097B (en) | The corrosion-resistant tubing and casing of high strength martensitic ferrite diphasic stainless steel and manufacture method thereof | |
| CN103572176A (en) | Low-carbon martensite steel and method for preparing flying ring using same | |
| CN105296876A (en) | High-strength fastener steel containing nickel and copper and thermal treatment method for high-strength fastener steel | |
| CN104562050B (en) | A kind of preparation method of heavy-duty gear | |
| CN108866443B (en) | Normalized low yield ratio high strength steel plate and preparation method thereof | |
| CN105525077A (en) | Heating processing technology for improving mechanical property of spring steel | |
| Chen et al. | Processing, microstructures and mechanical properties of ultra-high strength steel sheet | |
| CN104694834B (en) | Thermal treatment method of high-strength corrosion resistant steel special for anti-theft window frame |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C02 | Deemed withdrawal of patent application after publication (patent law 2001) | ||
| WD01 | Invention patent application deemed withdrawn after publication |
Application publication date: 20120711 |