WO2020135690A1 - 一种表层高塑性内层高强度的梯度钢铁材料及制造方法 - Google Patents

一种表层高塑性内层高强度的梯度钢铁材料及制造方法 Download PDF

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WO2020135690A1
WO2020135690A1 PCT/CN2019/129094 CN2019129094W WO2020135690A1 WO 2020135690 A1 WO2020135690 A1 WO 2020135690A1 CN 2019129094 W CN2019129094 W CN 2019129094W WO 2020135690 A1 WO2020135690 A1 WO 2020135690A1
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steel material
surface layer
ferrite
inner layer
strength
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PCT/CN2019/129094
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English (en)
French (fr)
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张所全
焦四海
丁建华
吴扣根
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宝山钢铁股份有限公司
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Priority to US17/415,107 priority Critical patent/US20220042122A1/en
Priority to JP2021536047A priority patent/JP7241179B2/ja
Priority to EP19901488.7A priority patent/EP3885460A4/en
Publication of WO2020135690A1 publication Critical patent/WO2020135690A1/zh

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/28—Normalising
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/84—Controlled slow cooling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2201/00—Treatment for obtaining particular effects
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Definitions

  • the invention relates to a steel material, in particular to a gradient steel material with a high plastic layer on the surface and a high strength on the inner layer and a manufacturing method.
  • the strength and plasticity of steel materials are often two contradictory performance indicators. It is often difficult to obtain satisfactory plasticity while pursuing strength.
  • the main deformation occurs in the surface layer of the material. As the distance from the surface to the core direction increases, the strain becomes smaller and smaller, and the plasticity requirements are increasing. The lower, so if you can develop a material with better surface plasticity but slightly lower strength and slightly lower inner layer plasticity but higher strength, it will be very helpful to solve this problem.
  • the surface material meets the large deformation of the surface layer and the inner layer material Provide higher strength. Under this background, it is very meaningful to develop a graded steel material with different surface structure and inner structure.
  • the existing solution is mainly to realize the compounding of different materials through rolling compounding, explosive compounding, bonding compounding, etc.
  • the rolled composite plate produced by Baosteel is composed of stainless steel, nickel-based alloy, titanium steel and other functional materials and carbon steel and other structural materials through the method of rolling after the billet, to obtain both surface stainless steel and nickel-based alloy , Titanium steel corrosion resistance and other properties, and composite materials with higher strength of the matrix material, to achieve a further upgrade of the material function
  • Gradient materials are a new type of composite materials. Compared with traditional composite materials, gradient materials have the characteristics of continuous changes in structure and mechanical properties. There is no obvious interface, which can effectively alleviate and eliminate materials caused by thermal stress damage at the interface. Failure. Northeastern University conducts unidirectional cooling of the steel plate by controlled cooling, which causes a gradient change in the steel structure. The surface distribution has high strength, high hardness and high wear resistance, such as martensite and bainite. Internally, there are microstructures with high toughness and good plasticity, such as ferrite and pearlite structures. This kind of material with gradient distribution and superior tissue performance on both sides can meet the needs of strength and wear resistance on the side of high strength and high hardness; the side with high toughness and good plasticity can meet the requirements of toughness and toughness. Deformation processing requirements.
  • ECAP equal angle extrusion
  • USP ultrasonic shot peening
  • SMAT surface mechanical grinding
  • HPT high pressure torsion
  • the purpose of the present invention is to provide a gradient steel material with high surface layer and high plastic inner layer and high strength.
  • the steel material does not need to be obtained by compound preparation of different materials, only a single material is processed and prepared, and the composition of the steel material is simple;
  • the steel material of the present invention is an organically unified whole. Although the internal and external structures are different, the difference is a gradual change process, and the metallurgical bonding strength between the two is good; at the same time, the carbon content of the entire material is low, which ensures good welding performance.
  • the surface layer of the steel material is a ferrite structure, and the inner layer is a ferrite + bainite structure.
  • the surface layer varies according to the thickness of the steel plate, and is usually within 1 mm.
  • the surface layer of the steel material is a ferrite structure, and the carbon content is relatively low, not higher than 0.02wt%, where 0.02wt% is the result of retaining two decimal places, that is, it covers 0.015wt% to 0.024
  • the value range of wt% preferably, the carbon content of the surface layer is not higher than 0.022wt%; the carbon content of the inner layer is higher and higher than the average carbon content of the entire gradient steel material, that is, the carbon content of the steel material surface layer is lower than that of the steel material inner layer Carbon content.
  • the manufacturing method of the surface layer high plasticity inner layer high strength gradient steel material of the present invention includes: smelting, casting, rolling, heat treatment; wherein, in the heat treatment step, the steel material is heated to austenite temperature Ac3 Above, keep the temperature for more than 3min to ensure that the material is fully austenitized; then cool at a cooling rate of less than 0.5°C/s to the temperature range between Ar3 and Ar1 in the two-phase area, and then at a cooling rate of more than 5°C/s Quickly cool to room temperature.
  • the entire steel material is heated to be fully austenitized, and then slowly cooled, so that the surface layer of the material preferentially obtains a ferrite structure, because the solid solubility of carbon in the ferrite structure is relatively low,
  • the new ferrite structure discharges carbon into the internal austenite, which makes the internal austenite structure tend to be more stable.
  • the surface ferrite layer becomes thicker and thicker, the carbon content in the intermediate austenite structure becomes higher and higher, and the structure becomes more and more stable.
  • the internal austenite structure is transformed into a high-strength rapid cooling structure, such as a mixed structure of bainite and ferrite.
  • the present invention Compared with the rolled composite, explosive composite and bonded composite composite plates, the present invention only rolls and heat-treats one material, and does not need to process the two materials into billets, etc. At the same time, in the final product, the steel material For an organically unified whole, although there are differences between the internal and external tissues, this difference is a gradual process, and the metallurgical bonding strength between the two is good.
  • unidirectional cooling of the steel plate by controlled cooling causes a gradient change in the steel structure, and the surface distribution has a structure with high strength, high hardness and high wear resistance, such as martensite and bainite;
  • the surface distribution has a structure with high strength, high hardness and high wear resistance, such as martensite and bainite;
  • microstructures with high toughness and good plasticity such as ferrite and pearlite, etc., because during the cooling process, the surface of the material cools quickly, and the inner layer cools slowly.
  • the desired structure of the present invention is exactly the opposite, so that the surface distribution of the material has a structure with high toughness and good plasticity, and the internal distribution of the material has a structure with high strength, high hardness and high wear resistance.
  • the present invention adopts different cooling rates in different temperature ranges to make the surface layer of the material change phase first, while the inner layer temporarily does not undergo phase change, and finally the surface layer is a ferrite structure with better plasticity, and the inner layer is
  • the high-strength bainite and ferrite structure is beneficial to the processing method with large surface deformation such as bending and torsion.
  • the carbon in the surface layer structure is transferred to the inner layer structure by ultra-long-range diffusion, the internal carbon is increased and the strength is increased, but the overall carbon content of the material is not high, maintaining good welding performance.
  • the present invention does not need to refine the structure through the large deformation technology, so as to realize the mechanical properties and the gradient change of the structure on the surface of the material, and the preparation method is simple.
  • FIG. 1 The material obtained by the method of the present invention is shown in FIG. 1 as follows: the outer structure of the material is ferrite, as shown in the part outside the dotted circle in FIG. 1, the inner structure is a mixed structure of ferrite and bainite, such as In Fig. 1, the portion within the dotted line is shown.
  • the gradient steel material with high surface layer plasticity and high internal layer strength can obtain a ferrite layer with better surface layer plasticity and a mixed structure of ferrite and bainite with higher inner layer strength, compared with the prior art Has the following advantages:
  • the present invention does not need to compound two materials, but only processes and prepares on a single material and a single material.
  • the method of the present invention has a short process flow, simple process and low cost.
  • the steel plate of the present invention is an organically unified whole.
  • the difference in the organization on both sides is a gradual change process, and the metallurgical bonding strength between the two layers is good.
  • FIG. 1 is a schematic diagram of the structure of the gradient steel material of the present invention, where B represents bainite and F represents ferrite;
  • FIG. 2 is a schematic diagram of the heat treatment process in the embodiment of the manufacturing method of the present invention.
  • FIG. 3 is a structure diagram of a sample end portion of Example 1 of the present invention.
  • Fig. 4 is a micrograph of the sample end portion of Example 4 of the present invention.
  • compositions of the examples and comparative examples of the present invention are shown in Table 1.
  • the rest are Fe and inevitable impurities.
  • the manufacturing method is as follows: steel obtained by smelting, heating and rolling in a converter or electric furnace, and then subjected to heat treatment to finally obtain a gradient steel material with surface ferrite, inner layer ferrite + bainite structure.
  • the comparative example of this application is intended to explain that when the contents of C, Si and Mn are not within the range of 0 ⁇ C ⁇ 0.15%, 0 ⁇ Si ⁇ 1%, 0 ⁇ Mn ⁇ 1.5% as defined in this application, or the cooling rate is not satisfied
  • the structure of a graded steel material in which the surface layer is pure ferrite and the inner layer is a mixture of ferrite and bainite cannot be obtained.
  • Table 2 shows the heat treatment processes in the manufacturing method examples and comparative examples of the present invention.
  • Fig. 1 shows the structure of the graded steel material according to the present invention.
  • the surface layer is a pure ferrite structure
  • the inner layer is a mixed structure of ferrite and bainite.
  • FIG. 2 shows the heat treatment process in the embodiment of the manufacturing method of the present invention.
  • the structure of the gradient steel material obtained in Example 1 has a pure ferrite structure in the surface layer of about 256um, and a mixed structure of ferrite and bainite in the inner layer.
  • Fig. 4 shows the structure of the gradient steel material obtained in Example 4 of the present invention.
  • the pure ferrite structure in the surface layer is about 171um, and the inner layer is a mixed structure of ferrite and bainite.
  • Example 1 A C Si Mn Example 1 0.054 0.26 0.51
  • Example 2 0.075 0.252 0.49
  • Example 3 0.081 0.243 1.23
  • Example 4 0.105 0.356 0.56
  • Example 5 0.112 0.366 0.76 Comparative Example 1 0.054 0.26 0.51 Comparative Example 2 0.15 1.5 0.48

Abstract

一种表层高塑性内层高强度的梯度钢铁材料及制造方法，其成分重量百分比为：C≤0.15％，Si≤1％，Mn≤1.5％，余量为Fe和不可避免杂质，且所述钢铁材料的表层为铁素体组织，内层为铁素体+贝氏体组织。其制造方法包括：冶炼、铸造、轧制、热处理；其中，热处理步骤中，将钢铁材料加热到奥氏体温度Ac3以上，保温3min以上；然后以小于0.5℃/s的冷却速度冷却到两相区内Ar3和Ar1之间的温度范围，再以大于5℃/s冷却速度冷却至室温。该钢铁材料不需要通过不同材料复合制备获得，仅对单一材质进行加工，同时钢铁材料成分简单，内外组织虽有差异，该差异为渐变过程，两者之间冶金结合强度良好。

Description

一种表层高塑性内层高强度的梯度钢铁材料及制造方法 技术领域
本发明涉及一种钢铁材料，尤其涉及一种表层高塑性内层高强度的梯度钢铁材料及制造方法。
背景技术
钢铁材料的强度和塑性往往是较矛盾的两个性能指标，追求强度的同时往往难以获得较满意的塑性。而对一些用于扭转或者折弯的材料而言，其主要变形发生在材料表层，随着往芯部方向距离表面越来越远的同时，应变变得越来越小，对塑性要求越来越低，因此如果能开发一种表层塑性较好但强度稍低，内层塑性稍差但强度较高的材料，将非常有利于解决这个难题，表层材料满足表层大变形的同时，内层材料提供较高的强度。这种背景下，开发一种表层组织和内层组织不一样的梯度钢铁材料，则非常具有意义。
现有的解决方法主要是通过轧制复合、爆炸复合、粘结复合等方法实现不同材料的复合，这方面的专利较多，超过1000个。比如宝钢为首生产的轧制复合板，将不锈钢、镍基合金，钛钢等功能材料和碳钢等结构材料，通过组坯后轧制的方法复合到一起，获得既具有表层不锈钢、镍基合金，钛钢耐腐蚀等性能，又具有基体材料较高强度的复合板产品，实现了材料功能的进一步升级，中国专利CN201110045798.8、CN201310211969.9、CN201410707715.0、CN201310212003.7、CN201310213371.3、CN201510173144.1、CN201611223874.9、CN201510621011.6、CN201510173145.6等均是介绍此类复合轧制相关技术。此外爆炸复合也得到一些应用，此技术在表层金属上均布炸药并引爆，使得表层金属和基层金属复合，中国专利CN201520878950.4、CN201510738639.4、CN201620972383.3等则介绍这一类相关技术。也有很多专利通过粘结的方法，将金属或者非金属粘结到一起，获得满足功能 需求的复合板，比如中国专利CN201720527381.8、CN201810506236.0、CN201711015280.3等。综合上述文献所公开的方法，目前主要通过不同的复合方法，将不同的材料经过冶金或者机械的方法，使两块或者多块材料结合到一起，使其具有不同的组织及特殊的功能。
为了研发出能够承受巨大温差的新型耐热材料，日本学者新野正之等首先提出了梯度材料的概念。梯度材料是一种新型复合材料，与传统的复合材料相比，梯度材料具有组织、力学性能等连续变化的特点，不存在明显的界面，可以有效缓解和消除由于界面处热应力破坏导致的材料失效。东北大学通过控制冷却对钢板进行单向冷却，使钢材组织产生梯度变化，表面分布具有高强度、高硬度和高耐磨性的组织，如马氏体和贝氏体组织等；而在材料的内部则分布具有高韧性、塑性较好的组织，如铁素体和珠光体组织等。这种组织呈梯度分布、两侧组织性能各有优势的材料，其高强度、高硬度一侧能够满足对强度和耐磨性的需求；高韧性、塑性良好的一侧，能够满足对韧性和加工变形的需求。
大变形技术也能够有效细化组织并实现材料组织或性能的梯度变化。目前应用较多的大变形技术有等角挤压(ECAP)、超声喷丸(USP)、表面机械研磨(SMAT)、高压扭转(HPT)等。以上研究均是依靠大变形技术细化组织的作用，在材料表面实现力学性能和组织的梯度变化。
发明内容
本发明的目的在于提供一种表层高塑性内层高强度的梯度钢铁材料及制造方法，该钢铁材料不需要通过不同材料复合制备获得，仅对单一材质进行加工制备，同时该钢铁材料成分简单；本发明钢铁材料为有机统一的整体，内外组织虽然有差异，该差异为渐变过程，两者之间冶金结合强度良好；同时整个材料碳含量较低，保证了对良好的焊接性能。
为达到上述目的，本发明的技术方案是：
一种表层高塑性内层高强度的梯度钢铁材料，其成分重量百分比为：0<C≤0.15％，0<Si≤1％，0<Mn≤1.5％，其余为Fe和不可避免的杂质，且所述钢铁材料的表层为铁素体组织，内层为铁素体+贝氏体组织。其中，所述表层根据钢板厚度的不同而有所不同，通常在1mm以内。
优选的，所述钢铁材料的表层为铁素体组织，碳含量较低，不高于0.02wt％，其中，0.02wt％为保留小数点后两位的结果，即其涵盖了0.015wt％～0.024wt％的数值范围，优选地，表层碳含量不高于0.022wt％；内层碳含量较高，高于整个梯度钢铁材料的平均碳含量，即钢铁材料表层的碳含量低于钢铁材料内层的碳含量。
本发明所述的表层高塑性内层高强度的梯度钢铁材料的制造方法，其包括：冶炼、铸造、轧制、热处理；其中，所述热处理步骤中，将钢铁材料加热到奥氏体温度Ac3以上，保温3min以上，保证材料完全奥氏体化；随后以小于0.5℃/s的冷却速度冷却到两相区内Ar3和Ar1之间的温度范围内，再以大于5℃/s的冷却速度快速冷却至室温。
本发明制造方法中，在热处理时，将整个钢铁材料加热完全奥氏体化，然后通过缓慢冷却，使得材料表层优先获得铁素体组织，由于铁素体组织中碳的固溶度比较低，新生铁素体组织向内部奥氏体中排碳，这样就使得内部奥氏体组织趋于更加稳定。随着铁素体组织的进一步形核、长大，表层铁素体层越来越厚，中间奥氏体组织中的碳含量越来越高，并且组织越来越稳定。在之后的快速冷却过程，内部的奥氏体组织转变为高强度的快冷组织，比如贝氏体和铁素体的混合组织。
相对于轧制复合、爆炸复合和粘结复合的复合板，本发明仅对一种材料进行轧制及热处理，不需要将两种材料进行组坯等处理，同时最终获得的产品中，钢铁材料为有机统一的整体，内外组织虽然有差异，但该差异为渐变过程，两者之间冶金结合强度良好。
现有技术中，通过控制冷却对钢板进行单向冷却，使钢材组织产生梯度变化，表面分布具有高强度、高硬度和高耐磨性的组织，如马氏体和贝氏体组织等；而在材料的内部则分布具有高韧性、塑性较好的组织，如铁素体和珠光体组织等，这是因为冷却过程中，材料表面冷却快，内层冷却慢。而本发明希望获得的组织结构恰恰相反，使材料表面分布具有高韧性、塑性较好的组织，而材料内部分布具有高强度、高硬度和高耐磨性的组织。因此，本发明通过在不同的温度范围内采取不同的冷速，使材料表层先发生相变，而内层暂时不发生相变，最终得到表层为塑性较好的铁素体组织，内层为强度较高的贝氏体及铁素体组织，该组织有利于折弯及扭转等表层 变形较大的加工方式。同时，本发明中，由于表层组织中的碳通过超长程扩散，转移到内层组织中，使得内部碳提高而增加强度，但材料整体碳含量不高，保持较好的焊接性能。
同时，本发明不需要通过大变形技术细化组织，从而在材料表面实现力学性能和组织的梯度变化，制备方法简单。
通过本发明方法获得的材料如图1所示下：材料外层组织为铁素体，如图1中虚线圈以外部分所示，内层组织为铁素体和贝氏体的混合组织，如图1中虚线圈以内部分所示。
本发明的有益效果：
本发明中的表层高塑性内层高强度的梯度钢铁材料，可以获得表层塑性较好的铁素体层，内层强度较高的铁素体和贝氏体的混合组织，相比现有技术具有以下优点：
(1)本发明不需要对两种材料进行复合，只在单一材质，单个材料上进行加工制备。
(2)本发明方法流程短，工序简单，成本低。
(3)本发明钢板为有机统一的整体，两侧组织的差异为渐变过程，两层之间冶金结合强度良好。
(4)本发明中，由于表层组织中的碳通过超长程扩散，转移到内层组织中，使得内部碳提高而增加强度，但材料整体碳含量不高，保持较好的焊接性能。
附图说明
图1为本发明所述梯度钢铁材料的组织示意图，其中B代表贝氏体，F代表铁素体；
图2为本发明制造方法实施例中的热处理工艺示意图；
图3为本发明实施例1试样端部的组织图；
图4为本发明实施例4试样端部的组织图。
具体实施方式
下面结合实施例和附图对本发明做进一步说明。
本发明实施例及对比例的成分参见表1，其余均为Fe和不可避免的杂质。其制造方法为：经过转炉或者电炉冶炼、加热、轧制获得的钢材，再进行热处理，最终得到表层铁素体，内层铁素体+贝氏体组织的梯度钢铁材料。
本申请的对比例意在说明，当C、Si、Mn的含量不在本申请限定的0<C≤0.15％，0<Si≤1％，0<Mn≤1.5％范围内，或者冷速不满足本申请的限定时，均无法得到表层为纯铁素体、内层为铁素体和贝氏体的混合的梯度钢铁材料的组织。
表2所示为本发明制造方法实施例和对比例中的热处理工艺。
图1所示为本发明所述梯度钢铁材料的组织，表层为纯铁素体组织，内层为铁素体和贝氏体的混合组织。
图2所示为本发明制造方法的实施例中的热处理工艺。
从图3可以发现，实施例1得到的梯度钢铁材料的组织中表层大约256um范围为纯铁素体组织，内层为铁素体和贝氏体的混合组织。
图4所示为本发明实施例4得到梯度钢铁材料的组织，表层大约171um范围的纯铁素体组织，内层为铁素体和贝氏体的混合组织。
表1    单位：重量百分比
  C Si Mn
实施例1 0.054 0.26 0.51
实施例2 0.075 0.252 0.49
实施例3 0.081 0.243 1.23
实施例4 0.105 0.356 0.56
实施例5 0.112 0.366 0.76
对比例1 0.054 0.26 0.51
对比例2 0.15 1.5 0.48
表2
Figure PCTCN2019129094-appb-000001

Claims (3)

  1. 一种表层高塑性内层高强度的梯度钢铁材料，其成分重量百分比为：0<C≤0.15％，0<Si≤1％，0<Mn≤1.5％，其余为Fe和不可避免的杂质，且所述钢铁材料的表层为铁素体组织，内层为铁素体+贝氏体组织。
  2. 如权利要求1所述的表层高塑性内层高强度的梯度钢铁材料，其特征在于，所述钢铁材料的表层为铁素体组织，碳含量不高于0.02wt％；且所述钢铁材料表层的碳含量低于所述钢铁材料内层的碳含量。
  3. 如权利要求1或2所述的表层高塑性内层高强度的梯度钢铁材料的制造方法，其特征在于，包括：冶炼、铸造、轧制、热处理；其中，所述热处理步骤中，将钢铁材料加热到奥氏体温度Ac3以上，保温3min以上，保证材料完全奥氏体化；随后以小于0.5℃/s的冷却速度冷却到两相区内Ar3和Ar1之间的温度范围内，再以大于5℃/s的冷却速度快速冷却至室温。
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Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103459643A (zh) * 2011-03-25 2013-12-18 日新制钢株式会社 耐久性优异的带状冲切刀具用钢板及带状冲切刀具
CN105143486A (zh) * 2013-04-15 2015-12-09 杰富意钢铁株式会社 高强度热轧钢板及其制造方法
CN107663609A (zh) * 2016-07-29 2018-02-06 本钢板材股份有限公司 一种低成本高扩孔用540MPa级热轧酸洗板的生产方法
WO2018110152A1 (ja) * 2016-12-12 2018-06-21 Ｊｆｅスチール株式会社 低降伏比角形鋼管用熱延鋼板およびその製造方法並びに低降伏比角形鋼管およびその製造方法

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH10130782A (ja) * 1996-11-01 1998-05-19 Nippon Steel Corp 超高強度冷延鋼板およびその製造方法
JP2000096181A (ja) * 1998-09-25 2000-04-04 Sumitomo Metal Ind Ltd 溶接熱影響部においてｕｔｓ欠陥を生じない鋼板とその製造方法
JP2001059129A (ja) * 1999-08-20 2001-03-06 Nippon Steel Corp 高温降伏強度と加工性の優れたアパーチャーフレーム用鋼板およびその製造方法
JP5434960B2 (ja) * 2010-05-31 2014-03-05 Ｊｆｅスチール株式会社 曲げ性および溶接性に優れる高強度溶融亜鉛めっき鋼板およびその製造方法
TWI468534B (zh) * 2012-02-08 2015-01-11 Nippon Steel & Sumitomo Metal Corp 高強度冷軋鋼板及其製造方法
JP5833966B2 (ja) * 2012-04-20 2015-12-16 株式会社神戸製鋼所 疲労特性に優れた溶接継手
JP5803836B2 (ja) * 2012-07-30 2015-11-04 新日鐵住金株式会社 熱間プレス鋼板部材、その製造方法と熱間プレス用鋼板
CN103789686B (zh) * 2014-02-27 2015-09-16 中国科学院金属研究所 一种消除加氢反应器用钢混晶、粗晶组织的热处理工艺
CN108085591A (zh) * 2017-11-24 2018-05-29 南阳汉冶特钢有限公司 一种具有低焊接裂纹敏感性能的钢板htnm400及其生产方法
CN109023057B (zh) * 2018-08-27 2020-11-20 南京钢铁股份有限公司 一种提高x80m级管线钢心部冲击的生产方法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103459643A (zh) * 2011-03-25 2013-12-18 日新制钢株式会社 耐久性优异的带状冲切刀具用钢板及带状冲切刀具
CN105143486A (zh) * 2013-04-15 2015-12-09 杰富意钢铁株式会社 高强度热轧钢板及其制造方法
CN107663609A (zh) * 2016-07-29 2018-02-06 本钢板材股份有限公司 一种低成本高扩孔用540MPa级热轧酸洗板的生产方法
WO2018110152A1 (ja) * 2016-12-12 2018-06-21 Ｊｆｅスチール株式会社 低降伏比角形鋼管用熱延鋼板およびその製造方法並びに低降伏比角形鋼管およびその製造方法

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP3885460A4

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