WO2018099347A1 - 一种马氏体不锈钢轧制复合钢板及其制造方法 - Google Patents

一种马氏体不锈钢轧制复合钢板及其制造方法 Download PDF

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WO2018099347A1
WO2018099347A1 PCT/CN2017/113115 CN2017113115W WO2018099347A1 WO 2018099347 A1 WO2018099347 A1 WO 2018099347A1 CN 2017113115 W CN2017113115 W CN 2017113115W WO 2018099347 A1 WO2018099347 A1 WO 2018099347A1
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stainless steel
martensitic stainless
composite
layer
base layer
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PCT/CN2017/113115
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English (en)
French (fr)
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张爱文
丁建华
焦四海
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宝山钢铁股份有限公司
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Priority to EP17877002.0A priority Critical patent/EP3550052A4/en
Priority to AU2017370198A priority patent/AU2017370198B2/en
Publication of WO2018099347A1 publication Critical patent/WO2018099347A1/zh

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/011—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of iron alloys or steels
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • 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
    • C21D2211/008—Martensite
    • 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
    • C21D2211/009—Pearlite
    • 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
    • C21D2251/00—Treating composite or clad material
    • C21D2251/02—Clad material

Definitions

  • the invention relates to a composite board and a manufacturing method thereof, in particular to a rolled composite steel sheet and a manufacturing method thereof.
  • martensitic stainless steel clad steel plate As an important steel material, martensitic stainless steel clad steel plate has unique comprehensive performance advantages of stainless steel corrosion resistance and carbon steel mechanical properties, making it widely used in metallurgy, mining machinery, hydropower stations and other industries. With the rapid development of China's industry and the increasing requirements for the service life of various military and civilian equipments, as well as the requirements for green and ultra-low carbon emissions during production and use, the performance requirements for composite panels have also increased.
  • the composite steel sheet is usually subjected to conventional mechanical compounding and explosive composite, and the above two processes can be separately controlled while controlling the composite layer and the performance of the base layer, and then combined. That is, before the compounding, the respective required properties of the stainless steel and the carbon steel can be respectively processed to a suitable state, and then the mechanical composite force or the explosive impact force is applied to combine them into one to obtain a composite plate.
  • these two composite methods each have their own shortcomings. For example, a mechanical composite composite panel has no complete metallurgical bond between the stainless steel composite layer and the carbon steel base layer, but is simply attached by mechanical force.
  • the composite interface is easy to crack and fall off during use, and the failure is fast;
  • the disadvantage of explosion composite is that
  • the process method itself has strict requirements on the process environment, and it needs to be carried out in the deep forests and old places where the environment is sparsely populated.
  • the noise, vibration and shock waves generated during the explosion have a great impact on the surrounding environment.
  • this process The method is limited by environmental factors.
  • the composite panel produced by explosive composite has a low shear strength at the composite interface.
  • One of the objects of the present invention is to provide a martensitic stainless steel rolled composite steel sheet having high hardness, good mechanical properties, and certain cold bending and forming properties.
  • the present invention provides a martensitic stainless steel rolled composite steel sheet comprising a base layer and a martensite stainless steel double layer laminated on the base layer; the chemical element mass percentage of the base layer is:
  • Martensitic stainless steels known to those skilled in the art such as 30Cr13, 20Cr13, 40Cr13, and other types of martensitic stainless steels may be employed for the martensitic stainless steel laminate.
  • Carbon is an important alloying element in steel.
  • the increase in carbon content can improve the strength and hardness of the steel sheet, but the excessive mass of carbon can also cause the plastic toughness of the steel sheet to decrease, which affects the welding performance of the steel sheet.
  • the influence of carbon on the performance of the base steel sheet and the diffusion migration of the carbon of the martensite stainless steel layer to the base layer during rolling compounding are considered, and thus the carbon content of the base layer is appropriately increased, and the mass percentage thereof is It is limited to 0.1-0.2% to ensure high strength and hardness of martensitic stainless steel rolled composite steel sheets.
  • Si Adding silicon to steel can improve the purity of steel, and Si can act as a deoxidation. In addition, silicon acts as a solid solution strengthening in steel, but excess silicon is detrimental to solderability. Since the martensite stainless steel layer also has silicon, the mass percentage of silicon in the base layer is limited to 0 ⁇ Si ⁇ 0.35%, which is beneficial to reduce the influence on the corrosion resistance of the martensitic stainless steel double layer, and can also ensure Good solderability of the base layer.
  • Mn acts as a strengthening alloying element, while manganese increases the hardenability of steel and lowers the critical cooling rate of martensite formation.
  • manganese is beneficial for increasing the strength level of steel.
  • the mass percentage of the base layer to manganese of the martensitic stainless steel rolled composite steel sheet according to the present invention is limited to 0.5 to 1.5%.
  • the martensite stainless steel rolled composite steel sheet according to the present invention preferably has a Mn of 0.8 to 1.2%.
  • Al is a strong deoxidizing element for reducing the mass percentage of oxygen in the steel.
  • the mass percentage of aluminum controlled is 0.02-0.04% because aluminum and nitrogen elements can form AlN precipitates after deoxidation, which is beneficial to increase the strength of the steel and to refine the grains.
  • Titanium is a strong carbide forming element.
  • the addition of a small amount of Ti in the steel is beneficial to fixing the N in the steel, and the TiN formed suppresses the excessive growth of the crystal grains and acts to refine the crystal grains.
  • titanium may also be combined with carbon and sulfurized in steel to form TiC, TiS, Ti 4 C 2 S 2 , and the above compounds exist in the form of inclusions and second phase particles.
  • the above-mentioned carbonitride precipitates of titanium can also prevent grain growth in the heat-affected zone during welding and improve the welding performance. Therefore, the mass percentage of Ti in the base layer of the martensitic stainless steel rolled composite steel sheet according to the present invention is controlled to be Ti: 0.005 to 0.018%.
  • Nb niobium is a strong carbide forming element. Adding niobium to the base layer is beneficial to increase the recrystallization temperature, thereby promoting grain refinement and facilitating the improvement of the low temperature impact toughness of the base layer. Therefore, the mass percentage of ruthenium in the base layer of the martensitic stainless steel rolled composite steel sheet according to the present invention is controlled to be 0.005 to 0.020%.
  • N is an austenite stabilizing element which is a residual margin as a steelmaking gas element in the base layer, and therefore, the mass percentage of N in the martensitic stainless steel rolled composite steel sheet according to the present invention is controlled at N ⁇ 0.006%.
  • the unavoidable impurities are mainly S and P elements, and thus it is necessary to control P ⁇ 0.015% and S ⁇ 0.010% in the base layer.
  • the substrate further contains at least one of elements of Ni, Cr and Mo, wherein Ni ⁇ 0.20%, Cr ⁇ 0.20%, Mo ⁇ 0.10% .
  • At least one of Ni, Cr and Mo elements may be added because:
  • Ni The addition of Ni to the martensitic stainless steel rolled composite steel sheet according to the present invention is advantageous for stabilizing austenite and is advantageous for increasing the strength of the steel.
  • the addition of Ni to steel can greatly improve the low temperature impact toughness of steel.
  • nickel is a precious alloying element, excessive addition will increase production costs.
  • an appropriate amount of Ni is added to improve the low temperature impact toughness of the base layer. Therefore, the mass percentage of Ni in the martensitic stainless steel rolled composite steel sheet according to the present invention is controlled at Ni ⁇ 0.20%. .
  • the mass percentage of Cr in the martensitic stainless steel rolled composite steel sheet according to the present invention is limited to Cr ⁇ 0.20%.
  • Molybdenum helps to refine grains and improve the strength and toughness of steel.
  • molybdenum can reduce the temper brittleness of steel, and at the same time, it can precipitate very fine carbides during tempering, which is beneficial to strengthening the base matrix of steel.
  • the addition of molybdenum is advantageous for suppressing the self-temper brittleness of the martensitic stainless steel rolled composite steel sheet. Therefore, the mass percentage of molybdenum in the martensitic stainless steel rolled composite steel sheet according to the present invention is limited to Mo ⁇ 0.10%.
  • the microstructure of the martensitic stainless steel composite layer is all martensite or martensite + a small amount of carbide, wherein the ratio of carbides is not More than 2%.
  • the microstructure of the base layer is ferrite + pearlite.
  • a transition layer is provided at a joint of the base layer and the martensitic stainless steel composite layer, and the thickness of the transition layer is ⁇ 200 ⁇ m.
  • the mass percentages of the respective elements in the base layer and the martensitic stainless steel double layer are different, the element having a high mass percentage is diffused toward the side having a low mass percentage. Further, the mass percentage of the elements at the junction is distributed in a gradient to form a transition layer.
  • the microstructure of the transition layer is ferrite + carbide.
  • the base layer yield strength is ⁇ 235 MPa, the elongation A50 ⁇ 18%, the 0° C. Charpy impact energy Akv ⁇ 100 J, and the martensitic stainless steel composite steel plate shear. Cutting strength ⁇ 385 MPa.
  • another object of the present invention is to provide a method for producing the above-described martensitic stainless steel rolled composite steel sheet, which has high strength and a certain coldness. Bending and forming properties.
  • the present invention also provides a method for manufacturing the above-described martensitic stainless steel rolled composite steel plate, comprising the steps of:
  • (3) composite rolling firstly, the composite billet is heated at a temperature of 1100 to 1180 ° C, and then subjected to multi-pass rolling, the total rolling reduction rate is controlled to be not less than 70%, and the finishing rolling temperature is not lower than 900 ° C;
  • the composite sheet is sent to the cold sheet to be air-cooled, and the single air-cooling final cooling temperature is ⁇ 80 °C after the lower cooling bed to complete the martensite transformation.
  • the martensitic stainless steel rolled composite steel plate obtained after rolling has good mechanical properties and good performance. Welding performance.
  • the surface of the slab to be composited is pretreated between the substrate slab and the multi-layer slab before the substrate slab and the multi-layer slab are assembled, and the oxide of the surface to be composited is removed.
  • the number of layers of the composite can be set according to the specific conditions of each embodiment, for example, the number of the layer of the preform is two layers, and one layer is the substrate slab.
  • the other layer is a multi-layer slab; for example, the number of layers is set to four, the substrate slab is two layers, and the multi-layer slab is two layers, wherein two layers of martensitic stainless steel multi-layer slab are composited.
  • the time is located on the upper and lower surfaces of the composite blank, and the base slab is located in the middle of the composite blank.
  • a layer of separator is disposed between the layers of the base slab and the base slab. Further, in other preferred embodiments, the bonding interface of the base layer and the composite layer is evacuated.
  • the hardness of the martensitic stainless steel sheet according to the present invention is high.
  • the single steel sheet is not allowed to be stacked until the sheet is The air-cooled final cooling temperature is ⁇ 80 °C.
  • the composite sheet obtained in the step (5) may not be cold-corrected, but may be flattened to prevent cracking of the martensite stainless steel double layer.
  • the composite plate with a large number of slab combination layers can be separated into a sub-plate in the thickness direction and then flattened to improve the flattening effect. For example, when the number of slab combination layers is 4 layers, the flattening can be flattened. Before the cutting edge is separated into two composite board sub-plates in the thickness direction, the flattening is performed to improve the flattening effect.
  • the hot straightening stop temperature is ⁇ 550 °C.
  • the finish rolling temperature is 920 to 1000 °C.
  • the martensitic stainless steel rolled composite steel plate according to the invention is controlled by optimizing composition design and process parameters, so that The obtained martensitic stainless steel rolled composite steel plate has a base yield strength ⁇ 235 MPa, an elongation A50 ⁇ 18%, a 0°C Charpy impact energy Akv ⁇ 100J, and a martensitic stainless steel composite steel plate shear strength ⁇ 385 MPa.
  • the manufacturing method of the present invention enables the composite steel sheet to have both excellent mechanical properties, high hardness, and certain cold bending and forming properties by composite rolling of the substrate and the composite slab.
  • Example 1 is a metallographic structure of a base layer of a martensitic stainless steel rolled composite steel plate of Example 2.
  • Example 2 is a metallographic structure of a composite layer of a martensitic stainless steel rolled composite steel sheet of Example 2.
  • FIG. 3 is a metallographic structure of a transition layer of a martensitic stainless steel rolled composite steel plate of Example 3.
  • FIG. 3 is a metallographic structure of a transition layer of a martensitic stainless steel rolled composite steel plate of Example 3.
  • FIG. 4 is an enlarged view of a metallographic structure of a transition layer of a martensitic stainless steel rolled composite steel sheet of Example 3.
  • FIG. 4 is an enlarged view of a metallographic structure of a transition layer of a martensitic stainless steel rolled composite steel sheet of Example 3.
  • Table 1 lists the mass percentages of the chemical elements of the respective layers of the martensitic stainless steel rolled composite steel sheets of Examples 1-9.
  • Hot straightening stop temperature is ⁇ 550 °C
  • the composite sheet is sent to the cold sheet to be air-cooled, and the single air-cooling final cooling temperature is ⁇ 80 °C after the lower cooling bed to complete the martensite transformation.
  • the substrate slab forms the base layer of the martensitic stainless steel rolled composite steel sheet of each embodiment
  • the double-layer stainless steel slab forms the martensitic stainless steel composite layer of the martensitic stainless steel rolled composite steel sheet of each embodiment.
  • Table 2 lists the specific process parameters of the method for producing the martensitic stainless steel rolled composite steel sheets of Examples 1-9.
  • Table 3 lists the test results of various performance tests of the martensitic stainless steel rolled composite steel sheets of Examples 1-9.
  • the base layer yield strength of each embodiment is ⁇ 235 MPa
  • the shear strength of martensitic stainless steel rolled composite steel plate is ⁇ 385 MPa
  • the hardness of the base layer is higher than 110 HB
  • the hardness of the martensite stainless steel layer is higher than 48 HRC.
  • the mechanical properties of the examples are shown to be good.
  • the elongation of each embodiment is A50 ⁇ 18%
  • the Charpy impact energy Akv ⁇ 100 J at 0 ° C indicating that the base steel plate of the embodiment 1-9 of the present invention has excellent toughness
  • the results of the inner bending performance test of the composite layer on the inner side indicate that the case Each of the examples has cold bending and forming properties.
  • Example 1 is a metallographic structure of a base layer of a martensitic stainless steel rolled composite steel plate of Example 2. As can be seen from Fig. 1, the microstructure of the base layer of Example 2 was ferrite + pearlite.
  • Example 2 is a metallographic structure of a composite layer of a martensitic stainless steel rolled composite steel sheet of Example 2. As can be seen from FIG. 2, the microstructure of the martensitic stainless steel composite layer of Example 2 is martensite.
  • FIG. 3 is a metallographic structure of a transition layer of a martensitic stainless steel rolled composite steel plate of Example 3.
  • FIG. 3 there is a transition layer at the junction of the base layer of Example 3 and the martensitic stainless steel composite layer, the transition layer having a thickness of ⁇ 200 ⁇ m.
  • Fig. 4 is a further enlarged view showing the metallographic structure of the transition layer of the martensitic stainless steel rolled composite steel sheet of Example 3.
  • the microstructure of the transition layer of Example 3 is ferrite + carbide.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
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Abstract

一种马氏体不锈钢轧制复合钢板，包括基层和轧制复合于基层上的马氏体不锈钢复层；所述基层的化学元素质量百分比为：C：0.1-0.2％、0＜Si≤0.35％、Mn：0.5-1.5％、Al：0.02-0.04％、Ti：0.005-0.018％、Nb：0.005-0.020％、N≤0.006％，余量为铁和其他不可避免杂质。相应地，还公开了一种上述的马氏体不锈钢轧制复合钢板的制造方法。上述的马氏体不锈钢轧制复合钢板，其基层屈服强度≥235MPa，延伸率A50≥18％，0℃夏比冲击功Akv≥100J，马氏体不锈钢轧制复合钢板的剪切强度≥85MPa。

Description

一种马氏体不锈钢轧制复合钢板及其制造方法 技术领域
本发明涉及一种复合板及其制造方法，尤其涉及一种轧制复合钢板及其制造方法。
背景技术
马氏体不锈钢复合钢板作为一种重要的钢铁材料，其独特的兼具不锈钢耐蚀性能和碳钢力学性能的综合性能优势，使之被广泛应用于冶金、矿山机械、水电站等行业。随着我国工业的飞速发展以及各类军用及民用对设备的使用寿命的要求提升，以及生产及使用过程的对绿色环保超低碳排放的要求，使得对复合板的性能要求也随之提高。
现有技术中，复合钢板通常采用传统的机械复合和爆炸复合，上述两种工艺在控制复合板复层和基层性能的时候能够分开控制，然后再将其组合在一起。即在复合前可以分别将不锈钢和碳钢的各自所要求的性能处理到合适的状态，再施以机械复合力或爆炸冲击力使之合二为一，获得复合板。但是这两种复合方法各有各的缺点。例如：机械复合的复合板其不锈钢复层和碳钢基层中间没有完整的冶金结合，只是通过机械的力贴在一起，使用过程中复合界面容易开裂、脱落，失效快；爆炸复合的缺点是其本身工艺方法对工艺环境要求较为严格，需要在深山老林，环境人烟稀少的地方执行，此外，爆炸时产生的噪音、震动和冲击波对周边环境影响极大，在环境意识崛起的当前时期，这种工艺方法受环境条件因素限制较大。另外，爆炸复合生产的复合板其复合界面的剪切强度较低。
发明内容
本发明的目的之一在于提供一种马氏体不锈钢轧制复合钢板，所述的马氏体不锈钢轧制复合钢板具有硬度高、力学性能好以及一定的冷弯及成型性能。
为了实现上述目的，本发明提出了一种马氏体不锈钢轧制复合钢板，其包括基层和轧制复合于基层上的马氏体不锈钢复层；所述基层的化学元素质量百分比为：
C：0.1～0.2％、0＜Si≤0.35％、Mn：0.5～1.5％、Al：0.02～0.04％、Ti：0.005～0.018％、Nb：0.005～0.020％、N≤0.006％，余量为铁和其他不可避免杂质。
对于马氏体不锈钢复层可采用本领域内技术人员所知晓的马氏体不锈钢，例如：30Cr13、20Cr13、40Cr13以及其它类型的马氏体不锈钢。
C：碳是钢中重要的合金元素。碳含量的提高能使钢板的强度和硬度得到提升，但质量百分比过高的碳也会导致钢板的塑性韧性下降，影响钢板的焊接性能。在本发明所述的技术方案中，考虑碳对基层钢板性能的影响以及轧制复合时避免马氏体不锈钢复层的碳向基层的扩散迁移，因而，适当提高基层的碳含量，其质量百分比限定在0.1-0.2％，以保证马氏体不锈钢轧制复合钢板获得高强度和硬度。
Si：钢中添加硅能提高钢的纯净度，并且Si能起到脱氧的作用。此外，硅在钢中起固溶强化作用，但过量的硅不利于焊接性能。由于马氏体不锈钢复层内也具有硅，故对于基层中硅的质量百分比限定在0＜Si≤0.35％，有利于降低其对马氏体不锈钢复层耐腐蚀性的影响，同时也能够保证基层的良好的焊接性能。
Mn：在本发明所述的技术方案中，锰起到强化合金元素，同时锰增加钢的淬透性，降低马氏体形成的临界冷速。另外，锰有利于提高钢的强度级别。考虑到过量的锰具有较高的偏析倾向，因而本发明所述的马氏体不锈钢轧制复合钢板的基层对锰的质量百分比限定在0.5～1.5％。
为了进一步提高本发明所述的马氏体不锈钢轧制复合钢板的，本发明所述的马氏体不锈钢轧制复合钢板的Mn更为优选范围为：0.8-1.2％。
Al：Al在本发明所述的技术方案中，Al为强脱氧元素，用于降低钢中的氧的质量百分比。本发明所述的技术方案中控制铝的质量百分比在0.02～0.04％，是因为脱氧后铝会和氮元素能形成AlN析出物，有利于提高钢强度并且起到细化晶粒的作用。
Ti：钛是强碳化物形成元素，钢中加入微量的Ti有利于固定钢中的N，形成的TiN，抑制晶粒过分长大，起到细化晶粒的作用。此外，钛在钢中还可分别与碳和硫化合生成TiC、TiS、Ti4C2S2，上述化合物以夹杂物和第二相粒子的形式存在。钛上述碳氮化物析出物在焊接时还可阻止热影响区晶粒长大，改善焊接性能。因此，在本发明所述的马氏体不锈钢轧制复合钢板的基层对Ti的质量百分比控制在Ti：0.005～0.018％。
Nb：铌是强碳化物形成元素，在基层中添加铌有利于提高再结晶温度，从而起到晶粒细化作用，有利于基层的低温冲击韧性的提高。因此，在本发明所述的马氏体不锈钢轧制复合钢板的基层中对铌的质量百分比控制在0.005～0.020％。
N：N是奥氏体稳定化元素，其在基层中是作为炼钢气体元素的残留余量，因而，在本发明所述的马氏体不锈钢轧制复合钢板中对N的质量百分比控制在N≤0.006％。
此外，在本发明所述的马氏体不锈钢轧制复合钢板中，不可避免的杂质主要是S和P元素，因而需要控制基层中P≤0.015％，S≤0.010％。
进一步地，本发明所述的马氏体不锈钢轧制复合钢板中，所述基板还含有Ni、Cr和Mo元素的至少其中之一，其中Ni≤0.20％、Cr≤0.20％、Mo≤0.10％。
为了进一步提高本发明所述的马氏体不锈钢轧制复合钢板的实施效果，可以添加Ni、Cr和Mo元素的至少其中之一，这是因为：
Ni：在本发明所述的马氏体不锈钢轧制复合钢板中添加Ni，有利于稳定奥氏体，并且有利于提高钢的强度。钢中添加Ni能大幅提高钢的低温冲击韧性。但由于镍属于贵重合金元素，添加过多将提高生产成本。对于马氏体不锈钢轧制复合板而言，适量添加Ni有利于提高基层的低温冲击韧性，因此，本发明所述的马氏体不锈钢轧制复合钢板对Ni的质量百分比控制在Ni≤0.20％。
Cr：由于铬的偏析倾向相较于锰小，因而，当基层的钢中有明显的偏析带及带状组织的时候，通过添加铬来改善钢的性能。其次，基层添加铬也有利于抑制马氏体不锈钢复层的铬向基层的扩散。鉴于此，本发明所述的马氏体不锈钢轧制复合钢板对Cr的质量百分比限定在Cr≤0.20％。
Mo：钼有利于细化晶粒，提高钢的强度和韧性。此外，钼能减少钢的回火脆性，同时回火时还能析出非常细小的碳化物，有利于强化钢的基层基体。另外，钼的添加有利于抑制马氏体不锈钢轧制复合钢板产生的自回火脆性。因此，本发明所述的马氏体不锈钢轧制复合钢板中对钼的质量百分比限定在Mo≤0.10％。
进一步地，本发明所述的马氏体不锈钢轧制复合钢板中，所述马氏体不锈钢复层的微观组织全部为马氏体或马氏体+少量碳化物，其中碳化物的相比例不超过2％。
进一步地，本发明所述的马氏体不锈钢轧制复合钢板中，所述基层的微观组织为铁素体+珠光体。
进一步地，本发明所述的马氏体不锈钢轧制复合钢板中，在基层和马氏体不锈钢复层的结合处具有过渡层，所述过渡层的厚度≤200μm。
在本发明所述的马氏体不锈钢轧制复合钢板中，由于位于基层和马氏体不锈钢复层中各元素的质量百分比不同，导致质量百分比高的元素会向质量百分比低的一侧扩散，进而使得结合处的元素的质量百分比呈梯度分布，形成过渡层。
进一步地，本发明所述的马氏体不锈钢轧制复合钢板中，所述过渡层的微观组织为铁素体+碳化物。
进一步地，本发明如所述的马氏体不锈钢轧制复合钢板中，其基层屈服强度≥235MPa，延伸率A50≥18％，0℃夏比冲击功Akv≥100J，马氏体不锈钢复合钢板剪切强度≥385MPa。
相应地，本发明的另一目的还在于提供一种可用于制造上述马氏体不锈钢轧制复合钢板的制造方法，采用该制造方法的马氏体不锈钢轧制复合钢板具有高强度、一定的冷弯和成型性能。
为了达到上述发明目的，本发明还提出了一种上述马氏体不锈钢轧制复合钢板的制造方法，包括步骤：
(1)制得基板板坯和复层不锈钢板坯；
(2)将至少一层基板板坯和至少一层复层板坯进行组坯；
(3)复合轧制：先将复合坯在1100～1180℃的温度下加热，然后进行多道次轧制，控制总压下率不低于70％，终轧温度不低于900℃；
(4)复合板热矫直；
(5)复合板送冷床单张空冷，下冷床后单张空冷终冷温度≤80℃以完成马氏体相变。
在本发明所述的制造方法中，通过将基板板坯与复层不锈钢板坯轧制复合，使得轧制后所获得马氏体不锈钢轧制复合钢板既具有良好的力学性能，又具有较好的焊接性能。
为了提高复合效果，在基板板坯和复层板坯组坯前，对基板板坯与复层板坯需要复合的板坯表面进行预处理，去除需要复合的表面的氧化物。在本发明所述的制造方法中，对于组坯的层数，本领域内技术人员可以根据各实施方式的具体情况进行设置，例如：设置组坯层数为两层，一层为基板板坯，另一层为复层板坯；又例如：设置组坯层数为四层，基板板坯为两层，复层板坯为两层，其中将两层马氏体不锈钢复层板坯复合时位于复合坯上下表面，基层板坯位于复合坯中间。在一些优选的实施方式中，基层板坯与基层板坯的层间铺设分离剂层。此外，在另一些优选实施方式中，基层与复层的结合界面抽真空。
为了保证马氏体不锈钢复层充分完成马氏体相变，使得本发明所述的马氏体不锈钢钢板的硬度较高，在步骤(5)中，单张钢板不允许堆垛，直至单张空冷终冷温度≤80℃。
此外，需要说明的是，步骤(5)获得的复合板不可以冷矫，但可以采用压平，以防止马氏体不锈钢复层开裂。此外，压平时，可以对板坯组合层数多的复合板在厚度方向上分离成子板后进行压平，以提高压平效果，例如，板坯组合层数为4层时，可在压平前进行切边分离成厚度方向上两块复合板子板后进行压平，以提高压平效果。
进一步地，本发明所述的制造方法，在所述步骤(4)中，热矫直停矫温度≥550℃。
进一步地，本发明所述的制造方法，在所述步骤(3)中，终轧温度为920～1000℃。
本发明所述的马氏体不锈钢轧制复合钢板通过优化成分设计和工艺参数控制，使得所 获的马氏体不锈钢轧制复合钢板其基层屈服强度≥235MPa，延伸率A50≥18％，0℃夏比冲击功Akv≥100J，马氏体不锈钢复合钢板剪切强度≥385MPa。
此外，本发明所述的制造方法通过将基板与复层板坯的复合轧制，使得复合钢板既具有优良的力学性能，又具有较高的硬度和一定的冷弯及成型性能。
附图说明
图1为实施例2的马氏体不锈钢轧制复合钢板的基层的金相组织。
图2为实施例2的马氏体不锈钢轧制复合钢板的复层的金相组织。
图3为实施例3的马氏体不锈钢轧制复合钢板的过渡层的金相组织。
图4为实施例3的马氏体不锈钢轧制复合钢板过渡层的金相组织放大图。
具体实施方式
下面将结合说明书附图和具体的实施例对本发明所述的马氏体不锈钢轧制复合钢板及其制造方法做进一步的解释和说明，然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例1-9
表1列出了实施例1-9的马氏体不锈钢轧制复合钢板的各坯层的化学元素的质量百分比。
表1.(wt％，余量为Fe和除了P、S以外其他不可避免的杂质)
Figure PCTCN2017113115-appb-000001
Figure PCTCN2017113115-appb-000002
实施例1-9的马氏体不锈钢轧制复合钢板的制造方法采用以下步骤制得(各实施例中的具体工艺参数参见表2)：
(1)按照表1所列的各坯层的质量百分配比制得基板板坯和复层不锈钢板坯；
(2)将至少一层基板板坯和至少一层复层板坯进行组坯；
(3)复合轧制：先将复合坯在1100～1180℃的温度下加热，然后进行多道次轧制，终轧温度不低于900℃；
(4)复合板热矫直：热矫直停矫温度≥550℃；
(5)复合板送冷床单张空冷，下冷床后单张空冷终冷温度≤80℃以完成马氏体相变。
需要说明的是，基板板坯形成各实施例的马氏体不锈钢轧制复合钢板的基层，复层不锈钢板坯则形成各实施例的马氏体不锈钢轧制复合钢板的马氏体不锈钢复层。
表2列出了实施例1-9的马氏体不锈钢轧制复合钢板的制造方法的具体工艺参数。
表2.
Figure PCTCN2017113115-appb-000003
Figure PCTCN2017113115-appb-000004
表3列出了实施例1-9的马氏体不锈钢轧制复合钢板各项性能测试的测试结果。
表3.
Figure PCTCN2017113115-appb-000005
由表3可以看出，各实施例其基层屈服强度≥235MPa，马氏体不锈钢轧制复合钢板剪切强度≥385MPa，其中基层硬度高于110HB，马氏体不锈钢复层的硬度高于48HRC，说明各实施例的力学性能良好。此外，各实施例的延伸率A50≥18％，0℃夏比冲击功Akv≥100J，说明本案实施例1-9的基层钢板韧性优良，并且复层在内侧的内弯性能测试的结果表明本案各实施例具备冷弯和成型性能。
图1为实施例2的马氏体不锈钢轧制复合钢板的基层的金相组织。从图1可以看出，实施例2的基层的微观组织为铁素体+珠光体。
图2为实施例2的马氏体不锈钢轧制复合钢板的复层的金相组织。从图2可以看出，实施例2的马氏体不锈钢复层的微观组织为马氏体。
图3为实施例3的马氏体不锈钢轧制复合钢板的过渡层的金相组织。从图3可以看出，在实施例3的基层和马氏体不锈钢复层的结合处具有过渡层，所述过渡层的厚度≤200μm。
图4进一步放大显示了实施例3的马氏体不锈钢轧制复合钢板过渡层的金相组织。从图4可以看出，实施例3的过渡层的微观组织为铁素体+碳化物。
需要注意的是，以上列举的仅为本发明的具体实施例，显然本发明不限于以上实施例，随之有着许多的类似变化。本领域的技术人员如果从本发明公开的内容直接导出或联想到的所有变形，均应属于本发明的保护范围。

Claims (10)

  1. 一种马氏体不锈钢轧制复合钢板，其特征在于，包括基层和轧制复合于基层上的马氏体不锈钢复层；所述基层的化学元素质量百分比为：
    C：0.1～0.2％、0＜Si≤0.35％、Mn：0.5～1.5％、Al：0.02～0.04％、Ti：0.005～0.018％、Nb：0.005～0.020％、N≤0.006％，余量为铁和其他不可避免杂质。
  2. 如权利要求1所述的马氏体不锈钢轧制复合钢板，其特征在于，所述基层还含有Ni、Cr和Mo元素的至少其中之一，其中Ni≤0.20％、Cr≤0.20％、Mo≤0.10％。
  3. 如权利要求1所述的马氏体不锈钢轧制复合钢板，其特征在于，所述马氏体不锈钢复层的微观组织全部为马氏体或马氏体+少量碳化物，其中碳化物的相比例不超过2％。
  4. 如权利要求1所述的马氏体不锈钢轧制复合钢板，其特征在于，所述基层的微观组织为铁素体+珠光体。
  5. 如权利要求1所述的马氏体不锈钢轧制复合钢板，其特征在于，在基层和马氏体不锈钢复层的结合处具有过渡层，所述过渡层的厚度≤200μm。
  6. 如权利要求5所述的马氏体不锈钢轧制复合钢板，其特征在于，所述过渡层的微观组织为铁素体+碳化物。
  7. 如权利要求1-6中任意一项所述的马氏体不锈钢轧制复合钢板，其基层屈服强度≥235MPa，延伸率A50≥18％，0℃夏比冲击功Akv≥100J，马氏体不锈钢轧制复合钢板的剪切强度≥385MPa。
  8. 如权利要求1-7中任意一项所述的马氏体不锈钢轧制复合钢板的制造方法，其特征在于，包括步骤：
    (1)制得基板板坯和复层不锈钢板坯；
    (2)将至少一层基板板坯和至少一层复层板坯进行组坯；
    (3)复合轧制：先将复合坯在1100～1180℃的温度下加热，然后进行多道次轧制，
    终轧温度不低于900℃；
    (4)复合板热矫直；
    (5)复合板送冷床单张空冷，下冷床后单张空冷终冷温度≤80℃以完成马氏体相变。
  9. 如权利要求8所述的制造方法，其特征在于，在所述步骤(4)中，热矫直停矫温度≥550℃。
  10. 如权利要求8所述的制造方法，其特征在于，在所述步骤(3)中，终轧温度为920～1000℃。
PCT/CN2017/113115 2016-11-30 2017-11-27 一种马氏体不锈钢轧制复合钢板及其制造方法 WO2018099347A1 (zh)

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