WO2023078299A1 - 一种高强高硬增强型耐磨钢及其制造方法 - Google Patents

一种高强高硬增强型耐磨钢及其制造方法 Download PDF

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WO2023078299A1
WO2023078299A1 PCT/CN2022/129272 CN2022129272W WO2023078299A1 WO 2023078299 A1 WO2023078299 A1 WO 2023078299A1 CN 2022129272 W CN2022129272 W CN 2022129272W WO 2023078299 A1 WO2023078299 A1 WO 2023078299A1
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strength
resistant steel
hardness
enhanced wear
temperature
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PCT/CN2022/129272
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English (en)
French (fr)
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李红斌
丁建华
刘自成
吴扣根
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宝山钢铁股份有限公司
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Priority to AU2022382748A priority Critical patent/AU2022382748A1/en
Priority to CA3236848A priority patent/CA3236848A1/en
Publication of WO2023078299A1 publication Critical patent/WO2023078299A1/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
    • 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
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    • 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
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    • 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
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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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • 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
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    • 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
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    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the invention relates to a steel material and a manufacturing method thereof, in particular to a wear-resistant steel and a manufacturing method thereof.
  • Wear-resistant steel has the characteristics of high strength and high wear resistance, and its performance is quite excellent. It can be effectively used in fields such as mining, agriculture, cement production, ports, electric power, and metallurgy to manufacture such as bulldozers, loaders, excavators, and automatics. Mechanical products such as unloading trucks, grabs, stackers and reclaimers have broad application prospects.
  • wear-resistant steel In recent years, the development and application of wear-resistant steel has developed rapidly. At present, the most widely used is martensitic wear-resistant steel. This type of wear-resistant steel is generally increased by increasing the carbon content and adding an appropriate amount of alloying elements, such as chromium. , molybdenum, nickel, vanadium, boron, etc., make full use of methods such as phase transformation strengthening after heat treatment to improve the mechanical properties of wear-resistant steel.
  • alloying elements such as chromium. , molybdenum, nickel, vanadium, boron, etc.
  • the present invention expects to obtain a new high-strength and high-hardness enhanced wear-resistant steel, which is lower in strength and hardness than the existing traditional ultra-high-strength hardness wear-resistant steel plate , which will bring greater convenience to users in mechanical processing; in actual use, the high-strength and high-hardness enhanced wear-resistant steel is prone to plastic-induced phase transformation, which can significantly improve the strength and hardness of the steel plate, thereby improving the wear resistance of the steel plate; through This effect can make the mechanical performance and wear resistance of the high-strength and high-hardness enhanced wear-resistant steel plate described in the present invention higher than that of the wear-resistant steel plate of the same hardness level in actual use.
  • One of the objectives of the present invention is to provide a high-strength, high-hardness enhanced wear-resistant steel, which has excellent mechanical properties, and also has excellent machinability, thermal stability and welding performance , which realizes the matching of high strength hardness and high toughness, has excellent machinability, and has excellent mechanical properties and good wear resistance in actual use, and has very good promotion prospects and application value.
  • the high-strength and high-hardness enhanced wear-resistant steel involved in the present invention is easy to process, which not only provides convenience for conventional mechanical processing, but also can obtain excellent strength, toughness and wear resistance through plasticity-induced phase transformation during use, It has excellent performance and can be popularized and applied in wear-resistant parts of construction machinery.
  • the present invention provides a high-strength and high-hardness enhanced wear-resistant steel, which contains Fe and unavoidable impurities, and it also contains the following chemical elements in mass percentage:
  • the mass percentage of each chemical element is:
  • the high-strength and high-hardness enhanced wear-resistant steel of the present invention is mainly based on the addition of C, Si elements and Mn, Cr alloy elements, and can be appropriately added Mo, Ni and other precious metal elements as required, which can control the cost of the alloy At the same time, ensure the performance of steel.
  • C In the high-strength and high-hardness enhanced wear-resistant steel described in the present invention, C is the most basic and most important element in the wear-resistant steel. Adding an appropriate amount of C element can increase the strength and hardness of the steel, and then improve the resistance of the steel. Abrasive. However, it should be noted that the C element will also have an adverse effect on the toughness and weldability of the steel. Therefore, the content of the C element in the steel needs to be reasonably controlled.
  • the mass percentage of C element is controlled between 0.22% and 0.33%, which can be further preferably 0.23-0.28%. In some embodiments, the mass percentage of C is 0.22-0.31%. In some embodiments, the mass percentage of C is 0.23-0.31%. In some embodiments, the mass percentage of C is 0.23-0.30%.
  • Si In the high-strength and high-hardness enhanced wear-resistant steel described in the present invention, Si can be dissolved in ferrite and austenite, thereby improving their hardness and strength. However, when the content of Si element is too high, it will also This leads to a sharp drop in the toughness of the steel. At the same time, considering that the affinity between Si and O is stronger than that of Fe, it is easy to produce silicate with a low melting point during welding, which increases the fluidity of slag and molten metal and affects the quality of the weld. Therefore, the content of Si in steel should not be excessive.
  • the mass percentage of Si element is controlled between 0.10% and 1.00%. In some embodiments, the mass percentage of Si is 0.10-0.80%. In some embodiments, the mass percentage of Si is 0.15-0.80%. In some embodiments, the mass percentage of Si is 0.15-0.65%.
  • Mn In the high-strength and high-hardness enhanced wear-resistant steel of the present invention, adding an appropriate amount of Mn element can strongly increase the hardenability of the steel, reduce the transformation temperature of the steel and the critical cooling rate of the steel.
  • the content of Mn element in the steel should not be too high. When the content of Mn element in the steel is too high, it will not only tend to coarsen the grain, but also increase the temper embrittlement sensitivity of the steel, and it is easy to cause Segregation and cracks appear in the slab, reducing the performance of the steel plate.
  • the mass percentage of the Mn element is controlled between 0.50-1.80%, preferably 1.05-1.65%. In some embodiments, the mass percentage of Mn is 1.00 ⁇ 1.80%. In some embodiments, the mass percentage of Mn is 1.10-1.80%. In some embodiments, the mass percentage of Mn is 1.10-1.80%. In some embodiments, the mass percentage of Mn is 1.15-1.80%. In some embodiments, the mass percentage of Mn is 0.65-1.65%.
  • the Cr element can reduce the critical cooling rate and improve the hardenability of the steel.
  • Cr can form various carbides such as (Fe, Cr) 3 C, (Fe, Cr) 7 C 3 and (Fe, Cr) 23 C 7 in steel, which can effectively improve the strength and hardness of steel.
  • adding an appropriate amount of Cr to the steel can prevent or slow down the precipitation and aggregation of carbides during tempering, thereby improving the tempering stability of the steel.
  • the mass percentage of the Cr element can be controlled between 0.80% and 2.30%, and can be further preferably 1.25-2.10%. %. In some embodiments, the mass percentage of Cr is 1.10-2.20%. In some embodiments, the mass percentage of Cr is 1.10-2.00%. In some embodiments, the mass percentage of Cr is 1.15-2.00%. In some embodiments, the mass percentage of Cr is 0.95-2.10%.
  • the Al element can form fine and insoluble AlN particles with the N element in the steel, and refine the grains of the steel. Adding an appropriate amount of Al to steel can effectively refine the grains of the steel, fix N and O in the steel, reduce the sensitivity of the steel to notches, reduce or eliminate the aging phenomenon of the steel, and improve the toughness of the steel.
  • the mass percentage of the Al element is controlled between 0.010-0.10%, and can be further preferably 0.035-0.080%. In some embodiments, the mass percentage of Al is 0.010-0.080%. In some embodiments, the mass percentage of Al is 0.015-0.075%. In some embodiments, the mass percentage of Al is 0.015-0.070%. In some embodiments, the mass percentage of Al is 0.025-0.080%.
  • rare earth can reduce the segregation of elements such as sulfur and phosphorus, improve the shape, size and distribution of non-metallic inclusions, and refine the grains at the same time , to increase hardness.
  • rare earth can also increase the yield ratio, which is beneficial to improve the toughness of low-alloy high-strength steel, and can improve the thermal stability of the steel plate.
  • the content of rare earth in steel should not be too much, otherwise severe segregation will occur, thereby reducing the quality and mechanical properties of the billet.
  • the mass percentage of RE is controlled between 0.01-0.10%, and can be further preferably 0.03-0.10%. In some embodiments, the mass percentage of RE is 0.025-0.080%.
  • tungsten can increase the tempering stability and thermal strength of the steel, and can also play a certain role in refining grains.
  • tungsten can also form hard carbides to increase the wear resistance of steel. Therefore, in order to exert the beneficial effect of tungsten, in the high-strength and high-hardness enhanced wear-resistant steel of the present invention, the mass percentage of W element is controlled between 0.01-1.0%, and can be more preferably 0.05-0.85%. In some embodiments, the mass percentage of W is 0.05-0.85%.
  • Mo in the high-strength and high-hardness enhanced wear-resistant steel described in the present invention, adding an appropriate amount of Mo can effectively refine the grains and improve the strength and toughness of the steel. Mo exists in solid solution phase and carbide phase in steel, therefore, Mo-containing steel has the functions of solid solution strengthening and carbide dispersion strengthening at the same time. In addition, Mo is also an element that reduces temper brittleness. Adding an appropriate amount of Mo element to steel can also improve the temper stability of the material. Based on this, in the high-strength and high-hardness enhanced wear-resistant steel of the present invention, when added, the mass percentage of Mo element is controlled between 0.01-0.80%, preferably between 0.08-0.55%.
  • Ni and Fe can be miscible in any proportion, which can improve the low-temperature toughness of the steel by refining ferrite grains, and has the ability to significantly reduce the cold-brittle transition The role of temperature.
  • the content of Ni element in the steel should not be too high.
  • the mass percentage of Ni element is controlled between 0.01-1.00%, preferably between 0.25-0.85%.
  • Nb In the high-strength and high-hardness enhanced wear-resistant steel described in the present invention, adding an appropriate amount of Nb element can play the role of refining grain and precipitation strengthening, and its contribution to improving the strength and toughness of the material is extremely significant; Nb element through The effect of grain refinement can effectively improve the strength and toughness of steel, and it can also improve and improve the performance of steel through precipitation strengthening and phase transformation strengthening. Nb has become one of the most effective strengthening agents in high-strength low-alloy structural steel ; In addition, Nb is also a strong C and Ni oxide forming element, which can strongly inhibit the growth of austenite grains. Based on this, in the high-strength and high-hardness enhanced wear-resistant steel of the present invention, when added, the mass percentage of Nb element is controlled between 0.005-0.080%, preferably between 0.01-0.045%.
  • V In the high-strength and high-hardness enhanced wear-resistant steel described in the present invention, adding an appropriate amount of V element can effectively refine the grains, so that the austenite grains will not grow too thick during the heating stage of the billet. In the subsequent multi-pass rolling process, the grains of the steel can be further refined, thereby improving the strength and toughness of the steel. Based on this, in the high-strength and high-hardness enhanced wear-resistant steel of the present invention, when added, the mass percentage of V element is controlled between 0.01-0.20%, preferably 0.03-0.15%.
  • Ti is one of the strong carbide-forming elements, and Ti element can be combined with C element to form fine TiC particles.
  • the TiC particles are fine, which can be distributed in the grain boundaries, so as to achieve the effect of refining the grains; in addition, the TiC particles are relatively hard, which can improve the wear resistance of the steel.
  • the mass percentage of Ti element is controlled between 0.001% and 0.50%, preferably between 0.015% and Between 0.45%.
  • the mass percentage of each chemical element in the high-strength and high-hardness enhanced wear-resistant steel described in the present invention satisfies: C: 0.22-0.31%, Si: 0.10-0.80%, Mn: 1.00-1.80%, Cr: 1.10- 2.20%, Al: 0.010-0.080%.
  • the mass percentages of the chemical elements in the high-strength and high-hardness enhanced wear-resistant steel of the present invention satisfy: C: 0.23-0.31%, Si: 0.15-0.80%, Mn: 1.10-1.80%, Cr: 1.10 ⁇ 2.00%, Al: 0.015 ⁇ 0.075%.
  • the mass percentage of each chemical element in the high-strength and high-hardness enhanced wear-resistant steel described in the present invention satisfies: C: 0.23-0.30%, Si: 0.15-0.65%, Mn: 1.15-1.80%, Cr: 1.15- 2.00%, Al: 0.015-0.070%.
  • both P and S are unavoidable impurity elements.
  • the lower the content of the impurity elements in the steel the better, if conditions permit.
  • Both P and S are harmful elements, and their content should be strictly controlled. Therefore, in the high-strength and high-hardness enhanced wear-resistant steel described in the present invention, the inevitable impurity elements can be controlled to satisfy: P ⁇ 0.030%, and/or S ⁇ 0.010%.
  • the volume fraction of retained austenite is equal to or greater than 5%, and the volume fraction of martensite is equal to or less than 90%.
  • the volume fraction of retained austenite is 5-15%, and the volume fraction of martensite is 65-90%.
  • the volume fraction of retained austenite is 5.3-12.0%, such as 5.5-8.5%, and the volume fraction of martensite is 70-88%. , such as 77.5-85.6%.
  • the microstructure of the high-strength, high-hardness enhanced wear-resistant steel described in the present invention is different from the more common martensite structure, which forms martensite + bainite + Microstructure of retained austenite + carbide.
  • the mechanical properties of the high-strength, high-hardness enhanced wear-resistant steel described in the present invention can be ensured.
  • the strength and hardness of the high-strength, high-hardness enhanced wear-resistant steel is slightly lower, which will bring greater convenience to the user's mechanical processing , suitable for easy processing conditions.
  • the wear resistance of the high-strength, high-hardness enhanced wear-resistant steel described in the present invention is very excellent, which is mainly due to the TRIP (transition-induced plasticity) effect occurring in the use process, that is: due to the In addition to a certain amount of martensite or bainite, the steel plate also contains a certain proportion of austenite, which makes the steel plate undergo plastic-induced phase transformation when it is impacted, pressed, or worn during use, which can significantly improve the toughness of the steel plate degree, thereby improving the wear resistance of the steel plate.
  • the mechanical properties and wear resistance of the high-strength and high-hardness enhanced wear-resistant steel plate described in the present invention are actually higher than those of conventional wear-resistant steel plates of the same hardness level during actual use.
  • the Brinell hardness is 400-500HBW
  • its tensile strength is 1200-1600MPa (such as 1300-1600MPa)
  • its elongation is 10-15%.
  • the Charpy V-type longitudinal impact energy at -40°C is >40J.
  • the Brinell hardness of the high-strength and high-hardness enhanced wear-resistant steel described in the present invention is 420-480HBW
  • the tensile strength is 1220-1450MPa
  • the elongation is 10-15%
  • the summer temperature at -40°C is
  • the specific V-shaped longitudinal impact energy is >40J, such as 41 ⁇ 60J.
  • the yield strength of the high-strength, high-hardness enhanced wear-resistant steel of the present invention is 800-1000 MPa, such as 830-980 MPa.
  • the yield ratio of the high-strength, high-hardness enhanced wear-resistant steel of the present invention is ⁇ 0.75, preferably ⁇ 0.70.
  • the measured Brinell hardness on the surface of the steel plate has an increase of more than 10% compared with the Brinell hardness of the steel plate before the test, Preferably there is an increase of 13% or more.
  • the surface Brinell hardness of the steel plate is measured to be ⁇ 480HBW, such as 480-560HBW.
  • another object of the present invention is to provide a method for manufacturing high-strength, high-hardness enhanced wear-resistant steel.
  • the process of the manufacturing method is simple and feasible.
  • the performance is very excellent, its Brinell hardness is 400-500HBW, the tensile strength is 1200-1600MPa (such as 1300-1600MPa), the elongation is 10-15%, and the Charpy V-type longitudinal impact energy at -40°C is > 40J. It has very good promotion prospect and application value.
  • the present invention proposes a method for manufacturing the above-mentioned high-strength and high-hardness enhanced wear-resistant steel, which includes the steps of:
  • the initial cooling temperature is: (Ar3'+5) ⁇ (Ar3'+50)°C, M 90 ⁇ final cooling temperature ⁇ Bs, cooling speed is 2 ⁇ 15°C/s; then Air cool to room temperature.
  • each smelting raw material is added according to the chemical composition ratio designed by the inventor, and then undergoes the steps of smelting, casting, heating, rolling and on-line quenching in sequence, The high-strength and high-hardness enhanced wear-resistant steel can be obtained.
  • water cooling or oil cooling can be used for the primary cooling.
  • Ar3' represents the temperature at which austenite begins to transform into ferrite during online quenching of steel; Bs represents the temperature at which bainite begins to transform; M90 represents the temperature at which the volume ratio of martensite is 90% .
  • the heating temperature for making the slab is 1030-1230° C., and the temperature is kept for 1-3 hours. In some embodiments, the heating temperature for making the slab is 1050-1210° C., and the temperature is kept for 1-3 hours.
  • step (2) the heating temperature of the slab is controlled to be 1030-1180°C.
  • the heating temperature can be controlled to be 1030-1160° C.; in order to improve production efficiency and prevent excessive growth of austenite grains and severe oxidation of the billet surface, it is most preferable to control
  • the heating temperature is 1030-1140°C.
  • step (3) the rough rolling temperature is controlled to be 930-1180°C, and the finish rolling temperature is controlled to be 870-970°C. In some embodiments, in step (3), the rough rolling temperature is controlled to be 950-1150°C, and the finish rolling temperature is controlled to be 885-955°C.
  • step (3) the rough rolling temperature is controlled to be 930-1130°C, and the finish rolling temperature is controlled to be 875-945°C.
  • step (3) the rolling reduction in the rough rolling stage is controlled to be greater than 35%, and the rolling reduction in the finish rolling stage is controlled to be greater than 55%. Further, in the manufacturing method of the present invention, in step (3), the rolling reduction in the rough rolling stage is controlled to be 35-75%, and the rolling reduction in the finish rolling stage is controlled to be 55-80%.
  • the present invention can further preferably control the rough rolling temperature to be 930-1110°C, control the rolling reduction in the rough rolling stage to be greater than or equal to 38%, and control the finishing rolling temperature It is 875-935°C, and the rolling reduction in the finishing rolling stage is controlled to be greater than or equal to 58%.
  • the rough rolling temperature in the rolling process of step (3) can be controlled to be 935-1105°C
  • the rolling reduction rate in the rough rolling stage is controlled to be greater than 40%
  • the finish rolling temperature is controlled to be 875-930°C
  • the finishing rolling temperature is controlled to be 875-930°C.
  • the rolling reduction in the rolling stage is greater than 60%.
  • the initial cooling temperature is: (Ar3'+5) ⁇ (Ar3'+45)°C, (M 90 +5°C) ⁇ Final cooling temperature ⁇ (B s -15°C), the cooling rate is 2 ⁇ 12°C/s.
  • the initial cooling temperature can be controlled to be: (Ar3'+5) ⁇ (Ar3'+40)°C
  • the final cooling temperature should be controlled to satisfy: (M 90 +5°C) ⁇
  • the final cooling temperature is ⁇ (B s -20°C), and the cooling rate is controlled to be 2-11°C/s.
  • the initial cooling temperature can be controlled to be: (Ar3'+5) ⁇ (Ar3'+38)°C
  • the final cooling temperature can be controlled to satisfy: (M 90 +5°C) ⁇ final cooling temperature ⁇ (B s - 23°C), and control the cooling rate to 3-11°C/s.
  • the final cooling temperature is controlled to be 350-450°C.
  • the thickness of the high-strength and high-hardness enhanced wear-resistant steel of the present invention is 9-25mm.
  • the high-strength and high-hardness enhanced wear-resistant steel and its manufacturing method according to the present invention have the following advantages and beneficial effects:
  • the high-strength and high-hardness enhanced wear-resistant steel described in the present invention fully optimizes the alloy composition, which is mainly based on the addition of C, Si elements and Mn, Cr alloy elements, and can be added as needed Appropriate addition of precious metal elements such as Mo and Ni can ensure the performance of the steel while controlling the cost of the alloy at a low level.
  • the high-strength and high-hardness enhanced wear-resistant steel of the present invention can obtain the microstructure of martensite+bainite+retained austenite+carbide (wherein the volume fraction of martensite ⁇ 90 %, retained austenite volume fraction > 5%, and the rest are bainite and carbides), resulting in the TRIP effect of the steel plate during use, improving the strength, hardness and wear resistance of the steel plate, thereby improving the practicability and use of the steel plate life.
  • a large number of uniformly distributed hard phases, such as carbides of Ti, Cr, Mo and W can further improve the wear resistance and service life of the steel plate.
  • the high-strength and high-hardness enhanced wear-resistant steel of the present invention is relatively lower in strength and hardness, which will bring greater convenience to users in machining, and is suitable for easy Processing conditions; in addition, due to the addition of RE and W elements, the high-strength and high-hardness enhanced wear-resistant steel of the present invention also has certain high temperature resistance, and the strength and hardness of the steel plate do not lose much at higher temperatures.
  • the present invention scientifically designs carbon, alloy components and their proportioning ratio under reasonable production process conditions, reduces alloy cost, and its production process is simple and feasible, which is beneficial to industrial production; correspondingly, the present invention
  • the high-strength and high-hardness enhanced wear-resistant steel has excellent mechanical properties (such as hardness, strength, elongation, impact toughness and certain high temperature resistance) and processing performance and usability.
  • Its Brinell hardness is 400-500HBW, tensile
  • the strength is 1200-1600MPa (such as 1300-1600MPa)
  • the elongation is 10-15%
  • the Charpy V-shaped longitudinal impact energy at -40°C is greater than 40J, which has very good promotion prospects and application value.
  • Figure 1 Microstructure photo of the high-strength and high-hardness enhanced wear-resistant steel prepared in Example 3.
  • the high-strength and high-hardness enhanced wear-resistant steels of Examples 1-8 are all prepared by the following steps:
  • Heating heating the obtained slab, controlling the heating temperature of the slab to 1030-1230°C, and keeping it warm for 1-3 hours; of course, the heating temperature of the slab can also be preferably controlled at 1030-1180°C.
  • the initial cooling temperature is: (Ar3'+5) ⁇ (Ar3'+50)°C, M 90 ⁇ final cooling temperature ⁇ Bs, cooling speed is 2 ⁇ 15°C/s, then air cooling to room temperature; of course, it is also preferable to control the initial cooling temperature to be: (Ar3'+5) ⁇ (Ar3'+45)°C, and it is preferable to control the final cooling temperature to satisfy: (M 90 +5°C) ⁇ final cooling temperature ⁇ (B s -15°C), and preferably control the cooling rate to be 2-12°C/s.
  • Table 1 lists the mass percent of each chemical element in the high-strength and high-hardness enhanced wear-resistant steel of Examples 1-8.
  • Table 2-1 and Table 2-2 list the specific process parameters of the high-strength and high-hardness enhanced wear-resistant steel of Examples 1-8 in each step of the above-mentioned manufacturing method.
  • Ar3' in Table 2-2 represents the temperature at which austenite begins to transform into ferrite during online quenching of the test steel; Bs represents the temperature at which bainite begins to transform; M 90 represents the volume ratio of martensite 90% temperature.
  • the high-strength, high-hardness enhanced wear-resistant steel samples of Examples 1-8 that were finally prepared were respectively sampled, and the high-strength, high-hardness enhanced wear-resistant steel samples of Examples 1-8 were observed and analyzed, and it was found that Examples 1-
  • the microstructure of the high-strength and high-hardness enhanced wear-resistant steel in 8 is martensite + bainite + retained austenite + carbide.
  • the photo of the metallographic structure of Example 3 is shown in FIG. 1 .
  • the volume fraction of retained austenite in the high-strength and high-hardness enhanced wear-resistant steel of Examples 1-8 is between 5.6% and 8.3%.
  • Tensile test SCL233200kN normal temperature tensile testing machine was used at room temperature, and the tensile performance test was carried out according to the GB/T 228.1 standard to measure the resistance of the high-strength and high-hardness enhanced wear-resistant steel samples of Examples 1-8 at room temperature. Tensile strength and elongation.
  • Brinell hardness test SCL246 Brinell hardness testing machine is used at room temperature, and the Brinell hardness test is carried out according to GB/T 231.1 standard. Hardness tests were performed on the surface positions of the high-strength and high-hardness enhanced wear-resistant steel samples of Examples 1-8, so as to obtain the Brinell hardness of the corresponding examples.
  • the steel plates of each embodiment can be hit with the same 550J impact energy by using self-made drop hammer equipment, and then the surface Brinell hardness of the steel plates can be measured , to obtain enhanced Brinell hardness.
  • Impact test SCL186750J instrumented impact testing machine is used at -40°C, and the impact performance test is carried out according to the GB/T 229 standard.
  • the impact toughness of the high-strength, high-hardness enhanced wear-resistant steel samples of Examples 1-8 were tested respectively to obtain the corresponding impact energy.
  • Table 4 lists the mechanical performance test results at the surface of the high-strength and high-hardness enhanced wear-resistant steel of Examples 1-8.
  • Hardness after enhancement the surface Brinell hardness of the steel plate is measured after the impact energy of 550J on the sample steel plate is hit by the self-made drop hammer equipment.
  • the high-strength, high-hardness enhanced wear-resistant steel of the embodiments 1-8 of the present invention has very excellent mechanical properties, and it not only has the characteristics of high strength, high hardness, and high elongation, but also has Excellent low temperature impact toughness, its yield strength is between 835-980MPa, its tensile strength is between 1240-1415MPa, its elongation is between 12-15%, and its surface Brinell hardness is between 422-475HBW, its The Charpy V-type longitudinal impact energy at -40°C is between 42-57J.
  • the high-strength and high-hardness enhanced wear-resistant steels of Examples 1-8 of the present invention still have good Brinell hardness after being strengthened. After the sample steel plate is hit with 550J impact energy by self-made drop hammer equipment, the measured The reinforced Brinell hardness of the steel plates of each embodiment is between 493-545HBW.
  • the high-strength, high-hardness enhanced wear-resistant steels of Examples 1-8 of the present invention all have excellent cold bending properties, and there is no visible crack on the outer surface of the samples after the bending test, all of which are "qualified". Because the yield strength of the steel plate of the invention is very low, compared with the conventional wear-resistant steel with the same level of hardness, the steel plate has excellent forming and processing properties such as bending.
  • the high-strength and high-hardness enhanced wear-resistant steel described in the present invention can obtain a microstructure of martensite + bainite + retained austenite through reasonable chemical element composition design and optimization process +Carbide wear-resistant steel; this high-strength and high-hardness enhanced wear-resistant steel has excellent mechanical properties (such as hardness, strength, elongation, impact toughness and certain high temperature resistance), and also has good processing performance and usability.
  • the high-strength and high-hardness enhanced wear-resistant steel of the present invention is easy to process, it not only provides convenience for conventional mechanical processing, but also has excellent strength, toughness and wear resistance during use, and can be used in wear-resistant parts of construction machinery Promote the application.

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Abstract

本发明公开了一种高强高硬增强型耐磨钢，其含有Fe和不可避免的杂质，其还含有质量百分比如下的下述化学元素：C：0.22～0.33％，Si：0.10～1.00％，Mn：0.50～1.80％，Cr：0.80～2.30％，Al：0.010～0.10％，RE：0.01～0.10％，W：0.01～1.0％；以及Mo：0.01～0.80％，Ni：0.01～1.00％，Nb：0.005～0.080％，V：0.01～0.20％，Ti：0.001～0.50％中的至少其中之一。此外，本发明还公开了上述高强高硬增强型耐磨钢的制造方法，其包括步骤：(1)冶炼和铸造；(2)加热；(3)轧制；(4)在线淬火：其中初次冷却的开冷温度为：(Ar3'+5)～(Ar3'+50)℃，M 90＜终冷温度＜Bs，冷却速度为2～15℃/s；然后再空冷至室温。

Description

一种高强高硬增强型耐磨钢及其制造方法 技术领域
本发明涉及一种钢材及其制造方法，尤其涉及一种耐磨钢及其制造方法。
背景技术
耐磨钢具有高强度、高耐磨性能的特点，其性能相当优异，可以有效应用于采矿、农业、水泥生产、港口、电力以及冶金等领域中，制造如推土机、装载机、挖掘机、自卸车及抓斗、堆取料机等机械产品，具有广阔的应用前景。
近些年来，耐磨钢的开发与应用发展很快，目前应用最为普遍的为马氏体耐磨钢，这种类型的耐磨钢一般均通过增加碳含量并加入适量的合金元素，如铬、钼、镍、钒、硼等，充分利用热处理后相变强化等方法，来提高耐磨钢的力学性能。
然而，对于工况比较恶劣的情况，往往需要采用硬度非常高的耐磨钢板，此类耐磨钢具备的超高强硬度导致在机械切割、钻孔、弯曲等方面对于加工设备的要求非常高，其机械加工十分困难，给用户带来很大困难。
基于此，针对现有耐磨钢的不足和缺陷，本发明期望获得一种新的高强高硬增强型耐磨钢，相较于现有传统的超高强硬度耐磨钢板，其强硬度更低，会给用户机械加工带来较大便利；在实际使用过程中，该高强高硬增强型耐磨钢容易发生塑性诱导相变，能够显著提高钢板的强硬度，进而提高钢板耐磨性能；通过这一效应，可以使得本发明所述的高强高硬增强型耐磨在实际使用过程中的力学性能和耐磨性能反而高于同硬度级别的耐磨钢板。
发明内容
本发明的目的之一在于提供一种高强高硬增强型耐磨钢，该高强高硬增强型耐磨钢在具有优异力学性能的同时，还具有优异的机械加工性、热稳定性和焊接性能，其实现了高强硬度和高韧性的匹配，具有优异的机械加工性能，并在实际使用过程中具有优异的力学性能和良好的耐磨性能，其具有十分良好的推广前景和应用价值。
本发明所涉及的高强高硬增强型耐磨钢易于加工，其既为常规的机械加工提供了便利，又能够在使用过程中，通过塑性诱导相变，获得优异的强韧性和耐磨性，其性能优异，可以在工程机械耐磨部件上推广应用。
为了实现上述目的，本发明提供了一种高强高硬增强型耐磨钢，其含有Fe和不可避免的杂质，其还含有质量百分比如下的下述化学元素：
C：0.22～0.33％，Si：0.10～1.00％，Mn：0.50～1.80％，Cr：0.80～2.30％，Al：0.010～0.10％，RE：0.01～0.10％，W：0.01～1.0％；以及Mo：0.01～0.80％，Ni：0.01～1.00％，Nb：0.005～0.080％，V：0.01～0.20％，Ti：0.001～0.50％中的至少其中之一。
进一步地，在本发明所述的高强高硬增强型耐磨钢中，其各化学元素质量百分比为：
C：0.22～0.33％，Si：0.10～1.00％，Mn：0.50～1.80％，Cr：0.80～2.30％，Al：0.010～0.10％，RE：0.01～0.10％，W：0.01～1.0％；以及Mo：0.01～0.80％，Ni：0.01～1.00％，Nb：0.005～0.080％，V：0.01～0.20％，Ti：0.001～0.50％中的至少其中之一；余量为Fe和不可避免的杂质。
在本发明中，本发明的高强高硬增强型耐磨钢以添加C、Si元素和Mn、Cr合金元素为主，并可以根据需要适当添加Mo、Ni等贵金属元素，其可以在控制合金成本较低的同时，确保钢材的性能。
在本发明所述的高强高硬增强型耐磨钢中，各化学元素的设计原理如下所述：
C：在本发明所述的高强高硬增强型耐磨钢中，C是耐磨钢中最基本、最重要的元素，添加适量的C元素可以提高钢材的强度和硬度，进而提高钢材的耐磨性。但需要注意的是，C元素同时会对钢材的韧性和焊接性能产生不利影响，因此，需要合理控制钢中C元素含量。基于此，考虑到C元素含量对于耐磨钢性能的影响，在本发明所述的高强高硬增强型耐磨钢中，将C元素的质量百分比控制在0.22～0.33％之间，可进一步优选为0.23-0.28％。在一些实施方案中，C的质量百分比为0.22～0.31％。在一些实施方案中，C的质量百分比为0.23～0.31％。在一些实施方案中，C的质量百分比为0.23～0.30％。
Si：在本发明所述的高强高硬增强型耐磨钢中，Si可以固溶在铁素体和奥氏体中，进而可以提高它们的硬度和强度，然而Si元素含量过高时也会导致钢材的韧性 急剧下降。同时，结合考虑到Si元素与O的亲和力比Fe强，在焊接时很容易产生低熔点的硅酸盐，增加熔渣和熔化金属的流动性，影响焊缝质量，因此钢中Si元素含量不宜过多。基于此，在本发明所述的高强高硬增强型耐磨钢中，将Si元素的质量百分比控制在0.10～1.00％之间。在一些实施方案中，Si的质量百分比为0.10～0.80％。在一些实施方案中，Si的质量百分比为0.15～0.80％。在一些实施方案中，Si的质量百分比为0.15～0.65％。
Mn：在本发明所述的高强高硬增强型耐磨钢中，添加适量的Mn元素可以强烈地增加钢材的淬透性，降低钢材的转变温度和钢的临界冷却速度。但需要注意的是，钢中Mn元素含量不宜过高，当钢中Mn元素含量过高时，不仅有使晶粒粗化的倾向，还会增加钢的回火脆敏感性，而且很容易导致铸坯中出现偏析和裂纹，降低钢板的性能。基于此，在本发明所述的高强高硬增强型耐磨钢中，将Mn元素的质量百分比控制在0.50～1.80％之间，可以一步优选为1.05-1.65％。在一些实施方案中，Mn的质量百分比为1.00～1.80％。在一些实施方案中，Mn的质量百分比为1.10～1.80％。在一些实施方案中，Mn的质量百分比为1.10～1.80％。在一些实施方案中，Mn的质量百分比为1.15～1.80％。在一些实施方案中，Mn的质量百分比为0.65～1.65％。
Cr：在本发明所述的高强高硬增强型耐磨钢中，Cr元素可以降低临界冷却速度、提高钢的淬透性。Cr在钢中可以形成(Fe，Cr) 3C、(Fe，Cr) 7C 3和(Fe，Cr) 23C 7等多种碳化物，其可以有效提高钢材的强度和硬度。此外，需要说明的是，钢中添加适量的Cr可以在回火时阻止或减缓碳化物的析出与聚集，从而提高钢材的回火稳定性。基于此，考虑到Cr元素的有益效果，在本发明所述的高强高硬增强型耐磨钢中，可以将Cr元素的质量百分比控制在0.80～2.30％之间，可进一步优选为1.25-2.10％。在一些实施方案中，Cr的质量百分比为1.10～2.20％。在一些实施方案中，Cr的质量百分比为1.10～2.00％。在一些实施方案中，Cr的质量百分比为1.15～2.00％。在一些实施方案中，Cr的质量百分比为0.95～2.10％。
Al：在本发明所述的高强高硬增强型耐磨钢中，Al元素能够和钢中的N元素形成细小难溶的AlN颗粒，细化钢的晶粒。钢中添加适量的Al元素可以有效细化钢的晶粒，固定钢中的N和O，以减轻钢对缺口的敏感性，减小或消除钢材的时效现象，并提高钢材的韧性。基于此，在本发明所述的高强高硬增强型耐磨钢中，将Al元素的质量百分比控制在0.010～0.10％之间，可以进一步优选为0.035-0.080％。在一些 实施方案中，Al的质量百分比为0.010～0.080％。在一些实施方案中，Al的质量百分比为0.015～0.075％。在一些实施方案中，Al的质量百分比为0.015～0.070％。在一些实施方案中，Al的质量百分比为0.025～0.080％。
RE：在本发明所述的高强高硬增强型耐磨钢中，添加适量的稀土可以减少硫、磷等元素的偏析，改善非金属夹杂物的形状、大小和分布，同时可以细化晶粒，提高硬度。此外，稀土还可以提高屈强比，其有利于改善低合金高强度钢的强韧性，能够提高钢板的热稳定性。但需要注意的是，钢中稀土的含量不宜过多，否则会产生严重偏析，从而降低铸坯质量和力学性能。基于此，在本发明所述的高强高硬增强型耐磨钢中，将RE的质量百分比控制在0.01～0.10％之间，可以进一步优选为0.03-0.10％。在一些实施方案中，RE的质量百分比为0.025～0.080％。
W：在本发明所述的高强高硬增强型耐磨钢中，钨可以增加钢的回火稳定性和热强性，并可以起到一定的细化晶粒作用。此外，钨还可以形成硬质碳化物，以增加钢材的耐磨性。由此，为了发挥钨的有益效果，在本发明所述的高强高硬增强型耐磨钢中，将W元素的质量百分比控制在0.01～1.0％之间，可以进一步优选为0.05-0.85％。在一些实施方案中，W的质量百分比为0.05～0.85％。
Mo：在本发明所述的高强高硬增强型耐磨钢中，添加适量的Mo可以有效细化晶粒，提高钢材的强度和韧性。Mo在钢中存在于固溶体相和碳化物相中，因此，含Mo钢同时具有固溶强化和碳化物弥散强化的作用。此外，Mo还是减小回火脆性的元素，钢中添加适量的Mo元素，还可以提高材料的回火稳定性。基于此，在本发明所述的高强高硬增强型耐磨钢中，当添加时，将Mo元素的质量百分比控制在0.01～0.80％之间，优选在0.08～0.55％之间。
Ni：在本发明所述的高强高硬增强型耐磨钢中，Ni能与Fe以任何比例互溶，其可以通过细化铁素体晶粒改善钢的低温韧性，并具有明显降低冷脆转变温度的作用。但需要注意的是，钢中Ni元素含量不宜过高，当钢中Ni元素含量过高时，容易导致钢板表面氧化皮难以脱落，且显著增加成产成本。基于此，在本发明所述的高强高硬增强型耐磨钢中，当添加时，将Ni元素的质量百分比控制在0.01～1.00％之间，优选在0.25～0.85％之间。
Nb：在本发明所述的高强高硬增强型耐磨钢中，添加适量的Nb元素可以起到细化晶粒和析出强化的作用，其对于提高材料强韧性的贡献极为显著；Nb元素通过 晶粒细化的作用可以有效提高钢材的强度和韧性，其还可以通过析出强化和相变强化来提高并改善钢材的性能，Nb已成为高强度低合金结构钢中最有效的强化剂之一；此外，Nb还是强烈的C、N化物的形成元素，其可以强烈地抑制奥氏体晶粒长大。基于此，在本发明所述的高强高硬增强型耐磨钢中，当添加时，将Nb元素的质量百分比控制在0.005～0.080％之间，优选在0.01～0.045％之间。
V：在本发明所述的高强高硬增强型耐磨钢中，添加适量的V元素可以有效细化晶粒，使钢坯在加热阶段奥氏体晶粒不至于生长的过于粗大，这样，在随后的多道次轧制过程中，可以使钢的晶粒得到进一步细化，进而提高钢材的强度和韧性。基于此，在本发明所述的高强高硬增强型耐磨钢中，当添加时，将V元素的质量百分比控制在0.01～0.20％之间，优选在0.03～0.15％。
Ti：在本发明所述的高强高硬增强型耐磨钢中，Ti是强碳化物形成元素之一，Ti元素可以与C元素结合形成细微的TiC颗粒。其中，TiC颗粒细小，其可以分布在晶界，从而达到细化晶粒的效果；此外，TiC颗粒较硬，其可以提高钢材的耐磨性。基于此，考虑到Ti元素的有益效果，在本发明所述的高强高硬增强型耐磨钢中，当添加时，将Ti元素的质量百分比控制在0.001～0.50％之间，优选在0.015～0.45％之间。
进一步优选地，本发明所述的高强高硬增强型耐磨钢的各化学元素质量百分比满足：C：0.22～0.31％，Si：0.10～0.80％，Mn：1.00～1.80％，Cr：1.10～2.20％，Al：0.010～0.080％。
更进一步优选地，本发明所述的高强高硬增强型耐磨钢的各化学元素质量百分比满足：C：0.23～0.31％，Si：0.15～0.80％，Mn：1.10～1.80％，Cr：1.10～2.00％，Al：0.015～0.075％。
最优选地，本发明所述的高强高硬增强型耐磨钢的各化学元素质量百分比满足：C：0.23～0.30％，Si：0.15～0.65％，Mn：1.15～1.80％，Cr：1.15～2.00％，Al：0.015～0.070％。
进一步地，在本发明所述的高强高硬增强型耐磨钢中，在不可避免的杂质中，P≤0.030％，并且/或者S≤0.010％。
在本发明中，P和S均是不可避免的杂质元素，为了确保耐磨钢的质量，在条件允许的前提下，钢中杂质元素的含量越低越好。P、S均为有害元素，它们的含量 要严格控制。因此，在本发明所述的高强高硬增强型耐磨钢中，可以控制不可避免的杂质元素满足：P≤0.030％，并且/或者S≤0.010％。
进一步地，在本发明所述的高强高硬增强型耐磨钢中，其微观组织为马氏体+贝氏体+残余奥氏体+碳化物。
进一步地，在本发明所述的高强高硬增强型耐磨钢中，其中残余奥氏体的体积分数等于5％或大于5％，马氏体的体积分数等于90％或小于90％。在一些实施方案中，本发明所述的高强高硬增强型耐磨钢中，残余奥氏体的体积分数为5～15％，马氏体的体积分数为65～90％。在一些实施方案中，本发明的高强高硬增强型耐磨钢中，其中残余奥氏体的体积分数为5.3～12.0％，如5.5～8.5％，马氏体的体积分数为70～88％，如77.5-85.6％。
与常规同硬度级别的低合金钢板相比，本发明所述的高强高硬增强型耐磨钢的微观组织不同于现在较普遍的马氏体组织，其形成了马氏体+贝氏体+残余奥氏体+碳化物的微观组织。
基于上述微观组织，可以确保本发明所述的高强高硬增强型耐磨钢的力学性能，该高强高硬增强型耐磨钢的强硬度略低，会给用户的机械加工带来较大便利，适于易加工的工况。
此外，在实际使用过程中，本发明所述的高强高硬增强型耐磨钢的耐磨性能却十分优异，这主要是使用过程中发生了TRIP(相变诱导塑性)效应，即：由于该钢板除了含有一定量的马氏体或贝氏体外，还含有一定比例的奥氏体，这使得钢板在使用过程中受到冲击、打压、磨损时，发生塑性诱导相变，能够显著提高钢板的强硬度，进而提高钢板耐磨性能。通过这一效应，可以使得本发明所述的高强高硬增强型耐磨在实际使用过程中的力学性能和耐磨性能反而高于同硬度级别的常规耐磨钢板。
此外，需要注意的是，由于本发明所述的高强高硬增强型耐磨钢所具有特殊微观组织，以及所添加的RE和W元素，其还可以获得一定的耐高温性，在较高温度下，该钢板的强硬度损失不大。
进一步地，在本发明所述的高强高硬增强型耐磨钢中，其布氏硬度为400～500HBW，抗拉强度为1200～1600MPa(如1300～1600MPa)，延伸率为10～15％，-40℃下的夏比V型纵向冲击功＞40J。
在一些实施方案中，本发明所述的高强高硬增强型耐磨钢的布氏硬度为420～ 480HBW，抗拉强度为1220～1450MPa，延伸率为10～15％，-40℃下的夏比V型纵向冲击功＞40J，如41～60J。
在一些实施方案中，本发明所述高强高硬增强型耐磨钢的屈服强度为800～1000MPa，如830～980MPa。在一些实施方案中，本发明所述高强高硬增强型耐磨钢的屈强比≤0.75，优选≤0.70。
在一些实施方案中，本发明所述的高强高硬增强型耐磨钢进行550J冲击能量打击后，测得钢板表面布氏硬度相较于测试前钢板的布氏硬度有10％以上的提升，优选有13％以上的提升。在一些实施方案中，本发明所述的高强高硬增强型耐磨钢进行550J冲击能量打击后，测得钢板表面布氏硬度≥480HBW，如为480～560HBW。
相应地，本发明的另一目的在于提供一种高强高硬增强型耐磨钢的制造方法，该制造方法的工艺简便可行，采用该制造方法制得的高强高硬增强型耐磨钢的综合性能十分优异，其布氏硬度为400～500HBW，抗拉强度为1200～1600MPa(如1300～1600MPa)，延伸率为10～15％，-40℃下的夏比V型纵向冲击功＞40J，具有十分良好的推广前景和应用价值。
为了实现上述目的，本发明提出了上述的高强高硬增强型耐磨钢的制造方法，其包括步骤：
(1)冶炼和铸造；
(2)加热；
(3)轧制；
(4)在线淬火：其中初次冷却开冷温度为：(Ar3’+5)～(Ar3’+50)℃，M 90＜终冷温度＜Bs，冷却速度为2～15℃/s；然后再空冷至室温。
在本发明所述的高强高硬增强型耐磨钢的制造方法中，将各冶炼原料按照发明人设计的化学成分配比进行添加，依次经过冶炼、铸造、加热、轧制以及在线淬火步骤，可以获得所述的高强高硬增强型耐磨钢。
需要说明的是，在本发明上述步骤(4)的在线淬火过程中，初次冷却可以采用水冷，也可以采用油冷。
在本发明中，Ar3’表示钢材在在线淬火过程中奥氏体向铁素体开始转变的温度；Bs表示贝氏体开始转变的温度；M 90表示为马氏体体积比为90％的温度。
进一步地，在本发明所述的制造方法中，在步骤(2)中，制板坯加热温度为1030～ 1230℃，保温1-3小时。在一些实施方案中，制板坯加热温度为1050～1210℃，保温1-3小时。
进一步地，在本发明所述的制造方法中，在步骤(2)中，控制板坯加热温度为1030～1180℃。
相应地，在一些其他的实施方式中，更优选的，可以控制加热温度为1030-1160℃；为了提高生产效率并防奥氏体晶粒过分长大及钢坯表面严重氧化，最优选的可以控制加热温度为1030-1140℃。
进一步地，在本发明所述的制造方法中，在步骤(3)中，控制粗轧温度为930～1180℃，精轧温度为870～970℃。在一些实施方案中，在步骤(3)中，控制粗轧温度为950～1150℃，精轧温度为885～955℃。
进一步地，在本发明所述的制造方法中，在步骤(3)中，控制粗轧温度为930～1130℃，精轧温度为875～945℃。
进一步地，在本发明所述的制造方法中，在步骤(3)中，控制粗轧阶段轧制压下率大于35％，精轧阶段轧制压下率大于55％。进一步地，在本发明所述的制造方法中，在步骤(3)中，控制粗轧阶段轧制压下率为35～75％，精轧阶段轧制压下率为55～80％。
在一些其他的实施方式中，为了获得更优的实施效果，本发明可以进一步优选地控制粗轧温度为930-1110℃，控制粗轧阶段轧制压下率大于等于38％，控制精轧温度为875-935℃，控制精轧阶段轧制压下率大于等于58％。
最优选地，可以控制步骤(3)的轧制过程中的粗轧温度为935-1105℃，控制粗轧阶段轧制压下率大于40％，控制精轧温度为875-930℃，控制精轧阶段轧制压下率大于60％。
进一步地，在本发明所述的制造方法中，在步骤(4)中，其中初次冷却开冷温度为：(Ar3’+5)～(Ar3’+45)℃，(M 90+5℃)＜终冷温度＜(B s-15℃)，冷却速度为2～12℃/s。
在一些其他的实施方式中，更优选的，可以控制初次冷却开冷温度为：(Ar3’+5)～(Ar3’+40)℃，控制终冷温度满足：(M 90+5℃)＜终冷温度＜(B s-20℃)，并控制冷却速度为2-11℃/s。
最优选的，可以控制初次冷却开冷温度为：(Ar3’+5)～(Ar3’+38)℃，控制 终冷温度满足：(M 90+5℃)＜终冷温度＜(B s-23℃)，并控制冷却速度为3-11℃/s。
在一些实施方案中，控制终冷温度为350～450℃。
在一些实施方案中，本发明高强高硬增强型耐磨钢的厚度为9～25mm。
相较于现有技术，本发明所述的高强高硬增强型耐磨钢及其制造方法具有如下所述的优点以及有益效果：
(1)在化学成分设计时，本发明所述的高强高硬增强型耐磨钢对合金成分进行了充分优化，其以添加C、Si元素和Mn、Cr合金元素为主，并可以根据需要适当添加Mo、Ni等贵金属元素，实现在控制合金成本较低的同时，保证钢材的性能。
(2)从显微组织上看，本发明的高强高硬增强型耐磨钢可以获得马氏体+贝氏体+残余奥氏体+碳化物的微观组织(其中马氏体体积分数＜90％，残余奥氏体体积分数＞5％，其余为贝氏体和碳化物)，致使钢板在使用过程中发生TRIP效应，提高钢板的强硬度和耐磨性，进而提高钢板的实用性和使用寿命。此外，大量均匀分布的硬质相，如Ti、Cr、Mo和W的碳化物，能够进一步提高钢板的耐磨性能和使用寿命。
(3)相较于现有的常规马氏体耐磨钢，本发明的高强高硬增强型耐磨钢的强硬度相对较低，会给用户的机械加工带来较大便利，适于易加工的工况；此外，由于RE和W元素的添加，本发明的高强高硬增强型耐磨钢还具有一定的耐高温性，在较高温度下，该钢板的强硬度损失不大。
综上所述可以看出，本发明在合理的生产工艺条件下科学设计了碳、合金成分及其配比，降低了合金成本，其生产工艺简易可行，有利于工业生产；相应地，本发明的高强高硬增强型耐磨钢具有优异的力学性能(如硬度、强度、延伸率、冲击韧性及一定的耐高温性)和加工性能及使用性，其布氏硬度为400～500HBW，抗拉强度为1200～1600MPa(如1300～1600MPa)，延伸率为10～15％，-40℃下的夏比V型纵向冲击功＞40J，具有十分良好的推广前景和应用价值。
附图说明
图1：实施例3制备得到的高强高硬增强型耐磨钢的金相组织照片。
具体实施方式
下面将结合具体的实施例对本发明所述的高强高硬增强型耐磨钢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1-8
实施例1-8的高强高硬增强型耐磨钢均采用以下步骤制得：
(1)按照表1所示的化学成分配比进行冶炼和铸造。
(2)加热：对获得的板坯进行加热，控制板坯加热温度为1030～1230℃，保温1-3小时；当然，板坯加热温度也可以优选控制为1030～1180℃。
(3)轧制：对加热后的板坯进行轧制，控制粗轧温度为930～1180℃，精轧温度为870～970℃，控制粗轧阶段轧制压下率大于35％，精轧阶段轧制压下率大于55％；当然，在控制粗轧阶段轧制压下率大于35％，控制精轧阶段轧制压下率大于55％时，粗轧温度也可以优选控制为930～1130℃，精轧温度可以优选控制为875～945℃。
(4)在线淬火：其中初次冷却开冷温度为：(Ar3’+5)～(Ar3’+50)℃，M 90＜终冷温度＜Bs，冷却速度为2～15℃/s，再空冷至室温；当然，也可以优选地控制初次冷却开冷温度为：(Ar3’+5)～(Ar3’+45)℃，优选控制终冷温度满足：(M 90+5℃)＜终冷温度＜(B s-15℃)，并优选地控制冷却速度为2～12℃/s。
需要说明的是，本发明所述的实施例1-8的高强高硬增强型耐磨钢均采用以上步骤制得，其化学成分及相关工艺参数均满足本发明设计规范控制要求。
表1列出了实施例1-8的高强高硬增强型耐磨钢中的各化学元素的质量百分比。
表1(wt％，余量为Fe和除P、S以外其他不可避免的杂质)
Figure PCTCN2022129272-appb-000001
Figure PCTCN2022129272-appb-000002
表2-1和表2-2列出了实施例1-8的高强高硬增强型耐磨钢在上述制造方法各步骤中的具体工艺参数。
表2-1
Figure PCTCN2022129272-appb-000003
表2-2
Figure PCTCN2022129272-appb-000004
注：表2-2中的Ar3’表示试验钢在在线淬火过程中奥氏体向铁素体开始转变的温度；Bs表示贝氏体开始转变的温度；M 90表示为马氏体体积比为90％的温度。
将最终制得的实施例1-8的高强高硬增强型耐磨钢分别取样，并对实施例1-8的高强高硬增强型耐磨钢样品进行观察和分析，观察发现实施例1-8的高强高硬增强型耐磨钢的微观组织均为马氏体+贝氏体+残余奥氏体+碳化物。实施例3的金相组织照片如图1所示。
相应地，针对实施例1-8的高强高硬增强型耐磨钢的微观组织进行进一步的分析，以获得残余奥氏体组织的体积分数和马氏体组织的体积分数，其中，残余奥氏体的体积分数均＞5％，马氏体的体积分数均＜90％，其残余奥氏体组织的体积分数的结果列于下表3之中。
表3
Figure PCTCN2022129272-appb-000005
参阅上述表3可以看出，在本发明中，实施例1-8的高强高硬增强型耐磨钢的残余奥氏体的体积分数在5.6％-8.3％之间。
在完成针对本发明所述实施例1-8的高强高硬增强型耐磨钢的微观组织观察后，可以进一步地对实施例1-8的高强高硬增强型耐磨钢样品的力学性能进行测试，以得到实施例1-8的高强高硬增强型耐磨钢的力学性能参数，所得的测试结果可以列于下述的表4之中。
相关力学性能测试手段，如下所述：
拉伸试验：在室温下采用SCL233200kN常温拉伸试验机，依据GB/T 228.1标准进行拉伸性能测试，以测得实施例1-8的高强高硬增强型耐磨钢样品在室温下的抗拉强度和延伸率。
冷弯试验：分别对实施例1-8的高强高硬增强型耐磨钢在室温下进行弯曲测试，以得到对应的结果；在室温下采用YJW—2000电液私服弯曲试验机，依据GB/T 232标准进行弯曲试验；弯曲试验后不使用放大仪器观察，观察试样外表面无可见裂纹，则评定为“合格”。
布氏硬度测试：在室温下采用SCL246布氏硬度试验机，依据GB/T 231.1标准进行布氏硬度测试。分别对实施例1-8的高强高硬增强型耐磨钢样品的表面位置进行硬度测试，以得到对应实施例的布氏硬度。
在获得实施例1-8的高强高硬增强型耐磨钢样品的布氏硬度后，可以采用自制落锤设备对各实施例的钢板进行同等550J冲击能量打击后，测得钢板表面布氏硬度，以获得增强后的布氏硬度。
冲击试验：在-40℃下采用SCL186750J仪器化冲击试验机，依据GB/T 229标准进行冲击性能测试。分别对实施例1-8的高强高硬增强型耐磨钢样品的冲击韧性进行测试，以得到对应的冲击功。
表4列出了实施例1-8的高强高硬增强型耐磨钢在表面位置的力学性能测试结果。
表4
Figure PCTCN2022129272-appb-000006
Figure PCTCN2022129272-appb-000007
注：增强后硬度：采用自制落锤设备对试样钢板进行550J冲击能量打击后测得的钢板表面布氏硬度。
参阅上述表4可以看出，本发明所述的实施例1-8的高强高硬增强型耐磨钢具有十分优异的力学性能，其不但具有高强、高硬、高延伸率等特点，而且具有优异的低温冲击韧性，其屈服强度在835-980MPa之间，其抗拉强度在1240-1415MPa之间，其延伸率在12-15％之间，表面布氏硬度在422-475HBW之间，其在-40℃下的夏比V型纵向冲击功在42-57J之间。
本发明所述的实施例1-8的高强高硬增强型耐磨钢在增强后仍然具有良好的布氏硬度，其采用自制落锤设备对试样钢板进行550J冲击能量打击后，测得的各实施例钢板的增强后的布氏硬度在493-545HBW之间。
相应地，本发明所述的实施例1-8的高强高硬增强型耐磨钢均具有十分优异的冷弯性能，弯曲试验后试样外表面均无可见裂纹，均为“合格”。由于本发明钢板屈服强度很低，与同级别硬度的常规耐磨钢相比，钢板折弯等成形加工性能十分优异。
综上所述可以看出，本发明所述的高强高硬增强型耐磨钢通过合理的化学元素成分设计并配合优化工艺，可以获得微观组织为马氏体+贝氏体+残余奥氏体+碳化物的耐磨钢；该高强高硬增强型耐磨钢在具有优异的力学性能(如硬度、强度、延伸率、冲击韧性及一定的耐高温性)的同时，还具有良好的加工性能及使用性。
本发明所述的高强高硬增强型耐磨钢易于加工，其既为常规的机械加工提供了便利，又可以在使用过程中具有优异的强韧性和耐磨性，可以在工程机械耐磨部件上推广应用。
需要说明的是，本发明的保护范围中现有技术部分并不局限于本申请文件所给出的实施例，所有不与本发明的方案相矛盾的现有技术，包括但不局限于在先专利文献、在先公开出版物，在先公开使用等等，都可纳入本发明的保护范围。
此外，本案中各技术特征的组合方式并不限本案权利要求中所记载的组合方式或是具体实施例所记载的组合方式，本案记载的所有技术特征可以以任何方式进行自由组合或结合，除非相互之间产生矛盾。
还需要注意的是，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 (15)

  1. 一种高强高硬增强型耐磨钢，其含有Fe和不可避免的杂质，其特征在于，其还含有质量百分比如下的下述化学元素：
    C：0.22～0.33％，Si：0.10～1.00％，Mn：0.50～1.80％，Cr：0.80～2.30％，Al：0.010～0.10％，RE：0.01～0.10％，W：0.01～1.0％；以及Mo：0.01～0.80％，Ni：0.01～1.00％，Nb：0.005～0.080％，V：0.01～0.20％，Ti：0.001～0.50％中的至少其中之一。
  2. 如权利要求1所述的高强高硬增强型耐磨钢，其特征在于，其各化学元素质量百分比为：
    C：0.22～0.33％，Si：0.10～1.00％，Mn：0.50～1.80％，Cr：0.80～2.30％，Al：0.010～0.10％，RE：0.01～0.10％，W：0.01～1.0％；以及Mo：0.01～0.80％，Ni：0.01～1.00％，Nb：0.005～0.080％，V：0.01～0.20％，Ti：0.001～0.50％中的至少其中之一；余量为Fe和不可避免的杂质。
  3. 如权利要求1或2所述的高强高硬增强型耐磨钢，其特征在于，其各化学元素质量百分比满足：C：0.22～0.31％，Si：0.10～0.80％，Mn：1.00～1.80％，Cr：1.10～2.20％，Al：0.010～0.080％；或其各化学元素质量百分比满足：C：0.23～0.31％，Si：0.15～0.80％，Mn：1.10～1.80％，Cr：1.10～2.00％，Al：0.015～0.075％；或其各化学元素质量百分比满足：C：0.23～0.30％，Si：0.15～0.65％，Mn：1.15～1.80％，Cr：1.15～2.00％，Al：0.015～0.070％。
  4. 如权利要求1或2所述的高强高硬增强型耐磨钢，其特征在于，其化学元素质量百分比具有以下任意一项或多项特征：C含量为0.23～0.28％；Si含量为0.15～0.65％；Mn含量为1.05～1.65％；Cr含量为1.25～2.10％；和Al含量为0.035～0.080％。
  5. 如权利要求1或2所述的高强高硬增强型耐磨钢，其特征在于，在不可避免的杂质中，P≤0.030％，并且/或者S≤0.010％。
  6. 如权利要求1或2所述的高强高硬增强型耐磨钢，其特征在于，其微观组织为马氏体+贝氏体+残余奥氏体+碳化物。
  7. 如权利要求1或2所述的高强高硬增强型耐磨钢，其特征在于，其中残余 奥氏体的体积分数≥5％，马氏体的体积分数≤90％；优选地，残余奥氏体的体积分数为5～15％，马氏体的体积分数为60～90％；更优选地，残余奥氏体的体积分数为5.3～12.0％或5.5～8.5％，马氏体的体积分数为70～88％或77.5～85.6％。
  8. 如权利要求1或2所述的高强高硬增强型耐磨钢，其特征在于，其布氏硬度为400～500HBW，抗拉强度为1200～1600MPa，延伸率为10～15％，-40℃下的夏比V型纵向冲击功＞40J；优选地，其屈服强度为800～1000MPa，优选为830～980MPa；优选地，其屈强比≤0.75，优选≤0.70。
  9. 一种如权利要求1-8中任意一项所述的高强高硬增强型耐磨钢的制造方法，其特征在于，包括步骤：
    (1)冶炼和铸造；
    (2)加热；
    (3)轧制；
    (4)在线淬火：其中初次冷却的开冷温度为：(Ar3’+5)～(Ar3’+50)℃，M 90＜终冷温度＜Bs，冷却速度为2～15℃/s；然后再空冷至室温。
  10. 如权利要求9所述的制造方法，其特征在于，在步骤(2)中，控制板坯加热温度为1030～1230℃，保温1-3小时。
  11. 如权利要求10所述的制造方法，其特征在于，在步骤(2)中，控制板坯加热温度为1030～1180℃。
  12. 如权利要求9所述的制造方法，其特征在于，在步骤(3)中，控制粗轧温度为930～1180℃，精轧温度为870～970℃。
  13. 如权利要求12所述的制造方法，其特征在于，在步骤(3)中，控制粗轧温度为930～1130℃，精轧温度为875～945℃。
  14. 如权利要求9-13中任意一项所述的制造方法，其特征在于，在步骤(3)中，控制粗轧阶段轧制压下率大于35％，精轧阶段轧制压下率大于55％。
  15. 如权利要求9所述的制造方法，其特征在于，在步骤(4)中，其中初次冷却的开冷温度为：(Ar3’+5)～(Ar3’+45)℃，(M 90+5℃)＜终冷温度＜(B s-15℃)，冷却速度为2～12℃/s。
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