WO2024022531A1 - 一种耐腐蚀性耐磨钢板及其制造方法 - Google Patents

一种耐腐蚀性耐磨钢板及其制造方法 Download PDF

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WO2024022531A1
WO2024022531A1 PCT/CN2023/110178 CN2023110178W WO2024022531A1 WO 2024022531 A1 WO2024022531 A1 WO 2024022531A1 CN 2023110178 W CN2023110178 W CN 2023110178W WO 2024022531 A1 WO2024022531 A1 WO 2024022531A1
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resistant
steel plate
corrosion
wear
resistant steel
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English (en)
French (fr)
Inventor
李红斌
丁建华
苗雨川
刘自成
梅峰
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to CA3263561A priority Critical patent/CA3263561A1/en
Priority to EP23845735.2A priority patent/EP4563714A4/en
Priority to JP2025504829A priority patent/JP2025525673A/ja
Priority to AU2023312781A priority patent/AU2023312781A1/en
Publication of WO2024022531A1 publication Critical patent/WO2024022531A1/zh
Anticipated expiration legal-status Critical
Priority to ZA2025/01771A priority patent/ZA202501771B/en
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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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys 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
    • 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
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D2211/008—Martensite

Definitions

  • the present disclosure relates to a steel plate and a manufacturing method thereof, in particular to a corrosion-resistant and wear-resistant steel plate and a manufacturing method thereof.
  • the patent application number is 201010168491.2
  • the invention name is "Steel for hot-rolled U-shaped steel sheet piles resistant to alkaline soil corrosion and its production method", which provides A kind of steel and production method for hot-rolled U-shaped steel sheet piles that are resistant to alkaline soil corrosion, but the steel plate is only resistant to alkali.
  • the purpose of this disclosure is to provide a corrosion-resistant and wear-resistant steel plate and a manufacturing method thereof.
  • the corrosion-resistant and wear-resistant dry plate has excellent wear resistance, acid resistance and alkali resistance, and can satisfy the working conditions of the steel plate. There are requirements for the wear resistance and corrosion resistance of steel plates in particularly harsh environments, and to reduce manufacturing costs.
  • the present disclosure provides a corrosion-resistant wear-resistant steel plate, which contains, by weight percentage: C: 0.10% ⁇ C ⁇ 0.30%; Si: 0.10% ⁇ Si ⁇ 0.50%; Mn: 0.50% ⁇ Mn ⁇ 1.50%; Mo: 0.01% ⁇ Mo ⁇ 0.50%; Nb: 0.005% ⁇ Nb ⁇ 0.050%; V: 0.01% ⁇ V ⁇ 0.10%; Ti: 0.005% ⁇ Ti ⁇ 0.050%; Al: 0.010% ⁇ Al ⁇ 0.060%; Cr: 2.00% ⁇ Cr ⁇ 5.00%; B: 0.0005% ⁇ B ⁇ 0.0050%; Sb: 0.01% ⁇ Sb ⁇ 0.20%; P: 0.010% ⁇ P ⁇ 0.030%;
  • it also contains one or more of Cu: 0.10 ⁇ Cu ⁇ 0.40%, Ni: 0.20 ⁇ Ni ⁇ 1.00% and RE: 0.01 ⁇ RE ⁇ 0.10%, with the balance being Fe and unavoidable impurities.
  • Another embodiment of the present disclosure is a corrosion-resistant wear-resistant steel plate, characterized in that, except for Fe and unavoidable impurities, it contains: C: 0.10% ⁇ C ⁇ 0.30%; Si: 0.10% ⁇ Si ⁇ 0.50%; Mn: 0.50% ⁇ Mn ⁇ 1.50%; Mo: 0.01% ⁇ Mo ⁇ 0.50%; Nb: 0.005% ⁇ Nb ⁇ 0.050%; V: 0.01% ⁇ V ⁇ 0.10%; Ti: 0.005% ⁇ Ti ⁇ 0.050%; Al: 0.010% ⁇ Al ⁇ 0.060%; Cr: 2.00% ⁇ Cr ⁇ 5.00%; B: 0.0005% ⁇ B ⁇ 0.0050%; Sb: 0.01% ⁇ Sb ⁇ 0.20%; P: 0.010% ⁇ P ⁇ 0.030%;
  • Cu 0.10% ⁇ Cu ⁇ 0.40%
  • Ni 0.20% ⁇ Ni ⁇ 1.00%
  • RE 0.01% ⁇ RE ⁇ 0.10%.
  • the corrosion-resistant wear-resistant steel plate of the present disclosure includes: C: 0.15% ⁇ C ⁇ 0.25%; Si: 0.10% ⁇ Si ⁇ 0.50%; Mn: 0.50% ⁇ Mn ⁇ 1.50 %; Mo: 0.01% ⁇ Mo ⁇ 0.50%; Nb: 0.005% ⁇ Nb ⁇ 0.050%; V: 0.01% ⁇ V ⁇ 0.10%; Ti: 0.005% ⁇ Ti ⁇ 0.050%; Al: 0.010% ⁇ Al ⁇ 0.060 %; Cr: 2.00% ⁇ Cr ⁇ 5.00%; B: 0.0005% ⁇ B ⁇ 0.0050%; and P: 0.010% ⁇ P ⁇ 0.030%; also includes: Cu: 0.10 ⁇ Cu ⁇ 0.40%, Ni: 0.20 ⁇ Ni ⁇ 1.00%, RE: 0.01 ⁇ RE ⁇ 0.10% and Sb: 0.01% ⁇ Sb ⁇ 0.20%, and the balance is Fe and inevitable impurities.
  • the corrosion-resistant wear-resistant steel plate of the present invention includes: C: 0.10% ⁇ C ⁇ 0.30%; Si: 0.25% ⁇ Si ⁇ 0.45%; Mn: 0.65% ⁇ Mn ⁇ 1.50%; Mo: 0.10% ⁇ Mo ⁇ 0.35%; Nb: 0.01% ⁇ Nb ⁇ 0.045%; V: 0.01% ⁇ V ⁇ 0.08%; Ti: 0.010% ⁇ Ti ⁇ 0.045%; Al: 0.020% ⁇ Al ⁇ 0.050%; Cr: 2.30% ⁇ Cr ⁇ 4.60%; B: 0.0015% ⁇ B ⁇ 0.0040%; Sb: 0.06% ⁇ Sb ⁇ 0.19%; P: 0.010% ⁇ P ⁇ 0.016%; S: ⁇ 0.005%; Cu: ⁇ 0.35%; Ni: ⁇ 0.75%; RE: ⁇ 0.10%;
  • the balance is Fe and unavoidable impurities.
  • S in the inevitable impurities is: ⁇ 0.010% by weight percentage.
  • Carbon is the most basic and important element in wear-resistant steel. It can improve the strength and hardness of steel, thereby improving the wear resistance of steel, but it is detrimental to the toughness and welding performance of steel. Therefore, in the present disclosure, the carbon content is controlled to be 0.10% ⁇ C ⁇ 0.30%, and more preferably 0.12% ⁇ C ⁇ 0.29%.
  • Silicon (Si) Silicon solid solution in ferrite and austenite improves their hardness and strength. However, excessive silicon content will cause the toughness of steel to drop sharply. At the same time, considering that silicon has a stronger affinity with oxygen than iron, it is easy to produce silicates with low melting points during welding, which increases the fluidity of slag and molten metal and affects the quality of the weld, so the content should not be too much.
  • the content of silicon is controlled to be 0.10% ⁇ Si ⁇ 0.50%, more preferably 0.15% ⁇ Si ⁇ 0.50%. In some embodiments, the silicon content is controlled to be 0.25% ⁇ Si ⁇ 0.45%.
  • Manganese (Mn) Manganese strongly increases the hardenability of steel, reduces the transformation temperature of wear-resistant steel and the critical cooling rate of steel. However, when the manganese content is high, it tends to coarsen the grains and increase the temper brittleness sensitivity of the steel. It can also easily lead to segregation and cracks in the cast slab, reducing the performance of the steel plate.
  • the manganese content is controlled to be 0.50% ⁇ Mn ⁇ 1.50%, more preferably 0.60% ⁇ Mn ⁇ 1.50%. In some embodiments, the manganese content is controlled to be 0.65% ⁇ Mn ⁇ 1.50%.
  • Molybdenum can refine grains and increase strength and toughness. Molybdenum exists in the solid solution phase and carbide phase in steel. Therefore, molybdenum-containing steel has both solid solution strengthening and carbide dispersion strengthening effects. Molybdenum is an element that reduces temper brittleness and can improve temper stability. The molybdenum content is controlled to be 0.01% ⁇ Mo ⁇ 0.50%, more preferably 0.10% ⁇ Mo ⁇ 0.40%.
  • Niobium (Nb) Nb's grain refinement and precipitation strengthening effects are extremely significant in improving the strength and toughness of materials. It is a strong forming element of C and N compounds and strongly inhibits the growth of austenite grains. Nb simultaneously improves the strength and toughness of steel through grain refinement. Nb mainly improves and enhances the performance of steel through precipitation strengthening and phase transformation strengthening. Nb has been used as one of the most effective strengthening agents in HSLA steel. Therefore, niobium is controlled to be 0.005% ⁇ Nb ⁇ 0.050%, and more preferably 0.010% ⁇ Nb ⁇ 0.045%.
  • Vanadium (V) The main purpose of adding vanadium is to refine the grains so that the austenite grains of the billet will not grow too coarse during the heating stage. In this way, during the subsequent multi-pass rolling process, the steel can be The grains are further refined, improving the strength and toughness of the steel. Therefore, the vanadium content is controlled to be 0.01% ⁇ V ⁇ 0.10%, and more preferably 0.02% ⁇ V ⁇ 0.10%. In some embodiments, the vanadium content is controlled to be 0.01% ⁇ V ⁇ 0.08%.
  • Titanium is one of the strong carbide-forming elements and forms fine TiC particles with carbon.
  • the TiC particles are small and distributed at the grain boundaries to achieve the effect of refining the grains.
  • the harder TiC particles improve the wear resistance of steel. Therefore, the titanium content is controlled to be 0.005% ⁇ Ti ⁇ 0.050%, and more preferably 0.015% ⁇ Ti ⁇ 0.050%.
  • Aluminum (Al) Nitrogen in aluminum and steel can form small, insoluble AlN particles and refine the grains of steel. Aluminum can refine the grains of steel, fix nitrogen and oxygen 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. Therefore, the aluminum content is controlled to be 0.010% ⁇ Al ⁇ 0.060%, and more preferably 0.015% ⁇ Al ⁇ 0.060%. In some embodiments, the aluminum content is controlled to be 0.02% ⁇ V ⁇ 0.05%.
  • Chromium can reduce the critical cooling rate and improve the hardenability of steel. Chromium can form various carbides such as (Fe, Cr) 3 C, (Fe, Cr) 7 C 3 and (Fe, Cr) 23 C 7 in steel to increase strength and hardness. Chromium can prevent or slow down the precipitation and aggregation of carbides during tempering, which can improve the tempering stability of steel. In addition, it can improve the acid corrosion resistance of steel. In the oxidizing medium, there is a layer of strong and dense chromium oxide that forms on the surface of the steel to protect the steel. Chromium dissolved in steel can significantly increase the electrode potential of the steel and reduce electrochemical corrosion caused by different electrode potentials. Therefore, the chromium content is controlled to be 2.00% ⁇ Cr ⁇ 5.00%, and more preferably 2.50% ⁇ Cr ⁇ 5.00%.
  • B Boron increases the hardenability of steel, but excessive content will cause thermal embrittlement and affect the welding performance and hot processing performance of steel. Therefore, the B content needs to be strictly controlled. Therefore, the boron content is controlled to 0.0005% ⁇ B ⁇ 0.0050%, more preferably 0.0008% ⁇ B ⁇ 0.0050%. In some embodiments, the boron content is controlled to be 0.0015% ⁇ B ⁇ 0.0040%.
  • Antimony can improve the acid corrosion resistance of steel and increase the hardness of alloys. In an acidic environment, passivation occurs due to dissolution, and a passivation layer rich in Sb and other alloying elements is formed on the surface of the steel, which has high acid corrosion resistance. Therefore, the antimony content is controlled to be 0.01% ⁇ Sb ⁇ 0.20%, and more preferably 0.03% ⁇ Sb ⁇ 0.20%. In some embodiments, the antimony content is controlled to be 0.05% ⁇ Sb ⁇ 0.20%.
  • Copper (Cu) Mainly exists in solid solution and elemental phase precipitation in steel.
  • the solid solution of Cu plays a role in solid solution strengthening; since the solid solubility of Cu in ferrite decreases rapidly as the temperature decreases, Therefore, at lower temperatures, Cu in supersaturated solid solution precipitates in elemental form, which plays a precipitation strengthening role.
  • adding Cu to steel can significantly improve the steel's resistance to atmospheric corrosion. When it coexists with phosphorus, the effect is particularly significant. Therefore, when copper is added, the copper content can be controlled to be 0.10% ⁇ Cu ⁇ 0.40%, and more preferably 0.12% ⁇ Cu ⁇ 0.40%.
  • the content of phosphorus element is controlled to be 0.010% ⁇ P ⁇ 0.030%, more preferably 0.012% ⁇ P ⁇ 0.030%.
  • Nickel has the effect of significantly reducing the cold brittle transition temperature, but too high a content can easily cause the oxide scale on the surface of the steel plate to be difficult to fall off, and the cost will significantly increase. Therefore, when nickel is added, the nickel content is controlled to be 0.20% ⁇ Ni ⁇ 1.00%, and more preferably 0.45% ⁇ Ni ⁇ 0.8%.
  • Rare earth Adding rare earth to steel can reduce the segregation of elements such as sulfur and phosphorus, improve the shape, size and distribution of non-metallic inclusions, and at the same time refine the grains and increase the hardness. In addition, rare earths can improve the corrosion resistance of steel. The content of rare earths should not be too much, otherwise severe segregation will occur and the quality and mechanical properties of the slab will be reduced. Therefore, the RE content is controlled to be 0.01% ⁇ RE ⁇ 0.10%, and more preferably 0.02% ⁇ RE ⁇ 0.90%.
  • Sulfur is a harmful element, and its content must be strictly controlled.
  • the sulfur content in the steel types involved in this disclosure is controlled to be S ⁇ 0.010%.
  • the Brinell hardness of the steel plate of the present disclosure is 350-520HBW, such as 350-500HBW. In some embodiments, the steel plate of the present disclosure has a Brinell hardness of 370-520 HBW.
  • the steel plate of the present disclosure contains lath martensite structure, bainite and retained austenite, wherein the volume fraction of bainite is 10-40% and the volume fraction of retained austenite is 5-15% .
  • the thickness of the steel plate of the present disclosure is 15 to 40 mm.
  • the second aspect of the present disclosure is a method for manufacturing a corrosion-resistant wear-resistant steel plate, which is characterized by including the following steps:
  • the slab in the (2) heating step, the slab is heated to a temperature of 1000-1200°C and kept for 1-3 hours; in the (3) rolling step, the rough The rolling opening temperature is 900-1150°C (such as 1000 ⁇ 1100°C), the finishing rolling temperature is 780-880°C (such as 810 ⁇ 870°C); in the above (4) online cooling step, the cooling method can be Water cooling can be water-cooled to below 350°C (such as 150 ⁇ 350°C) and then air-cooled to room temperature. The cooling rate of water cooling can be 15-50°C/s.
  • the finish rolling deformation rate of the steel plate is 60 to 80%.
  • the corrosion-resistant wear-resistant steel plate and its manufacturing method of the present disclosure have the following advantages and beneficial effects:
  • the corrosion-resistant wear-resistant steel plate involved in the present disclosure has obvious advantages. By controlling the content of carbon and alloy elements and various heat treatment processes, it can obtain a wear-resistant steel plate with excellent acid resistance and wear resistance, and has low cost, simple process, It has high hardness, excellent machining performance, easy welding, and excellent acid corrosion resistance. Specifically:
  • the alloy composition of the corrosion-resistant and wear-resistant steel plate of the present disclosure is mainly low-carbon and low-alloy, making full use of the refinement and strengthening of Cr, Mo, Ni, Cu, Nb, Ti and other alloy elements. characteristics, ensuring that the steel plate has good mechanical properties and good corrosion resistance.
  • the corrosion-resistant and wear-resistant steel plate disclosed in the present disclosure has the advantages of high strength, high hardness, excellent acid resistance and alkali resistance, and has good welding properties. performance.
  • the corrosion-resistant wear-resistant steel plate of the present disclosure improves the structure refinement and strengthening effects by controlling process parameters such as opening and final rolling temperatures, finishing rolling deformation rate and cooling rate in the manufacturing method, and thereby Reduce the content of carbon and alloy elements to obtain steel plates with excellent mechanical properties and welding properties.
  • this process also has the characteristics of short production process, high efficiency, energy saving and low cost.
  • the corrosion-resistant wear-resistant steel plate of the present disclosure makes full use of alloy element addition and controlled rolling and controlled cooling processes to obtain lath martensite structure and residual austenite, which is beneficial to a good match of strength, hardness and toughness of the wear-resistant steel plate.
  • the higher the retained austenite content the higher the self-corrosion potential.
  • the lower the retained austenite content the lower the self-corrosion potential.
  • the increase in retained austenite helps to improve the corrosion resistance of the material.
  • Figure 1 is a metallographic structure diagram of the steel plate of the present disclosure.
  • Table 1 lists the mass percentage of each chemical element corresponding to the corrosion-resistant wear-resistant steel plates of Examples 1-8 and Comparative Example 1.
  • the corrosion-resistant and wear-resistant steel plates of Examples 1-8 of the present disclosure are prepared using the following steps:
  • the manufacturing method of the wear-resistant steel plate of Examples 1-8 is:
  • water cooling is used to cool to below 350°C (stop cooling temperature) and then air cooled to room temperature, where the water cooling cooling rate is 15-50°C/s.
  • the wear-resistant steel plate of Comparative Example 1 was manufactured using the same steps as described above, except that the raw material composition and specific process parameters in each process were different from those of Examples 1-8.
  • the specific process parameters of Examples 1-8 and Comparative Example 1 are shown in Table 2.
  • the corrosion-resistant and wear-resistant steel plates of Examples 1-8 and Comparative Example 1 were subjected to acid resistance test, alkali resistance test, and mechanical property test. The test results are listed in Tables 3 to 5.
  • the acid resistance test method is: use a constant temperature test tank to conduct a corrosion test under the conditions of "temperature 23 ⁇ 2°C, 10% H 2 SO 4 + 3.5% NaCl, full immersion for 24 hours".
  • a constant temperature test tank to conduct a corrosion test under the conditions of "temperature 23 ⁇ 2°C, 10% H 2 SO 4 + 3.5% NaCl, full immersion for 24 hours".
  • specific methods refer to "JB/T7901-2001 Metal Materials Laboratory Uniform Corrosion Total Immersion Test Method";
  • the alkali resistance test method is: perform a weekly immersion test in an alkaline atmosphere, the test temperature is 45 ⁇ 2°C, the relative humidity is 70 ⁇ 5%, the weekly immersion speed is: 1/60 (turn/minute), and the pH value is 9.5;
  • Brinell hardness test Use SCL246 Brinell hardness testing machine at room temperature to conduct Brinell hardness test according to GB/T 231.1 standard. Conduct hardness tests on the surface locations of the wear-resistant steel samples of Examples 1-8 and Comparative Example 1 to obtain the corresponding Brinell hardness.
  • the acid corrosion and alkali corrosion rates of the steel plate of Comparative Example 1 are much greater than the corrosion rates of the steel plate of the present invention, that is, the acid resistance and alkali resistance are poor, and the hardness is also poor. That is, the invention obtained by optimizing chemical elements and controlling the manufacturing process
  • the acid and alkali resistance of the steel plate has been greatly improved.
  • the wear-resistant steel plate has excellent acid and alkali resistance, and the hardness HBW is greater than 375.
  • the steel plate of the present disclosure has excellent acid resistance, alkali resistance and wear resistance, and its production process is simple and can be used for work It can be used in harsh environments, improves service life, and has broad application prospects.

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Abstract

本公开公开了一种耐腐蚀性耐磨钢板及其制造方法。该钢板按重量百分比计，包含：C：0.15％≤C≤0.25％；Si：0.10％≤Si≤0.50％；Mn：0.50％≤Mn≤1.50％；Mo：0.01％≤Mo≤0.50％；Nb：0.005％≤Nb≤0.050％；V：0.01％≤V≤0.10％；Ti：0.005％≤Ti≤0.050％；Al：0.010％≤Al≤0.060％；Cr：2.00％≤Cr≤5.00％；B：0.0005-0.0050wt.％；P：0.010％≤P≤0.030％，此外，还包含：Cu：0.10≤Cu≤0.40％、Ni：0.20≤Ni≤1.00％、RE：0.01≤RE≤0.10％、Sb：0.01％≤Sb≤0.20％中的一种以上，余量为Fe和不可避免的杂质，上述钢板的制造方法，其包括步骤：(1)冶炼铸造步骤；(2)加热步骤；(3)轧制步骤；(4)在线冷却步骤。本公开的钢板兼顾了优异的耐酸性耐碱性和耐磨性。

Description

一种耐腐蚀性耐磨钢板及其制造方法 技术领域
本公开涉及一种钢板及其制造方法，特别涉及一种耐腐蚀性耐磨钢板及其制造方法。
背景技术
工程、采矿、水泥生产、港口、电力以及冶金等机械设备的工作条件特别恶劣，如刮板运输机、自卸车箱体等产品需要具有高强度、高硬度、高韧性。然而在某些特殊工况，如处理工业垃圾等耐磨设备使用寿命很短，这主要是由于垃圾锈蚀、腐烂等引起的环境极易造成设备的腐蚀进而缩短使用寿命。
目前对耐酸性钢板的研究正在进行，例如申请号为201480021680.3、发明名称为“耐酸性、耐压碎特性及低温韧性优异的厚壁高强度线管用钢板和线管”的专利，其提供了一种提供耐酸性、耐压碎特性及低温韧性优异的厚壁高强度线管用钢板及其制造方法，但是该钢板仅具有耐酸性。
另外，对于耐碱性的钢板的研究也在进行中，例如申请号为201010168491.2，发明名称为“耐碱性土壤腐蚀的热轧U型钢板桩用钢及其生产方法”的专利，其提供了一种耐碱性土壤腐蚀的热轧U型钢板桩用钢及生产方法，但是该钢板仅具有耐碱性。
但是应对环境变化，没有一种能够即具有耐碱性又具有耐酸性，同时又具有优异的耐磨性的钢板。
鉴于现有技术的上述缺陷，期望获得一种兼顾耐腐蚀性和耐磨性的低碳低合金的钢板，在保证材料具有优异的耐磨性能同时，又具有优异的耐酸性和耐碱性，并且可以降低制造成本，适合于大量生产。
发明内容
本公开的目的在于提供一种以耐腐蚀性耐磨钢板及其制造方法，该耐腐蚀性耐磨性干板兼具优异的耐磨性能、耐酸性和耐碱性，可以满足钢板在工作条件特别恶劣环境下对钢板的耐磨性能及耐腐蚀性能的要求，并降低制造成本。
为了实现上述目的，本公开提供一种耐腐蚀性耐磨钢板，按重量百分比计，该耐腐蚀性耐磨钢板包含：
C：0.10％≤C≤0.30％；
Si：0.10％≤Si≤0.50％；
Mn：0.50％≤Mn≤1.50％；
Mo：0.01％≤Mo≤0.50％；
Nb：0.005％≤Nb≤0.050％；
V：0.01％≤V≤0.10％；
Ti：0.005％≤Ti≤0.050％；
Al：0.010％≤Al≤0.060％；
Cr：2.00％≤Cr≤5.00％；
B：0.0005％≤B≤0.0050％；
Sb：0.01％≤Sb≤0.20％；
P：0.010％≤P≤0.030％；
此外，还包含：Cu：0.10≤Cu≤0.40％、Ni：0.20≤Ni≤1.00％和RE：0.01≤RE≤0.10％中的一种以上，余量为Fe和不可避免的杂质。
本公开的另一个实施方式为一种耐腐蚀性耐磨钢板，其特征在于，除Fe和不可避免的杂质，按重量百分比计，包含：
C：0.10％≤C≤0.30％；
Si：0.10％≤Si≤0.50％；
Mn：0.50％≤Mn≤1.50％；
Mo：0.01％≤Mo≤0.50％；
Nb：0.005％≤Nb≤0.050％；
V：0.01％≤V≤0.10％；
Ti：0.005％≤Ti≤0.050％；
Al：0.010％≤Al≤0.060％；
Cr：2.00％≤Cr≤5.00％；
B：0.0005％≤B≤0.0050％；
Sb：0.01％≤Sb≤0.20％；
P：0.010％≤P≤0.030％；
还包含：Cu：0.10％≤Cu≤0.40％、Ni：0.20％≤Ni≤1.00％和RE：0.01％≤RE≤0.10％中的一种以上。
在一些实施方案中，按重量百分比计，本公开的耐腐蚀性耐磨钢板包含：C：0.15％≤C≤0.25％；Si：0.10％≤Si≤0.50％；Mn：0.50％≤Mn≤1.50％；Mo：0.01％≤Mo≤0.50％；Nb：0.005％≤Nb≤0.050％；V：0.01％≤V≤0.10％；Ti：0.005％≤Ti≤0.050％；Al：0.010％≤Al≤0.060％；Cr：2.00％≤Cr≤5.00％；B：0.0005％≤B≤0.0050％；和P：0.010％≤P≤0.030％；还包含：Cu：0.10≤Cu≤0.40％、Ni：0.20≤Ni≤1.00％、RE：0.01≤RE≤0.10％和Sb：0.01％≤Sb≤0.20％中的一种以上，余量为Fe和不可避免的杂质。
在一些实施方案中，按重量百分比计，本发明耐腐蚀性耐磨钢板包含：
C：0.10％≤C≤0.30％；
Si：0.25％≤Si≤0.45％；
Mn：0.65％≤Mn≤1.50％；
Mo：0.10％≤Mo≤0.35％；
Nb：0.01％≤Nb≤0.045％；
V：0.01％≤V≤0.08％；
Ti：0.010％≤Ti≤0.045％；
Al：0.020％≤Al≤0.050％；
Cr：2.30％≤Cr≤4.60％；
B：0.0015％≤B≤0.0040％；
Sb：0.06％≤Sb≤0.19％；
P：0.010％≤P≤0.016％；
S：≤0.005％；
Cu：≤0.35％；
Ni：≤0.75％；
RE：≤0.10％；
余量为Fe和不可避免的杂质。
进一步地，本公开的钢板中，按重量百分比计：
0.10≤Mo≤0.40％；
0.010％≤Nb≤0.045％；
0.02％≤V≤0.10％；
0.015％≤Ti≤0.050％。
进一步地，本公开的钢板中，按重量百分比计：
2.50％≤Cr≤5.00％；
0.012％≤P≤0.030％；
0.12％≤Cu≤0.40％；
0.20％≤Ni≤0.90％。
进一步地，本公开的钢板中，按重量百分比计，所述不可避免的杂质中S：≤0.010％。
在本公开的耐腐蚀性耐磨钢板中，各化学元素的设计原理具体如下所述(以下的含量均以质量百分比计)：
碳(C)：碳是耐磨钢中最基本、最重要的元素，可以提高钢的强度和硬度，进而提高钢的耐磨性，但其对钢的韧性和焊接性能不利。因此，在本公开中将碳的含量控制为0.10％≤C≤0.30％，进一步优选为0.12％≤C≤0.29％。
硅(Si)：硅固溶在铁素体和奥氏体中提高它们的硬度和强度，然而硅含量过高会导致钢的韧性急剧下降。同时考虑到硅与氧的亲和力比铁强，焊接时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，因此含量不宜过多。将硅的含量控制为0.10％≤Si≤0.50％，进一步优选为0.15％≤Si≤0.50％。在一些实施方案中，将硅的含量控制为0.25％≤Si≤0.45％。
锰(Mn)：锰强烈增加钢的淬透性，降低耐磨钢转变温度和钢的临界冷却速度。但锰含量较高时，有使晶粒粗化的倾向，并增加钢的回火脆敏感性，而且容易导致铸坯中出现偏析和裂纹，降低钢板的性能。将锰的含量控制为0.50％≤Mn≤1.50％，进一步优选为0.60％≤Mn≤1.50％。在一些实施方案中，将锰的含量控制为0.65％≤Mn≤1.50％。
钼：钼可以细化晶粒，提高强度和韧性。钼在钢中存在于固溶体相和碳化物相中，因此，含钼钢同时具有固溶强化和碳化物弥散强化的作用。钼是减小回火脆性的元素，可以提高回火稳定。将钼的含量控制为0.01％≤Mo≤0.50％，进一步优选为0.10％≤Mo≤0.40％。
铌(Nb)：Nb的细化晶粒和析出强化作用，对提高材料强韧性贡献是极为显著的，是强烈的C、N化物的形成元素，强烈地抑制奥氏体晶粒长大。Nb通过晶粒细化同时提高钢的强度和韧性，Nb主要通过析出强化和相变强化来改善和提高钢的性能，Nb已经被作为HSLA钢中最有效的强化剂之一。因此，将铌控制为0.005％≤Nb≤0.050％，进一步优选为0.010％≤Nb≤0.045％。
钒(V)：钒的加入主要是为了细化晶粒，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，提高钢的强度和韧性。因此，将钒的含量控制为0.01％≤V≤0.10％，进一步优选为0.02％≤V≤0.10％。在一些实施方案中，将钒的含量控制为0.01％≤V≤0.08％。
钛(Ti)：钛是强碳化物形成元素之一，与碳形成细微的TiC颗粒。TiC颗粒细小，分布在晶界，达到细化晶粒的效果，较硬的TiC颗粒提高钢的耐磨性。因此，将钛的含量控制为0.005％≤Ti≤0.050％，进一步优选为0.015％≤Ti≤0.050％。
铝(Al)：铝和钢中氮能形成细小难溶的AlN颗粒，细化钢的晶粒。铝可细化钢的晶粒，固定钢中的氮和氧，减轻钢对缺口的敏感性，减小或消除钢的时效现象，并提高钢的韧性。因此，将铝的含量控制为0.010％≤Al≤0.060％，进一步优选为0.015％≤Al≤0.060％。在一些实施方案中，将铝的含量控制为0.02％≤V≤0.05％。
铬(Cr)：铬可以降低临界冷却速度、提高钢的淬透性。铬在钢中可以形成(Fe，Cr)3C、(Fe，Cr)7C3和(Fe，Cr)23C7等多种碳化物，提高强度和硬度。铬在回火时能阻止或减缓碳化物的析出与聚集，可以提高钢的回火稳定性。此外它还可以提高钢的耐酸性蚀性。在氧化性介质中，有使钢表面形成一层牢固而致密的铬的氧化物，使钢受到保护。铬溶于钢中能显著提高钢的电极电位，降低了因电极电位不同形成的电化学腐蚀。因此，将铬的含量控制为2.00％≤Cr≤5.00％，进一步优选为2.50％≤Cr≤5.00％。
硼(B)：硼增加钢的淬透性但含量过高将导致热脆现象，影响钢的焊接性能及热加工性能，因此需要严格控制B含量。因此，将硼的含量控制为 0.0005％≤B≤0.0050％，进一步优选为0.0008％≤B≤0.0050％。在一些实施方案中，将硼的含量控制为0.0015％≤B≤0.0040％。
锑(Sb)：锑可以提高钢的耐酸性腐蚀和增加合金的硬度。在酸性环境中，由于溶解而发生钝化，钢的表面形成一层富Sb等合金元素的钝化层，而具有高的耐酸腐蚀能力。因此，将锑的含量控制为0.01％≤Sb≤0.20％，进一步优选为0.03％≤Sb≤0.20％。在一些实施方案中，将锑的含量控制为0.05％≤Sb≤0.20％。
铜(Cu)：在钢中主要以固溶态和单质相沉淀析出状态存在，固溶的Cu起到固溶强化作用；由于Cu在铁素体中的固溶度随温度降低迅速减小，因而在较低温度下，以过饱和固溶的Cu以单质形式沉淀析出，起到析出强化作用。同时钢中加入Cu，可显著提高钢的抗大气腐蚀能力，当与磷共存时，效果特别显著。因此，当加入铜时，可将铜的含量控制为0.10％≤Cu≤0.40％，进一步优选为0.12％≤Cu≤0.40％。将磷元素的含量控制为0.010％≤P≤0.030％，进一步优选为0.012％≤P≤0.030％。
镍(Ni)：镍具有明显降低冷脆转变温度的作用，但含量过高易导致钢板表面氧化皮难以脱落，且成本显著增加。因此，当加入镍，将镍的含量控制为0.20％≤Ni≤1.00％，进一步优选为0.45％≤Ni≤0.8％。
稀土(RE)：在钢中添加稀土可以减少硫、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，提超高硬度。此外，稀土能提高钢的耐腐蚀性。稀土的含量不宜过多，否则会产生严重偏析，降低铸坯质量和力学性能。因此，将RE的含量控制为0.01％≤RE≤0.10％，进一步优选为0.02％≤RE≤0.90％。
硫：硫为有害元素，含量要严格控制，本公开所涉及钢种中控制硫含量S≤0.010％。
进一步地，本公开的钢板的布氏硬度为350-520HBW，如350～500HBW。在一些实施方案中，本公开的钢板的布氏硬度为370-520HBW。
进一步地，本公开的钢板包含板条马氏体组织、贝氏体及残余奥氏体，其中，贝氏体的体积分数为10-40％，残余奥氏体的体积分数为5-15％。
进一步地，本公开的钢板的厚度为15～40mm。
本公开的第二方面是一种耐腐蚀性耐磨钢板的制造方法，其特征在于，包括以下步骤：
(1)冶炼铸造步骤；
(2)加热步骤；
(3)轧制步骤；
(4)在线冷却步骤。
本公开的耐腐蚀性耐磨钢板的制造方法中，在所述(2)加热步骤中，板坯加热温度为1000-1200℃，保温1-3小时；在(3)轧制步骤中，粗轧开轧温度为900-1150℃(如1000～1100℃)，精轧终轧温度为780-880℃(如810～870℃)；在所述(4)在线冷却步骤中，冷却方式可为水冷，可水冷至350℃以下(如150～350℃)再空冷至室温，水冷的冷却速度可为15-50℃/s。
进一步地，本公开的钢板中，所述钢板的精轧变形率为60～80％。
有益效果
本公开的耐腐蚀性耐磨钢板及其制造方法相较于现有技术具有如下所述的优点以及有益效果：
本公开涉及的耐腐蚀性耐磨钢板具有较明显的优势，其通过控制碳和合金元素含量以及各热处理工艺得到的耐酸性和耐磨性均优异的耐磨钢板，且成本低、工艺简单、强硬度高，机械加工性能优异，易焊接，且具有优异的耐酸性腐蚀性能，具体而言：
1、从化学成分上看，本公开的耐腐蚀性耐磨钢板的合金成分以低碳低合金为主，充分利用Cr、Mo、Ni、Cu、Nb、Ti等合金元素的细化、强化等特点，保证钢板具有良好的力学性能和较好的耐腐蚀性能等，本公开的耐腐蚀性耐磨钢板具有高强度、高硬度和优异的耐酸性及耐碱性等优点，并具有良好的焊接性能。
2、从生产工艺上看，本公开的耐腐蚀性耐磨钢板通过对制造方法中的开、终轧温度、精轧变形率及冷却速度等工艺参数的控制提高组织细化、强化效果，进而减少碳和合金元素含量，得到力学性能和焊接性能等均十分优异的钢板。此外，该工艺还具有生产流程短，效率高，节约能源，成本低等特点。
3、本公开的耐腐蚀性耐磨钢板，充分利用合金元素添加及控轧控冷工艺得到板条马氏体组织及残余奥氏体，有益于耐磨钢板强度、硬度及韧性的良好匹配。残余奥氏体含量越高，自腐蚀电位越高，残余奥氏体含量越低，自腐蚀电位越低，残余奥氏体的增多有助于提高材料的耐腐蚀性。
附图说明
图1为本公开钢板的金相组织图。
具体实施方式
以下由特定的具体实施例说明本公开的实施方式，本领域技术人员可由本说明书所揭示的内容轻易地了解本公开的其他优点及功效。虽然本公开的描述将结合较佳实施例一起介绍，但这并不代表此发明的特征仅限于该实施方式。恰恰相反，结合实施方式作发明介绍的目的是为了覆盖基于本公开的权利要求而有可能延伸出的其它选择或改造。为了提供对本公开的深度了解，以下描述中将包含许多具体的细节。本公开也可以不使用这些细节实施。此外，为了避免混乱或模糊本公开的重点，有些具体细节将在描述中被省略。
实施例1-8以及对比例1
表1列出了实施例1-8以及对比例1的耐腐蚀性耐磨钢板对应的各化学元素质量百分比。
表1：实施例1-8和对比例1的化学成分(wt.％)

本公开实施例1-8耐腐蚀性耐磨钢板采用以下步骤制得：
实施例1-8的耐磨钢板的制造方法为：
(1)冶炼、铸造步骤、加热、轧制、在线淬火等步骤；
(2)加热步骤，板坯加热温度为1000-1200℃，保温1-3小时；
(3)轧制步骤，粗轧开轧温度为900-1150℃，精轧终轧温度为780-880℃；
(4)在线淬火等步骤，采用水冷冷却至350℃(停冷温度)以下再空冷至室温，其中水冷冷却速度15-50℃/s。
对比例1的耐磨钢板，除了原料成分以及各工序中的具体工艺参数与上述实施例1-8不同外，以上述相同的步骤制造耐磨钢板。实施例1-8和对比例1的具体工艺参数如表2所示。
表2：实施例1-8和对比例1中的具体工艺参数

对实施例1-8以及对比例1的耐腐蚀耐磨钢板进行耐酸性测试、耐碱性测试、力学性能测试，所得测试结果列于表3～5中。
其中，耐酸性测试方法为：采用恒温试验槽，在“温度23±2℃、10％H2SO4+3.5％NaCl、全浸24小时”条件下进行腐蚀试验。具体方法参照《JB/T7901-2001金属材料实验室均匀腐蚀全浸试验方法》；
耐碱性测试方法为：在碱性气氛下进行周浸实验，实验温度45±2℃，相对湿度70±5％，周浸速度：1/60(圈/分钟)，PH值9.5；
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以及对比例1的耐磨钢样品的表面位置进行硬度测试，以得到对应的布氏硬度。
表3：实施例1-8和对比例1的腐蚀性能
表4：实施例1-8和对比例1的耐碱性腐蚀性能

表5：实施例1-8和对比例1的力学性能
由表1-5可以看出，通过优化化学元素以及控制制造工艺得到的实施例1-8的钢板的酸腐蚀速率最大仅为0.33g/(m2·h)，碱腐蚀速率最大仅为0.51g/(m2·h)，硬度(HBW)最小也为375。对比例1的化学元素以及制造方法与本发明不同，对比例1的酸腐蚀速率为3.51g/(m2·h)，碱腐蚀速率为2.56g/(m2·h)，硬度(HBW)为235。对比例1的钢板的酸腐蚀和碱腐蚀速率远远大于本发明的钢板腐蚀速率，即耐酸性耐碱性较差，且硬度也较差。即通过优化化学元素以及控制制造工艺得到的本发明的 钢板的耐酸性耐碱性得到了极大的提高。耐磨性钢板的耐酸性耐碱性优异，且硬度HBW大于375。
综上所述，可以看出，通过合理的化学成分设计并结合优化工艺，本公开的钢板的同时具有优异的耐酸性、耐碱性和耐磨性，且其生产工艺简单，可以用于工作环境恶劣，提高使用寿命，具有广阔的应用前景。
需要说明的是，本公开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，所有不与本公开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，都可纳入本公开的保护范围。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，以上所列举的实施例仅为本公开的具体实施例。显然本公开不局限于以上实施例，随之做出的类似变化或变形是本领域技术人员能从本公开公开的内容直接得出或者很容易便联想到的，均应属于本公开的保护范围。

Claims (15)

  1. 一种耐腐蚀性耐磨钢板，其特征在于，按重量百分比计，包含：C：0.15％≤C≤0.25％；Si：0.10％≤Si≤0.50％；Mn：0.50％≤Mn≤1.50％；Mo：0.01％≤Mo≤0.50％；Nb：0.005％≤Nb≤0.050％；V：0.01％≤V≤0.10％；Ti：0.005％≤Ti≤0.050％；Al：0.010％≤Al≤0.060％；Cr：2.00％≤Cr≤5.00％；B：0.0005％≤B≤0.0050％；和P：0.010％≤P≤0.030％；还包含：Cu：0.10≤Cu≤0.40％、Ni：0.20≤Ni≤1.00％、RE：0.01≤RE≤0.10％和Sb：0.01％≤Sb≤0.20％中的一种以上，余量为Fe和不可避免的杂质。
  2. 一种耐腐蚀性耐磨钢板，其特征在于，除Fe和不可避免的杂质，按重量百分比计，包含：0.10％≤C≤0.30％；0.10％≤Si≤0.50％；0.50％≤Mn≤1.50％；0.01％≤Mo≤0.50％；0.005％≤Nb≤0.050％；0.01％≤V≤0.10％；0.005％≤Ti≤0.050％；0.010％≤Al≤0.060％；2.00％≤Cr≤5.00％；0.0005％≤B≤0.0050％；和P：0.010％≤P≤0.030％；还包含：Cu：0.10≤Cu≤0.40％、Ni：0.20≤Ni≤1.00％、RE：0.01≤RE≤0.10％和Sb：0.01％≤Sb≤0.20％中的一种以上。
  3. 一种耐腐蚀性耐磨钢板，其特征在于，按重量百分比计，该耐腐蚀性耐磨钢板包含：C：0.10％≤C≤0.30％；Si：0.10％≤Si≤0.50％；Mn：0.50％≤Mn≤1.50％；Mo：0.01％≤Mo≤0.50％；Nb：0.005％≤Nb≤0.050％；V：0.01％≤V≤0.10％；Ti：0.005％≤Ti≤0.050％；Al：0.010％≤Al≤0.060％；Cr：2.00％≤Cr≤5.00％；B：0.0005％≤B≤0.0050％；Sb：0.01％≤Sb≤0.20％；P：0.010％≤P≤0.030％；还包含：Cu：0.10≤Cu≤0.40％、Ni：0.20≤Ni≤1.00％和RE：0.01≤RE≤0.10％中的一种以上，余量为Fe和不可避免的杂质。
  4. 如权利要求1～3中任一项所述的耐腐蚀性耐磨钢板，其特征在于：
    按重量百分比计：0.10≤Mo≤0.40％；0.010％≤Nb≤0.045％；0.02％≤V≤0.10％；0.015％≤Ti≤0.050％；和/或
    按重量百分比计：2.50％≤Cr≤5.00％；0.012％≤P≤0.030％；0.12≤Cu≤0.40％；0.20≤Ni≤0.90％。
  5. 如权利要求1～3中任一项所述的耐腐蚀性耐磨钢板，其特征在于，按重量百分比计，所述不可避免的杂质中S：＜0.010％。
  6. 如权利要求1～3中任一项所述的耐腐蚀性耐磨钢板，其特征在于，按重量百分比计：0.0015％≤B≤0.0040％。
  7. 如权利要求1～3中任一项所述的耐腐蚀性耐磨钢板，其特征在于，按重量百分比计，所述耐腐蚀性耐磨钢板包含：C：0.10％≤C≤0.30％；Si：0.25％≤Si≤0.45％；Mn：0.65％≤Mn≤1.50％；Mo：0.10％≤Mo≤0.35％；Nb：0.01％≤Nb≤0.045％；V：0.01％≤V≤0.08％；Ti：0.010％≤Ti≤0.045％；Al：0.020％≤Al≤0.050％；Cr：2.30％≤Cr≤4.60％；B：0.0015％≤B≤0.0040％；Sb：0.06％≤Sb≤0.19％；P：0.010％≤P≤0.016％；S：≤0.005％；Cu：≤0.35％；Ni：≤0.75％；RE：≤0.10％；余量为Fe和不可避免的杂质。
  8. 如权利要求1～7中任一项所述的耐腐蚀性耐磨钢板，其特征在于，所述钢板的布氏硬度为350～520HBW，优选350～500HBW。
  9. 如权利要求1～8中任一项所述的耐腐蚀性耐磨钢板，其特征在于，所述钢板中包含板条马氏体组织、贝氏体及残余奥氏体，其中，所述贝氏体的体积分数为10～40％，所述残余奥氏体的体积分数为5～15％。
  10. 如权利要求1～9中任一项所述的耐腐蚀性耐磨钢板的制造方法，其特征在于，包括：
    (1)冶炼、铸造步骤；
    (2)加热步骤；
    (3)轧制步骤，精轧终轧温度为780-880℃；
    (4)在线冷却步骤。
  11. 如权利要求10所述的耐腐蚀性耐磨钢板的制造方法，其特征在于，在线冷却步骤(4)中通过水冷冷却，所述水冷的冷却速度15～50℃/s。
  12. 如权利要求10所述的耐腐蚀性耐磨钢板的制造方法，其特征在于，在所述(2)加热步骤中，板坯加热温度为1000～1200℃，保温1-3小时；在在线冷却步骤(4)中，水冷冷却至350℃以下再空冷至室温。
  13. 如权利要求10所述的耐腐蚀性耐磨钢板的制造方法，其特征在于，所述钢板的精轧变形率为60％～80％。
  14. 如权利要求10所述的耐腐蚀性耐磨钢板的制造方法，其特征在于，步骤(3)中，粗轧开轧温度为900～1150℃。
  15. 如权利要求12所述的耐腐蚀性耐磨钢板的制造方法，其特征在于，(4)轧制步骤中，水冷冷却至150～350℃再空冷至室温。
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