WO2019119725A1 - 一种布氏硬度大于550hb的高级别低合金耐磨钢板及制造方法 - Google Patents

一种布氏硬度大于550hb的高级别低合金耐磨钢板及制造方法 Download PDF

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WO2019119725A1
WO2019119725A1 PCT/CN2018/088129 CN2018088129W WO2019119725A1 WO 2019119725 A1 WO2019119725 A1 WO 2019119725A1 CN 2018088129 W CN2018088129 W CN 2018088129W WO 2019119725 A1 WO2019119725 A1 WO 2019119725A1
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steel plate
alloy wear
resistant steel
grade low
brinell hardness
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PCT/CN2018/088129
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English (en)
French (fr)
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姜在伟
邓想涛
闫强军
王昭东
杨柳
靳建锋
吴俊平
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南京钢铁股份有限公司
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Priority to AU2018387506A priority Critical patent/AU2018387506A1/en
Publication of WO2019119725A1 publication Critical patent/WO2019119725A1/zh

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    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/18—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

Definitions

  • the invention relates to the field of wear-resistant steel manufacturing, in particular to a high-grade low-alloy wear-resistant steel plate with a Brinell hardness of more than 550HB and a manufacturing method thereof.
  • low-alloy wear-resistant steel plate Compared with traditional wear-resistant cast steel, low-alloy wear-resistant steel plate has the advantages of low alloy content, high low-temperature impact toughness, bendable molding, etc., as well as flexible production and low production cost, and is widely used in work. Poor conditions, requiring high strength and hardness, good wear resistance engineering, mining, construction, agriculture, cement, port, electricity and metallurgical machinery and equipment manufacturing, such as bulldozers, loaders, excavators, dump trucks, ball mills and Mining machinery, grabs, stacker and reclaimer, conveying material bending structure, etc. These parts are generally operated under the extremely harsh conditions of dry and wet environment. It is difficult to replace, and the steel plate is required to have high strength, hardness, excellent wear resistance and corrosion resistance, and good welding performance. Equipped with a higher service life.
  • the technical problem to be solved by the present invention is that, in view of the shortcomings of the above prior art, a high-grade low-alloy wear-resistant steel plate with a Brinell hardness of more than 550HB and a manufacturing method thereof are proposed, which adopt a medium-high carbon and alloyed composition design and pass Alloying elements such as carbon, manganese, chromium, nickel, molybdenum and copper, and micro-alloying elements such as niobium, titanium and vanadium, and auxiliary control of rolling and off-line heat treatment, so that the obtained steel sheet has a Brinell hardness of more than 550HB.
  • the high level, -20 ° C low temperature impact toughness ⁇ 20J while ensuring extremely high wear resistance, but also has good corrosion resistance.
  • a high-grade low-alloy wear-resistant steel plate having a Brinell hardness of more than 550HB comprises the following components by weight percentage: C: 0.33-0.41%, Si: 0.50-0.60%, Mn: 0.30-0.80%, P ⁇ 0.012 %, S ⁇ 0.003%, Cr: 0.30-1.00%, Mo: 0.20-0.60%, Ni: 0.80-1.20%, Ti: 0.008-0.030%, Nb: 0.015-0.050%, V: 0.080-0.150%, B : 0.0008-0.0025%, N ⁇ 0.0040%, O ⁇ 0.0025%, and the balance is Fe and unavoidable impurities.
  • the invention discloses a method for manufacturing a high-grade low-alloy wear-resistant steel plate with a Brinell hardness of more than 550HB, comprising the following processes: hot metal desulfurization pretreatment-converter smelting-LF+RH refining-continuous casting or die casting-casting hot charging-casting billet Heating - phosphorus removal - rolling - controlled cooling or air cooling - flaw detection - shot blasting - quenching - tempering - straightening - cutting - sampling - printing marking - inspection - storage, slab or billet heated at 1180-1220 ° C Rolling is performed in the austenite recrystallization zone and the non-recrystallization zone respectively; the recrystallization zone rolling requires a pass reduction ratio of ⁇ 12%, a finish rolling temperature finish rolling temperature ⁇ 980 ° C; and the non-recrystallization zone Rolling requirements cumulative rolling rate ⁇ 50%, rolling rolling temperature finishing rolling temperature ⁇ 950 ° C, finishing rolling temperature ⁇
  • the microstructure obtained by the present invention is mainly martensite structure, and the wear resistance is improved mainly by the high hardness and good toughness of martensite.
  • the aforementioned high-grade low-alloy wear-resistant steel plate having a Brinell hardness of more than 550HB has a tensile strength of more than 1900 MPa, a hardness of more than 570 HBW, and a low temperature impact toughness of -20 °C of -20 °C.
  • the continuous casting slab has a thickness of 150-300 mm.
  • the invention is obtained by the composite addition of various alloying elements such as chromium, nickel and molybdenum, and the obtained steel plate has good corrosion resistance while ensuring extremely high wear resistance, and the effects of each element are as follows:
  • Carbon is the most critical element for high strength and hardness of wear-resistant steel.
  • carbon is the most important element, and carbon element can significantly improve the hardenability of the steel sheet.
  • the toughness and weldability of the steel sheet are lowered. Therefore, if the steel plate needs to obtain high hardness and has certain toughness and weldability, the carbon content of the present invention is 0.33-0.41%.
  • Silicon element has solid solution strengthening effect in steel, and its solubility in austenite is large. Increasing silicon content is beneficial to increase the strength and hardness of steel, and can improve the stability of austenite. However, if the content of silicon is too high, the toughness of the steel will decrease, and the viscosity of the steel sheet with high silicon content will be large when heated, and the descaling after the furnace is difficult, resulting in serious red scale on the surface of the steel sheet after rolling and poor surface quality. In addition, high silicon is not conducive to the welding performance of steel plates. Considering the influence of various aspects of the silicon element, the content of the silicon element of the present invention is 0.50-0.60%.
  • Manganese can expand into the austenite region and stabilize the austenite structure. Its ability is second only to the alloying element nickel. It is an inexpensive stable austenite and strengthening alloying element, and manganese can increase the hardenability of steel. Reduce the critical cooling rate of martensite formation. However, when the content of manganese is too high, the steel sheet tends to coarsen the crystal grains, and the tempering and brittle sensitivity of the steel is increased, and segregation and cracking in the billet are easily caused, and the performance of the steel sheet is lowered.
  • the present invention combines the control of its carbon element and sulfur element, and the content of manganese element is controlled to be 0.30-0.80%.
  • Sulfur and phosphorus Sulfur is easily combined with manganese in steel to form vulcanized inclusions, especially for the transverse plasticity and toughness of steel. Therefore, the sulfur content should be as low as possible. Phosphorus is also a harmful element in steel, which seriously damages the plasticity and toughness of the steel sheet. For the present invention, both sulfur and phosphorus are inevitable impurity elements, and should be as low as possible. Considering the actual steelmaking level of the steel mill, the present invention requires P ⁇ 0.012% and S ⁇ 0.003%.
  • Chromium reduces the critical cooling rate and improves the hardenability of steel. Chromium can form various carbides such as (Fe,Cr)3C, (Fe,Cr)7C3 and (Fe,Cr)23C7 in steel to improve strength and hardness. Chromium can prevent or slow the precipitation and aggregation of carbides during tempering, which can improve the tempering stability of steel. In the present invention, the content of chromium element should be controlled to be 0.30-1.00%.
  • Molybdenum can significantly refine grains and improve strength and toughness. Molybdenum can reduce the temper brittleness of steel, and at the same time, it can precipitate very fine carbides during tempering, which significantly strengthens the steel matrix. Since molybdenum is a very expensive strategic alloying element, no more than 0.60% of molybdenum may be added in the present invention. In the present invention, the molybdenum element content is from 0.20 to 0.60%.
  • Nickel is an element that stabilizes austenite. Adding nickel to quenched and tempered steel can greatly improve the toughness of steel, especially low temperature toughness.
  • a high carbon element is added in the design of the alloy, which makes the toughness and plasticity of the steel sheet very poor.
  • the content of nickel in the present invention is from 0.80 to 1.20%.
  • Titanium is a strong carbide forming element. The addition of trace amounts of titanium to steel helps to fix the nitrogen in the steel. The TiN formed can cause the austenite grains to grow abnormally when the billet is heated. Grain size. The titanium content of the present invention is controlled to be from 0.008 to 0.030%.
  • ⁇ element in steel can prevent recrystallization and hinder recrystallized grain growth and increase strength.
  • niobium elements can strongly form niobium carbides and nitrides in steel, which affects the properties of steel, and niobium can refine grains and reduce the superheat sensitivity and temper brittleness of steel.
  • the content of the lanthanum element is controlled to be 0.015 to 0.050%.
  • Hardenable element plays an important role in improving the hardenability of steel sheets, especially the hardenability of thick gauge steel sheets. Adding a small amount of boron to steel can greatly increase the hardenability of the steel plate, and the boron resources are rich and cheap. Adding a small amount of boron can significantly save valuable alloying elements such as manganese, nickel, chromium and molybdenum. Add to. However, excessive boron will increase the segregation of grain boundaries, thus reducing the ductility of steel materials. In the present invention, the content of boron element is from 0.0008 to 0.0025%.
  • converter blowing and vacuum treatment is to ensure the basic composition requirements of molten steel, remove harmful gases such as oxygen and hydrogen in steel, and add necessary alloying elements such as manganese and titanium to adjust the alloying elements.
  • the beneficial effects of the present invention are as follows: 1.
  • the steel sheet obtained by the present invention has an extremely high hardness and a Brinell hardness of more than 570 HB. 2.
  • the method of hot rolling and offline heat treatment of the invention is produced, and the production process is simple.
  • the microstructure obtained by the present invention is mainly martensite structure, and the wear resistance is improved mainly by the high hardness and good toughness of martensite.
  • the wear-resistant steel plate obtained by the invention has good low temperature impact toughness and cold bending forming performance, and satisfies the low temperature impact toughness of -20 ° C ⁇ 20 J. 5.
  • the steel sheet obtained by the invention has good corrosion resistance in addition to excellent wear resistance.
  • This embodiment is a high-grade low-alloy wear-resistant steel plate having a Brinell hardness of more than 550HB.
  • the steel plate includes the following components by weight percentage: C: 0.41%, Si: 0.50%, Mn: 0.56%, P ⁇ 0.012%, S ⁇ 0.003%, Cr: 0.65%, Mo: 0.36%, Ni: 1.20%, Ti: 0.008-0.030%, Nb: 0.015-0.050%, V: 0.080-0.150%, B: 0.0008-0.0025%, N ⁇ 0.0040%, O ⁇ 0.0025%, the balance being Fe and unavoidable impurities.
  • the molten steel obtained by the above-mentioned ratio smelting is subjected to vacuum degassing treatment, and then continuous casting is performed, and the thickness of the continuous casting blank is 150 mm, and the slab is heated to 1180 ° C.
  • the furnace temperature after 180 min of heat preservation, is taken out for austenite recrystallization zone rolling and non-recrystallization zone rolling, wherein the recrystallization zone finish rolling temperature is 1025 ° C, and the non-recrystallization zone finishing rolling temperature is 910 ° C, the final of the steel plate
  • the rolling thickness was 12 mm, air-cooled to room temperature after rolling, and then quenched and tempered, the quenching temperature was 880 ° C, and the tempering temperature was 170 ° C.
  • This embodiment is a high-grade low-alloy wear-resistant steel plate with a Brinell hardness of more than 550HB.
  • the steel plate includes the following components by weight percentage: C: 0.33%, Si: 0.52%, Mn: 0.80%, P ⁇ 0.012%, S ⁇ 0.003%, Cr: 0.68%, Mo: 0.60%, Ni: 0.95%, Ti: 0.008-0.030%, Nb: 0.015-0.050%, V: 0.080-0.150%, B: 0.0008-0.0025%, N ⁇ 0.0040%, O ⁇ 0.0025%, the balance being Fe and unavoidable impurities.
  • the molten steel obtained by the above-mentioned ratio smelting is subjected to vacuum degassing treatment, and then continuous casting is performed, and the thickness of the continuous casting blank is 220 mm, and the steel slab is heated to 1200 ° C.
  • the furnace temperature after 200 min of heat preservation, is taken out for austenite recrystallization zone rolling and non-recrystallization zone rolling, wherein the recrystallization zone finishing rolling temperature is 1030 ° C, and the non-recrystallization zone finishing rolling temperature is 850 ° C, the final of the steel plate
  • the rolling thickness was 40 mm, air-cooled to room temperature after rolling, and then quenched and tempered, the quenching temperature was 920 ° C, and the tempering temperature was 250 ° C.
  • This embodiment is a high-grade low-alloy wear-resistant steel plate with a Brinell hardness of more than 550HB.
  • the steel plate includes the following components by weight percentage: C: 0.40%, Si: 0.51%, Mn: 0.64%, P ⁇ 0.012%, S ⁇ 0.003%, Cr: 1.00%, Mo: 0.42%, Ni: 0.80%, Ti: 0.008-0.030%, Nb: 0.015-0.050%, V: 0.080-0.150%, B: 0.0008-0.0025%, N ⁇ 0.0040%, O ⁇ 0.0025%, the balance being Fe and unavoidable impurities.
  • the molten steel obtained by the above ratio smelting is subjected to vacuum degassing treatment, and then continuous casting is performed, and the thickness of the continuous casting blank is 260 mm, and the slab is heated to 1220 ° C.
  • the furnace temperature after 220 min of heat preservation, is taken out for austenite recrystallization zone rolling and non-recrystallization zone rolling, wherein the recrystallization zone finishing rolling temperature is 1040 ° C, the non-recrystallization zone finishing rolling temperature is 890 ° C, the final of the steel plate
  • the rolling thickness was 25 mm, air-cooled to room temperature after rolling, and then quenched and tempered, the quenching temperature was 930 ° C, and the tempering temperature was 180 ° C.
  • This embodiment is a high-grade low-alloy wear-resistant steel plate having a Brinell hardness of more than 550HB.
  • the steel plate includes the following components by weight percentage: C: 0.38%, Si: 0.60%, Mn: 0.30%, P ⁇ 0.012%, S ⁇ 0.003%, Cr: 0.30%, Mo: 0.20%, Ni: 0.50%, Ti: 0.008-0.030%, Nb: 0.015-0.050%, V: 0.080-0.150%, B: 0.0008-0.0025%, N ⁇ 0.0040%, O ⁇ 0.0025%, the balance being Fe and unavoidable impurities.
  • the molten steel obtained by the above ratio smelting is subjected to vacuum degassing treatment, and then continuous casting is performed, and the thickness of the continuous casting blank is 260 mm, and the steel slab is heated to 1180 ° C.
  • the furnace temperature after 180 minutes of heat preservation, is taken out for austenite recrystallization zone rolling and non-recrystallization zone rolling, wherein the recrystallization zone finish rolling temperature is 980 ° C, the non-recrystallization zone finishing rolling temperature is 830 ° C, the final of the steel plate
  • the rolling thickness was 25 mm, air-cooled to room temperature after rolling, and then subjected to off-line quenching and tempering treatment, the quenching temperature was 820 ° C, and the tempering temperature was 100 ° C.
  • the wear resistance steel of the present invention has a Brinell hardness of more than 550HB, a tensile strength of more than 1800 MPa, an elongation of more than 8%, and an impact energy of -20 ° C of more than 27 J, and the wear-resistant steel according to the present invention can be seen. It has good resistance to deformation and wear, and also has good low temperature impact toughness.

Abstract

一种布氏硬度大于550HB的低合金耐磨钢板，按重量百分比计包括以下组分：C0.33-0.41％、Si0.50-0.60％、Mn0.30-0.80％、P≤0.012％、S≤0.003％、Cr0.30-1.00％、Mo0.20-0.60％、Ni0.80-1.20％、Ti0.008-0.030％、Nb0.015-0.050％、V0.080-0.150％、B0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。该钢板采用中高碳和合金化的成分设计，并通过碳、锰、铬、镍、钼和铜等合金元素以及铌、钛、钒等微合金元素的相互配合作用，并辅控制轧制和离线热处理的方法，使获得的钢板具有布氏硬度大于550HB，-20℃低温冲击韧性≥20J。

Description

一种布氏硬度大于550HB的高级别低合金耐磨钢板及制造方法 技术领域
本发明涉及耐磨钢制造领域，具体涉及一种布氏硬度大于550HB的高级别低合金耐磨钢板及其制造方法。
背景技术
低合金耐磨钢板相对于传统的耐磨铸钢，具有合金含量低，低温冲击韧性高，可折弯成型等良好的综合性能，以及生产灵活方便、生产成本低等优点，被广泛应用于工作条件恶劣，要求高的强度和硬度、耐磨性好的工程、采矿、建筑、农业、水泥、港口、电力以及冶金等机械装备制造，如推土机，装载机，挖掘机，自卸车，球磨机及各种矿山机械、抓斗、堆取料机、输料弯曲结构等。该类部件一般都在干湿交加的环境极其恶劣的条件下工作，更换困难，要求钢板具有高的强度、硬度及优异的耐磨和耐蚀性能，以及良好的焊接性能等，以此来保证装备有更高的使用寿命。
目前，已经有不少关于低合金耐磨钢的专利报导，但是其级别均较低，且硬度韧塑性和成型性均不理想，焊接性能较差，不同时具备优异的耐磨和耐蚀性能，难以满足装备制造大型化、轻量化和长寿命化制造的需求，尤其是对于布氏硬度大于550HB的低合金耐磨钢板，现有技术没有相关公开。
发明内容
本发明所要解决的技术问题是，针对以上现有技术存在的缺点，提出一种布氏硬度大于550HB的高级别低合金耐磨钢板及制造方法，采用中高碳和合金化的成分设计，并通过碳、锰、铬、镍、钼和铜等合金元素以及铌、钛、钒等微合金元素的相互配合作用，并辅控制轧制和离线热处理的方法，使获得的钢板具有布氏硬度大于550HB的高级别，-20℃低温冲击韧性≥20J，在保证极高耐磨性能的同时，还具有良好的耐蚀性能。
本发明解决以上技术问题的技术方案是：
一种布氏硬度大于550HB的高级别低合金耐磨钢板，钢板按重量百分比计包括以下组分：C：0.33-0.41％、Si：0.50-0.60％、Mn：0.30-0.80％、P≤0.012％、S≤0.003％、Cr：0.30-1.00％、Mo：0.20-0.60％、Ni：0.80-1.20％、Ti：0.008-0.030％、Nb：0.015-0.050％、V：0.080-0.150％、B：0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。
本发明的布氏硬度大于550HB的高级别低合金耐磨钢板的制造方法，包括以下流程：铁水脱硫预处理-转炉冶炼-LF+RH精炼-连铸或模铸-铸坯热装-铸坯加热-除磷-轧制-控冷或空冷-探伤-抛丸-淬火-回火-矫直-切割-取样-喷印标识-检验-入库，铸坯或钢坯于1180-1220℃加热后在奥氏体再结晶区和未再结晶区分别进行轧制；所述再结晶区轧制要求道次压下率≥12％，终轧温度终轧温度≥980℃；所述未再结晶区轧制要求累积压下率≥50％，开轧温度终轧温度≤950℃，终轧温度≥800℃；轧后控冷或空冷至室温，然后进行离线热处理，其中淬火温度为：820-930℃，回火温度为100-250℃。
本发明进一步限定的技术方案是：
前述的布氏硬度大于550HB的高级别低合金耐磨钢板，钢板中，马氏体在组织中的含量大于95％。本发明明得到的组织主要为马氏体组织，主要通过马氏体的高硬度和良好的韧性来提高耐磨性能。
前述的布氏硬度大于550HB的高级别低合金耐磨钢板，钢板的抗拉强度大于1900MPa，硬度大于570HBW，-20℃低温冲击韧性≥20J。
前述的布氏硬度大于550HB的高级别低合金耐磨钢板的制造方法，连铸的铸坯厚度为150-300mm。
本发明由于铬、镍和钼等多种合金元素的复合添加，获得的钢板在保证极高耐磨性能的同时，还具有良好的耐蚀性能，各元素的作用如下：
碳：碳元素是耐磨钢板获得高的强度和硬度的最关键元素。对于要获得组织为95％及以上马氏体组织以及布氏硬度在570-630HB的钢板而言，碳元素是最重要的元素，且碳元素可以显著提高钢板的淬透性。但由于碳元素的增加，会降低钢板的韧塑性和焊接性能。所以如果钢板既要获得高硬度，又要具备一定的韧塑性和焊接性能，综合考虑，本发明的碳元素含量为0.33-0.41％。
硅：硅元素在钢中起固溶强化作用，其在奥氏体中的溶解度较大，提高硅含量有利于提高钢的强度和硬度，且能提高奥氏体的稳定性。但硅元素含量过高会导致钢的韧性下降，且高硅含量的钢板加热时的氧化皮粘度较大，出炉后除鳞困难，导致轧后钢板表面红色氧化皮严重、表面质量较差。此外，高硅还不利于钢板的焊接性能。综合考虑硅元素各方面的影响，本发明硅元素的含量为0.50-0.60％。
锰：锰元素能够扩到奥氏体区，稳定奥氏体组织，其能力仅次于合金元素镍，是廉价的稳定奥氏体和强化合金元素，同时锰元素能够增加钢的淬透性，降低马氏体形成的临界冷速。但锰元素含量过高时，会使钢板有使晶粒粗化的倾向，并增加钢的回火脆敏感性，且容易导致铸坯中出现偏析和裂纹，降低钢板的性能。本发明结合其碳元素和硫元素的控制，锰元素的含量控制在0.30-0.80％。
硫和磷：硫元素在钢中易与锰元素等结合形成硫化夹杂物，尤其对钢的横向塑性和韧性不利，因此硫的含量应尽可能地低。磷也是钢中的有害元素，严重损害钢板的塑性和韧性。对于本发明而言，硫和磷均是不可避免的杂质元素，应该越低越好，考虑到钢厂实际的炼钢水平，本发明要求P≤0.012％、S≤0.003％。
铬：铬元素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。在本发明中，铬元素的含量应控制为0.30-1.00％。
钼：钼元素能显著地细化晶粒，提高强度和韧性。钼元素能减少钢的回火脆性，同时回火时还能析出非常细小的碳化物，显著强化钢的基体。由于钼元素是非常昂贵的战略合金元素，所以本发明中可添加不超过0.60％的钼。本发明中，钼元素含量为0.20-0.60％。
镍：镍元素是稳定奥氏体的元素，在调质钢中加镍元素，可以大幅提高钢的韧性尤其是低温韧性。在本发明中，为了保证得到极高的强度和硬度，在合金设计时添加了较高的碳元素，从而会使得钢板的韧塑性非常差。为了保证钢板既具有高的强度和硬度，而且还具有一定的韧塑性，同时还考虑到镍元素属于贵重合金元素，所以本发明中镍的含量为0.80-1.20％。
钛：钛元素是强碳化物形成元素，钢中加入微量的钛元素有利于固定钢中的氮，形成的TiN，能使钢坯加热时奥氏体晶粒出现异常的长大，细化原始奥氏体晶粒度。本发明钛含量控制在0.008-0.030％。
铌：铌元素在钢中可以阻止再结晶和阻碍再结晶晶粒长大，提高强度。同时，铌元素在钢中可强烈地形成铌的碳化物和氮化物，从而影响钢的性能，且铌元素能细化晶粒和降低钢的过热敏感性及回火脆性。在本发明中，铌元素的含量控制为0.015-0.050％。
硼：淬透性元素，对提高钢板淬透性尤其是厚规格钢板的淬透性有着重要作用。钢中添加少量的硼元素即可起到较大的增加钢板的淬透性，且硼元素资源富有，价格便宜，添加少量的硼可以显著的节省锰、镍、铬、钼等贵重的合金元素添加。但过多的硼元素会增加晶界的偏聚，从而降低钢铁材料的韧塑性。在本发明中，硼元素的含量为：0.0008-0.0025％。
转炉吹炼和真空处理的目的是确保钢液的基本成分要求，去除钢中的氧、氢等有害气体， 并加入锰、钛等必要的合金元素，进行合金元素的调整。
本发明的有益效果是：1.本发明获得的钢板具有极高的硬度，满足布氏硬度大于570HB。2.本发明热轧和离线热处理的方式生产，生产工艺简单。3.本发明得到的组织主要为马氏体组织，主要通过马氏体的高硬度和良好的韧性来提高耐磨性能。4.本发明得到的耐磨钢板的低温冲击韧性和冷弯成型性能良好，满足-20℃低温冲击韧性≥20J。5.本发明获得的钢板除了具有极佳的耐磨性能外，还具有良好的耐蚀性能。
具体实施方式
实施例1
本实施例是一种布氏硬度大于550HB的高级别低合金耐磨钢板，钢板按重量百分比计包括以下组分：C：0.41％、Si：0.50％、Mn：0.56％、P≤0.012％、S≤0.003％、Cr：0.65％、Mo：0.36％、Ni：1.20％、Ti：0.008-0.030％、Nb：0.015-0.050％、V：0.080-0.150％、B：0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。
本实施例布氏硬度大于550HB的高级别低合金耐磨钢板的制造方法，将上述配比冶炼完成的钢水经真空脱气处理后进行连铸，连铸坯厚度150mm，将钢坯加热至1180℃的炉温，保温180min后出炉进行奥氏体再结晶区轧制和未再结晶区轧制，其中再结晶区终轧温度为1025℃，未再结晶区终轧温度为910℃，钢板的最终轧制厚度为12mm，轧后空冷至室温，然后进行淬火和回火处理，淬火温度为880℃，回火温度为170℃。
实施例2
本实施例是一种布氏硬度大于550HB的高级别低合金耐磨钢板，钢板按重量百分比计包括以下组分：C：0.33％、Si：0.52％、Mn：0.80％、P≤0.012％、S≤0.003％、Cr：0.68％、Mo：0.60％、Ni：0.95％、Ti：0.008-0.030％、Nb：0.015-0.050％、V：0.080-0.150％、 B：0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。
本实施例布氏硬度大于550HB的高级别低合金耐磨钢板的制造方法，将上述配比冶炼完成的钢水经真空脱气处理后进行连铸，连铸坯厚度220mm，将钢坯加热至1200℃的炉温，保温200min后出炉进行奥氏体再结晶区轧制和未再结晶区轧制，其中再结晶区终轧温度为1030℃，未再结晶区终轧温度为850℃，钢板的最终轧制厚度为40mm，轧后空冷至室温，然后进行淬火和回火处理，淬火温度为920℃，回火温度为250℃。
实施例3
本实施例是一种布氏硬度大于550HB的高级别低合金耐磨钢板，钢板按重量百分比计包括以下组分：C：0.40％、Si：0.51％、Mn：0.64％、P≤0.012％、S≤0.003％、Cr：1.00％、Mo：0.42％、Ni：0.80％、Ti：0.008-0.030％、Nb：0.015-0.050％、V：0.080-0.150％、B：0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。
本实施例布氏硬度大于550HB的高级别低合金耐磨钢板的制造方法，将上述配比冶炼完成的钢水经真空脱气处理后进行连铸，连铸坯厚度260mm，将钢坯加热至1220℃的炉温，保温220min后出炉进行奥氏体再结晶区轧制和未再结晶区轧制，其中再结晶区终轧温度为1040℃，未再结晶区终轧温度为890℃，钢板的最终轧制厚度为25mm，轧后空冷至室温，然后进行淬火和回火处理，淬火温度为930℃，回火温度为180℃。
实施例4
本实施例是一种布氏硬度大于550HB的高级别低合金耐磨钢板，钢板按重量百分比计包括以下组分：C：0.38％、Si：0.60％、Mn：0.30％、P≤0.012％、S≤0.003％、Cr：0.30％、Mo：0.20％、Ni：0.50％、Ti：0.008-0.030％、Nb：0.015-0.050％、V：0.080-0.150％、B：0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。
本实施例布氏硬度大于550HB的高级别低合金耐磨钢板的制造方法，将上述配比冶炼完成的钢水经真空脱气处理后进行连铸，连铸坯厚度260mm，将钢坯加热至1180℃的炉温，保温180min后出炉进行奥氏体再结晶区轧制和未再结晶区轧制，其中再结晶区终轧温度为980℃，未再结晶区终轧温度为830℃，钢板的最终轧制厚度为25mm，轧后空冷至室温，然后进行离线淬火和回火处理，淬火温度为820℃，回火温度为100℃。
对实施例中的钢板的力学性能进行测试，其中强度按照GB/T228-2002金属材料室温拉伸试验方法进行，低温冲击韧性按GB/T 229-2007金属夏比V型缺口冲击试验方法测定，硬度按照GB/T231.1-2009方法测定，得到的结果见表2所示。
表2 本发明钢板的力学性能
Figure PCTCN2018088129-appb-000001
由表2可以看出，本发明的耐磨钢的布氏硬度大于550HB之间，抗拉强度大于1800MPa，延伸率大于8％，-20℃冲击功大于27J，可见本发明涉及的耐磨钢具有良好的抗变形和耐磨性能，同时也具有较好的低温冲击韧性。
除上述实施例外，本发明还可以有其他实施方式。凡采用等同替换或等效变换形成的技术方案，均落在本发明要求的保护范围。

Claims (9)

  1. 一种布氏硬度大于550HB的高级别低合金耐磨钢板，其特征在于：所述钢板按重量百分比计包括以下组分：C：0.33-0.41％、Si：0.50-0.60％、Mn：0.30-0.80％、P≤0.012％、S≤0.003％、Cr：0.30-1.00％、Mo：0.20-0.60％、Ni：0.80-1.20％、Ti：0.008-0.030％、Nb：0.015-0.050％、V：0.080-0.150％、B：0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。
  2. 如权利要求1所述的布氏硬度大于550HB的高级别低合金耐磨钢板，其特征在于：所述钢板中，马氏体在组织中的含量大于95％。
  3. 如权利要求1所述的布氏硬度大于550HB的高级别低合金耐磨钢板，其特征在于：所述钢板的抗拉强度大于1900MPa，硬度大于570HBW，-20℃低温冲击韧性≥20J。
  4. 如权利要求1所述的布氏硬度大于550HB的高级别低合金耐磨钢板，其特征在于：所述钢板按重量百分比计包括以下组分：C：0.41％、Si：0.50％、Mn：0.56％、P≤0.012％、S≤0.003％、Cr：0.65％、Mo：0.36％、Ni：1.20％、Ti：0.008-0.030％、Nb：0.015-0.050％、V：0.080-0.150％、B：0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。
  5. 如权利要求1所述的布氏硬度大于550HB的高级别低合金耐磨钢板，其特征在于：所棕钢板按重量百分比计包括以下组分：C：0.33％、Si：0.52％、Mn：0.80％、P≤0.012％、S≤0.003％、Cr：0.68％、Mo：0.60％、Ni：0.95％、Ti：0.008-0.030％、Nb：0.015-0.050％、V：0.080-0.150％、B：0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。
  6. 如权利要求1所述的布氏硬度大于550HB的高级别低合金耐磨钢板，其特征在于：所述钢板按重量百分比计包括以下组分：C：0.40％、Si：0.51％、Mn：0.64％、P≤0.012％、S≤0.003％、Cr：1.00％、Mo：0.42％、Ni：0.80％、Ti：0.008-0.030％、Nb：0.015-0.050％、 V：0.080-0.150％、B：0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。
  7. 如权利要求1所述的布氏硬度大于550HB的高级别低合金耐磨钢板，其特征在于：所述钢板按重量百分比计包括以下组分：C：0.38％、Si：0.60％、Mn：0.30％、P≤0.012％、S≤0.003％、Cr：0.30％、Mo：0.20％、Ni：0.50％、Ti：0.008-0.030％、Nb：0.015-0.050％、V：0.080-0.150％、B：0.0008-0.0025％、N≤0.0040％、O≤0.0025％，其余为Fe和不可避免的杂质。
  8. 如权利要求1-7中任一权利要求所述的布氏硬度大于550HB的高级别低合金耐磨钢板的制造方法，所述方法包括以下流程：铁水脱硫预处理-转炉冶炼-LF+RH精炼-连铸或模铸-铸坯热装-铸坯加热-除磷-轧制-控冷或空冷-探伤-抛丸-淬火-回火-矫直-切割-取样-喷印标识-检验-入库；其特征在于：铸坯或钢坯于1180-1220℃加热后在奥氏体再结晶区和未再结晶区分别进行轧制；所述再结晶区轧制要求道次压下率≥12％，终轧温度终轧温度≥980℃；所述未再结晶区轧制要求累积压下率≥50％，开轧温度终轧温度≤950℃，终轧温度≥800℃；轧后控冷或空冷至室温，然后进行离线热处理，其中淬火温度为：820-930℃，回火温度为100-250℃。
  9. 如权利要求8所述的布氏硬度大于550HB的高级别低合金耐磨钢板的制造方法，其特征在于：所述连铸的铸坯厚度为150-300mm。
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