WO2018176364A1 - 薄规格耐磨钢板及其制造方法 - Google Patents

薄规格耐磨钢板及其制造方法 Download PDF

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WO2018176364A1
WO2018176364A1 PCT/CN2017/078952 CN2017078952W WO2018176364A1 WO 2018176364 A1 WO2018176364 A1 WO 2018176364A1 CN 2017078952 W CN2017078952 W CN 2017078952W WO 2018176364 A1 WO2018176364 A1 WO 2018176364A1
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steel sheet
resistant steel
steel
temperature
wear
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PCT/CN2017/078952
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English (en)
French (fr)
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李烈军
周峰
高吉祥
彭政务
孙海波
戴杰涛
鲁艳军
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华南理工大学
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Priority to US16/481,055 priority Critical patent/US11453932B2/en
Priority to CN201780000191.3A priority patent/CN107109587B/zh
Priority to PCT/CN2017/078952 priority patent/WO2018176364A1/zh
Publication of WO2018176364A1 publication Critical patent/WO2018176364A1/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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/20—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
    • C22C38/26—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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese

Definitions

  • the invention belongs to the technical field of wear-resistant steel plate manufacturing, and particularly relates to a thin gauge wear-resistant steel plate and a manufacturing method thereof.
  • Anti-wear heat-resistant steel parts are widely used in high-temperature oxidizing atmosphere and abrasive wear conditions.
  • the performance of these parts directly affects the normal operation of the entire equipment, not only requires high high-temperature strength and certain wear resistance. , also have good oxidation resistance to meet the performance requirements.
  • the use of components with good performance and long life can greatly reduce material consumption and reduce production costs. It has good economic benefits and can ensure safe production, improve equipment operation efficiency, reduce equipment maintenance workload, reduce labor intensity, and improve workers. Labor conditions have good social benefits. It is widely used in:
  • Mining machinery various crusher components such as cover plates, wear plates, etc., vibrating screens, mining truck cargo tank liners, hopper linings, feed tank linings, etc.
  • An object of the present invention is to provide a thin gauge wear-resistant steel plate and a manufacturing method thereof, which are intended to adopt a smaller amount.
  • the alloy has a finer and finer microstructure, and has high wear resistance, weldability and corrosion resistance, and can mass-produce thin and wear-resistant steel with good shape, which reduces production cost and shortens delivery time.
  • the present invention is achieved in such a manner that the thin gauge wear-resistant steel sheet has an elemental composition and a weight percentage of C: 0.15 to 0.20 wt ⁇ 3 ⁇ 4, Si is 0.2 to 0.4 wt ⁇ 3 ⁇ 4, and Mn is 1.2 ⁇ .
  • Cu is 0.1 ⁇ 0.40wt ⁇ 3 ⁇ 4
  • Mo is 0.15 ⁇ 0.30wt ⁇ 3 ⁇ 4
  • Cr is 0.20 ⁇ 0.40wt ⁇ 3 ⁇ 4
  • Nb is 0.03 ⁇ 0.06wt ⁇ 3 ⁇ 4
  • Ti is 0.01 ⁇ 0.03wt%
  • B It is 0.0006 ⁇ 0.0015wt ⁇ 3 ⁇ 4, P ⁇ 0.015wt%, S ⁇ 0.010wt%, and the balance is Fe and unavoidable impurities.
  • the thickness of the steel sheet ranges from 3.0 to 8mm.
  • the surface of the steel sheet has a Brinell hardness of ⁇ 370 HBW; and/or the tensile strength of the steel sheet
  • the elongation at break of the steel sheet is A 5 . ⁇ 10 ⁇ 3 ⁇ 4.
  • Another object of the present invention is to provide a method for manufacturing the above-mentioned thin gauge wear-resistant steel sheet, comprising the following steps:
  • step S1 the molten iron having a temperature of >1250 ° C and [S] ⁇ 0.020 ⁇ 3 ⁇ 4 is subjected to condensing treatment.
  • step S 1 using an argon blowing process, the final alkalinity is controlled between 3.0 and 4.0.
  • step S5) the continuous casting speed control is between 3.0 and 3.5 m/min.
  • step S7) controlling the first two passes of the finishing rolling reduction rate ⁇ 50%, and the final pass rolling reduction rate ⁇ 15%.
  • the surface of the steel sheet after the end of the heat preservation has a Brinell hardness of ⁇ 370 HBW.
  • the tensile strength of the steel sheet after the end of the heat preservation is ⁇ 1200 MP a
  • the elongation after break is A 5 . ⁇ 10 ⁇ 3 ⁇ 4.
  • C is the most effective strengthening element in steel.
  • the interstitial solid solution strengthening of carbon atoms is the most important mechanism for quenching martensite strengthening in quenched steel.
  • the fine carbides and cementite obtained by desolvation during low temperature tempering are the most important mechanism for tempering martensite strengthening in quenched and tempered steel. Both the gap-solidified carbon and the cement-forming carbon will significantly impair the plasticity, toughness, weldability and cold formability of the steel.
  • the Si content ranges from 0.2 to 0.4 wt ⁇ 3 ⁇ 4.
  • Si has strong deoxidation ability and is a commonly used deoxidizer for steel making. Therefore, general steel contains Si.
  • the proper amount of silicon can significantly slow down the decomposition rate of tempered martensite at low temperature (200 ° C) and increase tempering. The stability, and the carbides precipitated by tempering are less likely to aggregate, which is advantageous against cracking performance.
  • the increase of silicon content will increase the silicate inclusions of Fe and Mn.
  • the plasticity is lower than that of sulfide, which will reduce the various mechanical properties of steel.
  • the low melting point silicate will increase the fluidity of molten and melted metals, affecting the welding. Seam quality.
  • Mn content ranges from 1.2 to 1.8% by weight.
  • Mn exists mainly in a solid solution state in alloy steel. Solid solution manganese will produce a certain solid solution strengthening effect. In low carbon steel, manganese can make the ferrite grain size after ⁇ phase transformation significantly thinner than that of manganese-free steel. Manganese hardly forms carbides in ordinary low-alloy high-strength steels, but it can synthesize MnS with residual vulcanization in steel. In general, MnS is an additive that is detrimental to the performance of steel, but after proper control and modification, it can significantly reduce the damage to steel properties.
  • the Cu content ranges from 0.1 to 0.40 wt ⁇ 3 ⁇ 4, and Cu mainly plays a role of solid solution strengthening, improving hardenability, and improving corrosion resistance in steel. However, too high Cu content will affect the welding performance of steel.
  • the Mo content ranges from 0.15 to 0.30 wt ⁇ 3 ⁇ 4, and Mo is soluble in ferrite, austenite and carbide, and is an element which reduces the austenite phase region. It has a solid solution strengthening effect on ferrite, which can improve the stability of carbides. Thereby increasing the strength of the steel, the same Mo has an advantageous effect on improving the ductility and toughness and wear resistance of the steel. In addition, Mo can improve the hardenability of steel, improve heat resistance, and prevent temper brittleness. However, too high Mo content can deteriorate the low temperature toughness and weldability of steel.
  • the Cr content ranges from 0.20 to 0.40 wt ⁇ 3 ⁇ 4.
  • the addition of Cr to steel can significantly improve the oxidation resistance of steel and enhance the corrosion resistance of steel.
  • Cr forms a continuous solid solution with Fe and forms a variety of carbides with carbon, which has a significant effect on the properties of steel.
  • Cr is also an effective element for improving the hardenability of steel, but it also increases the temper brittleness tendency of steel and increases the hardenability of steel to improve the sensitivity of steel cold cracking.
  • Nb content ranges from 0.03 to 0.06 wt ⁇ 3 ⁇ 4, and Nb is a strong carbide forming element having a strong grain refining effect, can significantly increase the austenite recrystallization temperature, and expand the rolling process range, and is effective. Avoid the appearance of mixed crystal structure, and ensure that the steel has a good toughness match. Carbonitride particles formed by Nb in steel can effectively inhibit the growth of austenite grains, improve strength and toughness, reduce the content of free carbon and nitrogen in steel, and reduce the strain sensitivity of steel.
  • Ti content ranges from 0.01 to 0.03 wt ⁇ 3 ⁇ 4.
  • Ti and carbon and nitrogen can be mutually insoluble, but because TiC and TiN have a very different solid solubility product in austenite, TiN is mainly formed at high temperature, which can well fix nitrogen in steel.
  • the B content ranges from 0.0006 to 0.0015 wt ⁇ 3 ⁇ 4, and B is used to improve the hardenability of the quenched and tempered steel, which increases as the carbon content in the steel decreases.
  • the combination of boron and nitrogen will cause the above effects to disappear. Therefore, the present invention adds a certain amount of Ti to effectively fix nitrogen.
  • the hardenability of the steel plate is increased by 1.4 to 1.5 times compared with the conventional reheating and quenching process, the toughness ratio of the steel is improved, and the wear resistance, welding performance and corrosion resistance are high, and the shape of the plate can be mass-produced.
  • the thin gauge wear-resistant steel sheet provided by the embodiment of the invention has an elemental composition and a weight percentage of C: 0.15 to 0.20 wt ⁇ 3 ⁇ 4, Si is 0.2 to 0.4 wt ⁇ 3 ⁇ 4, and Mn is 1.2 to 1.8 wt.
  • ⁇ 3 ⁇ 4 Cu is 0.1 to 0.40 wt ⁇ 3 ⁇ 4, Mo is 0.15 to 0.30 wt ⁇ 3 ⁇ 4, Cr is 0.20 to 0.40 wt ⁇ 3 ⁇ 4, Nb is 0.03 to 0.06 wt ⁇ 3 ⁇ 4, Ti is 0.01 to 0.03 wt ⁇ 3 ⁇ 4, B is 0.0006 ⁇ 0.0015wt ⁇ 3 ⁇ 4, P ⁇ 0.015wt%, S ⁇ 0.010wt%, and the rest is Fe and unavoidable impurities.
  • the thickness of the steel sheet ranges from 3.0 to 8mm.
  • the hardenability of the steel plate is increased by 1.4 ⁇ 1.5 times compared with the traditional reheating quenching process, the toughness ratio of the steel is improved, and the wear resistance, welding performance and corrosion resistance are high.
  • the surface of the steel sheet has a Brinell hardness of ⁇ 370 HBW.
  • the steel plate has a surface Brinell hardness of 370-430 HBW.
  • the tensile strength of the steel plate is ⁇ 1200 MP a
  • the elongation at break of the steel plate is ⁇ 5 . ⁇ 10%.
  • the thin gauge wear-resistant steel plate is a wear-resistant steel crucible 400. Its performance meets the technical requirements of ⁇ 400 national standard GB/T24186-2009.
  • the method for manufacturing the above-mentioned thin gauge wear-resistant steel plate provided by the embodiment of the invention includes the following steps:
  • finishing rolling outlet temperature is between 920 and 860 ° C, and the outlet thickness is between 3.0 and 8 mm;
  • S8 quenching the rolled steel plate by using an ultra-rapid cooling device, controlling the cooling rate between 40 and 120 ° C / s, and quenching termination temperature between 300 and 400 ° C.
  • it is on-line quenching, that is, direct quenching and cooling after splicing, making full use of the waste heat generated by the splicing, reducing energy consumption, shortening the process flow, and improving production efficiency.
  • the coiler takes up the steel plate and sends it to the insulation pit for 6 ⁇ 10 hours. In the leveling unit, it is leveled, finished, inspected, marked, judged and stored.
  • the hardenability of the steel plate is increased by 1.4 ⁇ 1.5 times compared with the traditional reheating quenching process, the toughness ratio of the steel is improved, and the wear resistance, welding performance and corrosion resistance are high.
  • step S1) the molten iron having a temperature of >1250 ° C and [S] ⁇ 0.020 ⁇ 3 ⁇ 4 is subjected to simmering treatment, and the bluntness is determined according to the temperature and weight of the incoming molten iron and the sulfur content of the desulfurization end point.
  • the amount of magnesium sprayed is desulfurized by spray passivation, and after the end of the spray, it is thickened and fully condensed.
  • the first 6 furnaces of the converter and the first two furnaces of the large refining furnace shall not smelt the steel, and the whole process adopts an argon blowing process, and the final alkalinity is controlled between 3.0 and 4.0.
  • pellets as a coolant
  • pellets And iron oxide scale must be added in accordance with relevant regulations. Fluorite should be added in small quantities according to the condition of the furnace. The amount of steel added per ton is ⁇ 413 ⁇ 4, Shuangcheng slag is ⁇ 5.5kg per ton of steel. It is strictly forbidden to add fluorite 2 minutes before the end of the blowing, using the cone and the block. Double-block clear steel, thickness of the layer ⁇ 501 ⁇ ⁇
  • the converter is made of ferrosilicon or silicon-manganese alloy for deoxidation and alloying, and the target is equipped with ferrosilicon.
  • step S5) the middle package is covered with carbon-free alkaline medium, and the medium carbon wear-resistant steel crystallizer is used for protection, and the superheat degree is controlled at 15 to 30 °C.
  • the continuous casting process is put into the electromagnetic stirring of the crystallizer, and the continuous casting soft pressing process is adopted in the segment.
  • the continuous casting speed is controlled at 3.0 ⁇ 3.5m/min, and the continuous casting blank thickness is 55 ⁇ 70mm.
  • step S7) the rolling reduction rate of the first two passes is controlled to be ⁇ 50%, and the final pass reduction rate is ⁇
  • the surface of the steel sheet after the end of the heat preservation has a Brinell hardness of ⁇ 370 HBW.
  • the steel sheet after the end of the heat preservation has a surface Brinell hardness of 370-430 HBW.
  • the tensile strength of the steel sheet after the end of the heat preservation is ⁇ 1200 MP a
  • the elongation after break is A 5 . ⁇ 10 ⁇ 3 ⁇ 4.
  • the thin gauge wear-resistant steel plate is wear-resistant steel NM400. Its performance meets the technical requirements of the NM400 national standard GB/T24186-2009.
  • C is 0.15wt ⁇ 3 ⁇ 4, Si is 0.25wt ⁇ 3 ⁇ 4, Mn is 1.25wt ⁇ 3 ⁇ 4, Cu is 0.12wt ⁇ 3 ⁇ 4, Mo is 0.28wt ⁇ 3 ⁇ 4, Cr is 0.22wt ⁇ 3 ⁇ 4, Nb is 0.031wt ⁇ 3 ⁇ 4, Ti is 0.011wt ⁇ 3 ⁇ 4, B is 0.0007wt ⁇ 3 ⁇ 4, P is 0.010wt%, S is 0.002wt%, and the balance is Fe and unavoidable impurities.
  • the production method is as follows: the qualified molten iron with a molten iron temperature of 1255 ° C and a [S] of 0.019% is firstly subjected to a simmering treatment, and the spray passivated magnesium is removed, and then the smelting treatment is carried out after the blowing is completed, and the clarification rate is 92%.
  • the hot metal end point [S] is 0.001 0%, and the whole process of argon blowing is used, and the final alkalinity is 3.5.
  • the [0] content in the steel is measured and recorded by a rapid oxygen probe, and then deoxidation and alloying are performed.
  • the aluminum wire and the titanium wire are sequentially added before the LF refining station, and the components of A1S and Ti are adjusted, and finally, B micro-alloying, continuous casting with long nozzle protection casting and Ar seal, medium package covered with carbon-free alkaline medium, with special medium carbon wear-resistant steel crystallizer protection, superheat control at 16 ° C, continuous casting
  • the process is put into the mold for electromagnetic stirring, and the fan-shaped section is subjected to continuous casting and soft pressing process, continuous casting.
  • the drawing speed is controlled at 3.0m/min, the thickness of the continuous casting blank is 70mm, the temperature of the continuous casting billet enters the heating furnace is 855°C, the heating time in the heating furnace is 62min, the heating temperature is 1050°C, and the temperature of the slab is heated. 1010 ° C, high-pressure water dephosphorization, 20 MPa in front of phosphorus removal pressure, 24 MPa in the latter stage, after phosphorus removal, enter the hot-rolling 5-stand finishing mill, the reduction rate of the first 2 passes is 55.2%, 53.4 % , the final pass reduction rate is 11.2%, the mill exit thickness is 8mm, and the finishing rolling exit temperature is 870°C.
  • the rolling mill After the rolling mill is taken out of the rolling mill, it is quenched by ultra-quick cooling device, the cooling rate is 45°C/s, and the quenching termination temperature is At 310 °C, the coiler takes up the coil and heats it for 10 hours. The leveling unit is leveled and finished.
  • the yield strength was examined to be 1095 MPa, and the tensile strength was 1285 MPa, A 5 .
  • the elongation is 13.5 ⁇ 3 ⁇ 4, the surface Brinell hardness is 402HBW, and the Charpy V-shaped impact energy is 72J, 65J, 62 J under the condition of -20 °C, and its performance meets the technical requirements of NM400 national standard GB/T24186-2009.
  • C is 0.16wt ⁇ 3 ⁇ 4, Si is 0.38wt ⁇ 3 ⁇ 4, Mn is 1.3wt ⁇ 3 ⁇ 4, Cu is 0.22wt ⁇ 3 ⁇ 4, Mo is 0.16wt ⁇ 3 ⁇ 4, Cr is 0.25 wt ⁇ 3 ⁇ 4, Nb is 0.035 wt ⁇ 3 ⁇ 4, Ti is 0.015 wt ⁇ 3 ⁇ 4, B is 0.0010 wt ⁇ 3 ⁇ 4, P is 0.010 wt%, S is 0.002 wt%, and the balance is Fe and unavoidable impurities.
  • the production method is as follows: the qualified molten iron with a molten iron temperature of 1280 ° C and a [S] of 0.015% is firstly subjected to a simmering treatment, and the spray passivated magnesium is removed. After the blowing is completed, the smelting treatment is carried out, and the ambiguity rate is 94%.
  • the hot metal end point [S] is 0.002 0%, and the whole process of argon blowing is used, and the final alkalinity is 3.2.
  • the aluminum wire and the titanium wire are sequentially added before the LF refining station, and the components of A1S and Ti are adjusted, and finally, B micro-alloying, continuous casting with long nozzle protection casting and Ar seal, medium package covered with carbon-free alkaline medium, with special medium carbon wear-resistant steel crystallizer protection, superheat control at 20 ° C, continuous casting
  • the process is put into the mold for electromagnetic stirring.
  • the fan-shaped section adopts the continuous casting and soft pressing process.
  • the continuous casting speed is controlled at 3.2m/min, the continuous casting blank is 70mm, and the continuous casting billet enters the heating furnace at 880°C.
  • the internal heating time is 80min, the heating temperature is 1080°C, the temperature of the slab is 1.05°C, and the high-pressure water dephosphorization is carried out.
  • the phosphorus removal pressure is 16MPa in the front section and the rear section is 24MPa. After the phosphorus removal, it enters the hot rolling 7 rack.
  • the finishing pass rate of the first two passes is 55.2%, 53.4%, the final pass reduction rate is 11.2%, the mill exit thickness is 6mm, the finishing rolling exit temperature is 912 °C, after the rolling mill exits the rolling mill Quenching with an ultra-fast cooling device, cold However, the rate is 68 ° C / s, the quenching termination temperature is 350 ° C, the coiler takes up, and the insulation pit is kept for 8 hours, and the leveling unit is leveled and finished.
  • the yield strength was 1135 MPa
  • the tensile strength was 1280 MPa
  • a 5 was tested.
  • the elongation is 12.5 ⁇ 3 ⁇ 4
  • the surface Brinell hardness is 415HBW
  • the Charpy V-shaped impact energy is 65J, 60J, 68J under the condition of -20 °C, and its performance meets the technical requirements of NM400 national standard GB/T24186-2009.
  • C is 0.18wt ⁇ 3 ⁇ 4
  • Si is 0.22wt ⁇ 3 ⁇
  • Mn is 1.75wt ⁇ 3 ⁇ 4
  • Cu is 0.38wt ⁇ 3 ⁇ 4
  • Mo is 0.16wt ⁇ 3 ⁇
  • Cr is 0.39wt ⁇ 3 ⁇ 4
  • Nb is 0.05wt ⁇ 3 ⁇ 4
  • Ti is 0.018wt ⁇ 3 ⁇ 4
  • B is 0.0012wt%
  • P is 0.010wt%
  • S is 0.002wt%
  • the balance is Fe and unavoidable impurities.
  • the production method is as follows: the molten iron with a molten iron temperature of 1255 ° C and a [S] of 0.019% is firstly subjected to a simmering treatment, and the spray passivated magnesium is removed. After the spraying is completed, the smelting treatment is carried out, and the clarification rate is 93%.
  • the hot metal end point [S] is 0.0010%, and the whole process of argon blowing is used, and the final alkalinity is 3.5.
  • the [0] content in the steel is measured and recorded by a rapid oxygen probe, and then deoxidation and alloying are performed.
  • the aluminum wire and the titanium wire are sequentially added before the LF refining station, and the components of A1S and Ti are adjusted, and finally, B micro-alloying, continuous casting with long nozzle protection casting and Ar seal, medium package covered with carbon-free alkaline medium, with special medium carbon wear-resistant steel crystallizer protection, superheat control at 19 ° C, continuous casting
  • the process is put into the mold for electromagnetic stirring.
  • the fan-shaped section adopts the continuous casting and soft pressing process.
  • the continuous casting speed is controlled at 3.5m/min, the continuous casting billet thickness is 55mm, and the continuous casting billet enters the heating furnace at a temperature of 925 °C.
  • the internal heating time is 65min, the heating temperature is 1150°C, the temperature of the slab is 1110°C, the high-pressure water is dephosphorized, the front part of the dephosphorization pressure is 20MPa, the latter part is 24MPa, and the phosphorus is removed into the hot rack.
  • the finishing pass rate of the first 2 passes is 54.2%, 52.3%, the final pass reduction rate is 10.8%, the mill exit thickness is 3mm, the finishing rolling exit temperature is 920 °C, after the rolling mill exits the rolling mill Quenching with ultra-fast cooling, cooling rate
  • the temperature is 115 °C / s
  • the quenching termination temperature is 400 ° C
  • the coiler takes up the coil
  • the insulation pit is kept for 6 hours
  • the flattening unit is leveled and finished.
  • the yield strength was checked to be 1115 MPa, and the tensile strength was 1305 MPa, A 5 .
  • the elongation is 10.5 ⁇ 3 ⁇ 4, the surface Brinell hardness is 403HBW, and the Charpy V-shaped impact energy is 86J, 72 J. 65 J under the condition of -20 °C, and its performance meets the technical requirements of NM400 national standard GB/T24186-2009.
  • C is 0.20wt ⁇ 3 ⁇ 4, Si is 0.25wt ⁇ 3 ⁇ 4, Mn is 1.25wt ⁇ 3 ⁇ 4, Cu is 0.12wt ⁇ 3 ⁇ 4, Mo is 0.28wt ⁇ 3 ⁇ 4, Cr is 0.22wt ⁇ 3 ⁇ 4, Nb is 0.031wt ⁇ 3 ⁇ 4, Ti is 0.011wt ⁇ 3 ⁇ 4, B is 0.0007wt ⁇ 3 ⁇ 4, P is 0.010wt%, S is 0.002wt%, and the balance is Fe and unavoidable impurities.
  • the preparation method is as follows: the qualified molten iron with a molten iron temperature of 1305 ° C and a [S] of 0.012% is firstly subjected to a simmering treatment, and the spray passivated magnesium is removed, and then the smelting treatment is carried out after the blowing is completed, and the ambiguity rate is 92%.
  • the hot metal end point [S] is 0.001 0%, and the whole process of argon blowing is used, and the final alkalinity is 3.5.
  • the [0] content in the steel is measured and recorded by a rapid oxygen probe, and then deoxidation and alloying are performed.
  • the aluminum wire and the titanium wire are sequentially added before the LF refining station, and the components of A1S and Ti are adjusted, and finally, Microalloying of B, continuous casting with long nozzle protection casting and Ar seal, medium covered with carbon-free alkaline encapsulation, special medium carbon wear-resistant steel crystallizer protection, superheat control at 25 ° C, continuous casting
  • the process is put into the mold for electromagnetic stirring.
  • the fan-shaped section adopts the continuous casting and soft pressing process.
  • the continuous casting speed is controlled at 3.0m/min, the continuous casting billet thickness is 60mm, and the continuous casting billet enters the heating furnace at 905°C.
  • the internal heating time is 80min, the heating temperature is 1100°C, the temperature of the slab is 1.0°C, the high-pressure water is dephosphorized, the front part of the dephosphorization pressure is 20MPa, the latter part is 24MPa, and the phosphorus is removed into the hot rack.
  • the finishing pass rate of the first two passes is 55.2%, 53.4%, the final pass reduction rate is 11.2%, the mill exit thickness is 4mm, the finish rolling exit temperature is 870 °C, after the rolling mill exits the rolling mill Quenching with ultra-fast cooling, cooling rate It is 80 °C / s, the quenching termination temperature is 360 ° C, the coiler is taken up, and the thermal insulation pit is kept for 8 hours, and the leveling unit is leveled and finished.
  • the yield strength was checked to be 1115 MPa, and the tensile strength was 1325 MPa, A 5 .
  • the elongation is 11.5 ⁇ 3 ⁇ 4, the surface Brinell hardness is 417HBW, and the Charpy V-shaped impact energy is 58J, 69J, 63J under the condition of -20 °C, and its performance meets the technical requirements of NM400 national standard GB/T24186-2009.

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Abstract

一种薄规格耐磨钢板，其元素组成及重量百分含量为：C为0.15～0.20wt％，Si为0.2～0.4wt％，Mn为1.2～1.8wt％，Cu为0.1～0.40wt％，Mo为0.15～0.30wt％，Cr为0.20～0.40wt％，Nb为0.03～0.06wt％，Ti为0.01～0.03wt％，B为0.0006～0.0015wt％，P＜0.015wt％，S＜0.010wt％，其余为Fe及不可避免的杂质，钢板厚度范围是3.0～8mm。其制造方法：铁水脱硫及转炉冶炼；转炉出钢用硅铁或者硅锰合金进行脱氧和合金化；RH炉精炼；LF炉精炼；进行连铸；在加热炉内加热，进行高压除磷；进行热连轧；进行淬火处理，保温。

Description

薄规格耐磨钢板及其制造方法 技术领域
[0001] 本发明属于耐磨钢板制造技术领域， 尤其涉及薄规格耐磨钢板及其制造方法。
背景技术
[0002] 抗磨耐热钢件广泛应用于高温氧化性气氛及磨料磨损的工况， 这些零部件的性 能直接影响整个设备的正常运行， 不仅要求材质具有高的高温强度和一定的耐 磨性， 还要有良好的抗氧化性， 才能满足其使用性能的要求。 使用性能好和寿 命长的零部件， 既可以大大降低材料消耗减少生产成本， 具有良好的经济效益 又可保证安全生产， 提高设备运行效率， 同吋减少设备维修工作量， 降低劳动 强度， 改善工人劳动条件， 具有良好的社会效益。 其广泛应用于：
[0003] (1) 矿山机械： 各式破碎机部件如盖板、 耐磨板等， 振动筛、 矿车卡车货槽 衬板、 料斗内衬、 输料槽内衬等。
[0004] (2) 电力工业： 风机叶片、 磨煤机部件、 出灰管、 空气处理系统和运输机等
[0005] (3) 水泥工业： 磨机内衬、 护套、 冲击盘、 管道， 泵壳、 破碎机零件、 选粉 机叶片、 各种罐衬、 各种底盘、 振动筛等。
[0006] (4) 煤处理业： 立磨衬板、 输料槽、 料斗、 破碎机零件和衬板、 输煤管道、 泵体等。
[0007] (5) 其它： 冶金行业的过料斗、 箕斗等、 港口机械的装载机、 刮板运输机等 ， 建筑行业的挖掘机、 推土机挖斗及刀板、 自卸卡车、 沥青搅拌机、 泥浆管道 、 洗沙机、 浮选机等。
[0008] 目前国内主要生产厂家有舞钢、 武钢、 宝钢、 南钢， 全部采用中厚板轧机或热 连轧机进行生产， 薄规格生产困难， 生产成本高， 板形难以保证， 生产周期长 ， 交货期难以保证。
技术问题
[0009] 本发明的目的在于提供一种薄规格耐磨钢板及其制造方法， 旨在采用更少量的 合金得到更优良更细密的微观组织， 并具有高的耐磨性能、 焊接性能和抗腐蚀 性能， 并能批量生产板形良好的薄规格耐磨钢， 降低了生产成本， 缩短了交货 周期。
问题的解决方案
技术解决方案
[0010] 本发明是这样实现的， 薄规格耐磨钢板， 其元素组成及重量百分含量为： C为 0 .15〜0.20wt<¾， Si为 0.2〜0.4wt<¾， Mn为 1.2〜1.8wt<¾， Cu为 0.1〜0.40wt<¾， Mo 为 0.15〜0.30wt<¾， Cr为 0.20〜0.40wt<¾， Nb为 0.03〜0.06wt<¾， Ti为 0.01〜0.03wt % , B为 0.0006〜0.0015wt<¾， P<0.015wt% , S<0.010wt% , 其余为 Fe及不可避免 的杂质， 所述钢板的厚度范围是 3.0~8mm。
[0011] 进一步地， 所述钢板的表面布氏硬度≥370HBW; 和 /或， 所述钢板的抗拉强度
>1200MPa, 所述钢板的断后延伸率 A 5。≥10<¾。
[0012] 本发明的另一目的在于提供上述薄规格耐磨钢板的制造方法， 包括以下步骤：
[0013] S1) 铁水脱硫及转炉冶炼， 控制铁水中的 [S]≤0.0030%， 澄层厚度≤501^^
[0014] S2) 转炉出钢用硅铁或者硅锰合金进行脱氧和合金化；
[0015] S3) RH炉精炼， 进行脱氧与合金化；
[0016] S4) LF炉精炼， 出站前加入铝线， 加入钛线或者钛合金， 进行 B的微合金化；
[0017] S5) 进行连铸， 采用长水口保护浇铸且 Ar封， 过热度控制在 15〜30°C之间， 得 到厚度在 55〜70mm之间的连铸坯;
[0018] S6) 在加热炉内对连铸坯加热， 连铸坯进入加热炉温度≥850 ， 控制加热吋间 ≥60min， 加热温度在 1050〜1150°C之间， 出加热炉温度≥1000°C， 进行高压除磷
[0019] S7) 进行热连轧， 轧制 5~7道次， 精轧出口温度在 920〜860°C之间， 出口厚度 在 3.0~8mm之间；
[0020] S8) 对轧制后的钢板进行淬火处理， 控制冷却速率为 40~120°C/s之间， 淬火终 止温度为 300~400°C之间； 保温 6~10小吋。
[0021] 进一步地， 在步骤 S1) 中， 将温度 >1250°C且 [S]≤0.020<¾的铁水进行扒澄处理
， 进行喷钝化镁脱硫， 喷吹结束后进行扒澄处理。 [0022] 进一步地， 在步骤 S 1 ) 中: 采用吹氩工艺， 终澄碱度控制在 3.0-4.0之间。
[0023] 进一步地， 在步骤 S5) 中: 中包覆盖无碳碱性中包澄， 采用中碳耐磨钢结晶器 保护澄
[0024] 进一步地， 在步骤 S5) 中: 连铸拉速控制在 3.0〜3.5m/min之间。
[0025] 进一步地， 在步骤 S7) 中: 控制前两道次精轧压下率≥50%， 最后道次压下率≤ 15%。
[0026] 进一步地， 保温结束后的钢板的表面布氏硬度≥370HBW。
[0027] 进一步地， 保温结束后的钢板的抗拉强度≥1200MPa， 断后延伸率 A 5。≥10<¾。
[0028] 本发明中各元素的作用：
[0029] C含量控制为 0.15〜0.20wt<¾。 C是钢中最有效的强化元素， 碳原子的间隙固溶 强化是淬火钢中淬火马氏体强化的最主要的机制。 低温回火过程中脱溶得到的 微细碳化物和渗碳体是淬火回火钢中回火马氏体强化的最主要机制。 无论是间 隙固溶的碳还是形成渗碳体的碳， 均将明显地损害钢材的塑性、 韧性、 焊接性 能和冷成型性能。
[0030] Si含量范围为 0.2〜0.4wt<¾。 Si脱氧能力较强， 是炼钢常用的脱氧剂， 故一般钢 中均含 Si， 适量的硅可显著地减慢回火马氏体在低温（200°C)吋的分解速度， 增 加回火稳定性， 并使回火吋析出的碳化物不易聚集， 对抗裂纹性能有利。 硅含 量增加会造成 Fe、 Mn的硅酸盐类夹杂物增加， 塑性比硫化物低， 会降低钢的各 种力学性能， 低熔点硅酸盐会增加熔澄和融化金属的流动性， 影响焊缝质量。
[0031] Mn含量范围为 1.2〜1.8wt%。 Mn在合金钢中主要以固溶态存在。 固溶的锰将产 生一定的固溶强化作用。 锰在低碳钢中可以使 γ→α相变后的铁素体晶粒尺寸比 不含锰的钢明显细化。 锰在普通低合金高强度钢中几乎不会形成碳化物， 但它 能够与钢中残存的硫化合成 MnS。 一般情况下， MnS是一种对钢材性能有害的夹 杂物， 但经适当控制和改性后， 可使其对钢材性能的危害程度明显降低。
[0032] Cu含量范围为 0.1〜0.40wt<¾， Cu在钢中主要起固溶强化作用、 提高淬透性、 改 善抗腐蚀能力的作用。 但 Cu含量过高会影响钢的焊接性能。
[0033] Mo含量范围为 0.15〜0.30wt<¾， Mo可固溶于铁素体、 奥氏体和碳化物中， 是缩 小奥氏体相区的元素。 对铁素体有固溶强化作用， 能够提高碳化物的稳定性， 从而提高钢的强度， 同吋 Mo对改善钢的延展性和韧性以及耐磨性起到有利作用 。 此外， Mo还能够提高钢的淬透性、 提高热强性、 防止回火脆性。 但过高的 Mo 含量会恶化钢的低温韧性和焊接性能。
[0034] Cr含量范围为 0.20〜0.40wt<¾。 Cr加入钢中能显著改善钢的抗氧化作用， 增强 钢的抗腐蚀能力。 Cr能和 Fe形成连续固溶体， 与碳形成多种碳化物， 对钢的性 能有显著影响。 同吋 Cr还是提高钢淬透性的有效元素， 但同吋也增加钢的回火 脆性倾向， 并会提高钢的淬硬性从而提高钢材的焊接冷裂纹的敏感性。
[0035] Nb含量范围为 0.03〜0.06wt<¾， Nb是一种强碳化物形成元素， 具有强烈的细化 晶粒作用， 能显著提高奥氏体再结晶温度， 扩大轧制工艺范围， 有效避免混晶 组织的出现， 确保钢材具有良好的的强韧性匹配。 Nb在钢中形成的碳氮化物颗 粒， 可有效抑制奥氏体晶粒的长大， 提高强度和韧性， 同吋减少了钢中游离碳 、 氮的含量， 降低钢的应变吋效敏感性。
[0036] Ti含量范围为 0.01〜0.03wt<¾。 Ti与碳、 氮可以无限制互溶， 但由于 TiC与 TiN 在奥氏体中的固溶度积相差甚远， 因而在高温下主要形成 TiN， 可以很好的起到 固定钢中氮的作用。
[0037] B含量范围为 0.0006〜0.0015wt<¾， B用于改善淬火回火钢的淬透性， 该作用随 着钢中碳含量的减少而增大。 硼与氮结合后将使上述作用消失， 因此， 本发明 加入一定的 Ti来有效固氮。
[0038] P含量 <0.015wt%， S含量 <0.010wt%。 S、 P是钢中有害杂质元素， 钢中 P、 S 含量越低越好。 当钢中 S含量较多吋， 热轧吋容易产生热脆等问题； 而钢中 P含 量较多吋， 钢容易发生冷脆， 此外， 磷还容易发生偏析。
发明的有益效果
有益效果
[0039] 通过合理的合金化设计， 选用微量 Cu、 Mo、 Cr、 Nb、 Ti、 B合金进行微合金 化， 通过控制轧制后超快速冷却淬火控制微观组织， 充分发挥合金的性能强化 作用， 减少合金的加入量及贵重合金的使用量。 并简化了传统的耐磨钢热轧后 进行离线淬火与回火工艺， 采用此制作方法与传统工艺相比较， 降低了能耗， 缩短了工艺流程， 从钢水冶炼到产品出厂吋间可缩短到 24小吋内。 轧后直接超 快速冷却后钢板的淬透性比传统再加热淬火工艺增大了 1.4~1.5倍， 提高钢的强 韧配比， 并具有高的耐磨性能、 焊接性能和抗腐蚀性能， 能批量生产板形良好 的薄规格耐磨钢， 产品性能均匀稳定， 节约社会资源， 降低生产成本。
本发明的实施方式
[0040] 为了使本发明的目的、 技术方案及优点更加清楚明白， 以下结合实施例， 对本 发明进行进一步详细说明。 应当理解， 此处所描述的具体实施例仅仅用以解释 本发明， 并不用于限定本发明。
[0041] 本发明实施例提供的薄规格耐磨钢板， 其元素组成及重量百分含量为： C为 0.1 5〜0.20wt<¾， Si为 0.2〜0.4wt<¾， Mn为 1.2〜1.8wt<¾， Cu为 0.1〜0.40wt<¾， Mo为 0 .15〜0.30wt<¾， Cr为 0.20〜0.40wt<¾， Nb为 0.03〜0.06wt<¾， Ti为 0.01〜0.03wt<¾， B为 0.0006〜0.0015wt<¾， P<0.015wt% , S<0.010wt% , 其余为 Fe及不可避免的杂 质， 钢板的厚度范围是 3.0~8mm。
[0042] 通过合理的合金化设计， 选用微量的 Cu、 Mo、 Cr、 Nb、 Ti、 B合金进行微合 金化， 通过控制轧制后超快速冷却淬火控制微观组织， 充分发挥合金的性能强 化作用， 减少合金的加入量及贵重合金的使用量。 并简化了传统的耐磨钢热轧 后进行离线淬火与回火工艺， 采用此制作方法与传统工艺相比较， 降低能耗， 缩短工艺流程， 从钢水冶炼到产品出厂吋间可缩短到 24小吋以内。 轧后直接超 快速冷却后钢板的淬透性比传统再加热淬火工艺增大了 1.4~1.5倍， 提高钢的强 韧配比， 并具有高的耐磨性能、 焊接性能和抗腐蚀性能， 能批量生产板形良好 的薄规格耐磨钢， 产品性能均匀稳定， 节约社会资源， 降低生产成本。
[0043] 进一步地， 钢板的表面布氏硬度≥370HBW。 钢板具有 370-430 HBW的表面布 氏硬度。 钢板的抗拉强度≥1200MPa， 钢板的断后延伸率 Α 5。≥10%。 薄规格耐磨 钢板为耐磨钢 ΝΜ400。 其性能满足 ΝΜ400国家标准 GB/T24186-2009技术条件。
[0044] 本发明实施例提供的上述薄规格耐磨钢板的制造方法， 包括以下步骤：
[0045] S1) 高炉铁水， 铁水脱硫， 将铁水和废钢经转炉炼钢， 控制铁水中的 [S]≤0.003 0% , 澄层厚度≤501^^ 以免带入转炉， 在氧化气氛下造成硫含量回升；
[0046] S2) 转炉出钢用硅铁或者硅锰合金进行脱氧和合金化； [0047] S3) RH炉精炼， 不得采用含 Al材料进行脱氧与合金化， 到 RH后， 用快速定氧 探头测定和记录钢中的 [0]含量， 进行脱氧与合金化；
[0048] S4) LF炉精炼， 出站前加入铝线， 加入钛线或者钛合金， 进行 B的微合金化； [0049] S5) 进行连铸， 采用长水口保护浇铸且 Ar封， 过热度控制在 15〜30°C之间， 得 到厚度在 55〜70mm之间的连铸坯；
[0050] S6) 在加热炉内对连铸坯加热， 连铸坯进入加热炉温度≥850 ， 控制加热吋间 ≥60min， 加热温度在 1050〜1150°C之间， 出加热炉温度≥1000°C， 进行高压水除 磷， 除磷压力≥16MPa;
[0051] S7) 进行热连轧， 轧制 5~7道次， 精轧出口温度在 920〜860°C之间， 出口厚度 在 3.0~8mm之间；
[0052] S8) 采用超快冷装置对轧制后的钢板进行淬火处理， 控制冷却速率为 40~120°C /s之间， 淬火终止温度为 300~400°C之间。 此处为在线淬火， 即扎制后直接淬火 冷却， 充分利用扎制产生的余热， 降低能耗， 缩短工艺流程， 提高生产效率。 卷取机卷取钢板， 送保温坑保温 6~10小吋， 在平整机组进行幵平， 精整， 检验 ， 标识， 判定与入库。
[0053] 通过合理的合金化设计， 选用微量的 Cu、 Mo、 Cr、 Nb、 Ti、 B合金进行微合 金化， 通过控制轧制后超快速冷却淬火控制微观组织， 充分发挥合金的性能强 化作用， 减少合金的加入量及贵重合金的使用量。 并简化了传统的耐磨钢热轧 后进行离线淬火与回火工艺， 采用此制作方法与传统工艺相比较， 降低能耗， 缩短工艺流程， 从钢水冶炼到产品出厂吋间可缩短到 24小吋以内。 轧后直接超 快速冷却后钢板的淬透性比传统再加热淬火工艺增大了 1.4~1.5倍， 提高钢的强 韧配比， 并具有高的耐磨性能、 焊接性能和抗腐蚀性能， 能批量生产板形良好 的薄规格耐磨钢， 产品性能均匀稳定， 节约社会资源， 降低生产成本。
[0054] 进一步地， 在步骤 S1) 中， 将温度 >1250°C且 [S]≤0.020<¾的铁水进行扒澄处理 ， 根据来料铁水的温度、 重量及脱硫终点硫含量要求， 确定钝化镁的喷吹量， 进行喷钝化镁脱硫， 喷吹结束后进行稠澄和充分扒澄处理。
[0055] 进一步地， 在步骤 S1) 中， 转炉新幵炉前 6炉及大补后前二炉不得冶炼此钢种 ， 全程采用吹氩工艺， 终澄碱度控制在 3.0-4.0之间。 用球团矿作冷却剂， 球团矿 和氧化铁皮必须按相关规定加入。 萤石应根据炉内澄情况分批少量加入， 每吨 钢加入量≤41¾， 双澄吋每吨钢≤5.5kg， 吹炼终点前 2min严禁加入萤石， 采用挡 澄锥、 挡澄塞进行双挡澄出钢， 澄层厚度≤501^^ 转炉出钢用硅铁或者硅锰合 金进行脱氧和合金化， 按目标配硅铁。
进一步地， 在步骤 S5) 中， 中包覆盖无碳碱性中包澄， 采用中碳耐磨钢结晶器 保护澄， 过热度控制在 15〜30°C。 连铸过程投入结晶器电磁搅拌， 在扇形段采用 连铸轻压下工艺， 连铸拉速控制在 3.0〜3.5m/min， 连铸坯厚度 55〜70mm。
[0057] 进一步地， 在步骤 S7) 中， 控制前两道次精轧压下率≥50%， 最后道次压下率≤
15% , 以保证厚度精确及板形良好。
[0058] 进一步地， 保温结束后的钢板的表面布氏硬度≥370HBW。 保温结束后的钢板 具有 370-430 HBW的表面布氏硬度。 保温结束后的钢板的抗拉强度≥1200MPa， 断后延伸率 A 5。≥10<¾。 薄规格耐磨钢板为耐磨钢 NM400。 其性能满足 NM400国 家标准 GB/T24186-2009技术条件。
[0059] 下面结合具体实施方式对本发明作进一步描述， 并非对本发明保护范围的限制
[0060] 实施例 1
[0061] 铸坯的化学成分及其含量是： C为 0.15wt<¾， Si为 0.25wt<¾， Mn为 1.25wt<¾， Cu 为 0.12wt<¾， Mo为 0.28wt<¾， Cr为 0.22wt<¾， Nb为 0.031wt<¾， Ti为 0.011wt<¾， B 为 0.0007wt<¾， P为 0.010wt%， S为 0.002wt%， 其余为 Fe及不可避免的杂质。 制 作方法是： 将铁水温度 1255°C， [S]为 0.019%的合格的铁水先进行扒澄处理， 进 行喷钝化镁脱 S， 喷吹结束后再进行扒澄处理， 扒澄率 92%， 铁水终点 [S]为 0.001 0% , 采用全程吹氩工艺， 终澄碱度 3.5。 加入球团矿和氧化铁皮作冷却剂； 萤石 分批加入每吨钢加入量 3.1kg， 采用挡澄锥、 挡澄塞进行双挡澄出钢， 澄厚为 48 mm, 转炉出钢用硅铁进行脱氧和合金化。 到 RH后， 用快速定氧探头测定和记录 钢中的 [0]含量， 然后进行脱氧与合金化等， LF精炼出站前依次加入铝线和钛线 ， 调整 A1S和 Ti的成分， 最后进行 B的微合金化， 连铸采用长水口保护浇铸且 Ar 封， 中包覆盖无碳碱性中包澄， 采用专用中碳耐磨钢结晶器保护澄， 过热度控 制在 16°C， 连铸过程投入结晶器电磁搅拌， 在扇形段采用连铸轻压下工艺， 连铸 拉速控制在 3.0m/min， 连铸坯厚度 70mm， 连铸坯进入加热炉温度为 855°C， 在加 热炉内加热吋间为 62min， 加热温度 1050°C， 板坯出加热炉温度为 1010°C， 进行 高压水除磷， 除磷压力前段 20MPa， 后段 24MPa， 除磷后进入热连轧 5机架精轧 机组， 前 2道次精轧压下率为别为 55.2%、 53.4% , 最后道次压下率为 11.2%， 轧 机出口厚度 8mm， 精轧出口温度 870°C， 轧件出轧机后采用超快冷装置淬火， 冷 却速率为 45°C/s， 淬火终止温度为 310°C， 卷取机卷取， 送保温坑保温 10小吋， 在平整机组进行幵平， 精整。
[0062] 检验其屈服强度为 1095MPa， 抗拉强度 1285MPa， A 5。延伸率 13.5<¾， 表面布氏 硬度 402HBW, -20°C条件下， 夏比 V形冲击功分别为 72J、 65J、 62 J, 其性能满 足 NM400国家标准 GB/T24186-2009技术条件。
[0063] 实施例 2
[0064] 铸坯的化学成分及其含量是： C为 0.16wt<¾， Si为 0.38wt<¾， Mn为 1.3wt<¾， Cu 为 0.22wt<¾， Mo为 0.16wt<¾， Cr为 0.25wt<¾， Nb为 0.035wt<¾， Ti为 0.015wt<¾， B 为 0.0010wt<¾， P为 0.010wt%， S为 0.002wt%， 其余为 Fe及不可避免的杂质。 制 作方法是： 将铁水温度 1280°C， [S]为 0.015%的合格的铁水先进行扒澄处理， 进 行喷钝化镁脱 S， 喷吹结束后再进行扒澄处理， 扒澄率 94%， 铁水终点 [S]为 0.002 0% , 采用全程吹氩工艺， 终澄碱度 3.2。 加入球团矿和氧化铁皮作冷却剂； 萤石 分批加入每吨钢加入量 3.2kg， 采用挡澄锥、 挡澄塞进行双挡澄出钢， 澄厚为 24 mm, 转炉出钢用硅铁进行脱氧和合金化。 到 RH后， 用快速定氧探头测定和记录 钢中的 [0]含量， 然后进行脱氧与合金化等， LF精炼出站前依次加入铝线和钛线 ， 调整 A1S和 Ti的成分， 最后进行 B的微合金化， 连铸采用长水口保护浇铸且 Ar 封， 中包覆盖无碳碱性中包澄， 采用专用中碳耐磨钢结晶器保护澄， 过热度控 制在 20°C， 连铸过程投入结晶器电磁搅拌， 在扇形段采用连铸轻压下工艺， 连铸 拉速控制在 3.2m/min， 连铸坯厚度 70mm， 连铸坯进入加热炉温度为 880°C， 在加 热炉内加热吋间为 80min， 加热温度 1080°C， 板坯出加热炉温度为 1055°C， 进行 高压水除磷， 除磷压力前段 16MPa， 后段 24MPa， 除磷后进入热连轧 7机架精轧 机组， 前 2道次精轧压下率为别为 55.2%， 53.4% , 最后道次压下率为 11.2%， 轧 机出口厚度 6mm， 精轧出口温度 912°C， 轧件出轧机后采用超快冷装置淬火， 冷 却速率为 68°C/s， 淬火终止温度为 350°C， 卷取机卷取， 送保温坑保温 8小吋， 在 平整机组进行幵平， 精整。
[0065] 检验其屈服强度为 1135MPa， 抗拉强度 1280MPa， A 5。延伸率 12.5<¾， 表面布氏 硬度 415HBW, -20°C条件下， 夏比 V形冲击功分别为 65J、 60J、 68J, 其性能满 足 NM400国家标准 GB/T24186-2009技术条件。
[0066] 实施例 3
[0067] 铸坯的化学成分及其含量是： C为 0.18wt<¾， Si为 0.22wt<¾， Mn为 1.75wt<¾， Cu 为 0.38wt<¾， Mo为 0.16wt<¾， Cr为 0.39wt<¾， Nb为 0.05wt<¾， Ti为 0.018wt<¾， B为 0.0012wt%, P为 0.010wt%， S为 0.002wt%， 其余为 Fe及不可避免的杂质。 制作 方法是： 将铁水温度 1255°C， [S]为 0.019%的合格的铁水先进行扒澄处理， 进行 喷钝化镁脱 S， 喷吹结束后再进行扒澄处理， 扒澄率 93%， 铁水终点 [S]为 0.0010 %, 采用全程吹氩工艺， 终澄碱度 3.5。 加入球团矿和氧化铁皮作冷却剂； 萤石 分批加入每吨钢加入量 3.2kg， 采用挡澄锥、 挡澄塞进行双挡澄出钢， 澄厚为 32 mm, 转炉出钢用硅铁进行脱氧和合金化。 到 RH后， 用快速定氧探头测定和记录 钢中的 [0]含量， 然后进行脱氧与合金化等， LF精炼出站前依次加入铝线和钛线 ， 调整 A1S和 Ti的成分， 最后进行 B的微合金化， 连铸采用长水口保护浇铸且 Ar 封， 中包覆盖无碳碱性中包澄， 采用专用中碳耐磨钢结晶器保护澄， 过热度控 制在 19°C， 连铸过程投入结晶器电磁搅拌， 在扇形段采用连铸轻压下工艺， 连铸 拉速控制在 3.5m/min， 连铸坯厚度 55mm， 连铸坯进入加热炉温度为 925°C， 在加 热炉内加热吋间为 65min， 加热温度 1150°C， 板坯出加热炉温度为 1110°C， 进行 高压水除磷， 除磷压力前段 20MPa， 后段 24MPa， 除磷后进入热连轧 5机架精轧 机组， 前 2道次精轧压下率为别为 54.2%， 52.3% , 最后道次压下率为 10.8%， 轧 机出口厚度 3mm， 精轧出口温度 920°C， 轧件出轧机后采用超快冷装置淬火， 冷 却速率为 115°C/s， 淬火终止温度为 400°C， 卷取机卷取， 送保温坑保温 6小吋， 在平整机组进行幵平， 精整。
[0068] 检验其屈服强度为 1115MPa， 抗拉强度 1305MPa， A 5。延伸率 10.5<¾， 表面布氏 硬度 403HBW, -20°C条件下， 夏比 V形冲击功分别为 86J、 72 J. 65 J, 其性能满 足 NM400国家标准 GB/T24186-2009技术条件。 [0069] 实施例 4
[0070] 铸坯的化学成分及其含量是： C为 0.20wt<¾， Si为 0.25wt<¾， Mn为 1.25wt<¾， Cu 为 0.12wt<¾， Mo为 0.28wt<¾， Cr为 0.22wt<¾， Nb为 0.031wt<¾， Ti为 0.011wt<¾， B 为 0.0007wt<¾， P为 0.010wt%， S为 0.002wt%， 其余为 Fe及不可避免的杂质。 制 作方法是： 将铁水温度 1305°C， [S]为 0.012%的合格的铁水先进行扒澄处理， 进 行喷钝化镁脱 S， 喷吹结束后再进行扒澄处理， 扒澄率 92%， 铁水终点 [S]为 0.001 0% , 采用全程吹氩工艺， 终澄碱度 3.5。 加入球团矿和氧化铁皮作冷却剂； 萤石 分批加入每吨钢加入量 3.0kg， 采用挡澄锥、 挡澄塞进行双挡澄出钢， 澄厚为 32 mm, 转炉出钢用硅铁进行脱氧和合金化。 到 RH后， 用快速定氧探头测定和记录 钢中的 [0]含量， 然后进行脱氧与合金化等， LF精炼出站前依次加入铝线和钛线 ， 调整 A1S和 Ti的成分， 最后进行 B的微合金化， 连铸采用长水口保护浇铸且 Ar 封， 中包覆盖无碳碱性中包澄， 采用专用中碳耐磨钢结晶器保护澄， 过热度控 制在 25°C， 连铸过程投入结晶器电磁搅拌， 在扇形段采用连铸轻压下工艺， 连铸 拉速控制在 3.0m/min， 连铸坯厚度 60mm， 连铸坯进入加热炉温度为 905°C， 在加 热炉内加热吋间为 80min， 加热温度 1100°C， 板坯出加热炉温度为 1080°C， 进行 高压水除磷， 除磷压力前段 20MPa， 后段 24MPa， 除磷后进入热连轧 7机架精轧 机组， 前 2道次精轧压下率为别为 55.2%， 53.4% , 最后道次压下率为 11.2%， 轧 机出口厚度 4mm， 精轧出口温度 870°C， 轧件出轧机后采用超快冷装置淬火， 冷 却速率为 80°C/s， 淬火终止温度为 360°C， 卷取机卷取， 送保温坑保温 8小吋， 在 平整机组进行幵平， 精整。
[0071] 检验其屈服强度为 1115MPa， 抗拉强度 1325MPa， A 5。延伸率 11.5<¾， 表面布氏 硬度 417HBW, -20°C条件下， 夏比 V形冲击功分别为 58J、 69J、 63J, 其性能满 足 NM400国家标准 GB/T24186-2009技术条件。
[0072] 以上所述仅为本发明的较佳实施例而已， 并不用以限制本发明， 凡在本发明的 精神和原则之内所作的任何修改、 等同替换和改进等， 均应包含在本发明的保 护范围之内。

Claims

权利要求书
[权利要求 1] 薄规格耐磨钢板， 其特征在于， 其元素组成及重量百分含量为： C为
0.15〜0.20wt<¾， Si为 0.2〜0.4wt<¾， Mn为 1.2〜1.8wt<¾， Cu为 0.1〜0.4 0wt% , Mo为 0.15〜0.30wt<¾， Cr为 0.20〜0.40wt<¾， Nb为 0.03〜0.06w t%， Ti为 0.01〜0.03wt<¾， B为 0.0006〜0.0015wt<¾， P<0.015wt% , S< 0.010wt% , 其余为 Fe及不可避免的杂质， 所述钢板的厚度范围是 3.0~ 8mm。
[权利要求 2] 如权利要求 1所述的薄规格耐磨钢板， 其特征在于， 所述钢板的表面 布氏硬度≥3701¾\¥； 和 /或， 所述钢板的抗拉强度≥1200MPa， 所述 钢板的断后延伸率 A 5。≥10%。
[权利要求 3] 如权利要求 1所述的薄规格耐磨钢板的制造方法， 其特征在于， 包括 以下步骤：
51) 铁水脱硫及转炉冶炼， 控制铁水中的 [S]≤0.0030<¾， 澄层厚度≤5 0mm;
52) 转炉出钢用硅铁或者硅锰合金进行脱氧和合金化；
53) RH炉精炼， 进行脱氧与合金化；
54) LF炉精炼， 出站前加入铝线， 加入钛线或者钛合金， 进行 B的微 合金化；
55) 进行连铸， 采用长水口保护浇铸且 Ar封， 过热度控制在 15〜30°C 之间， 得到厚度在 55〜70mm之间的连铸坯；
56) 在加热炉内对连铸坯加热， 连铸坯进入加热炉温度≥850 ， 控 制加热吋间≥60min， 加热温度在 1050〜1150°C之间， 出加热炉温度≥ 1000°C, 进行高压除磷；
57) 进行热连轧， 轧制 5~7道次， 精轧出口温度在 920〜860°C之间， 出口厚度在 3.0~8mm之间；
58) 对轧制后的钢板进行淬火处理， 控制冷却速率为 40~120°C/s之间 ， 淬火终止温度为 300~400°C之间； 保温 6~10小吋。
[权利要求 4] 如权利要求 3所述的薄规格耐磨钢板的制造方法， 其特征在于， 在步 骤 SI) 中， 将温度 >1250°C且 [S]≤0.020<¾的铁水进行扒澄处理， 进行 喷钝化镁脱硫， 喷吹结束后进行扒澄处理。
[权利要求 5] 如权利要求 3所述的薄规格耐磨钢板的制造方法， 其特征在于， 在步 骤 S1) 中， 采用吹氩工艺， 终澄碱度控制在 3.0-4.0之间。
[权利要求 6] 如权利要求 3所述的薄规格耐磨钢板的制造方法， 其特征在于， 在步 骤 S5) 中， 中包覆盖无碳碱性中包澄， 采用中碳耐磨钢结晶器保护澄
[权利要求 7] 如权利要求 3所述的薄规格耐磨钢板的制造方法， 其特征在于， 在步 骤 S5) 中， 连铸拉速控制在 3.0〜3.5m/min之间。
[权利要求 8] 如权利要求 3所述的薄规格耐磨钢板的制造方法， 其特征在于， 在步 骤 S7) 中， 控制前两道次精轧压下率≥50%， 最后道次压下率≤15%。
[权利要求 9] 如权利要求 3所述的薄规格耐磨钢板的制造方法， 其特征在于， 保温 结束后的钢板的表面布氏硬度≥370HBW。
[权利要求 10] 如权利要求 3所述的薄规格耐磨钢板的制造方法， 其特征在于， 保温 结束后的钢板的抗拉强度≥1200MPa， 断后延伸率 A 5。≥10<¾。
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