WO2018176908A1 - 一种薄规格高Ti耐磨钢NM450的制造方法 - Google Patents

一种薄规格高Ti耐磨钢NM450的制造方法 Download PDF

Info

Publication number
WO2018176908A1
WO2018176908A1 PCT/CN2017/115390 CN2017115390W WO2018176908A1 WO 2018176908 A1 WO2018176908 A1 WO 2018176908A1 CN 2017115390 W CN2017115390 W CN 2017115390W WO 2018176908 A1 WO2018176908 A1 WO 2018176908A1
Authority
WO
WIPO (PCT)
Prior art keywords
slag
molten steel
steel
temperature
rolling
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/CN2017/115390
Other languages
English (en)
French (fr)
Inventor
李烈军
周峰
高吉祥
孙海波
戴杰涛
彭政务
鲁艳军
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
South China University of Technology SCUT
Original Assignee
South China University of Technology SCUT
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by South China University of Technology SCUT filed Critical South China University of Technology SCUT
Priority to US16/499,324 priority Critical patent/US11649516B2/en
Publication of WO2018176908A1 publication Critical patent/WO2018176908A1/zh
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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 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
    • 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
    • C21D8/0236—Cold 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 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
    • C21D8/0242—Flattening; Dressing; Flexing
    • 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
    • C21D8/0247—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 heat treatment
    • C21D8/0263—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 heat treatment following 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/573—Continuous furnaces for strip or wire with cooling
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21B—MANUFACTURE OF IRON OR STEEL
    • C21B2400/00—Treatment of slags originating from iron or steel processes
    • C21B2400/02—Physical or chemical treatment of slags
    • C21B2400/022—Methods of cooling or quenching molten slag
    • C21B2400/026—Methods of cooling or quenching molten slag using air, inert gases or removable conductive bodies
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21B—MANUFACTURE OF IRON OR STEEL
    • C21B2400/00—Treatment of slags originating from iron or steel processes
    • C21B2400/02—Physical or chemical treatment of slags
    • C21B2400/03—Removing 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the invention belongs to the technical field of wear-resistant steel plate manufacturing. In particular, it relates to a method for manufacturing a thin gauge high Ti wear resistant steel NM450.
  • 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 does the material require high high temperature strength and certain wear resistance, but also good oxidation resistance to meet the performance requirements. Use components with good performance and long life, It can greatly reduce material consumption and reduce production cost. It has good economic benefits and can ensure safe production, improve equipment operation efficiency, reduce equipment maintenance workload and reduce labor intensity. Improve workers' working conditions and have good social benefits. It is widely used in mining machinery, power industry, cement industry, coal processing industry and other industries. Domestic low-alloy wear-resistant steel plate is used at 100% per year.
  • microalloyed wear-resistant steel has begun to receive attention, especially the development of low-cost and high-performance titanium microalloyed wear-resistant steel, using traditional slab continuous casting and rolling line to produce high Ti
  • Micro-alloy thin gauge wear-resistant steel can be shortened from steel smelting to product delivery time to less than 24 hours, and the production cost is low, the thin gauge shape is good, the product performance is uniform and stable, and the market has significant market competitiveness.
  • the object of the present invention is to provide a method for manufacturing a thin gauge high Ti wear-resistant steel NM450, which is more conventional than hot rolling + off-line quenching +
  • the tempering heat treatment wear-resistant steel production process adopts high Ti traditional slab continuous casting and rolling process and ultra-rapid cooling process to obtain better and finer microstructure, and fully exert Ti
  • the role of microalloying reduces the use of precious alloys and produces thin gauge wear-resistant steels with high wear resistance, corrosion resistance, high heat resistance and weldability, and good shape, reducing production costs and shortening
  • the delivery cycle improves the market competitiveness of the product.
  • a method for manufacturing a thin gauge high Ti wear resistant steel NM450 comprising the steps of:
  • the temperature is >1250 °C, [S] ⁇ 0.020%
  • the qualified molten iron is first treated with slag, and according to the temperature and weight of the incoming molten iron and the sulfur content of the desulfurization end point, KR is de-S, [S] ⁇ 0.0020%, and the whole argon blowing process is adopted, and the final slag alkalinity is adopted. 3.0 ⁇ 4.0 ;
  • the molten steel is sent to the LF refining station. After the molten steel enters the refining station, the molten steel is stirred at a flow rate of 300 to 800 NL/min for 1 to 2 minutes to slag; the graphite electrode is inserted into the molten steel, the power supply is heated, and the molten steel is simultaneously supplied to the molten steel.
  • argon flow rate is maintained at 100 ⁇ 400NL / min, argon blowing 4 ⁇ 10min; argon flow rate during desulfurization of molten steel is 100 ⁇ 450NL / min, argon blowing 4 ⁇ 10min temperature measurement; argon flow rate during sampling is 100 ⁇ 400NL / min; argon pressure 1.2 ⁇ 1.8MPa, the molten steel in the refining process, the slagging material is added to the molten steel slag, desulfurization refining process to inclusions, the slag basicity R (CaO / Si0 2) control 1.3 ⁇ 2.8, and the Fe0+Mn0 ⁇ 2.0% in the slag, the outbound molten steel [S] ⁇ 0.008%;
  • the ladle clearance height, slag thickness and temperature are measured.
  • the ladle clearance is controlled at 300-700mm, the molten steel top slag thickness is less than 100mm, and the molten steel temperature is 1615 °C ⁇ 1630 °C; according to the clearance height of the ladle and the slag thickness ascending ladle, ensure that the insertion tube is inserted into the molten steel to a depth of not less than 600mm.
  • the alloying composition is finely adjusted according to the temperature, oxygen content and steel composition.
  • the alloying sequence first add AL alloy; then Add SiFe, MnFe, CrFe, MoFe, NbFe. After the alloy is added, it is circulated under the ultimate vacuum for 3 minutes to measure temperature, sample and oxygen. After alloying, the [O] oxygen content in the steel is controlled below 3ppm, and the temperature is controlled. 1590 ⁇ 1600 °C, RH refining before feeding the aluminum wire and titanium wire or Ti alloy, adjusting the composition of Al S and Ti, and finally the microalloying of B;
  • double-layer covering agent is used for the surface of the tundish steel, the basic layer is added with a sufficient amount of alkaline covering agent, and the upper layer is added with low-carbonity covering agent, and the tundish is operated by constant weight; the molten steel is from the big bag to the middle.
  • the bag is casted by long nozzle and protected by argon.
  • the special medium carbon wear-resistant steel mold is used to protect the slag.
  • the superheat degree is controlled. 15 ⁇ 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 1.0 ⁇ 1.2m/min, and the continuous casting blank thickness is 220mm.
  • the chemical composition and content of the slab obtained after continuous casting of the conventional slab are: C is 0.16 ⁇ 0.20wt%, Si is 0.2 ⁇ 0.4wt%, and Mn is 0.8 ⁇ 1.5wt%. , Mo is 0.10 ⁇ 0.20wt%, Cr is 0.30 ⁇ 0.50wt%, Nb is 0.02 ⁇ 0.05wt%, Ti is 0.10 ⁇ 0.15wt% , B is 0.0005 ⁇ 0.0010wt%, P ⁇ 0.015wt%, S ⁇ 0.010wt%, and the rest is Fe and unavoidable impurities; The slab is cooled to room temperature, and the quality and surface of the slab are inspected, and a layer of skin on the surface of the continuous casting blank is removed;
  • the same steel type shall not be smelted in the first 6 furnaces of the converter and the first 2 furnaces after the large compensation.
  • the heating time in the heating furnace is ⁇ 60 min, and the heating temperature is 1050 to 1150 °C. .
  • the mill exit thickness is 6 to 12 mm
  • the finishing rolling outlet temperature is 820 to 860 °C.
  • step (2) The step-by-step deoxidation process comprises: adding a composite deoxidizer and a metal aluminum block to the ladle at the time of tapping of the converter, and performing initial deoxidation on the molten steel, and the addition amount of the composite deoxidizer and the metal aluminum block is required to dissolve oxygen according to the end of the molten steel.
  • the target oxygen content is determined after initial deoxidation; then low carbon ferromanganese, ferrosilicon, ferromolybdenum and ferrochrome are added to the ladle; the molten steel in the ladle is argon blown and argon is blown. After 3 ⁇ 8min, the molten steel temperature, oxygenation and sampling were measured. According to the oxygen content of molten steel, the aluminum wire was fed to the molten steel to carry out the final deoxidation and aluminum alloying of the molten steel, and the argon blowing was kept for 2 to 10 minutes.
  • the slag-forming material according to the step (3) includes lime, synthetic slag, pre-dissolved slag or slagging agent.
  • the shot peening speed is ⁇ 2 ⁇ 4 m/min, and the roughness of the steel sheet after shot blasting is 25 ⁇ 55 ⁇ m. .
  • the invention selects low cost and high Ti through reasonable alloying design.
  • the microalloying technology controls the microstructure by ultra-rapid cooling quenching after two-stage controlled rolling, fully exerts the performance strengthening effect of the alloy, reduces the amount of alloy added and the amount of precious alloy used, and reduces the use of this method compared with the conventional process.
  • the addition of precious alloys increases the toughness ratio of steel, saves social resources and reduces production costs.
  • a method for manufacturing a thin gauge high Ti wear resistant steel NM450 comprising the steps of:
  • the molten steel temperature, oxygenation and sampling were measured. According to the oxygen content of molten steel, the aluminum wire was fed to the molten steel to carry out the final deoxidation and aluminum alloying of the molten steel, and the argon blowing was kept for 10 min.
  • the molten steel is sent to the LF refining station. After the molten steel enters the refining station, the molten steel is stirred with a flow rate of 780 NL/min argon gas for 1.2 min; the graphite electrode is inserted into the molten steel, the power supply is heated, and argon is blown into the molten steel.
  • the flow rate of argon was kept at 390 NL/min, argon was blown for 4.5 min; the flow rate of argon blowing during desulfurization of molten steel was 450 NL/min, and the temperature of argon blowing was 4 min; the flow rate of argon blowing during sampling was 200 NL/min; the pressure of argon blowing was 1.4 MPa.
  • slag-forming slag is added to the molten steel, such as lime, synthetic slag, pre-dissolved slag or slagging agent; desulfurization refining is carried out to remove the inclusion, and the binary alkalinity R (CaO/Si0 2 ) in the slag is obtained. Controlled at 1.5, and the Fe0+Mn0 ⁇ 2.0% in the slag, and the outbound molten steel [S] is 0.003%;
  • the ladle is opened to the position to be treated, the ladle clearance height, slag thickness and temperature are measured, the ladle clearance is controlled at 350mm, the molten steel top slag thickness is 90mm, the molten steel temperature is 1620 °C, and the insertion tube is inserted into the molten steel.
  • the depth is 650mm, and the alloying composition is finely adjusted according to temperature, oxygen content and steel sample composition.
  • the alloying sequence first add AL alloy; then add SiFe, MnFe, CrFe, MoFe, NbFe, etc., after the alloy is added, it is circulated under the ultimate vacuum.
  • double-layer covering agent is used for the surface of the tundish steel, the basic layer is added with a sufficient amount of alkaline covering agent, and the upper layer is added with low-carbonity covering agent, and the tundish is operated by constant weight; the molten steel is from the big bag to the middle.
  • the bag is casted by long nozzle and protected by argon.
  • the special medium carbon wear-resistant steel mold is used to protect the slag.
  • the superheat degree is controlled. 20 °C, the continuous casting process is put into the mold for electromagnetic stirring, and the fan-shaped section adopts the continuous casting and soft pressing process.
  • the continuous casting speed is controlled at 1.0m/min, and the continuous casting blank thickness is 220mm.
  • the slab is cooled to room temperature, and the quality and surface of the slab are inspected, and a layer of skin on the surface of the continuous casting blank is removed;
  • the heating time in the heating furnace is 280min, the heating temperature is 1250 °C, and the temperature of the slab is out of the furnace. 1160 °C, using two-stage controlled rolling; for recrystallization zone rolling, reducing rolling passes under the conditions of equipment, increasing rolling pass reduction rate; and appropriately extending post-laying residence time to increase deformed austenite The amount of recrystallization, homogenizing the tissue ;
  • rough rolling 9 passes rough rolling, rough rolling is completed until the steel temperature drops to 900 ° C , performing austenite non-recrystallization zone finish rolling. Ensure that the total reduction ratio of the non-recrystallization zone is >45%, and the rolling reduction capacity is appropriately added according to the rolling capacity, especially the three-pass reduction ratio before finishing rolling is ⁇ 50%.
  • the final pass reduction rate is 6% to ensure the thickness is accurate. Good shape, the thickness of the mill exit 12mm , finishing rolling outlet temperature 820 °C ;
  • the chemical composition and content of the slab obtained after the conventional slab continuous casting in the step (5) are: C is 0.16 wt%, Si is 0.4 wt%, and Mn is 1.5 wt%, Mo. It is 0.20 wt%, Cr is 0.32 wt%, Nb is 0.031 wt%, Ti is 0.11 wt%, B is 0.0006 wt%, P is 0.010 wt%, S is 0.002 wt%, and the balance is Fe and unavoidable impurities.
  • the yield strength of the thin gauge high Ti wear-resistant steel NM450 provided in this embodiment is 985 MPa, tensile strength 1195 MPa, A 50 elongation 13.5%, surface Brinell hardness 370 HBW, -20 °C, Charpy V-shaped impact work respectively For 78J, 76J, 80J, its performance meets the technical requirements of NM450 national standard GB/T24186-2009.
  • a method for manufacturing a thin gauge high Ti wear resistant steel NM450 comprising the steps of:
  • the molten steel temperature, oxygenation and sampling were measured. According to the oxygen content of molten steel, the aluminum wire was fed to the molten steel to carry out the final deoxidation and aluminum alloying of the molten steel, and the argon blowing was kept for 2 min.
  • the molten steel is sent to the LF refining station. After the molten steel enters the refining station, the molten steel is stirred with a flow rate of 500 NL/min argon gas for 1.5 min.
  • the graphite electrode is inserted into the molten steel, the power supply is heated, and argon is blown into the molten steel.
  • the argon flow rate was maintained at 350 NL/min, argon blowing for 6 min; the argon flow rate during desulfurization of molten steel was 400 NL/min, and the argon blowing was performed for 8 min; the argon flow rate during sampling was 250 NL/min; the argon pressure was 1.2 MPa, during the refining process.
  • slag-forming slag to the molten steel, such as lime, synthetic slag, pre-dissolving slag or slagging agent; performing desulfurization refining to remove the inclusion, and controlling the binary alkalinity R (CaO/Si0 2 ) in the slag to 2.8.
  • the slag Fe0+Mn0 ⁇ 2.0%, the outbound molten steel [S] is 0.004%;
  • double-layer covering agent is used for the surface of the tundish steel, the basic layer is added with a sufficient amount of alkaline covering agent, and the upper layer is added with low-carbonity covering agent, and the tundish is operated by constant weight; the molten steel is from the big bag to the middle.
  • the bag is casted by long nozzle and protected by argon.
  • the special medium carbon wear-resistant steel mold is used to protect the slag.
  • the superheat degree is controlled. 15 °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 1.2m/min, and the continuous casting blank thickness is 220mm.
  • the slab is cooled to room temperature, and the quality and surface of the slab are inspected, and a layer of skin on the surface of the continuous casting blank is removed;
  • the heating time in the heating furnace is 300min, the heating temperature is 1200 °C, and the temperature of the slab is out of the furnace. 1180 °C, using two-stage controlled rolling.
  • the rolling pass is reduced under the permission of the equipment, the rolling reduction rate of the rolling pass is increased; and the dwell time after the dipping is appropriately extended to increase the amount of recrystallization of the deformed austenite to homogenize the structure. ;
  • the rough rolling is carried out 7 times of rough rolling, and the rough rolling is completed until the temperature of the steel drops to 900 ° C. , performing austenite non-recrystallization zone finish rolling. Ensure that the total reduction ratio of the non-recrystallization zone is >45%, and the rolling reduction capacity is appropriately added according to the rolling capacity, especially the three-pass reduction ratio before finishing rolling is ⁇ 50%.
  • the final pass reduction rate is 7.3% to ensure the thickness is accurate.
  • the outlet of the rolling mill has a thickness of 6 mm and a finishing rolling outlet temperature of 860 ° C ;
  • the chemical composition and content of the slab obtained after the conventional slab continuous casting in the step (5) are: C is 0.20 wt%, Si is 0.20 wt%, and Mn is 0.85 wt%, Mo. It is 0.20 wt%, Cr is 0.50 wt%, Nb is 0.045 wt%, Ti is 0.15 wt%, B is 0.0010 wt%, P is 0.011 wt%, S is 0.002 wt%, and the balance is Fe and unavoidable impurities.
  • the yield strength of the thin gauge high Ti wear-resistant steel NM450 provided in this embodiment is 1010 MPa, tensile strength 1215 MPa, A 50 elongation 14.5%, surface Brinell hardness 367 HBW, -20 °C, Charpy V-shaped impact work respectively For 82J, 83J, 89J, its performance meets the technical requirements of NM450 national standard GB/T24186-2009.
  • a method for manufacturing a thin gauge high Ti wear resistant steel NM450 comprising the steps of:
  • the molten steel temperature, oxygenation and sampling were measured. According to the oxygen content of molten steel, the aluminum wire was fed to the molten steel to carry out the final deoxidation and aluminum alloying of the molten steel, and the argon blowing was kept for 2 min.
  • the molten steel is sent to the LF refining station. After the molten steel enters the refining station, the molten steel is stirred for 2 min with 400 NL/min argon flow; the graphite electrode is inserted into the molten steel, the power supply is heated, and argon is blown into the molten steel, and the flow of argon is blown.
  • argon flow rate during desulfurization of molten steel is 320NL/min, argon blowing for 8min temperature measurement; argon flow rate is 250NL/min when sampling; argon pressure is 1.2MPa, during molten steel refining, Adding slag-forming slag into molten steel, such as lime, synthetic slag, pre-dissolved slag or slag-reducing agent; performing desulfurization refining and inclusion treatment, controlling the binary alkalinity R (CaO/Si0 2 ) in the slag to 2.0, and Fe0+Mn0 ⁇ 2.0% in the slag and 0.003% in the outbound molten steel [S];
  • double-layer covering agent is used for the surface of the tundish steel, the basic layer is added with a sufficient amount of alkaline covering agent, and the upper layer is added with low-carbonity covering agent, and the tundish is operated by constant weight; the molten steel is from the big bag to the middle.
  • the bag is casted by long nozzle and protected by argon.
  • the special medium carbon wear-resistant steel mold is used to protect the slag.
  • the superheat degree is controlled.
  • the continuous casting process is put into the electromagnetic stirring of the crystallizer, and the continuous casting soft pressing process is adopted in the fan-shaped section.
  • the continuous casting speed is controlled at 1.1 m/min, and the continuous casting blank thickness is 220 mm.
  • the slab is cooled to room temperature, and the quality and surface of the slab are inspected, and a layer of skin on the surface of the continuous casting blank is removed;
  • the heating time in the heating furnace is 300min, the heating temperature is 1180 °C, and the temperature of the slab is out of the furnace. 1160 °C, using two-stage controlled rolling, for recrystallization zone rolling, reducing the rolling pass under the conditions of equipment, increasing the rolling pass reduction rate; and extending the post-laying residence time to increase the deformed austenite The amount of recrystallization, homogenizing the tissue ;
  • the finishing temperature is controlled to be close to the Ar3 phase transition temperature, the last pass pressure The rate is 7.3% To ensure the thickness is accurate and the shape of the plate is good, the thickness of the mill exit is 8mm , and the finishing temperature is 840 °C ;
  • the chemical composition and content of the slab obtained after the conventional slab continuous casting in the step (5) are: C is 0.18 wt%, Si is 0.25 wt%, and Mn is 1.5 wt%, Mo. It is 0.15 wt%, Cr is 0.45 wt%, Nb is 0.050 wt%, Ti is 0.10 wt%, B is 0.0007 wt%, P is 0.010 wt%, S is 0.002 wt%, and the balance is Fe and unavoidable impurities.
  • the yield strength of the thin gauge high Ti wear-resistant steel NM450 provided in this embodiment is 1015 MPa, the tensile strength is 1295 MPa, the A 50 elongation is 13.5%, the surface Brinell hardness is 385 HBW, and the Charpy V-shaped impact energy is -20 °C respectively.
  • the yield strength of the thin gauge high Ti wear-resistant steel NM450 provided in this embodiment is 1015 MPa, the tensile strength is 1295 MPa, the A 50 elongation is 13.5%, the surface Brinell hardness is 385 HBW, and the Charpy V-shaped impact energy is -20 °C respectively.
  • 64J, 60J, 65J its performance meets the technical requirements of NM450 national standard GB/T24186-2009.
  • a method for manufacturing a thin gauge high Ti wear resistant steel NM450 comprising the steps of:
  • the molten steel temperature, oxygenation and sampling were measured. According to the oxygen content of molten steel, the aluminum wire was fed to the molten steel to carry out the final deoxidation and aluminum alloying of the molten steel, and the argon blowing was kept for 2 min.
  • the molten steel is sent to the LF refining station. After the molten steel enters the refining station, the molten steel is stirred for 2 min with 400 NL/min argon flow; the graphite electrode is inserted into the molten steel, the power supply is heated, and argon is blown into the molten steel, and the flow of argon is blown.
  • argon flow rate during desulfurization of molten steel is 100NL/min, argon blowing for 8min temperature measurement; argon flow rate during sampling is 250NL/min; argon pressure is 1.2MPa, during molten steel refining, Adding slag-forming slag into molten steel, such as lime, synthetic slag, pre-dissolved slag or slag-reducing agent; performing desulfurization refining and inclusion treatment, controlling the binary alkalinity R (CaO/Si0 2 ) in the slag to 2.0, and Fe0+Mn0 ⁇ 2.0% in the slag and 0.003% in the outbound molten steel [S];
  • double-layer covering agent is used for the surface of the tundish steel, the basic layer is added with a sufficient amount of alkaline covering agent, and the upper layer is added with low-carbonity covering agent, and the tundish is operated by constant weight; the molten steel is from the big bag to the middle.
  • the bag is casted by long nozzle and protected by argon.
  • the special medium carbon wear-resistant steel mold is used to protect the slag.
  • the superheat degree is controlled.
  • the continuous casting process is put into the electromagnetic stirring of the crystallizer, and the continuous casting soft pressing process is adopted in the fan-shaped section.
  • the continuous casting speed is controlled at 1.1 m/min, and the continuous casting blank thickness is 220 mm.
  • the slab is cooled to room temperature, and the quality and surface of the slab are inspected, and a layer of skin on the surface of the continuous casting blank is removed;
  • the heating time in the heating furnace is 300min, the heating temperature is 1200 °C, and the temperature of the slab is out of the furnace. 1160 °C, using two-stage controlled rolling, for recrystallization zone rolling, reducing the rolling pass under the conditions of equipment, increasing the rolling pass reduction rate; and extending the post-laying residence time to increase the deformed austenite The amount of recrystallization, homogenizing the tissue ;
  • the chemical composition and content of the slab obtained after the conventional slab continuous casting in the step (5) are: C is 0.18 wt%, Si is 0.25 wt%, and Mn is 1.5 wt%, Mo. It is 0.15 wt%, Cr is 0.45 wt%, Nb is 0.050 wt%, Ti is 0.10 wt%, B is 0.0007 wt%, P is 0.010 wt%, S is 0.002 wt%, and the balance is Fe and unavoidable impurities.
  • the yield strength of the thin gauge high Ti wear-resistant steel NM450 provided in this embodiment is 1015 MPa, the tensile strength is 1295 MPa, the A 50 elongation is 13.5%, the surface Brinell hardness is 385 HBW, and the Charpy V-shaped impact energy is -20 °C respectively.
  • the yield strength of the thin gauge high Ti wear-resistant steel NM450 provided in this embodiment is 1015 MPa, the tensile strength is 1295 MPa, the A 50 elongation is 13.5%, the surface Brinell hardness is 385 HBW, and the Charpy V-shaped impact energy is -20 °C respectively.
  • 64J, 60J, 65J its performance meets the technical requirements of NM450 national standard GB/T24186-2009.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

一种薄规格高Ti耐磨钢NM450的制造方法，包括步骤：高炉铁水、铁水预处理、转炉冶炼、LF炉精炼、RH炉精炼、传统板坯连铸、加热炉、高压水除磷、热连轧机组、超快速冷却、卷取、开平、加热、淬火、回火、精整。

Description

一种薄规格高Ti耐磨钢NM450的制造方法
技术领域
本发明属于耐磨钢板制造技术领域。尤其涉及 一种薄规格高 Ti 耐磨钢 NM450 的制造方法。
背景技术
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 , 同时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。其广泛应用于矿山机械、电力工业、水泥工业、煤处理工业等行业。 国内仅低合金耐磨钢板年用量在 100 万吨左右，另有大量的耐磨铸钢、高锰钢也在逐渐的被替代 ，目前国内 10mm 及其以下规格少量使用国内产品，主要使用瑞典 SSAB 的 hardox 系列，价格高，供货周期长。过去，耐磨钢通常以 Ni 、 Cu 、 Mo 、 Nb 、 V 等贵重合金的微合金化为主，但随着 Ni 、 Cu 、 Mo 、 Nb 价格的不断上涨，产品成本居高不下，在钢铁材料近年来微利甚至无利的艰难时期，钢材最终产品的价格成本就是市场竞争力，就是钢铁企业生产与发展之动力，而以 Ti 微合金化为主的耐磨钢的研发开始受到重视，尤其是低成本高性能的钛微合金化耐磨钢的开发，采用传统板坯连铸连轧线生产高 Ti 微合金薄规格耐磨钢从钢水冶炼到产品出厂时间可缩短到 24 小时以内，并且生产成本低，薄规格板形好，产品性能均匀稳定，具有显著的市场竞争能力。
发明内容
本发明目的是提供 一种薄规格高 Ti 耐磨钢 NM450 的制造方法 ，使其较传统的热轧 + 离线淬火 + 回火热处理耐磨钢生产工艺采用高 Ti 传统板坯连铸连轧工艺和超快冷工艺结合得到更优良更细密的微观组织，充分发挥 Ti 微合金化的作用，降低贵重合金的使用，生产出具有高的耐磨性能、抗腐蚀性能、高耐热性和焊接性能、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，提高了产品的市场竞争能力。
为实现上述目的，本发明采用的技术方案是：
一种薄规格高 Ti 耐磨钢 NM450 的制造方法，包括步骤：
(1) 将温度 >1250 ℃ 、 [S]≤0.020% 的合格的铁水先进行扒渣处理，根据来料铁水的温度、重量及脱硫终点硫含量要求，进行 KR 脱 S, [S]≤0.0020% ，采用全程吹氩工艺，终渣碱度 3.0~4.0 ；
(2) 进行转炉冶炼，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；萤石应根据炉内渣情况分批少量加入，每吨钢加入量 ≤4kg ，双渣时每吨钢 ≤5.5kg ，吹炼终点前 2min 严禁加入萤石，采用挡渣锥、挡渣塞进行双挡渣出钢，渣厚 ≤50mm ，在转炉出钢过程中采用分步脱氧工艺进行脱氧；
( 3 ) 钢水送入 LF 精炼站，钢水进入精炼站后，对钢水用 300 ～ 800NL/min 氩气流量搅拌 1 ~ 2min ，以便化渣；将石墨电极插入钢水中，供电升温，同时向钢水中吹氩，吹氩流量保持在 100 ~ 400NL/min ，吹氩 4 ~ 10min ；钢水脱硫时吹氩流量为 100 ~ 450NL/min ，吹氩 4 ~ 10min 测温；取样时吹氩流量为 100 ~ 400NL/min ；吹氩压力 1.2 ~ 1.8MPa ，在钢水精炼过程中，向钢水中加入造渣料造渣，进行脱硫精炼去夹杂处理，将渣中二元碱度 R(CaO/Si02) 控制在 1.3 ~ 2.8 ，并使渣中 Fe0+Mn0<2.0% ，出站钢水 [S] ≤ 0.008% ；
( 4) RH 炉精炼，到 RH 后，钢包开到待处理位，测量钢包净空高度、渣厚及温度，钢包净空控制在 300 ～ 700mm ，钢水顶渣厚度应小于 100mm ，钢水温度为 1615 ℃ ~1630 ℃；根据钢包净空高度及渣厚顶升钢包，确保插入管插入钢水深度不小于 600mm, 根据温度、氧含量和钢样成分进行合金化成分精调，合金化顺序：先加 AL 合金；然后加入 SiFe 、 MnFe 、 CrFe 、 MoFe 、 NbFe ，合金加入后在极限真空度下循环 3 分钟，测温、取样、定氧；合金化后要求钢中 [O] 氧量控制在 3ppm 以下，温度控制在 1590 ～ 1600 ℃， RH 精炼出站前依次喂铝线和钛线或者 Ti 合金，调整 AlS 和 Ti 的成分，最后进行 B 的微合金化 ；
(5) 进行传统板坯连铸，对中间包钢水表面采用双层覆盖剂，下层加足量碱性覆盖剂，而上层加低碳酸性覆盖剂，中间包采用恒重操作；钢水从大包到中间包采用长水口浇注、氩气保护，采用专用中碳耐磨钢结晶器保护渣，过热度控制在 15 ~ 30 ℃ ，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 1.0 ~ 1.2m/min ，连铸坯厚度 220mm ，传统板坯连铸 后得到的铸坯的化学成分及其含量为： C 为 0.16~0.20wt% ， Si 为 0.2~0.4wt% ， Mn 为 0.8~1.5wt% ， Mo 为 0.10~0.20wt% ， Cr 为 0.30~0.50wt% ， Nb 为 0.02~0.05wt% ， Ti 为 0.10~0.15wt% ， B 为 0.0005~0.0010wt% ， P<0.015wt ％， S<0.010wt ％，其余为 Fe 及不可避免的杂质； 板坯冷却到室温，对板坯质量及表面进行检查，扒去连铸坯表面一层表皮 ；
(6) 送入炉加热，在加热炉内加热时间≥ 240min ，加热温度 1180 ~ 1260 ℃ ，板坯出加热炉温度≥ 1150 ℃，采用两阶段控制轧制。对于再结晶区轧制，在设备允许条件下减少轧制道次，提高轧制道次压下率；并适当延长扎后停留时间，以增加变形奥氏体的再结晶数量，使组织均匀化 ；
(7) 出加热炉后进行高压水除磷，除磷压力≥ 16MPa ；
(8) 除磷后进行粗轧 5~9 道次粗轧，粗轧完待钢温降到 900~950 ° C ，进行奥氏体非再结晶区精轧。保证非再结晶区的总压下率 >45% ，按轧制能力适当加大道次压下量，特别是精轧前 3 道次压下率≥ 50% ，为随后的奥氏体向铁素体相变形核创造有利条件，增加形核部位，以达到细化铁素体晶粒的目的，终轧温度控制在 820~860 ° C ，最后道次压下率≤ 12% ，以保证厚度精确及板形良好 ；
(9) 轧件出轧机后采用超快冷装置冷却，冷却速率为 15 ~ 30 ℃ /s ，淬火终止温度为 550 ~ 650 ℃ ；
(10) 卷取机卷取，进行堆垛冷却 ；
(11) 送热处理车间进行开平 ；
(12) 对钢板进行抛丸处理去除表面氧化铁皮；
( 13 ) 开平后进入热处理炉加热到 900~950 ℃，保温 1.5~2h ，进行淬火处理 ；
(14) 温度降至 300 ~ 400 ℃时进行回火处理 ；
(15) 在精整机组进行精整、检验。
进一步地，步骤 (2) 中，所述 转炉新开炉前 6 炉及大补后前 2 炉不得冶炼相同钢种 。
进一步地，步骤 (6) 中， 在加热炉内加热时间≥ 60min ，加热温度 1050 ~ 1150 ℃ 。
进一步地，步骤 (8) 中，所述轧机出口厚度 6~12mm ，精轧出口温度 820~860 ℃。
进一步地，步骤 (2) 中所述分步脱氧工艺包括：在转炉出钢时向钢包中先加入复合脱氧剂及金属铝块，对钢水进行初脱氧，复合脱氧剂及金属铝块的加入量需根据钢水终点溶解氧和初脱氧后目标氧含量确定；接着向钢包中加入低碳锰铁、硅铁、钼铁和铬铁；对钢包中钢水进行全程吹氩，吹氩 3 ~ 8min 后测量钢水温度、定氧、取样，根据钢水氧含量向钢水中喂铝线进行钢水终脱氧及铝合金化，并保持吹氩 2 ～ 10min 。
进一步地，步骤 (3) 所述的 造渣料包括石灰、合成渣、预溶渣或调渣剂。
进一步地，步骤 (12) 中抛丸速度≤ 2~4m/min ，抛丸后钢板粗糙度为 25~55μm 。
相比现有技术，本发明通过合理的合金化设计，选用低成本高 Ti 微合金化技术，通过两阶段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，采用此方法与传统工艺相比较，减少贵重合金的加入量，提高了钢的强韧配比，节约社会资源，降低生产成本。
具体实施方式
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。
实施例 1
一种薄规格高 Ti 耐磨钢 NM450 的制造方法，包括步骤：
(1) 将温度 >1250℃ 、 [S]≤0.020% ( 铁水中 S 的质量百分比 ) 的合格的铁水先进行扒渣处理，根据来料铁水的温度、重量及脱硫终点硫含量要求，进行 KR 脱 S ， [S] 为 0.0010% ，采用全程吹氩工艺，终渣碱度 3.0 ；
(2) 进行转炉冶炼，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；萤石应根据炉内渣情况分批少量加入，每吨钢加入量 3.9kg ，吹炼终点前 2min 严禁加入萤石，采用挡渣锥、挡渣塞进行双挡渣出钢，渣厚 48mm ； 在转炉出钢过程中采用分步脱氧工艺进行脱氧：在转炉出钢时向钢包中先加入复合脱氧剂及金属铝块，对钢水进行初脱氧；接着向钢包中加入低碳锰铁、硅铁、钼铁和铬铁，对钢包中钢水进行全程吹氩，吹氩 8min 后测量钢水温度、定氧、取样，根据钢水氧含量向钢水中喂铝线进行钢水终脱氧及铝合金化，并保持吹氩 10min ；
( 3 ) 钢水送入 LF 精炼站，钢水进入精炼站后，对钢水用 780NL/min 氩气流量搅拌 1 . 2min 化渣；将石墨电极插入钢水中，供电升温，同时向钢水中吹氩，吹氩流量保持在 390NL/min ，吹氩 4 .5 min ；钢水脱硫时吹氩流量为 450NL/min ，吹氩 4 min 测温；取样时吹氩流量为 200NL/min ；吹氩压力 1.4MPa ，在钢水精炼过程中，向钢水中加入造渣料造渣，如石灰、合成渣、预溶渣或调渣剂；进行脱硫精炼去夹杂处理，将渣中二元碱度 R(CaO/Si02) 控制在 1.5 ，并使渣中 Fe0+Mn0<2.0% ，出站钢水 [S] 为 0.003% ；
( 4) RH 炉精炼，到 RH 后，钢包开到待处理位，测量钢包净空高度、渣厚及温度，钢包净空控制在 350mm ，钢水顶渣厚度 90mm ，钢水温度为 1620 ℃，插入管插入钢水深度 650mm, 根据温度、氧含量和钢样成分进行合金化成分精调，合金化顺序：先加 AL 合金；然后加入 SiFe 、 MnFe 、 CrFe 、 MoFe 、 NbFe 等，合金加入后在极限真空度下循环 3 分钟，测温、取样、定氧；合金化后要求钢中 [O] ( 钢 水中 O 的质量百分比 ) 氧量控制在 2ppm ，温度控制在 1595 ℃ ， RH 精炼出站前依次喂铝线和钛线或者 Ti 合金，调整 AlS 和 Ti 的成分，最后进行 B 的微合金化 ；
(5) 进行传统板坯连铸，对中间包钢水表面采用双层覆盖剂，下层加足量碱性覆盖剂，而上层加低碳酸性覆盖剂，中间包采用恒重操作；钢水从大包到中间包采用长水口浇注、氩气保护，采用专用中碳耐磨钢结晶器保护渣，过热度控制在 20 ℃ ，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 1.0m/min ，连铸坯厚度 220mm ，板坯冷却到室温，对板坯质量及表面进行检查，扒去连铸坯表面一层表皮 ；
(6) 送入炉加热，在加热炉内加热时间为 280min ，加热温度 1250 ℃ ，板坯出加热炉温度 1160 ℃，采用两阶段控制轧制；对于再结晶区轧制，在设备允许条件下减少轧制道次，提高轧制道次压下率；并适当延长扎后停留时间，以增加变形奥氏体的再结晶数量，使组织均匀化 ；
(7) 出加热炉后进行高压水除磷，除磷压力 18MPa ；
(8) 除磷后进行粗轧 9 道次粗轧，粗轧完待钢温降到 900 ° C ，进行奥氏体非再结晶区精轧。保证非再结晶区的总压下率 >45% ，按轧制能力适当加大道次压下量，特别是精轧前 3 道次压下率≥ 50% ，为随后的奥氏体向铁素体相变形核创造有利条件，增加形核部位，以达到细化铁素体晶粒的目的，最后道次压下率为 6% ，以保证厚度精确及板形良好， 所述轧机出口厚度 12mm ，精轧出口温度 820 ℃ ；
(9) 轧件出轧机后采用超快冷装置冷却，冷却速率为 15 ℃ /s ，淬火终止温度为 550 ℃ ；
(10) 卷取机卷取，进行堆垛冷却 ；
(11) 送热处理车间进行开平，开平时钢卷温度 20 ℃ ；
(12) 对钢板进行抛丸处理去除表面氧化铁皮，抛丸速度 4m/min ，抛丸后钢板粗糙度为 55μm ；
( 13 ) 开平后进入热处理炉加热到 950 ℃，保温 1.5h ，进行淬火处理 ；
(14) 温度降至 300 ℃时进行回火处理 ；
(15) 在精整机组进行精整、检验。
本实施例中， 所述 步骤（ 5 ）中 进行 传统板坯连铸 后得到的铸坯的化学成分及其含量为： C 为 0.16wt% ， Si 为 0.4wt% ， Mn 为 1.5wt% ， Mo 为 0.20wt% ， Cr 为 0.32wt% ， Nb 为 0.031wt% ， Ti 为 0.11wt% ， B 为 0.0006wt% ， P 为 0.010wt ％， S 为 0.002wt ％，其余为 Fe 及不可避免的杂质。本实施例提供的 薄规格高 Ti 耐磨钢 NM450 的 屈服强度为 985MPa ，抗拉强度 1195MPa ， A50 延伸率 13.5% ，表面布氏硬度 370HBW ， -20 ℃条件下，夏比 V 形冲击功分别为 78J 、 76J 、 80J ，其性能满足 NM450 国家标准 GB/T24186-2009 技术条件。
实施例 2
一种薄规格高 Ti 耐磨钢 NM450 的制造方法，包括步骤：
(1) 将温度 >1250℃ 、 [S]≤0.020% ( 铁水中 S 的质量百分比 ) 的合格的铁水先进行扒渣处理，根据来料铁水的温度、重量及脱硫终点硫含量要求，进行 KR 脱 S, [S] 为 0.0010% ，采用全程吹氩工艺，终渣碱度 3.5 ；
(2) 进行转炉冶炼，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；萤石应根据炉内渣情况分批少量加入，每吨钢加入量 3.2kg ，吹炼终点前 2min 严禁加入萤石，采用挡渣锥、挡渣塞进行双挡渣出钢，渣厚 45mm ； 在转炉出钢过程中采用分步脱氧工艺进行脱氧：在转炉出钢时向钢包中先加入复合脱氧剂及金属铝块，对钢水进行初脱氧；接着向钢包中加入低碳锰铁、硅铁、钼铁和铬铁，对钢包中钢水进行全程吹氩，吹氩 5min 后测量钢水温度、定氧、取样，根据钢水氧含量向钢水中喂铝线进行钢水终脱氧及铝合金化，并保持吹氩 2min ；
( 3 ) 钢水送入 LF 精炼站，钢水进入精炼站后，对钢水用 500NL/min 氩气流量搅拌 1 . 5min 化渣；将石墨电极插入钢水中，供电升温，同时向钢水中吹氩，吹氩流量保持在 350NL/min ，吹氩 6min ；钢水脱硫时吹氩流量为 400NL/min ，吹氩 8min 测温；取样时吹氩流量为 250NL/min ；吹氩压力 1.2MPa ，在钢水精炼过程中，向钢水中加入造渣料造渣，如石灰、合成渣、预溶渣或调渣剂；进行脱硫精炼去夹杂处理，将渣中二元碱度 R(CaO/Si02) 控制在 2.8 ，并使渣中 Fe0+Mn0<2.0% ，出站钢水 [S] 为 0.004% ；
( 4) RH 炉精炼，到 RH 后，钢包开到待处理位，测量钢包净空高度、渣厚及温度，钢包净空控制在 350mm ，钢水顶渣厚度 90mm ，钢水温度为 1615 ℃；插入管插入钢水深度 650mm, 根据温度、氧含量和钢样成分进行合金化成分精调，合金化顺序：先加 AL 合金；然后加入 SiFe 、 MnFe 、 CrFe 、 MoFe 、 NbFe 等，合金加入后在极限真空度下循环 3 分钟，测温、取样、定氧；合金化后要求钢中 [O] 氧量控制在 2ppm ，温度控制在 1595 ℃ ， RH 精炼出站前依次喂铝线和钛线或者 Ti 合金，调整 AlS 和 Ti 的成分，最后进行 B 的微合金化 ；
(5) 进行传统板坯连铸，对中间包钢水表面采用双层覆盖剂，下层加足量碱性覆盖剂，而上层加低碳酸性覆盖剂，中间包采用恒重操作；钢水从大包到中间包采用长水口浇注、氩气保护，采用专用中碳耐磨钢结晶器保护渣，过热度控制在 15 ℃ ，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 1.2m/min ，连铸坯厚度 220mm ，板坯冷却到室温，对板坯质量及表面进行检查，扒去连铸坯表面一层表皮 ；
(6) 送入炉加热，在加热炉内加热时间为 300min ，加热温度 1200 ℃ ，板坯出加热炉温度 1180 ℃，采用两阶段控制轧制。对于再结晶区轧制，在设备允许条件下减少轧制道次，提高轧制道次压下率；并适当延长扎后停留时间，以增加变形奥氏体的再结晶数量，使组织均匀化 ；
(7) 出加热炉后进行高压水除磷，除磷压力 20MPa ；
(8) 除磷后进行粗轧 7 道次粗轧，粗轧完待钢温降到 900 ° C ，进行奥氏体非再结晶区精轧。保证非再结晶区的总压下率 >45% ，按轧制能力适当加大道次压下量，特别是精轧前 3 道次压下率≥ 50% ，为随后的奥氏体向铁素体相变形核创造有利条件，增加形核部位，以达到细化铁素体晶粒的目的，最后道次压下率为 7.3% ，以保证厚度精确及板形良好， 所述轧机出口厚度 6mm ，精轧出口温度 860 ℃ ；
(9) 轧件出轧机后采用超快冷装置冷却，冷却速率为 30 ℃ /s ，淬火终止温度为 500 ℃ ；
(10) 卷取机卷取，进行堆垛冷却 ；
(11) 送热处理车间进行开平，开平时钢卷温度 60 ℃ ；
(12) 对钢板进行抛丸处理去除表面氧化铁皮，抛丸速度 2m/min ，抛丸后钢板粗糙度为 30μm ；
( 13 ) 开平后进入热处理炉加热到 900 ℃，保温 2h ，进行淬火处理 ；
(14) 温度降至 350 ℃时进行回火处理 ；
(15) 在精整机组进行精整、检验。
本实施例中， 所述 步骤（ 5 ）中 进行 传统板坯连铸 后得到的铸坯的化学成分及其含量为： C 为 0.20wt% ， Si 为 0.20wt% ， Mn 为 0.85wt% ， Mo 为 0.20wt% ， Cr 为 0.50wt% ， Nb 为 0.045wt% ， Ti 为 0.15wt% ， B 为 0.0010wt% ， P 为 0.011wt ％， S 为 0.002wt ％，其余为 Fe 及不可避免的杂质。本实施例提供的 薄规格高 Ti 耐磨钢 NM450 的 屈服强度为 1010MPa ，抗拉强度 1215MPa ， A50 延伸率 14.5% ，表面布氏硬度 367HBW ， -20 ℃条件下，夏比 V 形冲击功分别为 82J 、 83J 、 89J ，其性能满足 NM450 国家标准 GB/T24186-2009 技术条件。
实施例 3
一种薄规格高 Ti 耐磨钢 NM450 的制造方法，包括步骤：
(1) 将温度 >1250℃ 、 [S]≤0.020% ( 铁水中 S 的质量百分比 ) 的合格的铁水先进行扒渣处理，根据来料铁水的温度、重量及脱硫终点硫含量要求，进行 KR 脱 S, [S] 为 0.0010% ，采用全程吹氩工艺，终渣碱度 3.0 ；
(2) 进行转炉冶炼，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；萤石应根据炉内渣情况分批少量加入，每吨钢加入量 3.2kg ，吹炼终点前 2min 严禁加入萤石，采用挡渣锥、挡渣塞进行双挡渣出钢，渣厚 40mm ； 在转炉出钢过程中采用分步脱氧工艺进行脱氧：在转炉出钢时向钢包中先加入复合脱氧剂及金属铝块，对钢水进行初脱氧；接着向钢包中加入低碳锰铁、硅铁、钼铁和铬铁，对钢包中钢水进行全程吹氩，吹氩 10min 后测量钢水温度、定氧、取样，根据钢水氧含量向钢水中喂铝线进行钢水终脱氧及铝合金化，并保持吹氩 2min ；
( 3 ) 钢水送入 LF 精炼站，钢水进入精炼站后，对钢水用 400NL/min 氩气流量搅拌 2min 化渣；将石墨电极插入钢水中，供电升温，同时向钢水中吹氩，吹氩流量保持在 350NL/min ，吹氩 8min ；钢水脱硫时吹氩流量为 320NL/min ，吹氩 8min 测温；取样时吹氩流量为 250NL/min ；吹氩压力 1.2MPa ，在钢水精炼过程中，向钢水中加入造渣料造渣，如石灰、合成渣、预溶渣或调渣剂；进行脱硫精炼去夹杂处理，将渣中二元碱度 R(CaO/Si02) 控制在 2.0 ，并使渣中 Fe0+Mn0<2.0% ，出站钢水 [S] 为 0.003% ；
( 4) RH 炉精炼，到 RH 后，钢包开到待处理位，测量钢包净空高度、渣厚及温度，钢包净空控制在 300mm ，钢水顶渣厚度 80mm ，钢水温度为 1625 ℃；插入管插入钢水深度 660mm, 根据温度、氧含量和钢样成分进行合金化成分精调，合金化顺序：先加 AL 合金；然后加入 SiFe 、 MnFe 、 CrFe 、 MoFe 、 NbFe 等，合金加入后在极限真空度下循环 3 分钟，测温、取样、定氧；合金化后要求钢中 [O] 氧量控制在 2ppm ，温度控制在 1599 ℃ ， RH 精炼出站前依次喂铝线和钛线或者 Ti 合金，调整 AlS 和 Ti 的成分，最后进行 B 的微合金化 ；
(5) 进行传统板坯连铸，对中间包钢水表面采用双层覆盖剂，下层加足量碱性覆盖剂，而上层加低碳酸性覆盖剂，中间包采用恒重操作；钢水从大包到中间包采用长水口浇注、氩气保护，采用专用中碳耐磨钢结晶器保护渣，过热度控制在 30 ℃ ，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 1.1m/min ，连铸坯厚度 220mm ，板坯冷却到室温，对板坯质量及表面进行检查，扒去连铸坯表面一层表皮 ；
(6) 送入炉加热，在加热炉内加热时间为 300min ，加热温度 1180 ℃ ，板坯出加热炉温度 1160 ℃，采用两阶段控制轧制，对于再结晶区轧制，在设备允许条件下减少轧制道次，提高轧制道次压下率；并适当延长扎后停留时间，以增加变形奥氏体的再结晶数量，使组织均匀化 ；
(7) 出加热炉后进行高压水除磷，除磷压力 16MPa ；
(8) 除磷后进行粗轧 5 道次粗轧，粗轧完待钢温降到 950 ° C ，进行奥氏体非再结晶区精轧，保证非再结晶区的总压下率 >45% ，按轧制能力适当加大道次压下量，特别是精轧前 3 道次压下率≥ 50% ，为随后的奥氏体向铁素体相变形核创造有利条件，增加形核部位，以达到细化铁素体晶粒的目的，终轧温度控制在接近 Ar3 相变温度，最后道次压下率为 7.3% ，以保证厚度精确及板形良好， 所述轧机出口厚度 ,8mm ，精轧出口温度 840 ℃ ；
(9) 轧件出轧机后采用超快冷装置冷却，冷却速率为 25 ℃ /s ，淬火终止温度为 550 ℃ ；
(10) 卷取机卷取，进行堆垛冷却 ；
(11) 送热处理车间进行开平，开平时钢卷温度 30 ℃ ；
(12) 对钢板进行抛丸处理去除表面氧化铁皮，抛丸速度 4m/min ，抛丸后钢板粗糙度为 35μm ；
( 13 ) 开平后进入热处理炉加热到 900 ℃，保温 2h ，进行淬火处理 ；
(14) 温度降至 350 ℃时进行回火处理 ；
(15) 在精整机组进行精整、检验。
本实施例中， 所述 步骤（ 5 ）中 进行 传统板坯连铸 后得到的铸坯的化学成分及其含量为： C 为 0.18wt% ， Si 为 0.25wt% ， Mn 为 1.5wt% ， Mo 为 0.15wt% ， Cr 为 0.45wt% ， Nb 为 0.050wt% ， Ti 为 0.10wt% ， B 为 0.0007wt% ， P 为 0.010wt ％， S 为 0.002wt ％，其余为 Fe 及不可避免的杂质。本实施例提供的 薄规格高 Ti 耐磨钢 NM450 的 屈服强度为 1015MPa ，抗拉强度 1295MPa ， A50 延伸率 13.5% ，表面布氏硬度 385HBW ， -20 ℃条件下，夏比 V 形冲击功分别为 64J 、 60J 、 65J ，其性能满足 NM450 国家标准 GB/T24186-2009 技术条件。
实施例 4
一种薄规格高 Ti 耐磨钢 NM450 的制造方法，包括步骤：
(1) 将温度 >1250℃ 、 [S]≤0.020% ( 铁水中 S 的质量百分比 ) 的合格的铁水先进行扒渣处理，根据来料铁水的温度、重量及脱硫终点硫含量要求，进行 KR 脱 S, [S] 为 0.0010% ，采用全程吹氩工艺，终渣碱度 3.5 ；
(2) 进行转炉冶炼，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；萤石应根据炉内渣情况分批少量加入，每吨钢加入量 3.5kg ，吹炼终点前 2min 严禁加入萤石，采用挡渣锥、挡渣塞进行双挡渣出钢，渣厚 40mm ； 在转炉出钢过程中采用分步脱氧工艺进行脱氧：在转炉出钢时向钢包中先加入复合脱氧剂及金属铝块，对钢水进行初脱氧；接着向钢包中加入低碳锰铁、硅铁、钼铁和铬铁，对钢包中钢水进行全程吹氩，吹氩 10min 后测量钢水温度、定氧、取样，根据钢水氧含量向钢水中喂铝线进行钢水终脱氧及铝合金化，并保持吹氩 2min ；
( 3 ) 钢水送入 LF 精炼站，钢水进入精炼站后，对钢水用 400NL/min 氩气流量搅拌 2min 化渣；将石墨电极插入钢水中，供电升温，同时向钢水中吹氩，吹氩流量保持在 350NL/min ，吹氩 8min ；钢水脱硫时吹氩流量为 100NL/min ，吹氩 8min 测温；取样时吹氩流量为 250NL/min ；吹氩压力 1.2MPa ，在钢水精炼过程中，向钢水中加入造渣料造渣，如石灰、合成渣、预溶渣或调渣剂；进行脱硫精炼去夹杂处理，将渣中二元碱度 R(CaO/Si02) 控制在 2.0 ，并使渣中 Fe0+Mn0<2.0% ，出站钢水 [S] 为 0.003% ；
( 4) RH 炉精炼，到 RH 后，钢包开到待处理位，测量钢包净空高度、渣厚及温度，钢包净空控制在 300mm ，钢水顶渣厚度 80mm ，钢水温度为 1630 ℃；插入管插入钢水深度 665mm, 根据温度、氧含量和钢样成分进行合金化成分精调，合金化顺序：先加 AL 合金；然后加入 SiFe 、 MnFe 、 CrFe 、 MoFe 、 NbFe 等，合金加入后在极限真空度下循环 3 分钟，测温、取样、定氧；合金化后要求钢中 [O] 氧量控制在 2ppm ，温度控制在 1595 ℃ ， RH 精炼出站前依次喂铝线和钛线或者 Ti 合金，调整 AlS 和 Ti 的成分，最后进行 B 的微合金化 ；
(5) 进行传统板坯连铸，对中间包钢水表面采用双层覆盖剂，下层加足量碱性覆盖剂，而上层加低碳酸性覆盖剂，中间包采用恒重操作；钢水从大包到中间包采用长水口浇注、氩气保护，采用专用中碳耐磨钢结晶器保护渣，过热度控制在 30 ℃ ，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 1.1m/min ，连铸坯厚度 220mm ，板坯冷却到室温，对板坯质量及表面进行检查，扒去连铸坯表面一层表皮 ；
(6) 送入炉加热，在加热炉内加热时间为 300min ，加热温度 1200 ℃ ，板坯出加热炉温度 1160 ℃，采用两阶段控制轧制，对于再结晶区轧制，在设备允许条件下减少轧制道次，提高轧制道次压下率；并适当延长扎后停留时间，以增加变形奥氏体的再结晶数量，使组织均匀化 ；
(7) 出加热炉后进行高压水除磷，除磷压力 18MPa ；
(8) 除磷后进行粗轧 5 道次粗轧，粗轧完待钢温降到 950 ° C ，进行奥氏体非再结晶区精轧，保证非再结晶区的总压下率 >45% ，按轧制能力适当加大道次压下量，特别是精轧前 3 道次压下率≥ 50% ，为随后的奥氏体向铁素体相变形核创造有利条件，增加形核部位，以达到细化铁素体晶粒的目的，最后道次压下率为 8% ，以保证厚度精确及板形良好， 所述轧机出口厚度为 10mm ，精轧出口温度 860 ℃ ；
(9) 轧件出轧机后采用超快冷装置冷却，冷却速率为 20 ℃ /s ，淬火终止温度为 550 ℃ ；
(10) 卷取机卷取，进行堆垛冷却 ；
(11) 送热处理车间进行开平，开平时钢卷温度 30 ℃ ；
(12) 对钢板进行抛丸处理去除表面氧化铁皮，抛丸速度 3m/min ，抛丸后钢板粗糙度为 40μm ；
( 13 ) 开平后进入热处理炉加热到 920 ℃，保温 1.5h ，进行淬火处理 ；
(14) 温度降至 300 ℃时进行回火处理 ；
(15) 在精整机组进行精整、检验。
本实施例中， 所述 步骤（ 5 ）中 进行 传统板坯连铸 后得到的铸坯的化学成分及其含量为： C 为 0.18wt% ， Si 为 0.25wt% ， Mn 为 1.5wt% ， Mo 为 0.15wt% ， Cr 为 0.45wt% ， Nb 为 0.050wt% ， Ti 为 0.10wt% ， B 为 0.0007wt% ， P 为 0.010wt ％， S 为 0.002wt ％，其余为 Fe 及不可避免的杂质。本实施例提供的 薄规格高 Ti 耐磨钢 NM450 的 屈服强度为 1015MPa ，抗拉强度 1295MPa ， A50 延伸率 13.5% ，表面布氏硬度 385HBW ， -20 ℃条件下，夏比 V 形冲击功分别为 64J 、 60J 、 65J ，其性能满足 NM450 国家标准 GB/T24186-2009 技术条件。
本发明的上述实施例仅仅是为清楚地说明本发明所作的举例，而并非是对本发明的实施方式的限定。对于所属领域的普通技术人员来说，在上述说明的基础上还可以做出其它不同形式的变化或变动。这里无需也无法对所有的实施方式予以穷举。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，均应包含在本发明权利要求的保护范围之内。

Claims (7)

  1. 一种薄规格高 Ti 耐磨钢 NM450 的制造方法，其特征在于，包括步骤：
    (1) 将温度 >1250 ℃ 、 [S]≤0.020% 的合格的铁水先进行扒渣处理，根据来料铁水的温度、重量及脱硫终点硫含量要求，进行 KR 脱 S, [S]≤0.0020% ，采用全程吹氩工艺，终渣碱度 3.0~4.0 ；
    (2) 进行转炉冶炼，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；萤石应根据炉内渣情况分批少量加入，每吨钢加入量 ≤4kg ，双渣时每吨钢 ≤5.5kg ，吹炼终点前 2min 严禁加入萤石，采用挡渣锥、挡渣塞进行双挡渣出钢，渣厚 ≤50mm ，在转炉出钢过程中采用分步脱氧工艺进行脱氧；
    ( 3 ) 钢水送入 LF 精炼站，钢水进入精炼站后，对钢水用 300 ～ 800NL/min 氩气流量搅拌 1 ~ 2min ，以便化渣；将石墨电极插入钢水中，供电升温，同时向钢水中吹氩，吹氩流量保持在 100 ~ 400NL/min ，吹氩 4 ~ 10min ；钢水脱硫时吹氩流量为 100 ~ 450NL/min ，吹氩 4 ~ 10min 测温；取样时吹氩流量为 100 ~ 400NL/min ；吹氩压力 1.2 ~ 1.8MPa ，在钢水精炼过程中，向钢水中加入造渣料造渣，进行脱硫精炼去夹杂处理，将渣中二元碱度 R(CaO/Si02) 控制在 1.3 ~ 2.8 ，并使渣中 Fe0+Mn0<2.0% ，出站钢水 [S] ≤ 0.008% ；
    ( 4) RH 炉精炼，到 RH 后，钢包开到待处理位，测量钢包净空高度、渣厚及温度，钢包净空控制在 300 ～ 700mm ，钢水顶渣厚度应小于 100mm ，钢水温度为 1615 ℃ ~1630 ℃；根据钢包净空高度及渣厚顶升钢包，确保插入管插入钢水深度不小于 600mm, 根据温度、氧含量和钢样成分进行合金化成分精调，合金化顺序：先加 AL 合金；然后加入 SiFe 、 MnFe 、 CrFe 、 MoFe 、 NbFe ，合金加入后在极限真空度下循环 3 分钟，测温、取样、定氧；合金化后要求钢中 [O] 氧量控制在 3ppm 以下，温度控制在 1590 ～ 1600 ℃， RH 精炼出站前依次喂铝线和钛线或者 Ti 合金，调整 AlS 和 Ti 的成分，最后进行 B 的微合金化 ；
    (5) 进行传统板坯连铸，对中间包钢水表面采用双层覆盖剂，下层加足量碱性覆盖剂，而上层加低碳酸性覆盖剂，中间包采用恒重操作；钢水从大包到中间包采用长水口浇注、氩气保护，采用专用中碳耐磨钢结晶器保护渣，过热度控制在 15 ~ 30 ℃ ，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 1.0 ~ 1.2m/min ，连铸坯厚度 220mm ， 进行 传统板坯连铸 后得到的铸坯的化学成分及其含量为： C 为 0.16~0.20wt% ， Si 为 0.2~0.4wt% ， Mn 为 0.8~1.5wt% ， Mo 为 0.10~0.20wt% ， Cr 为 0.30~0.50wt% ， Nb 为 0.02~0.05wt% ， Ti 为 0.10~0.15wt% ， B 为 0.0005~0.0010wt% ， P<0.015wt ％， S<0.010wt ％，其余为 Fe 及不可避免的杂质； 板坯冷却到室温，对板坯质量及表面进行检查，扒去连铸坯表面一层表皮 ；
    (6) 送入炉加热，在加热炉内加热时间≥ 240min ，加热温度 1180 ~ 1260 ℃ ，板坯出加热炉温度≥ 1150 ℃，采用两阶段控制轧制 ；
    (7) 出加热炉后进行高压水除磷，除磷压力≥ 16MPa ；
    (8) 除磷后进行粗轧 5~9 道次粗轧，粗轧完待钢温降到 900~950 ° C ，进行奥氏体非再结晶区精轧 , 保证非再结晶区的总压下率 >45% ，按轧制能力适当加大道次压下量，特别是精轧前 3 道次压下率≥ 50% ，终轧温度控制 820~860 ° C ，最后道次压下率≤ 12% ；
    (9) 轧件出轧机后采用超快冷装置冷却，冷却速率为 15 ~ 30 ℃ /s ，淬火终止温度为 550 ~ 650 ℃ ；
    (10) 卷取机卷取，进行堆垛冷却 ；
    (11) 送热处理车间进行开平 ；
    (12) 对钢板进行抛丸处理去除表面氧化铁皮；
    ( 13 ) 开平后进入热处理炉加热到 900~950 ℃，保温 1.5~2h ，进行淬火处理 ；
    (14) 温度降至 300 ~ 400 ℃时进行回火处理 ；
    (15) 在精整机组进行精整、检验。
  2. 根据权利要求 1 所述的 薄规格高 Ti 耐磨钢 NM450 的制造方法 ，其特征在于：步骤 (2) 中，所述 转炉新开炉前 6 炉及大补后前 2 炉不得冶炼相同钢种 。
  3. 根据权利要求 1 所述的 薄规格高 Ti 耐磨钢 NM450 的制造方法 ，其特征在于：步骤 (6) 中， 在加热炉内加热时间≥ 60min ，加热温度 1050 ~ 1150 ℃ 。
  4. 根据权利要求 1 所述的 薄规格高 Ti 耐磨钢 NM450 的制造方法 ，其特征在于：步骤 (8) 中，所述轧机出口厚度 6~12mm ，精轧出口温度 860 ~ 920 ℃ 。
  5. 根据权利要求 1 所述的 薄规格高 Ti 耐磨钢 NM450 的制造方法 ，其特征在于：步骤 (2) 中所述分步脱氧工艺包括：在转炉出钢时向钢包中先加入复合脱氧剂及金属铝块，对钢水进行初脱氧，复合脱氧剂及金属铝块的加入量需根据钢水终点溶解氧和初脱氧后目标氧含量确定；接着向钢包中加入低碳锰铁、硅铁、钼铁和铬铁；对钢包中钢水进行全程吹氩，吹氩 3 ~ 8min 后测量钢水温度、定氧、取样，根据钢水氧含量向钢水中喂铝线进行钢水终脱氧及铝合金化，并保持吹氩 2 ～ 10min 。
  6. 根据权利要求 1 所述的 薄规格高 Ti 耐磨钢 NM450 的制造方法 ，其特征在于：步骤 (3) 所述的 造渣料包括石灰、合成渣、预溶渣或调渣剂。
  7. 根据权利要求 1 所述的 薄规格高 Ti 耐磨钢 NM450 的制造方法 ，其特征在于：步骤 (12) 中抛丸速度≤ 2~4m/min ，抛丸后钢板粗糙度为 25~55μm 。
PCT/CN2017/115390 2017-03-31 2017-12-11 一种薄规格高Ti耐磨钢NM450的制造方法 Ceased WO2018176908A1 (zh)

Priority Applications (1)

Application Number Priority Date Filing Date Title
US16/499,324 US11649516B2 (en) 2017-03-31 2017-12-11 Method for manufacturing thin-specification high-Ti wear-resistant steel NM450

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201710204549.6 2017-03-31
CN201710204549.6A CN107099728B (zh) 2017-03-31 2017-03-31 一种薄规格高Ti耐磨钢NM450的制造方法

Publications (1)

Publication Number Publication Date
WO2018176908A1 true WO2018176908A1 (zh) 2018-10-04

Family

ID=59675986

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2017/115390 Ceased WO2018176908A1 (zh) 2017-03-31 2017-12-11 一种薄规格高Ti耐磨钢NM450的制造方法

Country Status (3)

Country Link
US (1) US11649516B2 (zh)
CN (1) CN107099728B (zh)
WO (1) WO2018176908A1 (zh)

Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN114525392A (zh) * 2022-02-22 2022-05-24 新疆八一钢铁股份有限公司 一种钛碳双稳定碳素结构钢冷轧板的制备方法
EP4019658A4 (en) * 2019-09-26 2022-07-20 Institute Of Research Of Iron And Steel, Jiangsu Province/Sha-Steel, Co. Ltd (CN) WIRE ROD FOR ULTRA HIGH STRENGTH STEEL CABLE AND PROCESS FOR ITS PRODUCTION
CN114908208A (zh) * 2022-04-18 2022-08-16 包头钢铁（集团）有限责任公司 一种利用转炉终点温度冶炼Mn含量12%以上高合金钢方法
CN116748300A (zh) * 2021-07-30 2023-09-15 日照钢铁控股集团有限公司 一种无Cr成分1.5mm45钢的连铸连轧生产方法
CN116987970A (zh) * 2023-08-02 2023-11-03 武汉钢铁有限公司 一种厚度≤10mm的700MPa级冷加工成形用桥壳钢及生产方法
CN118308645A (zh) * 2024-04-08 2024-07-09 新疆八一钢铁股份有限公司 一种高韧性合金结构钢板的制备方法

Families Citing this family (29)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107099728B (zh) * 2017-03-31 2018-09-14 华南理工大学 一种薄规格高Ti耐磨钢NM450的制造方法
CN109055869B (zh) * 2018-08-07 2020-02-18 鞍钢股份有限公司 一种炼化加热炉炉管用宽规格耐热钢板及其生产方法
CN109468527B (zh) * 2018-10-08 2020-05-19 湖南华菱涟源钢铁有限公司 一种双金属带锯条背材用钢及其制造方法
CN109182666A (zh) * 2018-11-12 2019-01-11 南京钢铁股份有限公司 一种宽薄规格nm450耐磨钢钢板及制造方法
US12221664B2 (en) * 2018-11-14 2025-02-11 Nippon Steel Corporation Apparatus for manufacturing thin steel sheet and method for manufacturing thin steel sheet
CN109852766B (zh) * 2018-12-05 2020-11-03 敬业钢铁有限公司 一种rh炉精炼氢氧控制工艺
CN109706399B (zh) * 2019-03-01 2021-06-04 攀钢集团攀枝花钢铁研究院有限公司 高钛耐磨钢及其制备方法
CN110004371B (zh) * 2019-05-07 2020-12-18 南京钢铁股份有限公司 一种耐磨钢及冶炼方法
CN110724792B (zh) * 2019-09-30 2021-08-24 河钢股份有限公司 一种用lf精炼炉生产低温环境用高锰钢的冶炼方法
CN110964979B (zh) * 2019-12-05 2021-09-14 邯郸钢铁集团有限责任公司 具有良好成型性能的自卸车厢体用耐磨钢及其生产方法
CN111304426B (zh) * 2020-03-31 2021-09-03 湖南华菱湘潭钢铁有限公司 一种高强钢薄板的生产方法
CN111500919B (zh) * 2020-05-29 2021-12-14 攀钢集团攀枝花钢铁研究院有限公司 高洁净度高钛低碳钢的生产方法
CN111647720A (zh) * 2020-07-29 2020-09-11 攀钢集团西昌钢钒有限公司 一种高铝高钒板坯n含量的控制方法
CN112296294B (zh) * 2020-09-30 2022-09-13 首钢集团有限公司 一种提高板坯洁净度的方法
CN112795834B (zh) * 2020-11-19 2021-12-03 唐山钢铁集团有限责任公司 一种中碳中硅高铝双相钢连铸坯的生产方法
CN112517865B (zh) * 2020-11-23 2022-09-09 首钢集团有限公司 一种控制板坯液渣层厚度均匀性的方法
CN113249644B (zh) * 2021-03-24 2022-07-29 江阴兴澄特种钢铁有限公司 一种薄规格nm450钢板及其制造方法
CN113265574B (zh) * 2021-03-30 2022-05-17 北京首钢股份有限公司 一种超高碳合金钢的制备方法
CN113088613A (zh) * 2021-03-31 2021-07-09 山东泰山钢铁集团有限公司 一种控制400系不锈钢板坯中间裂纹的操作方法
CN113462963B (zh) * 2021-06-10 2022-05-20 江阴市万众精密机械有限公司 一种增速箱联轴器用耐冲击、耐低温止推盘及其制备方法
CN113957323B (zh) * 2021-10-30 2022-08-30 日照宝华新材料有限公司 一种浅冲压级dc01级别用钢生产方法
CN114480944A (zh) * 2021-11-29 2022-05-13 安阳钢铁股份有限公司 一种超低碳低硅低铝钢的制备方法
CN115537637B (zh) * 2022-08-29 2023-11-10 邯郸钢铁集团有限责任公司 一种无铝脱氧高碳铬轴承钢的冶炼方法
CN117845124A (zh) * 2022-09-30 2024-04-09 上海梅山钢铁股份有限公司 一种减少低碳含硼钢连铸板坯鼓包缺陷的方法
CN116770161A (zh) * 2023-06-21 2023-09-19 湖南华菱涟源钢铁有限公司 一种中高碳钢及其制备方法
CN116590605B (zh) * 2023-07-03 2026-04-24 华北理工大学 一种铁素体马氏体双相钢的制备方法
CN116871478B (zh) * 2023-07-17 2025-08-12 山东钢铁集团日照有限公司 一种提高钢包自开率方法
CN116949345B (zh) * 2023-07-31 2025-08-08 达力普石油专用管有限公司 一种低碳含钨钢及其生产方法
CN116987841A (zh) * 2023-09-28 2023-11-03 吕梁建龙实业有限公司 用于优质碳素结构钢生产的中包覆盖剂及其制备方法

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20120134872A1 (en) * 2010-11-30 2012-05-31 Kennametal Inc. Abrasion resistant steel, method of manufacturing an abrasion resistant steel and articles made therefrom
CN103194684A (zh) * 2013-03-28 2013-07-10 宝山钢铁股份有限公司 一种耐磨钢板及其制造方法
JP2014227583A (ja) * 2013-05-24 2014-12-08 新日鐵住金株式会社 曲げ加工性と耐摩耗性に優れた高強度熱延鋼板及びその製造方法
CN104962834A (zh) * 2015-06-14 2015-10-07 秦皇岛首秦金属材料有限公司 一种高韧性、布氏硬度稳定特厚耐磨钢及其制备方法
CN105063497A (zh) * 2015-09-17 2015-11-18 东北大学 一种高耐磨性能易加工低合金耐磨钢板及其制造方法
JP2016160513A (ja) * 2015-03-04 2016-09-05 Ｊｆｅスチール株式会社 耐摩耗鋼板およびその製造方法
CN107099730A (zh) * 2017-03-31 2017-08-29 华南理工大学 一种薄规格高Ti耐磨钢NM360的制造方法
CN107099728A (zh) * 2017-03-31 2017-08-29 华南理工大学 一种薄规格高Ti耐磨钢NM450的制造方法

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2110066A (en) * 1935-05-09 1938-03-01 Heuer Russell Pearce Iron and steel desulphurization
US4371392A (en) * 1978-12-27 1983-02-01 Daido Tokishuko Kabushiki Kaisha Process for refining a molten metal
JPS57188647A (en) * 1981-05-18 1982-11-19 Nippon Kokan Kk <Nkk> Steel pipe with wear resistance
JP3003451B2 (ja) * 1992-03-11 2000-01-31 日本鋼管株式会社 加工性および溶接性に優れた耐摩耗鋼
US6447622B1 (en) * 1999-06-16 2002-09-10 Nippon Steel Corporation High carbon steel wire excellent in wire-drawability and in fatigue resistance after wire drawing
CN101451220A (zh) * 2007-12-03 2009-06-10 舞阳钢铁有限责任公司 一种高强度耐磨钢板及其制备方法
CN101254527B (zh) * 2008-02-01 2010-12-08 湖南华菱涟源钢铁有限公司 基于薄板坯连铸连轧流程生产低碳贝氏体高强钢的方法
CN101775545B (zh) * 2009-01-14 2011-10-12 宝山钢铁股份有限公司 一种低合金高强度高韧性耐磨钢板及其制造方法
CN101758176B (zh) * 2010-01-21 2012-03-21 山西太钢不锈钢股份有限公司 一种双层中间包覆盖剂
CN103205651A (zh) * 2013-04-14 2013-07-17 首钢总公司 一种低成本高强度耐磨钢板的在线淬火生产方法
CN104726668B (zh) * 2013-12-23 2017-07-21 鞍钢股份有限公司 一种高效生产高磁感取向硅钢的方法
CN103789655A (zh) * 2014-01-16 2014-05-14 北京科技大学 一种在线淬火生产Nb合金化高强度耐磨钢板的方法
CN105755373B (zh) * 2016-04-01 2017-07-28 华南理工大学 一种生产nm400钢的方法

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20120134872A1 (en) * 2010-11-30 2012-05-31 Kennametal Inc. Abrasion resistant steel, method of manufacturing an abrasion resistant steel and articles made therefrom
CN103194684A (zh) * 2013-03-28 2013-07-10 宝山钢铁股份有限公司 一种耐磨钢板及其制造方法
JP2014227583A (ja) * 2013-05-24 2014-12-08 新日鐵住金株式会社 曲げ加工性と耐摩耗性に優れた高強度熱延鋼板及びその製造方法
JP2016160513A (ja) * 2015-03-04 2016-09-05 Ｊｆｅスチール株式会社 耐摩耗鋼板およびその製造方法
CN104962834A (zh) * 2015-06-14 2015-10-07 秦皇岛首秦金属材料有限公司 一种高韧性、布氏硬度稳定特厚耐磨钢及其制备方法
CN105063497A (zh) * 2015-09-17 2015-11-18 东北大学 一种高耐磨性能易加工低合金耐磨钢板及其制造方法
CN107099730A (zh) * 2017-03-31 2017-08-29 华南理工大学 一种薄规格高Ti耐磨钢NM360的制造方法
CN107099728A (zh) * 2017-03-31 2017-08-29 华南理工大学 一种薄规格高Ti耐磨钢NM450的制造方法

Non-Patent Citations (3)

* Cited by examiner, † Cited by third party
Title
DENG, XIANGTAO: "Designing Chemical Composition and Heat Treatment Technology Study on NM450 Grade Super-High Strength Low Alloy Plate", WANFANG DATA MASTER'S THESES, 31 May 2011 (2011-05-31) *
DENG, XIANGTAO: "Microstructure and Mechanical Property Control and Wear Mechanism Study for Low-alloy Abrasion Resistant Steel", WANFANG DATA DOCTOR'S THESES, 31 August 2016 (2016-08-31) *
LI, JING: "Development of Wear-resistant Steel Grade NM450 for Engineering Machinery", WANFANG DATA MASTER'S THESES, 29 May 2014 (2014-05-29) *

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4019658A4 (en) * 2019-09-26 2022-07-20 Institute Of Research Of Iron And Steel, Jiangsu Province/Sha-Steel, Co. Ltd (CN) WIRE ROD FOR ULTRA HIGH STRENGTH STEEL CABLE AND PROCESS FOR ITS PRODUCTION
CN116748300A (zh) * 2021-07-30 2023-09-15 日照钢铁控股集团有限公司 一种无Cr成分1.5mm45钢的连铸连轧生产方法
CN114525392A (zh) * 2022-02-22 2022-05-24 新疆八一钢铁股份有限公司 一种钛碳双稳定碳素结构钢冷轧板的制备方法
CN114525392B (zh) * 2022-02-22 2024-01-30 新疆八一钢铁股份有限公司 一种钛碳双稳定碳素结构钢冷轧板的制备方法
CN114908208A (zh) * 2022-04-18 2022-08-16 包头钢铁（集团）有限责任公司 一种利用转炉终点温度冶炼Mn含量12%以上高合金钢方法
CN114908208B (zh) * 2022-04-18 2023-09-26 包头钢铁（集团）有限责任公司 一种利用转炉终点温度冶炼Mn含量12%以上高合金钢方法
CN116987970A (zh) * 2023-08-02 2023-11-03 武汉钢铁有限公司 一种厚度≤10mm的700MPa级冷加工成形用桥壳钢及生产方法
CN118308645A (zh) * 2024-04-08 2024-07-09 新疆八一钢铁股份有限公司 一种高韧性合金结构钢板的制备方法

Also Published As

Publication number Publication date
CN107099728A (zh) 2017-08-29
CN107099728B (zh) 2018-09-14
US11649516B2 (en) 2023-05-16
US20200056254A1 (en) 2020-02-20

Similar Documents

Publication Publication Date Title
CN107099728B (zh) 一种薄规格高Ti耐磨钢NM450的制造方法
CN106987760B (zh) 一种在线淬火生产薄规格高Ti耐磨钢NM400的方法
US11453932B2 (en) Thin gauge wear-resistant steel sheet and method of manufacturing the same
CN107099729B (zh) 热连轧超快冷工艺生产薄规格耐磨钢nm450的方法
CN107099727B (zh) 一种超快冷在线淬火生产薄规格耐磨钢nm400的方法
CN102424933A (zh) 一种热轧高强带钢及其制造方法
CN106929634B (zh) 薄板坯连铸连轧工艺生产薄规格耐磨钢的方法
CN107099731B (zh) 一种在线淬火生产薄规格高Ti耐磨钢NM360的方法
CN116790983B (zh) 一种优质低碳低硅焊接用热轧盘条及其制备方法
CN116005081B (zh) 一种以V代Mo的低成本Q550D钢板及其生产方法
CN107099730B (zh) 一种薄规格高Ti耐磨钢NM360的制造方法
CN106191662A (zh) 一种钛脱氧易焊接调质高强韧性钢板及其制造方法
CN108165888A (zh) 一种退火态交货的4140塑料模具钢板及其生产方法
CN111893402A (zh) 一种超低温耐候桥梁钢及其生产方法
CN114672724A (zh) 一种稀土和氮微合金化含钼hrb500e盘螺钢筋及其生产方法
CN114480945A (zh) 一种利用在线余热生产30mm以下调质耐磨钢板NM400的方法
CN105177416B (zh) 一种炉壳用耐热压力容器钢板及其制造方法
CN109706375B (zh) 一种420～600mm大厚度低合金高强度结构钢的生产方法
CN108359899A (zh) 一种超高强结构钢bg960及制备方法
CN103469107A (zh) 一种低成本、高韧性A517Gr.B大型压力用钢板及其生产方法
CN103215504A (zh) 一种易成型高强度中厚钢板的生产方法
CN115287554A (zh) 一种切割工具用高强度合金钢及其热轧卷板的制造方法
CN103215500B (zh) 一种易成型高强度中厚钢板的生产方法
CN113604734A (zh) 一种超厚度规格低残余应力叉车用钢及其制备方法
CN116694992B (zh) 搅拌罐用高强轻量化耐磨钢及其制造方法

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 17904025

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

32PN Ep: public notification in the ep bulletin as address of the adressee cannot be established

Free format text: NOTING OF LOSS OF RIGHTS PURSUANT TO RULE 112(1) EPC

122 Ep: pct application non-entry in european phase

Ref document number: 17904025

Country of ref document: EP

Kind code of ref document: A1