WO2018040859A1 - 一种大厚度q960e超高强钢生产方法 - Google Patents

一种大厚度q960e超高强钢生产方法 Download PDF

Info

Publication number
WO2018040859A1
WO2018040859A1 PCT/CN2017/096431 CN2017096431W WO2018040859A1 WO 2018040859 A1 WO2018040859 A1 WO 2018040859A1 CN 2017096431 W CN2017096431 W CN 2017096431W WO 2018040859 A1 WO2018040859 A1 WO 2018040859A1
Authority
WO
WIPO (PCT)
Prior art keywords
ultra
thickness
strength steel
rolling
temperature
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/CN2017/096431
Other languages
English (en)
French (fr)
Inventor
郑建平
闫强军
姜在伟
陈林恒
王新
张仪杰
王思聪
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.)
Nanjing Iron and Steel Co Ltd
Original Assignee
Nanjing Iron and Steel Co Ltd
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 Nanjing Iron and Steel Co Ltd filed Critical Nanjing Iron and Steel Co Ltd
Priority to EP17845161.3A priority Critical patent/EP3467136B1/en
Publication of WO2018040859A1 publication Critical patent/WO2018040859A1/zh
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Images

Classifications

    • 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
    • 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
    • C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
    • 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
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C21D8/0242—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
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • C21D2211/009—Pearlite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Definitions

  • the invention relates to a method for producing ultra-high-strength steel, in particular to a method for producing a large-thickness Q960E ultra-high-strength steel, belonging to the technical field of steel.
  • Ultra-high-strength steel is a resource-saving type and a high-tech and high-value-added product. With the vigorous development of large-scale domestic projects, high-strength steel of Q890D and above is used in construction machinery, mining, and lifting and mining.
  • Vehicles, offshore platforms and other aspects have been vigorously applied, characterized by: simple structure, light weight, high safety, capable of carrying large dynamic and static loads, and long service life; however, due to the thickness of domestic cast billets, Large-thickness structural parts can only be replaced by conventional Q345-Q550 series low-alloy structural steel, and such structural steels are not strong in use under severe service conditions due to low strength, and are prone to engineering accidents; For engineering structural steel parts, domestic enterprises can only import high-strength steel with large thickness at high price;
  • the publication No. CN102560274A discloses a quenched and tempered ultra-high strength steel with a yield strength of 1000 MPa and a production method thereof. Through reasonable composition design, after quenching and tempering, reasonable performance is obtained, but the production thickness of the patent is 12-50 mm. And the impact energy at -40 °C is relatively low, only 60J or less, and the toughness is not good;
  • the publication No. CN102134680A discloses a super-high strength steel with a yield strength of 960 MPa and a production method thereof, which adopts a low carbon + 1.05% Cr alloy design, and obtains a strength with a yield strength of more than 960 MPa through quenching and tempering heat treatment, but the whole production method
  • the hot rolling process and the thickness of the production are only 8mm, the production process is cumbersome and the production method is only laboratory data;
  • the technical problem to be solved by the present invention is to overcome the shortcomings of the prior art and provide a method for producing a large thickness Q960E ultra-high strength steel, which is simple and easy to operate, has a short production process, low cost, and has excellent mechanical properties of the produced steel. , large thickness, high strength, good plasticity, impact energy value and good welding performance.
  • the present invention provides a large-thickness Q960E ultra-high-strength steel production method, which comprises the following processes: hot metal desulfurization pretreatment-converter smelting-LF+RH refining-continuous casting-casting billet stacking slow cooling- Slab inspection - slab determination - slab acceptance - slab heating - descaling - rolling - air cooling - flaw detection - shot blasting - quenching - tempering - straightening - cutting, sampling - printing marking - inspection - storage, among them:
  • the chemical composition of the ultra-high strength steel includes, by weight: C: 0.14-0.16%, Si: 0.2-0.3%, Mn: 1.1-1.2%, P ⁇ 0.008%, S ⁇ 0.0015%, Cr: 0.4 -0.6%, Cu ⁇ 0.1%, Ni: 0.6-0.8%, Mo: 0.1-0.3%, Nb: 0.02-0.04%, Ti: 0.01-0.02%, V: 0.04-0.06%, B: ⁇ 0.0015%, Alt: 0.025-0.04%, Ceq ⁇ 0.61%, the balance is Fe and unavoidable impurities;
  • the carbon equivalent Ceq (percentage) of the chemical composition of the ultra-high strength steel is calculated by the following formula:
  • the heating section temperature is 1240-1250 °C
  • the soaking section temperature is controlled at 1220 °C
  • the tapping temperature is between 1180-1200 °C
  • the furnace time is 350-420 min
  • the two-stage rolling temperature is ⁇ 1050 ° C
  • the thickness of the finished product is 70 mm
  • the thickness of the blank to be warmed is controlled at ⁇ 133 mm
  • the second-stage finishing temperature is 850-860 ° C, and air-cooled after rolling;
  • tempering heat treatment quenching temperature control at 880-890 ° C, heating rate is 1.5 ⁇ 0.1min / mm, furnace time is 125-135min, tempering temperature is controlled at 590-600 ° C, heating rate is 2.5 ⁇ 0.1min/mm, in the furnace time is 220-230min, slowly cooling to room temperature;
  • Pre-correction is first performed at 790-830 °C in the hot-rolled state.
  • the chemical composition of the ultra-high-strength steel includes: C: 0.16%, Si: 0.23%, Mn: 1.19%, P ⁇ 0.005%, S ⁇ 0.0012. %, Cu ⁇ 0.1%, Cr: 0.45%, Ni: 0.78%, Mo: 0.2%, Nb: 0.02%, Ti: 0.013%, V: 0.044%, B: 0.0012%, Alt: 0.033%, Ceq: 0.55%, balance Fe and inevitable Impurities.
  • the mechanical properties of the ultra-high-strength steel reach the following levels: yield strength ⁇ 1000 MPa, tensile strength ⁇ 1050 MPa, elongation ⁇ 13%, -40 ° C, Akv impact work value ⁇ 90 J;
  • the microstructure is tempered sorbite structure, the grain size is controlled from 10 ⁇ m to 12 ⁇ m, and the grain size is controlled at 8-9.
  • the yield strength is ⁇ 1000MPa and the tensile strength is ⁇ 1050MPa, elongation ⁇ 13%, -40°C, Akv impact energy value ⁇ 90J; (3)
  • the method of the invention successfully solves the high strength, low plasticity, low impact energy value and high carbon equivalent of 70mm large thickness ultra high strength steel
  • the prepared steel has excellent mechanical properties, large thickness, high strength, good plasticity, impact work value and good welding performance;
  • the method of the invention successfully solves the rolling force in the roughing mill 5000 tons, finishing mill rolling force of 4000 tons, four-roll reversible 2800mm rolling mill production line can produce high-strength, high-toughness and high-density Q960E high-strength steel, applied to domestic large-scale construction machinery and equipment, greatly reducing dependence High cost; (5) Due to the high strength of the 70mm thick steel plate after rolling, it needs to be pre-corrected at 790-830 °C to ensure the original shape.
  • the quenching can be hardened.
  • the medium carbon and a small amount of Cr and B elements to improve the hardenability can be used to improve the cooling speed design idea to solve the requirements of producing high-grade equipment; (6) due to the high strength of the experimental steel, the 70mm steel plate is controlled by the high temperature and large reduction mode.
  • the overall compression ratio is >4 times, so the 320mm thick billet is selected, and the soaking temperature is controlled at about 1220 °C, which is properly extended in the furnace time to ensure the overall temperature of the billet steel is uniform and avoid the "red and black" phase steel temperature; 7) Since the thickness of the finished product is 70mm, in order to avoid the segregation of the core during the rolling process and affect the strength and impact value, the two-stage rolling method is adopted, and the deformation rate of the first-stage rolling is ⁇ 55%, and the total deformation rate of the second stage is ⁇ 45%, ensuring no significant differences in surface-to-heart tissue.
  • FIG. 1(a) is a photograph of a metallographic structure of a 1/4 thickness of a large-thickness Q960E ultra-high strength steel according to the present invention
  • Fig. 1(b) is a photograph showing the metallographic structure of the 1/2 thickness of the large-thickness Q960E ultra-high strength steel of the present invention.
  • the present invention provides a method for producing a large-thickness Q960E ultra-high-strength steel, and the production method comprises the following processes: hot metal desulfurization pretreatment-converter smelting-LF+RH refining-continuous casting-casting billet stacking slow-casting billet inspection- Slab determination - slab acceptance - slab heating - descaling - rolling - air cooling - flaw detection - shot blasting - quenching - tempering - straightening - cutting, sampling - printing marking - inspection - storage, where:
  • the chemical composition of the ultra-high strength steel includes: C: 0.15%, Si: 0.28%, Mn: 1.15%, P ⁇ 0.008%, S ⁇ 0.0015%, Cu ⁇ 0.1%, Cr: 0.59% , Ni: 0.61%, Mo: 0.28%, Nb: 0.023%, Ti: 0.018%, V: 0.058%, B: 0.0014%, Alt: 0.025%, Ceq: 0.57%, balance Fe and inevitable impurities ;
  • the carbon equivalent Ceq (percentage) of the chemical composition of the ultra-high strength steel is calculated by the following formula:
  • the heating section temperature is 1240-1250 °C
  • the soaking section temperature is controlled at 1207 °C
  • the tapping temperature is 1195 °C
  • the furnace time is 405 min
  • the second-stage rolling temperature is 886 °C
  • the finished thickness It is 70mm
  • the thickness of the blank to be warmed is 133mm
  • the second-stage finishing temperature is 856°C
  • air-cooling after rolling
  • Pre-correction is first carried out at 828 ° C in the hot-rolled state.
  • the two-stage rolling method is adopted in the rolling of the slab, the deformation rate of the first-stage rolling is ⁇ 55%, and the deformation rate of the second-stage rolling is ⁇ 45%; the mechanics of the ultra-high-strength steel is produced.
  • the performance reaches the following levels, as shown in Table 1 below:
  • the present invention provides a method for producing a large-thickness Q960E ultra-high-strength steel, and the production method comprises the following processes: hot metal desulfurization pretreatment-converter smelting-LF+RH refining-continuous casting-casting billet stacking slow-casting billet inspection- Slab determination - slab acceptance - slab heating - descaling - rolling - air cooling - flaw detection - shot blasting - quenching - tempering - straightening - cutting, sampling - printing marking - inspection - storage, where:
  • the chemical composition of the ultra-high strength steel includes: C: 0.16%, Si: 0.23%, Mn: 1.19%, P ⁇ 0.005%, S ⁇ 0.0012%, Cu ⁇ 0.1%, Cr: 0.45% , Ni: 0.78%, Mo: 0.2%, Nb: 0.02%, Ti: 0.013%, V: 0.044%, B: 0.0012%, Alt: 0.033%, Ceq: 0.55%, balance Fe and inevitable impurities ;
  • (2) 320mm thick slab is used to heat the slab, the heating section temperature is 1240-1250°C, the soaking section temperature is controlled at 1220°C, the tapping temperature is 1180°C, and the furnace time is 373min.
  • the rolling temperature is 890 ° C, the thickness of the finished product is 70 mm, the thickness of the blank to be warmed is controlled to be ⁇ 133 mm, the final rolling temperature of the second stage is 854 ° C, and air cooling after rolling;
  • Pre-correction is first carried out at 798 ° C in the hot-rolled state.
  • the two-stage rolling method is adopted in the rolling of the slab, the deformation rate of the first-stage rolling is ⁇ 55%, and the deformation rate of the second-stage rolling is ⁇ 45%; the mechanics of the ultra-high-strength steel is produced.
  • the performance reaches the following levels as shown in Table 2:
  • the present invention provides a method for producing a large-thickness Q960E ultra-high-strength steel, and the production method comprises the following processes: hot metal desulfurization pretreatment-converter smelting-LF+RH refining-continuous casting-casting billet stacking slow-casting billet inspection- Slab determination - slab acceptance - slab heating - descaling - rolling - air cooling - flaw detection - shot blasting - quenching - tempering - straightening - cutting, sampling - printing marking - inspection - storage, where:
  • the chemical composition of the ultra-high strength steel includes: C: 0.14%, Si: 0.25%, Mn: 1.1%, P ⁇ 0.008%, S ⁇ 0.0015%, Cu ⁇ 0.1%, Cr: 0.4% , Ni: 0.8%, Mo: 0.1%, Nb: 0.039%, Ti: 0.015%, V: 0.04%, B: 0.0011%, Alt: 0.038%, Ceq: 0.48%, balance Fe and inevitable impurities ;
  • the carbon equivalent Ceq (percentage) of the chemical composition of the ultra-high strength steel is calculated by the following formula:
  • the heating section temperature is 1240-1250 °C
  • the soaking section temperature is controlled at 1210 °C
  • the tapping temperature is 1189 °C
  • the furnace time is 378 min
  • the second-stage rolling temperature is 887 °C
  • the finished thickness It is 70mm
  • the thickness of the blank to be warmed is 133mm
  • the second-stage finishing temperature is 858°C
  • air-cooling after rolling
  • the quenching temperature is controlled at 885 ° C, the heating rate is 1.5 min / mm, the furnace time is 125 min, the tempering temperature is controlled at 591 ° C, the heating rate is 2.6 min / mm, and the furnace time is 228 min. , slowly cool to room temperature;
  • Pre-correction is first carried out at 825 ° C in the hot-rolled state.
  • the two-stage rolling method is adopted in the rolling of the slab, the deformation rate of the first-stage rolling is ⁇ 55%, and the deformation rate of the second-stage rolling is ⁇ 45%; the mechanics of the ultra-high-strength steel is produced.
  • the performance reaches the following levels, as shown in Table 3:
  • FIG. 1 (a) and (b) of Fig. 1 are the metallographic structure after tempering by heating temperature: 595 ° C, heating rate: 2.5 min/mm, heating time: 223 min, as can be seen from the structure in the figure, Metallographic structure from 1/4 thickness to 1/2, microstructure is tempered sorbite structure, tempering sorbite structure from 1/4 thickness to core, and grain size is controlled at 10 ⁇ m -12 ⁇ m, grain size reaches 8-9.
  • the invention develops a Q960E ultra-high strength steel with a thickness of 70 mm by designing a composition of medium carbon and a small amount of chromium, nickel, molybdenum alloy, niobium + vanadium + titanium + boron microalloying, with a reasonable controlled rolling process and quenching and tempering heat treatment process.
  • the strength has not yet been stipulated by the mechanical performance standard.
  • the strength and plastic toughness indexes obtained by the present invention all meet the design standards of mechanical properties of a large-scale enterprise engineering machinery in China. Due to high strength and large thickness, in the actual industrial production process, the rolling is performed. The equipment and the quenching machine have high cooling capacity requirements. At the same time, the 2800mm double-stand rolling mill is a reversible four-roll mill combination with a rolling force of 5,000 tons for the roughing mill and a rolling force of 4,000 tons for the finishing mill. The rolling force is low, and the production is low. In the process, the rolling reduction requirements cannot be met, and the original grain size is large, and even the phenomenon of mixed crystals is caused, which seriously affects the mechanical properties matched with the strength and low temperature toughness.
  • the design of alloying elements with high carbon hardenability and high hardenability makes up for the defects of Q960E high-strength steel which can not produce high strength, high toughness and high welding stability due to limited equipment capacity.
  • the rolling is ended, so that the strength in the high temperature state is low, so that the rolling ability of the low rolling force equipment is exerted.

Landscapes

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

Abstract

一种厚度为70mm的Q960E超高强钢生产方法，包括铸坯加热、淬火和回火步骤，钢的化学成分为；C：0.14-0.16％，Si：0.2-0.3％，Mn：1.1-1.2％，P≤0.008％，S≤0.0015％，Cr：0.4-0.6％，Cu≤0.1％，Ni：0.6-0.8％，Mo：0.1-0.3％，Nb：0.02-0.04％，Ti：0.01-0.02％，V：0.04-0.06％，B：≤0.0015％，Alt：0.025-0.04％，Ceq≤0.61％，余量为Fe及不可避免的杂质；淬火温度为880-890℃，回火温度为590-600℃。钢的屈服强度≥1000MPa，抗拉强度≥1050MPa。

Description

一种大厚度Q960E超高强钢生产方法 技术领域
本发明涉及一种超高强钢材生产方法，具体的说是一种大厚度Q960E超高强钢生产方法，属于钢铁技术领域。
背景技术
超高强度钢是一种资源节约型同时也是一种技术含量高、附加值高的产品，随着国内大型工程的大力发展，Q890D及以上等级的高强钢在工程机械、矿山开采、起重矿车、海洋平台等方面得到了大力应用，其特点是：结构简单，自重轻，安全性高，能够承载较大的动、静态载荷，服役时间较长；然而，由于国内铸坯受厚度影响，大厚度结构件目前只能采用常规Q345-Q550系列低合金结构钢代替，而此类结构钢因为强度低，在苛刻的服役条件下，使用强度不高，易出现工程事故；为此，针对大型工程结构钢件，国内企业只能花高价进口大厚度的超高强钢；
国内很多钢厂均在研究Q960及以上超高强钢的生产工艺，但对于大厚度Q960E超高强钢目前尚未有实质性的报道，已公布的专利文献内容中产品在实际工程应用更是微乎其微，本申请介绍了一种大厚度的Q960E超高强钢生产方法，且应用到国内某大型吊车底座，使用性能得到行业内的认可。
公开号为CN102560274A的专利公开了一种屈服强度1000MPa级调质超高强钢及其生产方法，通过合理的成分设计，经过调质，得到合理的性能，但该专利公布的生产厚度为12-50mm，且-40℃冲击功比较低，仅为60J以下，韧性不好；
公开号为CN102134680A的专利公开了一种屈服强度960MPa级超高强钢及其生产方法，采用低碳+1.05％Cr合金设计，通过调质热处理得到了屈服强度达到960MPa以上的强度，但整个生产方法采用热连轧工艺及生产的厚度仅为8mm，生产工序繁琐且生产方法仅为实验室的数据；
考虑到性能最优的70mm的大厚度Q960E超高强度结构钢板不仅要求较高的强度和韧性性能，还要求有良好的焊接性能，所有的要求均要易于生产且成本较低；因此，本申请针对70mm的大厚度Q960E超高强度钢板的化学成分和生产工艺进行了研究，设计了一种大厚度Q960E 超高强钢生产方法。
发明内容
本发明所要解决的技术问题是，克服现有技术的缺点，提供一种大厚度Q960E超高强钢生产方法，该生产方法简单易行，生产工序流程短，成本低，生产出的钢力学性能优良，大厚度，高强度，良好的塑性、冲击功值以及良好的焊接性能。
为了解决以上技术问题，本发明提供一种大厚度Q960E超高强钢生产方法，该生产方法包括以下流程：铁水脱硫预处理-转炉冶炼-LF+RH精炼-连铸-铸坯堆垛缓冷-铸坯检验-铸坯判定-铸坯验收-铸坯加热-除鳞-轧制-空冷-探伤-抛丸-淬火-回火-矫直-切割、取样-喷印标识-检验-入库，其中：
(1)该超高强钢的化学成分按重量百分比计包括：C：0.14-0.16％，Si：0.2-0.3％，Mn：1.1-1.2％，P≤0.008％，S≤0.0015％，Cr：0.4-0.6％，Cu≤0.1％，Ni：0.6-0.8％，Mo：0.1-0.3％，Nb：0.02-0.04％，Ti：0.01-0.02％，V：0.04-0.06％，B：≤0.0015％，Alt：0.025-0.04％，Ceq≤0.61％，余量为Fe及不可避免的杂质；
该超高强钢的化学成分中碳当量Ceq(百分比)按以下公式计算：
Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15≤0.61；
(2)对铸坯加热，加热段温度为1240-1250℃，均热段温度控制在1220℃，出钢温度介于1180-1200℃，在炉时间为350-420min，二阶段开轧温度≤1050℃，成品厚度为70mm，待温铸坯厚度控制在≥133mm，二阶段终轧温度850-860℃，轧后空冷；
(3)进行调质热处理，淬火温度控制在880-890℃，升温速率为1.5±0.1min/mm，在炉时间为125-135min，回火温度控制在590-600℃，升温速率为2.5±0.1min/mm，在炉时间为220-230min，缓冷至室温；
(4)热轧态矫直时先在790-830℃下进行预矫。
本发明进一步限定的技术方案是：
进一步的，前述大厚度Q960E超高强钢生产方法中，该超高强钢的化学成分按重量百分比计包括：C：0.16％，Si：0.23％，Mn：1.19％，P≤0.005％，S≤0.0012％，Cu≤0.1％，Cr： 0.45％，Ni：0.78％，Mo：0.2％，Nb：0.02％，Ti：0.013％，V：0.044％，B：0.0012％，Alt：0.033％，Ceq：0.55％，余量为Fe及不可避免的杂质。
前述大厚度Q960E超高强钢生产方法中，在对铸坯进行轧制时采用二阶段轧制法，一阶段轧制形变率≥55％，二阶段轧制形变率≥45％。
前述大厚度Q960E超高强钢生产方法中，该超高强钢的力学性能达到以下水平：屈服强度≥1000MPa，抗拉强度≥1050MPa，延伸率≥13％，-40℃，Akv冲击功值≥90J；显微组织为回火索氏体组织，晶粒尺寸控制在10μm-12μm，晶粒度控制在8-9级。
本发明的有益效果是：
(1)通过中碳加少量的铬、镍、钼合金、Nb+Ti+V+B微合金化成份设计，碳当量为≤0.61，生产工序流程短，成本低；(2)本方法采用合理的控轧工艺生产厚度达到70mm的超高强钢，通过最优的调质热处理工艺，各力学性能指标均达到国内某大型企业工程机械对材料设计的标准要求，屈服强度≥1000MPa，抗拉强度≥1050MPa，延伸率≥13％，-40℃，Akv冲击功值≥90J；(3)该发明方法成功解决了70mm的大厚度超高强钢的高强度低塑性、低冲击功值以及高碳当量对焊接性能影响的技术难点，制备出的钢力学性能优良，大厚度，高强度，良好的塑性、冲击功值以及良好的焊接性能；(4)该发明方法成功解决了在粗轧机轧制力为5000吨、精轧机轧制力为4000吨四辊可逆的2800mm轧机生产线能够生产高强度、高韧性大厚度的Q960E高强钢，应用到国内大型工程机械设备，大大降低了依赖进口高成本费用；(5)由于70mm厚度钢板轧后强度较高，需要在790-830℃进行预矫，保证原始板形，在坚持低成本生产要求的基础上，确保淬火能淬透，在成分设计中采用中碳加少量的提高淬透性的Cr、B元素从而可以提高冷速设计思路解决生产高等级设备要求；(6)由于实验钢强度高，70mm钢板采用高温大压下模式进行控轧，整体压缩比＞4倍，故选用320mm厚度坯料，且均热温度控制在1220℃左右，在炉时间适当延长，确保坯料钢温整体均匀，避免出现“红黑”相间的钢温；(7)由于成品厚度为70mm，在轧制过程中为避免出现心部偏析，影响强度和冲击值，故采用二阶段轧制方法，且一阶段轧制形变率≥55％，二阶段总形变率≥45％，确保表面到心部组织无明显差异性。
附图说明
图1(a)为本发明的大厚度Q960E超高强钢1/4厚度处金相组织照片；
图1(b)为本发明的大厚度Q960E超高强钢1/2厚度处金相组织照片。
具体实施方式
实施例1
本实施例提供的一种大厚度Q960E超高强钢生产方法，该生产方法包括以下流程：铁水脱硫预处理-转炉冶炼-LF+RH精炼-连铸-铸坯堆垛缓冷-铸坯检验-铸坯判定-铸坯验收-铸坯加热-除鳞-轧制-空冷-探伤-抛丸-淬火-回火-矫直-切割、取样-喷印标识-检验-入库，其中：
(1)该超高强钢的化学成分按重量百分比计包括：C：0.15％，Si：0.28％，Mn：1.15％，P≤0.008％，S≤0.0015％，Cu≤0.1％，Cr：0.59％，Ni：0.61％，Mo：0.28％，Nb：0.023％，Ti：0.018％，V：0.058％，B：0.0014％，Alt：0.025％，Ceq：0.57％，余量为Fe及不可避免的杂质；
该超高强钢的化学成分中碳当量Ceq(百分比)按以下公式计算：
Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15≤0.61；
(2)对铸坯加热，加热段温度为1240-1250℃，均热段温度控制在1207℃，出钢温度介于1195℃，在炉时间为405min，二阶段开轧温度886℃，成品厚度为70mm，待温铸坯厚度133mm，二阶段终轧温度856℃，轧后空冷；
(3)进行调质热处理，淬火温度控制在887℃，升温速率为1.4min/mm，在炉时间为122min，回火温度控制在599℃，升温速率为2.4min/mm，在炉时间为221min，缓冷至室温；
(4)热轧态矫直时先在828℃下进行预矫。
在本实施例中：在对铸坯进行轧制时采用二阶段轧制法，一阶段轧制形变率≥55％，二阶段轧制形变率≥45％；生产出的该超高强钢的力学性能达到以下水平，具体见下表1：
表1 力学性能
Figure PCTCN2017096431-appb-000001
屈服强度≥1000MPa，抗拉强度≥1050MPa，延伸率≥13％，-40℃，Akv冲击功值≥90J；显微组织为回火索氏体组织，晶粒尺寸控制在10μm-12μm，晶粒度控制在8-9级。
实施例2
本实施例提供的一种大厚度Q960E超高强钢生产方法，该生产方法包括以下流程：铁水脱硫预处理-转炉冶炼-LF+RH精炼-连铸-铸坯堆垛缓冷-铸坯检验-铸坯判定-铸坯验收-铸坯加热-除鳞-轧制-空冷-探伤-抛丸-淬火-回火-矫直-切割、取样-喷印标识-检验-入库，其中：
(1)该超高强钢的化学成分按重量百分比计包括：C：0.16％，Si：0.23％，Mn：1.19％，P≤0.005％，S≤0.0012％，Cu≤0.1％，Cr：0.45％，Ni：0.78％，Mo：0.2％，Nb：0.02％，Ti：0.013％，V：0.044％，B：0.0012％，Alt：0.033％，Ceq：0.55％，余量为Fe及不可避免的杂质；
(2)选用320mm厚的铸坯，对铸坯加热，加热段温度为1240-1250℃，均热段温度控制在1220℃，出钢温度介于1180℃，在炉时间为373min，二阶段开轧温度890℃，成品厚度为70mm，待温铸坯厚度控制为≥133mm，二阶段终轧温度854℃，轧后空冷；
(3)进行调质热处理，淬火温度控制在881℃，升温速率为1.5min/mm，在炉时间为130min，回火温度控制在595℃，升温速率为2.5min/mm，在炉时间为223min，缓冷至室温；
(4)热轧态矫直时先在798℃下进行预矫。
在本实施例中：在对铸坯进行轧制时采用二阶段轧制法，一阶段轧制形变率≥55％，二阶段轧制形变率≥45％；生产出的该超高强钢的力学性能达到以下水平见表2所示：
表2 力学性能
Figure PCTCN2017096431-appb-000002
实施例3
本实施例提供的一种大厚度Q960E超高强钢生产方法，该生产方法包括以下流程：铁水脱硫预处理-转炉冶炼-LF+RH精炼-连铸-铸坯堆垛缓冷-铸坯检验-铸坯判定-铸坯验收-铸坯加热-除鳞-轧制-空冷-探伤-抛丸-淬火-回火-矫直-切割、取样-喷印标识-检验-入库，其中：
(1)该超高强钢的化学成分按重量百分比计包括：C：0.14％，Si：0.25％，Mn：1.1％，P≤0.008％，S≤0.0015％，Cu≤0.1％，Cr：0.4％，Ni：0.8％，Mo：0.1％，Nb：0.039％，Ti：0.015％，V：0.04％，B：0.0011％，Alt：0.038％，Ceq：0.48％，余量为Fe及不可避免的杂质；
该超高强钢的化学成分中碳当量Ceq(百分比)按以下公式计算：
Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15≤0.61；
(2)对铸坯加热，加热段温度为1240-1250℃，均热段温度控制在1210℃，出钢温度介于1189℃，在炉时间为378min，二阶段开轧温度887℃，成品厚度为70mm，待温铸坯厚度133mm，二阶段终轧温度858℃，轧后空冷；
(3)进行调质热处理，淬火温度控制在885℃，升温速率为1.5min/mm，在炉时间为125min，回火温度控制在591℃，升温速率为2.6min/mm，在炉时间为228min，缓冷至室温；
(4)热轧态矫直时先在825℃下进行预矫。
在本实施例中：在对铸坯进行轧制时采用二阶段轧制法，一阶段轧制形变率≥55％，二阶段轧制形变率≥45％；生产出的该超高强钢的力学性能达到以下水平，见表3所示：
表3 力学性能
Figure PCTCN2017096431-appb-000003
屈服强度≥1000MPa，抗拉强度≥1050MPa，延伸率≥13％，-40℃，Akv冲击功值≥90J；
图1的(a)和(b)为通过加热温度：595℃，升温速率：2.5min/mm，加热时间为：223min，回火后的金相组织，从图中的组织可以看出，从1/4厚度处到1/2处金相组织，显微组织为回火索氏体组织，从1/4厚度处到心部均为回火索氏体组织，且晶粒尺寸控制在10μm-12μm，晶粒度达到8-9级。
本发明通过中碳和少量铬、镍、钼合金、铌+钒+钛+硼微合金化的成份设计，配合合理的控轧工艺、调质热处理工艺，开发出70mm厚度的Q960E超高强度钢，经过控轧、调质热处理后，其力学性能中屈服强度≥1000MPa，抗拉强度≥1050MPa，延伸率≥13％，-40℃，Akv冲击功值≥90J；由于国标对70mm厚度Q960E超高强度尚未有力学性能标准规定，本发明所获得的这些强度和塑韧性指标均达到国内某大型企业工程机械其力学性能的设计标准，由于强度高，厚度大，在实际工业生产过程中，对轧制设备和淬火机冷却能力要求较高，同时由于2800mm双机架轧机为粗轧机轧制力为5000吨、精轧机轧制力为4000吨的可逆四辊轧机组合，轧制力低，在生产过程中不能满足大压下轧制要求，易造成原始晶粒尺寸粗大，甚至出现混晶现象，从而严重影响强度和低温韧性相匹配的力学性能，通过中碳加淬透性较高的合金元素成分设计，从而弥补了满足常规轧制生产线因装备能力有限不能够生产高强度、高韧性、高焊接稳定性的Q960E高强钢的缺陷，同时采用高温结束轧制，使得高温态强度较低，使得低轧制力装备轧制能力得到发挥。
除上述实施例外，本发明还可以有其他实施方式。凡采用等同替换或等效变换形成的技术方案，均落在本发明要求的保护范围。

Claims (4)

  1. 一种大厚度Q960E超高强钢生产方法，其特征在于，该生产方法包括以下流程：铁水脱硫预处理-转炉冶炼-LF+RH精炼-连铸-铸坯堆垛缓冷-铸坯检验-铸坯判定-铸坯验收-铸坯加热-除鳞-轧制-空冷-探伤-抛丸-淬火-回火-矫直-切割、取样-喷印标识-检验-入库，其中：
    (1)该超高强钢的化学成分按重量百分比计包括：C：0.14-0.16％，Si：0.2-0.3％，Mn：1.1-1.2％，P≤0.008％，S≤0.0015％，Cr：0.4-0.6％，Cu≤0.1％，Ni：0.6-0.8％，Mo：0.1-0.3％，Nb：0.02-0.04％，Ti：0.01-0.02％，V：0.04-0.06％，B：≤0.0015％，Alt：0.025-0.04％，Ceq≤0.61％，余量为Fe及不可避免的杂质；
    该超高强钢的化学成分中碳当量Ceq(百分比)按以下公式计算：
    Ceq＝C+Mn/6+(Cr+Mo+V)/5+(Cu+Ni)/15≤0.61；
    (2)对铸坯加热，加热段温度为1240-1250℃，均热段温度控制在1220℃，出钢温度介于1180-1200℃，在炉时间为350-420min，二阶段开轧温度≤1050℃，成品厚度为70mm，待温铸坯厚度控制在≥133mm，二阶段终轧温度850-860℃，轧后空冷；
    (3)进行调质热处理，淬火温度控制在880-890℃，升温速率为1.5±0.1min/mm，在炉时间为125-135min，回火温度控制在590-600℃，升温速率为2.5±0.1min/mm，在炉时间为220-230min，缓冷至室温；
    (4)热轧态矫直时先在790-830℃下进行预矫。
  2. 根据权利要求1所述的大厚度Q960E超高强钢生产方法，其特征在于：该超高强钢的化学成分按重量百分比计包括：C：0.16％，Si：0.23％，Mn：1.19％，P≤0.005％，S≤0.0012％，Cu≤0.1％，Cr：0.45％，Ni：0.78％，Mo：0.2％，Nb：0.02％，Ti：0.013％，V：0.044％，B：0.0012％，Alt：0.033％，Ceq：0.55％。
  3. 根据权利要求1所述的大厚度Q960E超高强钢生产方法，其特征在于：在对铸坯进行轧制时采用二阶段轧制法，一阶段轧制形变率≥55％，二阶段轧制形变率≥45％。
  4. 根据权利要求1或2中任一权利要求所述的大厚度Q960E超高强钢生产方法，其特征在于：该超高强钢的力学性能达到以下水平：屈服强度≥1000MPa，抗拉强度≥1050MPa，延伸率≥13％，-40℃，Akv冲击功值≥90J；显微组织为回火索氏体组织，晶粒尺寸控制在10μm-12μm，晶粒度控制在8-9级。
PCT/CN2017/096431 2016-08-31 2017-08-08 一种大厚度q960e超高强钢生产方法 Ceased WO2018040859A1 (zh)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP17845161.3A EP3467136B1 (en) 2016-08-31 2017-08-08 Large-thickness q960e ultra-high strength steel production method

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201610766800.3 2016-08-31
CN201610766800.3A CN106244922B (zh) 2016-08-31 2016-08-31 一种大厚度q960e超高强钢生产方法

Publications (1)

Publication Number Publication Date
WO2018040859A1 true WO2018040859A1 (zh) 2018-03-08

Family

ID=58079421

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2017/096431 Ceased WO2018040859A1 (zh) 2016-08-31 2017-08-08 一种大厚度q960e超高强钢生产方法

Country Status (3)

Country Link
EP (1) EP3467136B1 (zh)
CN (1) CN106244922B (zh)
WO (1) WO2018040859A1 (zh)

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111456661A (zh) * 2020-04-30 2020-07-28 青岛宏新天机械有限公司 耐用钻杆浮阀
EP3859035A4 (en) * 2018-09-29 2021-08-18 Nanjing Iron & Steel Co., Ltd. ULTRA HIGH STRENGTH Q960E STEEL SLAB AND MANUFACTURING PROCESS
CN113637900A (zh) * 2021-07-27 2021-11-12 包头钢铁（集团）有限责任公司 一种1100MPa级重型机械吊臂用厚钢板的生产方法
CN115415311A (zh) * 2022-10-08 2022-12-02 包头钢铁（集团）有限责任公司 一种兼具超高强度和良好韧性的海洋工程结构用热轧h型钢的轧制方法
CN116060873A (zh) * 2021-11-03 2023-05-05 上海博众汽油机有限公司 一种凸轮轴罩盖总成制造方法
CN116351866A (zh) * 2023-02-01 2023-06-30 青岛特殊钢铁有限公司 一种合金化超高强高碳硬线钢高速线材轧制方法
CN117660841A (zh) * 2023-12-08 2024-03-08 新疆八一钢铁股份有限公司 一种q550级别工程机械用中厚钢板的生产方法

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106244922B (zh) * 2016-08-31 2018-12-11 南京钢铁股份有限公司 一种大厚度q960e超高强钢生产方法
CN108787751B (zh) * 2018-05-21 2020-02-07 南京钢铁股份有限公司 单机架炉卷轧机宽幅薄规格超级不锈钢板卷生产控制方法
CN110318008B (zh) * 2019-06-20 2022-01-14 江阴兴澄特种钢铁有限公司 一种大厚度抗层状撕裂屈服强度960MPa级高强钢板及其生产方法
CN113351645B (zh) * 2021-04-26 2026-04-07 山东久力新能源集团有限公司 一种板栅连铸连冲工艺
CN115216701B (zh) * 2022-04-25 2023-09-29 安阳钢铁股份有限公司 一种低压缩比抗层状撕裂q960高强钢及其制备方法
CN116497184A (zh) * 2023-04-24 2023-07-28 中国石油化工股份有限公司 一种低合金高强钢中厚板的热处理调控方法
CN117467828B (zh) * 2023-11-06 2026-02-13 南阳汉冶特钢有限公司 Q890f高强调质钢板及其生产方法
CN118639142B (zh) * 2024-08-15 2024-11-29 鞍钢股份有限公司 一种厚规格1000MPa级工程结构用钢的生产方法
CN119121071B (zh) * 2024-08-30 2026-04-14 新余钢铁股份有限公司 一种q960e钢板及其热处理方法和生产方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001164334A (ja) * 1999-12-03 2001-06-19 Nippon Steel Corp 耐食性と耐腐食疲労特性に優れた構造用鋼とその製造方法
CN101451221A (zh) * 2007-12-03 2009-06-10 舞阳钢铁有限责任公司 高强度钢板及其制备方法
CN102286695A (zh) * 2011-08-30 2011-12-21 南京钢铁股份有限公司 一种高塑性高韧性超高强度钢板及其生产方法
CN102560274A (zh) * 2011-12-12 2012-07-11 秦皇岛首秦金属材料有限公司 一种屈服强度1000MPa级调质超高强钢及其制造方法
CN106244922A (zh) * 2016-08-31 2016-12-21 南京钢铁股份有限公司 一种大厚度q960e超高强钢生产方法

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101451212B (zh) * 2007-12-03 2011-04-06 舞阳钢铁有限责任公司 一种高强度钢板及其制备方法
CN102286687A (zh) * 2011-08-30 2011-12-21 南京钢铁股份有限公司 炉卷轧机生产高强板q960的制造方法
CN103146997B (zh) * 2013-03-28 2015-08-26 宝山钢铁股份有限公司 一种低合金高韧性耐磨钢板及其制造方法
CN103589969B (zh) * 2013-11-12 2015-06-10 湖南华菱湘潭钢铁有限公司 一种调质高强度q890d特厚钢板的生产方法
CN104480406A (zh) * 2014-11-28 2015-04-01 宝山钢铁股份有限公司 一种低合金高强高韧钢板及其制造方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001164334A (ja) * 1999-12-03 2001-06-19 Nippon Steel Corp 耐食性と耐腐食疲労特性に優れた構造用鋼とその製造方法
CN101451221A (zh) * 2007-12-03 2009-06-10 舞阳钢铁有限责任公司 高强度钢板及其制备方法
CN102286695A (zh) * 2011-08-30 2011-12-21 南京钢铁股份有限公司 一种高塑性高韧性超高强度钢板及其生产方法
CN102560274A (zh) * 2011-12-12 2012-07-11 秦皇岛首秦金属材料有限公司 一种屈服强度1000MPa级调质超高强钢及其制造方法
CN106244922A (zh) * 2016-08-31 2016-12-21 南京钢铁股份有限公司 一种大厚度q960e超高强钢生产方法

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3859035A4 (en) * 2018-09-29 2021-08-18 Nanjing Iron & Steel Co., Ltd. ULTRA HIGH STRENGTH Q960E STEEL SLAB AND MANUFACTURING PROCESS
CN111456661A (zh) * 2020-04-30 2020-07-28 青岛宏新天机械有限公司 耐用钻杆浮阀
CN113637900A (zh) * 2021-07-27 2021-11-12 包头钢铁（集团）有限责任公司 一种1100MPa级重型机械吊臂用厚钢板的生产方法
CN116060873A (zh) * 2021-11-03 2023-05-05 上海博众汽油机有限公司 一种凸轮轴罩盖总成制造方法
CN115415311A (zh) * 2022-10-08 2022-12-02 包头钢铁（集团）有限责任公司 一种兼具超高强度和良好韧性的海洋工程结构用热轧h型钢的轧制方法
CN116351866A (zh) * 2023-02-01 2023-06-30 青岛特殊钢铁有限公司 一种合金化超高强高碳硬线钢高速线材轧制方法
CN117660841A (zh) * 2023-12-08 2024-03-08 新疆八一钢铁股份有限公司 一种q550级别工程机械用中厚钢板的生产方法

Also Published As

Publication number Publication date
EP3467136A1 (en) 2019-04-10
CN106244922B (zh) 2018-12-11
EP3467136B1 (en) 2020-07-29
EP3467136A4 (en) 2019-06-05
CN106244922A (zh) 2016-12-21

Similar Documents

Publication Publication Date Title
AU2022392619B2 (en) High-strength steel with good weather resistance and manufacturing method therefor
CN106244922A (zh) 一种大厚度q960e超高强钢生产方法
WO2020098306A1 (zh) 一种大厚度nm500耐磨钢及生产方法
CN105506494B (zh) 一种屈服强度800MPa级高韧性热轧高强钢及其制造方法
WO2020087961A1 (zh) 一种80mm大厚度高韧性低合金耐磨钢板及其制造方法
CN113549828B (zh) 一种低屈强比超高强海工钢及其制造方法
WO2022052335A1 (zh) 一种大厚度低碳当量高韧性耐磨钢板及其制造方法
EP3859035B1 (en) Ultrahigh strength steel q960e thick plate and manufacturing method
CN110846577A (zh) 690MPa级高强度低屈强比中锰钢中厚钢及制造方法
CN106282774B (zh) 一种高横纵向冲击比值大厚度q690e高强钢生产方法
WO2019119725A1 (zh) 一种布氏硬度大于550hb的高级别低合金耐磨钢板及制造方法
CN114134388B (zh) 一种抗拉强度1300MPa级薄规格超高强钢板及其制造方法
CN113930692B (zh) 一种先进压水堆核电站用高均质化超厚钢板及其制造方法
CN104278216A (zh) 一种厚度大于60mm屈服强度690MPa级钢板及其制备方法
WO2019222988A1 (zh) 一种屈服强度1100MPa级超细晶高强钢板及其制造方法
CN110527915B (zh) 一种460MPa级热轧H型钢及其生产方法
CN102234743A (zh) 一种低碳马氏体钢板及其制造方法
CN102618793A (zh) 一种屈服强度 960MPa 级钢板及其制造方法
CN110358970A (zh) 屈服强度1100MPa级的焊接结构贝氏体高强钢及其制备方法
CN110358971A (zh) 一种屈服强度1300MPa级的低碳超高强钢及其制备方法
CN106086657A (zh) 一种屈服强度大于1300MPa的超高强度结构钢板及其制备方法
CN108728728A (zh) 一种具有极低屈强比的高锰钢及其制造方法
CN114134387B (zh) 一种抗拉强度1300MPa级厚规格超高强钢板及其制造方法
CN116445818A (zh) 一种屈服强度600MPa级厚规格高韧性热轧带钢及其生产方法
CN104451380B (zh) 一种铌钼复合微合金化高强度贝氏体钢及其制备方法

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: 17845161

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 2017845161

Country of ref document: EP

Effective date: 20190102

NENP Non-entry into the national phase

Ref country code: DE