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WO2014114159A1 - 一种具有低屈服比的超高强韧钢板及其制造方法 - Google Patents

一种具有低屈服比的超高强韧钢板及其制造方法 Download PDF

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Publication number
WO2014114159A1
WO2014114159A1 PCT/CN2013/090270 CN2013090270W WO2014114159A1 WO 2014114159 A1 WO2014114159 A1 WO 2014114159A1 CN 2013090270 W CN2013090270 W CN 2013090270W WO 2014114159 A1 WO2014114159 A1 WO 2014114159A1
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Prior art keywords
steel sheet
yield ratio
strength
low yield
toughness
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PCT/CN2013/090270
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English (en)
French (fr)
Inventor
赵四新
姜洪生
姚连登
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Application filed by Baoshan Iron and Steel Co Ltd filed Critical Baoshan Iron and Steel Co Ltd
Priority to EP13872503.1A priority Critical patent/EP2949775B1/en
Priority to US14/761,488 priority patent/US10801090B2/en
Priority to JP2015552985A priority patent/JP6792946B2/ja
Priority to AU2013375524A priority patent/AU2013375524B2/en
Priority to KR1020157022771A priority patent/KR102357132B1/ko
Priority to RU2015136606A priority patent/RU2682074C2/ru
Publication of WO2014114159A1 publication Critical patent/WO2014114159A1/zh
Priority to ZA2015/05173A priority patent/ZA201505173B/en
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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
    • 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
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • 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 present invention relates to a steel sheet and a method of manufacturing the same, and, in particular, to an ultra high strength tough steel sheet and a method of manufacturing the same. Background technique
  • High-strength and tough steel plates are widely used in mechanical structures, building bridges and engineering structures.
  • the mechanical properties of the steel sheet include yield strength, tensile strength, elongation and low temperature impact work.
  • the yield strength is usually used as a reference and a certain safety factor is given.
  • the ratio of yield strength to tensile strength is called the yield ratio.
  • the yield ratio is mainly expressed as the safety factor of the steel sheet from the start of yield to the complete failure process when the joint member is subjected to the ultimate stress exceeding the yield strength.
  • steel plates with low yield strength are required.
  • steel structures such as high-rise buildings, water-voltage steel pipes, and coal mine hydraulic supports, etc., when encountering natural disasters such as earthquakes, landslides, and landslides, steel plates with low yield ratios can absorb more energy and delay structural damage. Time or avoid structural damage, prevent secondary disasters, and reduce the threat of human life.
  • the yield strength is expressed by the upper yield strength and the lower yield strength.
  • the yield strength is 0.2% plastic deformation strength Rp. 2 indicates.
  • the upper yield strength of the low carbon steel plate is due to the formation of the Cotower gas mass near the dislocations, which prevents the dislocation from starting to move. After the dislocation is started, the effect of the Cotower gas mass disappears, and the force required to be applied on the steel plate is reduced. , then form a lower yield. If the dislocation starts, including the interaction between the Cotower air mass and the dislocation loop and the dislocation wall, the yielding phenomenon is not obvious.
  • the yield strength represents the stress that widens the slip zone over a large scale range of dislocation proliferation and motion.
  • WO2007/051080 published on May 3, 2007, entitled "High-strength dual-phase steel with low yield ratio, high toughness and excellent weldability", which provides a soft Dual-phase high-strength steel with hard-phase composite microstructure, the composite microstructure provides low yield ratio, high strain capacity, excellent weldability and high toughness, and its chemical composition includes C: 0.03-0.12%, Ni: 0.1-1.0%, Nb: 0.005-0.05% Ti: 0.005-0.03% Mo: 0.1-0.6%, Mn: 0.5-2.5%, Cu: ⁇ 1.0%, Cr: ⁇ 1.0%, Ca: ⁇ 0.01% Also includes optional elements V: ⁇ 0.1%, B: ⁇ 0.002%, Mg: ⁇ 0.006% N: ⁇ 0.010% Si: ⁇ 0.5%, Cu: ⁇ 1.0%, Al: ⁇ 0.06% P: ⁇ 0.015% , S: ⁇ 0.004%.
  • the duplex steel comprises from about 10% by volume to about 60% by volume of the first phase or component consisting essentially of fine grained ferrite.
  • the first phase has ferrite having an average grain size of about 5 microns or less.
  • the duplex steel further comprises from about 40% by volume to about 90% by volume of the second phase or component comprising fine-grained martensite, fine-grained lower bainite, fine grains Granular bainite, fine grain degraded upper bainite or any mixture thereof.
  • the Chinese patent document entitled "800MPA grade high toughness low yield ratio thick steel plate and its manufacturing method" is disclosed in CN101045977A, published on October 3, 2007, and discloses a high strength and low yield ratio thick steel plate and The manufacturing method has a chemical composition including C: 0.05-0.09%, Si: 0.35-0.45%, Mm 1.5-1.90%, Ni: 0.30-0.70%, Nb: 0.04-0.08%, Al: 0.02-0.04%, Ti: 0.01-0.04%, the steel sheet has a low yield ratio and a tensile strength greater than 800 MPa.
  • the publication number is CN1924065A, and the publication date is March 7, 2007.
  • the Chinese patent document entitled "700MPA grade high toughness low yield ratio thick steel plate and its manufacturing method” also discloses a steel plate whose chemical composition mass percentage is: C 0.03 ⁇ 0.06, Si 0.35 ⁇ 0.55, Mn 1.00 ⁇ 1.55, Ni 0.50 ⁇ 0.70, Nb 0.02-0.06, A10.02 ⁇ 0.04, Ti 0.01-0.04, V 0.04-0.07, Cu 0.50 ⁇ 0.70, balance Fe And inevitable impurities.
  • the manufacturing method comprises the following: A. smelting and casting into a billet; B. heating to 1180 ⁇ 1220 ° C ; C.
  • rolling temperature is 1050 ⁇ 1100 ° C
  • the thickness of the rolled piece reaches 2 to 3 times the thickness of the finished steel sheet
  • the finishing temperature is 820 ⁇ 880 °C
  • D After the end of rolling, air cooling for 60 to 120 seconds, then accelerated cooling, cooling to 460 ⁇ 600 °C at a rate of 10 ⁇ 20 ° C / sec, and the steel plate is air-cooled after water.
  • the object of the present invention is to provide an ultra-high strength and toughness steel plate having a low yield ratio and a method for manufacturing the same, which has a high tensile strength level and a low yield ratio, thereby being able to satisfy mechanical structures, building bridges and engineering structures. Two-way requirements for low flexural strength and strength reduction of steel plates.
  • the present invention provides an ultra-high strength toughness steel sheet having a low yield ratio, the chemical element mass percentage of which is:
  • the balance is Fe and other unavoidable impurities.
  • C can enlarge the austenite phase zone of the steel plate, and control the content of C element in steel to obtain steel plates with different microstructure and mechanical properties.
  • the amount of C element added to the steel is different, and the type of phase change of the steel sheet will also be different. If the amount of C element and alloying element is low, ferrite and pearlite will occur. Equal diffusion type phase change. If the content of C element and alloying element is high, martensite transformation occurs.
  • the C atom When the martensite transforms, the C atom is solid-dissolved in the crystal lattice of the Fe atom, causing the c-axis of the crystal to be elongated, and a change of the Fee (face-centered cubic lattice)-Hep (close-packed hexagonal lattice) occurs.
  • the C atom greatly increases the strength of the steel sheet by changing the crystal structure.
  • the austenite stability increases with the increase of C atoms, and the steel plate can obtain martensite and retained austenite structure after rapid cooling, which reduces the yield ratio of the steel plate.
  • the C element content is too high, the plasticity and toughness of the steel sheet will be lowered.
  • the C content in the present invention is controlled to be 0.18 to 0.34%.
  • Si When Si is added to steel, it can increase the strength of the steel sheet by solid solution strengthening of the replacement atom. However, if the Si content is too high, the tendency of hot cracking during welding of the steel sheet is increased. Therefore, the Si content in the present invention is designed to be 0.10 to 0.40%.
  • Mm C and Mn elements are usually used in combination to obtain a steel sheet having good mechanical properties.
  • the Mn element is added to the steel sheet of the present invention, and the toughness of the steel sheet is improved by solid solution strengthening. Since the C content added to the steel sheet of the present invention is relatively high, in order to ensure the carbon equivalent and the weldability of the steel sheet, the Mn added in the present invention is 0.50-1.40%, which is used to adjust the yield ratio and strength of the steel sheet. Shopability.
  • Cr can improve the hardenability of the steel sheet and form a martensite structure when the steel sheet is cooled. If the Cr content is too high, the carbon equivalent of the steel sheet is increased, and the welding property of the steel sheet is deteriorated. Therefore, the Cr content in the present invention is controlled to be 0.20 to 0.70%.
  • Mo can effectively suppress the diffusive phase transition, and the steel sheet forms a low-temperature phase transition structure with high strength upon cooling.
  • Mo content is low, the effect of suppressing the diffusion phase transition of the steel sheet is not sufficiently exerted, so that the steel sheet cannot obtain more martensite structure upon cooling, thereby lowering the strength of the steel sheet.
  • Mo content is too high, the carbon equivalent is increased to deteriorate the weldability of the steel sheet.
  • the present invention controls the Mo content to be 0.30 to 0.90%.
  • Nb added to steel inhibits austenite grain boundary motion and causes the steel plate to recrystallize at higher temperatures.
  • Nb dissolved in austenite will form NbC particles at dislocations and grain boundaries due to strain-induced precipitation during rolling, inhibiting grain boundary motion and increasing steel plate strength.
  • toughness When the Nb content is too high, coarse NbC may be formed, which deteriorates the low-temperature impact properties of the steel sheet. Therefore, Nb of not more than 0.06% is added to the present invention to control the mechanical properties of the steel sheet.
  • Ni forms a solid solution with Fe in steel and improves the toughness of the steel sheet by reducing the stacking fault of the crystal lattice.
  • Organization reducing the yield ratio of the steel plate. If the Ni content is too high, on the one hand, the slab will form an oxide film which is difficult to remove when heated, which will affect the surface quality of the steel sheet; on the other hand, the production cost of the steel sheet will increase. Therefore, the Ni content in the present invention should be set between 0.50 and 2.40%.
  • V is added to steel as an alloying element, which enhances the toughness of the steel sheet by solid solution strengthening and precipitation strengthening effect of MC type carbide.
  • the MC type carbide will coarsen during the heat treatment, thereby affecting the low temperature toughness of the steel sheet. Therefore, in the present invention, not more than 0.06% of the V element is added to ensure the mechanical properties of the steel sheet.
  • Ti forms nitrides in the molten steel, and then forms oxides and carbides at a lower temperature range.
  • too high a Ti content leads to the formation of coarse TiN in the molten steel.
  • the TiN particles are cuboidal, and the corners of the particles are liable to cause stress concentration, which is a source of crack formation.
  • the Ti content in the present invention is controlled to be 0.002-0.04%.
  • Ah A1 is added to the steel to refine the grains by forming oxides and nitrides.
  • the content of A1 to be added in the present invention is 0.01-0.08%.
  • B B enriches the grain boundary in the steel plate to reduce the grain boundary energy, so that the steel plate forms a low temperature phase change structure during cooling.
  • B is added to the steel and combined with the contents of C and alloying elements, a martensite structure having high strength can be formed, and a steel sheet having good strength properties can be obtained.
  • the B content is too high, it will be enriched at the martensite grain boundary, which will lower the low-temperature impact properties and fatigue properties of the steel sheet. Therefore, in the present invention, the amount of B added is 0.0006-0.0020%.
  • N forms a nitride with Ti, Nb and V in the steel.
  • the undissolved nitride hinders the grain boundary motion of the austenite and achieves the effect of refining the austenite grains.
  • the content of N element is too high, N and Ti will form coarse TiN, which will deteriorate the mechanical properties of the steel sheet.
  • the N atom is also enriched in the defects in the steel, forming pores and porosity, and further deteriorates the mechanical properties of the steel sheet. Therefore, the N content in the present invention is controlled to be not more than 0.0060%.
  • 0 0 forms oxides with Al, Si and Ti in steel.
  • the oxide of A1 acts to inhibit the growth of austenite and refine the grains.
  • steel sheets having a large content of 0 tend to have hot cracks during welding. Therefore, the content of 0 in the present invention should be controlled to be not more than 0.0040%.
  • Ca is added to the steel to form CaS with the S element, which acts as a spheroidized sulfide and improves the low-temperature impact edge of the steel sheet.
  • the Ca content in the present invention is controlled to be not more than 0.0045%.
  • the present invention also provides a method for manufacturing the ultra-high strength toughness steel sheet having a low yield ratio, which comprises smelting, casting, heating, rolling, cooling, quenching and tempering, and obtaining the microstructure of the steel sheet for refinement.
  • the slab is heated to 1080 ⁇ 1250 ° C in a heating step; the quenching temperature of the quenching step is 860 to 940 ° C; the tempering temperature of the tempering step is 150 ⁇ 350. C.
  • the method for manufacturing an ultra-high-strength and toughness steel plate having a low yield ratio controls the temperature in a process step such as heating, quenching and tempering, and is combined with elemental composition design to make a chemical element There is a correlation between the composition design and the manufacturing process.
  • the temperature is controlled between 1080 and 1250 ° C to achieve austenitization.
  • the heating process is mainly carbonitride dissolution and austenite grain growth.
  • the carbide or carbonitride formed by the carbide forming elements such as Nb, V, Ti, Cr and Mo is partially dissolved in the steel, and the alloying element atoms are solid-dissolved in the austenite by diffusion.
  • the temperature in the furnace is controlled to 150-350 Torr for tempering.
  • the tempering of steel plates can be generally divided into four stages: 1) When tempering at 100 °C, 6 carbides are precipitated in the martensite of the square lattice, the squareness of martensite is lowered, and the steel containing less than 0.3% carbon No ⁇ carbide is formed, and fine carbides are formed only in the vicinity of defects such as dislocations; 2) Residual austenite is transformed into lower bainite and martensite at around 235 ° C; 3) at 300 ° C When left and right, ⁇ carbide turns into cementite; 4) At a temperature of 400 ⁇ 450 °C, the diffusion coefficient of carbon and iron increases, and the cementite particles coarsen.
  • the invention adopts tempering at a temperature of about 150-350 ° C, and forms fine carbide precipitation on the edge of the refined martensite lath, and the dislocation quenching occurs in the place where the dislocation density is high in the steel sheet, and the reduction is performed.
  • the internal stress of the steel plate increases the plasticity of the steel plate.
  • the control of the tempering temperature allows some of the retained austenite to remain in the steel sheet, which lowers the final yield ratio of the steel sheet and at the same time gives the steel sheet a higher tensile strength.
  • the rolled steel sheet is air-cooled or water-cooled.
  • the quenched steel sheet is water-cooled.
  • the ultra-high-strength steel plate with low yield ratio described in the present invention has the advantages of: 1) low carbon equivalent CEV due to the use of reasonable component design and optimized manufacturing process. Less alloying elements; 2) Yield ratio less than 0.85; 3) Tensile strength greater than 1500MPa; 3) Yield strength greater than 1200 MPa; 4) Elongation greater than 10%; 5) Excellent mechanical properties.
  • the method for manufacturing an ultra-high-strength and toughness steel sheet having a low yield ratio according to the present invention can obtain fine martensite structure and retained austenite by optimizing temperature control without increasing any process difficulty and suddenness.
  • the combination of soft and hard microstructures to obtain ultra-high strength and toughness steel sheets with low mechanical yield and excellent yield ratio is relatively loose, and can be widely applied to stable production in the field of engineering component manufacturing with high structural safety requirements.
  • Fig. 1 shows the microstructure of an ultrahigh-strength steel sheet having a low yield ratio according to Example 4 under an optical microscope. detailed description
  • the ultra high strength and toughness steel sheet having a low yield ratio according to the present invention is produced by the following steps:
  • quenching temperature is 860 ⁇ 940 °C, water quenching after quenching;
  • Tempering The tempering temperature is 150 ⁇ 350 °C, and it is air-cooled after tempering.
  • Fig. 1 shows the microstructure of an ultrahigh-strength steel sheet having a low yield ratio in Example 4 of the present invention under an optical microscope.
  • CEV carbon equivalent
  • CEV C + Mn / 6 + (Cr + Mo + V) /5 + (Ni + Cu) / 15
  • Table 2 shows the specific temperature parameters of Examples 1-6. Among them, the specific temperature parameters of the respective examples in Table 2 correspond to the corresponding Examples 1-6 in Table 1.
  • the ultra-high strength and toughness steel sheet with low yield ratio according to the present invention has a yield ratio of less than 0.85, a tensile strength of more than 1500 MPa, a yield strength of more than 1200 MPa, an elongation of more than 10%, and an impact energy Akv ( -20 ° C ) More than 27 J, the steel sheet with the above mechanical properties has ultra high strength and good toughness and strong plasticity.

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Abstract

一种具有低屈服比的超高强韧钢板，其化学元素质量百分含量为：C:0.18-0.34%，Si:0.10—0.40%，Mn:0.50-1.40%，Cr:0.20—0.70%，Mo:0.30—0.90%，Nb:0—0.06%，Ni:0.50-2.40%，V:0—0.06%，Ti:0.002-0.04%，Al:0.01-0.08%，B:0.0006-0.0020%，N≤0.0060%，O≤0.0040%，Ca:0-0.0045%，余量为Fe和其他不可避免的杂质。还提供了该钢板的制造方法包括：加热温度为1080∼1250°C；淬火温度为860〜940°C；回火温度为150〜350°C。

Description

一种具有低屈服比的超高强韧钢板及其制造方法 技术领域
本发明涉及一种钢板及其制造方法， 尤其涉及一种超高强韧钢板及其制 造方法。 背景技术
高强韧钢板广泛应用于机械结构、 建筑桥梁和工程结构。 钢板的力学性 能包括屈服强度、 抗拉强度、 延伸率和低温冲击功等。 在选用机械结构和建 筑桥梁等结构件用钢板时， 通常以屈服强度为基准并给予一定的安全系数。 屈服强度和抗拉强度之比称为屈强比， 在工程应用中屈强比主要体现为当结 构件在受到超过屈服强度的极限应力时， 钢板从屈服开始到完全失效过程的 安全性系数。如果钢板的屈强比较低，则当钢板受到高于屈服强度的应力时， 钢板在应力达到抗拉强度导致材料断裂或结构失稳之前， 具有较宽的安全范 围。 如果钢板的屈强比较高， 则当钢板在达到屈服强度之后， 钢板会迅速达 到抗拉强度而发生断裂。 因此， 对于结构件安全性能要求较高的情况下， 需 要采用具有低屈服强度的钢板。 例如， 高层建筑的钢结构、 水电压力钢管和 煤矿液压支架等结构件， 这样遇到类似于地震、 山体滑坡和塌方等自然灾害 时， 低屈强比的钢板可吸收更多能量， 延缓结构破坏时间或避免结构彻底破 坏， 防止次生灾害的发生， 降低人员生命的威胁。
钢板的屈服现象明显时， 屈服强度采用上屈服强度、 下屈服强度表示； 钢板的屈服现象不明显时， 屈服强度采用 0.2%塑性变形的强度 Rp。.2表示。 低碳钢板的上屈服强度是由于间隙原子在位错附近形成柯垂尔气团， 阻碍位 错开始运动； 在位错开动之后， 柯垂尔气团的作用消失， 需要在钢板上施加 的力减小， 则形成下屈服。 如果位错开动包括了柯垂尔气团及位错环和位错 墙的交互作用等， 则屈服现象不明显。 屈服强度代表着大尺度范围位错增殖 和运动而使滑移带变宽的应力。 部分文献认为屈服强度是可运动的刃型位错 全部滑出晶体对应的应力， 而抗拉强度是材料在拉伸过程中可抵抗的最大应 力， 通常伴随着微裂紋的形核长大和扩展。 具有低屈强比钢板的设计和制造， 通常采用软相和硬相结合的微观组织 来获得具有较低屈服强度和较高的抗拉强度。 例如：
公布号为 WO2007/051080, 公开日为 2007年 5月 3日， 名称为 "具有低屈 服比、 高韧性和优异可焊性的高强度双相钢" 的专利文献， 其提供了一种具 有软和硬相复合显微组织的双相高强度钢， 其复合显微组织可提供低的屈服 比、 高的应变能力、 优异可焊性及高韧性， 其化学成分包括 C: 0.03-0.12%, Ni: 0.1-1.0%、 Nb: 0.005-0.05% Ti: 0.005-0.03% Mo: 0.1-0.6%、 Mn: 0.5-2.5%、 Cu: ≤1.0%、 Cr: ≤1.0%、 Ca: <0.01%, 还包括可选元素 V: ≤0.1%、 B: <0.002%, Mg: <0.006% N: <0.010% Si:≤0.5%、 Cu:≤1.0%、 Al: <0.06% P: ≤0.015%、 S: ≤0.004%。 该双相钢包括约 10体积％至约 60体积％的主要由 细晶粒铁素体构成的第一相或组分。该第一相具有平均晶粒尺寸约 5微米或更 小的铁素体。 该双相钢还包括约 40体积％至约 90体积％的第二相或组分,所述 第二相或组分包括细晶粒马氏体、 细晶粒下贝氏体、 细晶粒粒状贝氏体、 细 晶粒退化上贝氏体或它们的任何混合物。
公开号为 CN101045977A, 公开日为 2007年 10月 3日， 名称为 " 800MPA 级高韧性低屈服比厚钢板及其制造方法" 的中国专利文献， 公开了一种高强 韧低屈服比厚钢板及其制造方法， 其化学成分包括 C : 0.05-0.09%、 Si: 0.35-0.45%、 Mm 1.5-1.90%、 Ni: 0.30-0.70%、 Nb: 0.04-0.08%、 Al: 0.02-0.04%, Ti: 0.01-0.04%, 该钢板具有低屈强比且抗拉强度大于 800MPa。
公开号为 CN1924065A, 公开日为 2007年 3月 7日， 名称为 "700MPA级高 韧性低屈服比厚钢板及其制造方法" 的中国专利文献也公开了一种钢板， 其 化学成分质量百分比为: C 0.03〜0.06， Si 0.35〜0.55，Mn 1.00〜1.55， Ni 0.50〜 0.70, Nb 0.02—0.06, A10.02~0.04, Ti 0.01—0.04, V 0.04—0.07, Cu 0.50~ 0.70, 余量为 Fe和不可避免杂质。 其制造方法包括： A.冶炼并浇铸成坯； B. 加热至 1180〜1220°C ; C.轧制， 开轧温度为 1050〜1100°C， 轧件厚度到达成 品钢板厚度的 2〜3倍时， 在辊道上待温至 920〜960°C， 随后进行第二阶段轧 制,道次变形量 5〜15MM， 道次变形率 10〜25%； 终轧温度 820〜880°C； D. 轧制结束，空冷 60〜120秒钟，然后加速冷却，以 10〜20°C/秒速度冷却至 460〜 600 °C , 钢板出水后空冷。
由此可见， 随着机械钢结构向着大型化及复杂化发展， 为了达到钢结构 增强减重及节能降耗的目的，需要钢板的强度不断增加并具有较低的屈服比。 发明内容
本发明的目的在于提供一种具有低屈服比的超高强韧钢板及其制造方 法， 该钢板抗拉强度级别高， 且具备较低屈服比， 从而能够满足机械结构、 建筑桥梁和工程结构等领域对于钢板低屈强韧及增强减重的双向要求。
为实现上述发明目的，本发明提供了一种具有低屈服比的超高强韧钢板， 其化学元素质量百分含量为：
C: 0.18-0.34%,
Si: 0.10-0.40%,
Mm 0.50-1.40%,
Cr: 0.20-0.70%,
Mo: 0.30-0.90%,
Nb: 0-0.06%,
Ni: 0.50-2.40%,
V： 0-0.06%,
Ti: 0.002-0.04%,
Ah 0.01-0.08%,
B: 0.0006-0.0020% ，
N<0.0060%,
O<0.0040%,
Ca: 0-0.0045%,
余量为 Fe和其他不可避免的杂质。
进一歩地， 本发明所述的具有低屈服比的超高强韧钢板的碳当量满足 CEV<0.75%, 其中碳当量 CEV = C+Mn/6+ (Cr+Mo+V) 15+ (Ni+Cu) /15。
在成分设计方面， 本发明所述的具有低屈服比的超高强韧钢板中的各化 学元素的设计原理为：
C: C能扩大钢板的奥氏体相区， 控制 C元素在钢中的含量可获得不同 微观组织和力学性能的钢板。 C元素在钢中的添加量不同， 钢板发生相变的 类型也会随之不同。 如 C元素和合金元素合量较低， 则发生铁素体、 珠光体 等扩散型相变。 如 C元素和合金元素含量较高， 则发生马氏体转变。 当马氏 体转变时， C原子固溶在 Fe原子的晶格中，使晶体的 c轴延长，发生 Fee (面 心立方晶格） -Hep (密排六方晶格） 的转变。 C原子通过改变晶体结构， 大 幅度地提高了钢板的强度。 奥氏体稳定性随着 C原子增加而提高， 钢板在快 速冷却后可获得马氏体和残余奥氏体组织， 降低钢板的屈强比。 但是， C元 素含量过高， 则会使得钢板的塑性和韧性下降。 综合考虑 C元素对于钢板对 强韧性和强塑性的影响， 本发明中的 C含量控制为 0.18-0.34%。
Si:当 Si添加到钢中时，其可以通过置换原子固溶强化提高钢板的强度， 但 Si含量过高， 会增加钢板焊接时的热裂紋倾向。 所以， 本发明中的 Si含 量设计为 0.10-0.40%。
Mm C和 Mn元素通常联合应用以获得具有良好力学性能的钢板。 Mn 元素添加到本发明的钢板中， 通过固溶强化来提高钢板的强韧性。 由于本发 明的钢板中所添加的 C含量相对较高， 为了保证钢板的碳当量和焊接性能， 故本发明中所加入的 Mn为 0.50-1.40%,用以调节该钢板的屈强比和强铺性。
Cr: Cr可以提高钢板的淬透性， 使钢板在冷却时形成马氏体组织。 可 Cr含量过高会增加钢板的碳当量， 恶化钢板焊接性能。 因此， 本发明中的 Cr含量控制为 0.20-0.70%。
Mo: Mo可以有效抑制扩散性相变， 使钢板在冷却时形成强度较高的低 温相变组织。 Mo含量较低时， 对钢板扩散性相变抑制的效果未充分发挥， 使得钢板在冷却时不能得到更多的马氏体组织， 从而降低钢板的强度。 Mo 含量过高时， 导致碳当量增加， 恶化钢板的焊接性能。 因而， 本发明将 Mo 含量控制为 0.30-0.90%。
Nb: 添加到钢中的 Nb可抑制奥氏体晶界运动， 使钢板在较高温度下发 生再结晶。 在较高温度奥氏体化时， 固溶到奥氏体中的 Nb会在轧制时由于 应变诱导析出效应， 在位错和晶界处形成 NbC颗粒， 抑制晶界运动， 提高钢 板的强韧性。 当 Nb含量过高时， 则可能形成粗大的 NbC, 恶化钢板的低温 冲击性能。 因此， 本发明中加入不大于 0.06%的 Nb以控制钢板的力学性能。
Ni: Ni在钢中能与 Fe形成固溶体， 通过降低晶格的层错而提高钢板韧 性。 为了获得具有良好低温韧性的高强度钢板， 需在钢板中加入一定的 Ni， Ni会增加奥氏体的稳定性，使得钢板在冷却过程中形成马氏体和残余奥氏体 组织， 降低钢板的屈强比。如果 Ni含量过高， 一方面会使板坯在加热时形成 难以去除的氧化膜， 影响钢板表面质量； 另一方面会增加钢板的生产成本。 因此， 本发明中的 Ni含量应设定在 0.50-2.40%范围之间。
V： V作为合金元素加入钢中，其通过固溶强化和 MC型碳化物的析出强 化效果来提高钢板的强韧性。 但 V元素含量过高时， MC型碳化物会在热处 理过程中发生粗化， 从而影响钢板的低温韧性。 因此， 在本发明中加入不大 于 0.06%的 V元素用来保证钢板的力学性能。
Ti: Ti在钢液中形成氮化物， 随后在较低的温度范围形成氧化物和碳化 物。 不过， Ti含量过高会导致钢液中形成粗大的 TiN。 TiN颗粒为立方形， 颗粒的角部容易导致应力集中， 即为裂紋的形成源。综合考虑 Ti在钢中的作 用， 本发明中的 Ti含量控制为 0.002-0.04%。
Ah A1加入钢中， 通过形成氧化物和氮化物细化晶粒。 为了达到细化晶 粒及提高钢板的韧性并保证其焊接性能的目的，在本发明中需要加入 A1的含 量为 0.01-0.08%
B: B 在钢板中的晶界富集从而降低晶界能量， 使钢板在冷却过程中形 成低温相变组织。 B加入钢中， 并结合 C和合金元素含量， 可以形成具有高 强度的马氏体组织， 进而获得具备良好的强度性能的钢板。 但是， B含量过 高， 则会在马氏体晶界富集， 降低钢板的低温冲击性能和疲劳性能。 因此， 本发明中 B的加入量为 0.0006-0.0020%。
N: N可与钢中的 Ti、 Nb和 V形成氮化物。钢板在奥氏体化过程中， 未 溶解的氮化物会阻碍奥氏体的晶界运动， 实现细化奥氏体晶粒的效果。 如 N 元素含量过高， 则 N与 Ti会形成粗大的 TiN， 恶化钢板的力学性能。 同时， N原子还会在钢中的缺陷处富集， 形成气孔和疏松， 进一歩恶化钢板的力学 性能。 因此， 在本发明中的 N含量控制为不大于 0.0060%。
0： 0在钢中与 Al、 Si和 Ti形成氧化物。 钢板在加热奥氏体化过程中， A1的氧化物会起到抑制奥氏体长大， 细化晶粒的作用。 不过， 0含量较多的 钢板在焊接时具有热裂紋倾向。 因而， 本发明中的 0 含量应控制为不大于 0.0040%。
Ca: Ca加入钢中， 与 S元素形成 CaS， 起到球化硫化物的作用， 提高 钢板的低温冲击刃性。 本发明中的 Ca含量需控制为不大于 0.0045%。 相应地， 本发明还提供了该具有低屈服比的超高强韧钢板的制造方法， 其包括冶炼、 浇铸、 加热、 轧制、 冷却、 淬火和回火歩骤， 获得钢板的微观 组织为细化马氏体和残余奥氏体， 其中： 加热歩骤中将板坯加热至 1080〜 1250°C ; 淬火歩骤的淬火温度为 860〜940°C ; 回火歩骤的回火温度为 150〜 350。C。
在制造工艺方面，本发明所述具有低屈服比的超高强韧钢板的制造方法， 对加热、 淬火及回火等工艺歩骤中的温度进行相应控制， 并结合元素成分设 计，使得化学元素的成分设计和制造工艺之间产生关联影响。在加热过程中， 将温度控制在 1080-1250°C之间实现奥氏体化。 在加热过程主要是碳氮化物 溶解和奥氏体晶粒长大过程。 如 Nb、 V、 Ti、 Cr和 Mo等碳化物形成元素的 所形成的碳化物或碳氮化物部分溶解于钢中， 合金元素原子通过扩散而固溶 在奥氏体中。 在轧制过程中， 部分碳氮化物通过应变诱导析出效应在缺陷处 形核长大， 细化最终晶粒， 从而提高钢板力学性能。 在淬火过程中， 温度设 定在 860-940°C之间， 因为在此温度区间加热保温， 可有效控制碳化物形成 元素 （如 Nb、 V、 Ti、 Cr和 Mo等元素） 的碳氮化物的部分溶解及奥氏体晶 粒长大的尺寸。 在回火过程中， 将加热炉内温度控制为 150-350Ό进行回火 处理。 钢板的回火一般可分为四个阶段： 1 )在 100°C回火时， 正方点阵的马 氏体中析出 6碳化物， 马氏体的正方度降低， 含碳 0.3%以下的钢中不形成 ε 碳化物， 仅在位错等缺陷附近形成细微的碳化物； 2)在 235°C附近时， 残余 奥氏体转变为下贝氏体和马氏体； 3 ) 在 300°C左右时， ε碳化物转变为渗碳 体； 4) 在 400〜450°C温度时， 碳和铁的扩散系数升高， 渗碳体颗粒粗化。 本发明采用在温度 150-350°C左右进行回火， 在细化的马氏体板条边缘形成 细化的碳化物析出， 钢板中位错密度很高的地方发生异号位错湮灭， 降低钢 板的内应力， 提高钢板的塑性。 此时， 回火温度的控制可使部分残余奥氏体 保留在钢板中， 降低了钢板最终屈服比， 同时使钢板具有较高的抗拉强度。
在上述具有低屈服比的超高强韧钢板的制造方法中， 轧制后的钢板空冷 或水冷。
进一歩地， 在上述具有低屈服比的超高强韧钢板的制造方法中， 淬火后 的钢板水冷。
进一歩地， 在上述具有低屈服比的超高强韧钢板的制造方法中， 回火后 的钢板空冷。
与现有技术方案相比， 由于采用了合理的成分设计和优化的制造工序使 得本发明所述的具有低屈服比的超高强韧钢板， 所具备的优点为： 1 )碳当量 CEV较低，合金元素较少； 2)屈强比小于 0.85; 3 )抗拉强度大于 1500MPa; 3 )屈服强度大于 1200 MPa; 4)延伸率大于 10%; 5 )优良的各项力学性能。
本发明所述的具有低屈服比的超高强韧钢板的制造方法， 通过优化温度 控制， 不增加任何工序难度和歩骤的情况下， 就可以获得细化马氏体组织和 残余奥氏体的软硬结合的微观组织， 以获得力学性能理想的具有低屈服比的 超高强韧钢板， 工艺制度比较宽松， 可广泛应用于结构安全性要求较高的工 程构件制造领域的稳定生产。 附图说明
图 1显示了实施例 4所涉及的具有低屈服比的超高强韧钢板在光学显微 镜下的微观组织。 具体实施方式
下面将根据具体实施例和说明书附图对本发明的技术方案作进一歩解 释， 但该解释并不构成对本发明的不当限定。
实施例 1-6
采用下述歩骤制造本发明所述的具有低屈服比的超高强韧钢板：
1 ) 冶炼， 控制各化学元素的质量百分含量的配比， 具体如表 1所示；
2) 浇铸；
3 ) 加热： 将板坯加热至 1080〜1250°C ;
4) 轧制： 轧制后的钢板空冷或水冷；
5 ) 冷却： 冷却至室温；
6) 淬火： 淬火温度为 860〜940°C， 淬火后水冷；
7) 回火： 回火温度为 150〜350°C， 回火后空冷。
图 1显示了本案实施例 4的具有低屈服比的超高强韧钢板在光学显微镜 下的微观组织。
表 1 实施例 1-6中的具有低屈服比的超高强韧钢板的各组分的质量百分配比 (wt.% , 余量为 Fe和其他不可避免的杂质)
Figure imgf000010_0001
注： CEV为碳当量， CEV=C+Mn/6+ (Cr+Mo+V) /5+ (Ni+Cu) /15 表 2显示了实施例 1-6的具体温度参数。其中， 表 2中的各实施例的具 体温度参数对应于表 1中相应实施例 1-6。
表 2 实施例 1-6的制造工艺中的具体温度参数
Figure imgf000010_0002
表 3 实施例 1-6所涉及的具有低屈服比的超高强韧钢板的力学性能参数
Figure imgf000010_0003
Figure imgf000011_0001
由表 3可以看出， 本发明所述的具有低屈服比的超高强韧钢板： 屈强比 小于 0.85， 抗拉强度大于 1500MPa， 屈服强度大于 1200 MPa， 延伸率大于 10%, 冲击功 Akv ( -20°C ) 大于 27J， 具有上述力学性能的钢板具有超高强 度和良好的强韧性和强塑性。 本技术领域中的普通技术人员应当认识到， 以上的实施例仅是用来说明 本发明， 而并非用作为对本发明的限定， 只要在本发明的实质精神范围内， 对以上所述实施例的变化、 变型都将落在本发明的权利要求书范围内。

Claims

权利要求书
1. 一种具有低屈服比的超高强韧钢板，其特征在于，其化学元素质量百分含
C: 0.18-0.34%,
Si: 0.10-0.40%,
Mm 0.50-1.40%,
Cr: 0.20-0.70%,
Mo: 0.30-0.90%,
Nb: 0-0.06%,
Ni: 0.50-2.40%,
V： 0-0.06%,
Ti: 0.002-0.04%,
Ah 0.01-0.08%,
B: 0.0006-0.0020% ，
N<0.0060%,
O<0.0040%,
Ca: 0-0.0045%,
余量为 Fe和其他不可避免的杂质。
2. 如权利要求 1所述的具有低屈服比的超高强韧钢板，其特征在于，其碳当 量满足 CEV≤0.75%，其中碳当量 CEV = C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu) /15。
3. 如权利要求 1或 2所述的具有低屈服比的超高强韧钢板，其特征在于，其 微观组织为细化马氏体和残余奥氏体。
4. 如权利要求 1或 2所述的具有低屈服比的超高强韧钢板的制造方法，其特 征在于， 包括冶炼、 浇铸、 加热、 轧制、 冷却、 淬火和回火歩骤， 获得钢 板的微观组织为细化马氏体和残余奥氏体，其中：加热歩骤中将板坯加热 至 1080〜1250°C ; 淬火歩骤的淬火温度为 860〜940°C ; 回火歩骤的回火 温度为 150〜350°C。
5. 如权利要求 4所述的具有低屈服比的超高强韧钢板的制造方法，其特征在 于， 轧制后的钢板空冷或水冷。
6. 如权利要求 4所述的具有低屈服比的超高强韧钢板的制造方法，其特征在 于， 淬火后的钢板水冷。
7. 如权利要求 4所述的具有低屈服比的超高强韧钢板的制造方法，其特征在 于， 回火后的钢板空冷。
8. 如权利要求 4所述的具有低屈服比的超高强韧钢板的制造方法，其特征在 于，其碳当量满足 CEV≤0.75%，其中碳当量 CEV=C+Mn/6+ (Cr+Mo+V) 15+ (Ni+Cu) /15。
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EP2949775B1 (en) 2020-01-22
JP2016509130A (ja) 2016-03-24
KR20150109462A (ko) 2015-10-01
KR102357132B1 (ko) 2022-01-28
AU2013375524B2 (en) 2018-04-05
EP2949775A4 (en) 2016-09-07
RU2682074C2 (ru) 2019-03-14
US10801090B2 (en) 2020-10-13
RU2015136606A (ru) 2017-09-26
AU2013375524A1 (en) 2015-08-13
US20150354040A1 (en) 2015-12-10
ZA201505173B (en) 2020-02-26

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