WO2021238915A1 - 一种耐延迟开裂的电镀锌超强双相钢及其制造方法 - Google Patents

一种耐延迟开裂的电镀锌超强双相钢及其制造方法 Download PDF

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WO2021238915A1
WO2021238915A1 PCT/CN2021/095802 CN2021095802W WO2021238915A1 WO 2021238915 A1 WO2021238915 A1 WO 2021238915A1 CN 2021095802 W CN2021095802 W CN 2021095802W WO 2021238915 A1 WO2021238915 A1 WO 2021238915A1
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super
electro
galvanized
delayed
phase steel
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PCT/CN2021/095802
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English (en)
French (fr)
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李伟
朱晓东
薛鹏
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宝山钢铁股份有限公司
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Priority to EP21813639.8A priority Critical patent/EP4159887A4/en
Priority to US17/927,771 priority patent/US20230243008A1/en
Priority to CA3180458A priority patent/CA3180458A1/en
Priority to JP2022572382A priority patent/JP2023527197A/ja
Publication of WO2021238915A1 publication Critical patent/WO2021238915A1/zh

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • 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
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    • 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
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    • 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
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
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    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
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    • 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
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    • 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
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    • 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
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—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
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
    • C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
    • C25D3/00—Electroplating: Baths therefor
    • C25D3/02—Electroplating: Baths therefor from solutions
    • C25D3/22—Electroplating: Baths therefor from solutions of zinc
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D2211/005—Ferrite
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    • 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

Definitions

  • the invention relates to a metal material and a manufacturing method thereof, in particular to an electro-galvanized super-strength dual-phase steel and a manufacturing method thereof.
  • Delayed fracture refers to a phenomenon in which materials under static stress suddenly break brittle after a certain period of time. This phenomenon is a kind of embrittlement caused by the interaction of materials and environmental stress, and it is a form of material deterioration caused by hydrogen. Delayed fracture is a major factor hindering the application of ultra-high-strength steel. It can be roughly divided into the following two categories:
  • Delayed fracture is mainly caused by hydrogen (external hydrogen) invaded from the external environment.
  • hydrogen external hydrogen
  • bolts used in bridges have delayed fracture due to long-term exposure in humid air, rain and other environments.
  • the former is generally caused by the intrusion of hydrogen generated by the corrosion reaction in the corrosion pit during the long-term exposure process; while the latter is caused by the hydrogen invaded into the steel during the manufacturing process such as pickling and electroplating. Caused by concentration at a concentration.
  • the publication number is CN107148486B, the publication date is January 8, 2019, and the name is "High-strength steel sheet, high-strength hot-dip galvanized steel sheet, high-strength hot-dip galvanized steel sheet and high-strength electro-galvanized steel sheet, and their manufacturing methods"
  • China Patent literature discloses a method for manufacturing electrogalvanized high-strength steel, the chemical composition of which is: C: 0.030% or more and 0.250% or less, Si: 0.01% or more and 3.00% or less, Mn: 2.60% or more and 4.20% or less, P: 0.001% or more and 0.100% or less, S: 0.0001% or more and 0.0200% or less, N: 0.0005% or more and 0.0100% or less, and Ti: 0.005% or more and 0.200% or less, the balance being composed of Fe and unavoidable impurities .
  • the billet is heated to 1100°C or higher and 1300°C or lower, hot rolled at a finish rolling exit temperature of 750°C or higher and 1000°C or lower, coiled at 300°C or higher and 750°C or lower, and then pickled to remove oxidation
  • the skin is cold-rolled at a temperature range of Ac1 transformation point + 20°C or more and Ac1 transformation point + 120°C or less for 600 seconds or more and 21600 seconds or less, and a reduction ratio of 30% or more. It is kept in the temperature range of not less than the transformation point and Ac1 transformation point + 100° C. for 20 seconds or more and 900 seconds or less, and then cooled, and then electro-galvanized.
  • the publication number is CN106282790B, the publication date is April 3, 2018, and the Chinese patent document entitled "An ultra-deep drawing cold-rolled steel sheet for electro-galvanizing and its production method" discloses an ultra-deep drawing cold-rolled steel sheet for electro-galvanizing.
  • the manufacturing method of rolled steel sheet, its chemical composition is: C ⁇ 0.002%, Si ⁇ 0.030%, Mn: 0.06% ⁇ 0.15%, P ⁇ 0.015%, S ⁇ 0.010%, Als: 0.030% ⁇ 0.050%, Ti: 0.040 ⁇ 0.070%, N ⁇ 0.0040%, the balance is Fe and unavoidable impurities.
  • the production method of the cold-rolled steel sheet includes the following steps: (1) hot metal pretreatment; (2) converter smelting; (3) alloy fine-tuning station; (4) RH furnace refining; (5) continuous casting; (6) heating Rolling; (7) cold rolling; (8) continuous annealing; (9) smoothing; the present invention can improve the surface quality of the electro-galvanized steel sheet and ensure that the electro-galvanized steel sheet has a good shape.
  • the mechanical properties of the cold-rolled steel sheet are: the yield strength is 120-180 MPa, and the tensile strength is higher than 260 MPa.
  • the publication number is CN1419607A
  • the publication date is May 21, 2003
  • the Chinese patent document entitled "High-strength dual-phase steel sheet and high-strength dual-phase electroplated steel sheet and manufacturing method thereof” discloses a tensile strength of 600 ⁇ 650MPa grade dual-phase steel plate and its manufacturing method, its chemical composition is: 0.01 ⁇ 0.08%C, not more than 2%Si, not more than 3.0%Mn, 0.01 ⁇ 0.5%V, V and C satisfy 0.5 ⁇ C/12 ⁇ V /51 ⁇ 3 ⁇ C/12, the balance is Fe and unavoidable impurities.
  • the steel plate was heated to 1250°C and soaked, and then rolled three times at the conveying temperature of the finishing mill of 900°C, followed by a heat preservation treatment of 650°C ⁇ 1 hour. Then, the thin steel sheet was cold-rolled at a compression rate of 70°C/s to obtain a cold-rolled thin steel sheet with a thickness of 1.2 mm. Then, recrystallization annealing was performed at 850°C for 60 seconds and cooled at a cooling rate of 30°C/s, followed by electroplating treatment.
  • the tensile strength grades of the products mentioned in the above-mentioned existing patent documents are all less than 980MPa, or the matrix is hot stamping steel. Based on this, it is desired to obtain an electro-galvanized ultra-high-strength dual-phase steel that is resistant to delayed cracking to meet the requirements of the industry. On demand.
  • One of the objectives of the present invention is to provide an electro-galvanized super dual-phase steel resistant to delayed cracking.
  • the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention adopts reasonable The composition design, through the reasonable design and process coordination of carbon, silicon, manganese and niobium, vanadium, chromium, molybdenum and other microalloys, the obtained steel has excellent delayed cracking resistance and ultra-high strength.
  • the delayed crack-resistant electrogalvanized super dual-phase steel has yield strength ⁇ 550MPa, tensile strength ⁇ 980MPa, elongation after fracture ⁇ 12%, initial hydrogen content ⁇ 3ppm, preferably ⁇ 2ppm, and its preset stress is greater than or equal to one
  • double the tensile strength no delayed cracking will occur after being soaked in 1mol/L hydrochloric acid for 300 hours.
  • the delayed cracking resistant electrogalvanized super dual-phase steel is immersed in 1 mol/L hydrochloric acid for 300 hours without delayed cracking when the preset stress is 1.2 times the tensile strength.
  • the excellent performance of the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention can meet the needs of industry, is used in the manufacture of automobile safety structural parts, and has good promotion and application value and prospects.
  • the present invention provides an electro-galvanized super dual-phase steel resistant to delayed cracking, the matrix structure of which is ferrite + tempered martensite, the delayed-cracking resistant electro-galvanized super dual-phase steel In addition to Fe, it also contains the following chemical elements with the following mass percentages:
  • the mass percentage of each chemical element is:
  • C In the electro-galvanized super-strength dual-phase steel resistant to delayed cracking of the present invention, C is a solid solution strengthening element, which is a guarantee for the material to obtain high strength. However, it should be noted that the higher the C content in the steel, the harder the martensite and the greater the tendency for delayed cracking to occur. Therefore, when designing the product, try to choose a low-carbon design, and control the mass percentage of C in the delayed crack-resistant electrogalvanized super dual-phase steel of the present invention to be between 0.07-0.1%.
  • Si and Al In the delayed crack-resistant electrogalvanized super dual-phase steel of the present invention, Si and Al elements can improve the tempering resistance of martensite, and can inhibit the precipitation and growth of Fe 3 C, thereby When tempering, the precipitates formed are mainly epsilon carbides.
  • Al is also a deoxidizing element, which can play a deoxidizing effect in steel. Therefore, in the delayed-cracking resistant electrogalvanized super dual-phase steel of the present invention, the mass percentage of Si is controlled to be between 0.05-0.3%, and the mass percentage of Al is controlled to be between 0.02-0.05%.
  • Mn In the delayed cracking resistant electrogalvanized super dual-phase steel of the present invention, Mn is an element that strongly improves the hardenability of austenite, which can effectively increase the strength of the steel by forming more martensite . Therefore, the mass percentage of Mn in the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention is controlled to be between 2.0-2.6%.
  • Cr In the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention, Cr can effectively improve the tempering resistance of martensite, which is very beneficial to the improvement of delayed cracking.
  • the mass percentage of Cr in the cracked electro-galvanized super dual-phase steel is controlled to be between 0.2-0.6%.
  • Mo In the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention, adding an appropriate amount of Mo element can be beneficial to the formation of dispersed fine precipitates and the aggregation of dispersed hydrogen. Mo element can form a large number of MoC precipitates in steel, which is conducive to the accumulation of dispersed hydrogen in local areas, and is very beneficial to the improvement of delayed cracking of steel. Therefore, the mass percentage of Mo in the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention is controlled to be between 0.1-0.25%.
  • Nb element is a carbonitride precipitation element, which can refine grains and precipitate carbonitrides, improve the strength of the material, and is at the same time coherent
  • the microalloy precipitates are beneficial to disperse the accumulation of hydrogen and are beneficial to delayed cracking. Therefore, the mass percentage of Nb in the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention is controlled to be between 0.02-0.04%.
  • V In the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention, V can play a role in grain refinement, and at the same time, coherent microalloy precipitates are conducive to the accumulation of dispersed hydrogen. Therefore, the mass percentage of V in the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention is controlled to be between 0.06-0.2%.
  • the delayed-cracking resistant electro-galvanized super dual-phase steel of the present invention also contains 0.0015-0.003% of the B element.
  • the delayed cracking resistant electrogalvanized super duplex steel of the present invention may also contain a small amount of B element.
  • B is used as a strong hardenability element, and an appropriate amount of B can improve steel Hardenability promotes the formation of martensite.
  • the inevitable impurities include P, S and N elements, and the content is controlled to at least one of the following items: P ⁇ 0.012%, S ⁇ 0.003%, N ⁇ 0.005%.
  • P, S, and N are unavoidable impurity elements in the steel.
  • the content of P, S and N in the steel is greater The lower the better.
  • S is easy to form MnS inclusions, which will seriously affect the hole expansion rate;
  • P element will reduce the toughness of the steel, which is detrimental to delayed cracking; too high content of N in the steel will easily cause cracks on the surface of the slab, which will greatly affect the performance of the steel.
  • the mass percentage of P is controlled to be P ⁇ 0.012%
  • the mass percentage of S is controlled to be S ⁇ 0.003%
  • the mass percentage of N is controlled to be N ⁇ 0.005%.
  • the phase ratio (volume ratio) of the tempered martensite is >50%.
  • the delayed-cracking resistant electrogalvanized super dual-phase steel of the present invention a large number of fine carbide particles are dispersed and precipitated in the matrix structure, and the carbide particles include MoC, VC, Nb ( C, N), the carbide particles are all distributed in the matrix structure in a coherent form.
  • the size of the aforementioned carbide particles is less than or equal to 60 nm.
  • the tempered martensite also contains coherent distribution of epsilon carbides.
  • the delayed-cracking resistant electrogalvanized super dual-phase steel of the present invention its performance satisfies at least one of the following items: yield strength ⁇ 550MPa, tensile strength ⁇ 980MPa, elongation after fracture ⁇ 12%, the initial hydrogen content is ⁇ 3ppm; when the preset stress is greater than or equal to one time the tensile strength, the delayed cracking will not occur after being soaked in 1mol/L hydrochloric acid for 300 hours.
  • the delayed cracking resistant electrogalvanized super dual-phase steel of the present invention meets the following requirements: yield strength ⁇ 550MPa, tensile strength ⁇ 980MPa, elongation after fracture ⁇ 12%, The initial hydrogen content is less than or equal to 3ppm; when the preset stress is greater than or equal to one time the tensile strength, the delayed cracking will not occur after being soaked in 1mol/L hydrochloric acid for 300 hours.
  • the yield ratio of the electro-galvanized super-strength dual-phase steel resistant to delayed cracking of the present invention is in the range of 0.55-0.70.
  • another object of the present invention is to provide a method for manufacturing an electro-galvanized super duplex steel resistant to delayed cracking.
  • the yield strength of the electro-galvanized super duplex steel resistant to delayed cracking produced by the method is ⁇ 550MPa, tensile strength ⁇ 980MPa, elongation after fracture ⁇ 12%, initial hydrogen content ⁇ 3ppm, preferably ⁇ 2ppm, when the preset stress is greater than or equal to one time the tensile strength, soak in 1mol/L hydrochloric acid for 300 Delayed cracking does not occur within hours.
  • the present invention proposes a method for manufacturing the above-mentioned delayed crack-resistant electro-galvanized super dual-phase steel, which includes the following steps:
  • Annealing increase the temperature to the annealing soaking temperature at a heating rate of 3-10°C/s to 780-820°C, preferably 790-810°C, the annealing time is 40-200s, preferably 40-160s, and then at 30-80°C /s, preferably 35-80°C/s rapid cooling, the starting temperature of rapid cooling is 650-730°C;
  • the tempering temperature is 200-280°C, preferably 210-270°C, and the tempering time is 100-400s, preferably 120-300s;
  • the relevant process parameters are controlled through the use of medium and low temperature tempering treatment, which is not only conducive to reducing martensite
  • the hardness can also effectively avoid the precipitation of coarse particles of martensite, which is very beneficial to the delayed cracking performance of steel.
  • step (1) the continuous casting pulling speed is controlled to be 0.9-1.5 m/min during the continuous casting process.
  • the continuous casting in step (1) can be performed in a large water volume secondary cooling mode.
  • step (2) the cast slab is controlled to be soaked at a temperature of 1200 to 1260°C, preferably 1210 to 1245°C; then rolled, and the final rolling temperature is controlled to be 840 to 900°C, cooling at a rate of 20 ⁇ 70°C/s after rolling; then coiling, the coiling temperature is 580 ⁇ 630°C, after coiling, heat preservation treatment or slow cooling treatment is carried out.
  • the temperature is kept for 1-5 hours, or slow cooling is performed at a cooling rate of 3-5°C/s.
  • the heating temperature is controlled to be above 1200°C, and at the same time to prevent The increase in oxidation burnout requires the upper limit of controlling the heating temperature to be 1260°C. Therefore, the final control of the casting slab is to soak at a temperature of 1200 to 1260°C.
  • step (2) heat preservation after hot rolling and coiling or slow cooling after coiling is conducive to the charging and analyzing of dispersed precipitates.
  • Various types of dispersed precipitates are beneficial to adsorb a small amount of hydrogen and disperse
  • the distribution of hydrogen avoids the accumulation of hydrogen and is beneficial to resist delayed cracking.
  • step (3) the cold rolling reduction ratio is controlled to be 45-65%.
  • the cold rolling reduction ratio is controlled to be 45-65%.
  • pickling can be used to remove the oxide scale on the surface of the steel sheet.
  • step (6) the leveling reduction rate is controlled to be ⁇ 0.3%.
  • the leveling reduction rate is controlled to be ⁇ 0.3%.
  • the step (7) can be implemented by a conventional electro-galvanizing method.
  • double-sided plating is performed, and the weight of the plating layer on one side is in the range of 10-100 g/m 2.
  • the electro-galvanized super-strength dual-phase steel with resistance to delayed cracking and its manufacturing method according to the present invention have the following advantages and beneficial effects:
  • the delayed-cracking resistant electrogalvanized super dual-phase steel of the present invention adopts reasonable composition design. Through the reasonable design and process cooperation of carbon, silicon, manganese, and niobium, vanadium, chromium, molybdenum and other microalloys, the obtained steel has Excellent resistance to delayed cracking and super high strength.
  • the delayed cracking resistant electrogalvanized super dual-phase steel has yield strength ⁇ 550MPa, tensile strength ⁇ 980MPa, elongation after fracture ⁇ 12%, initial hydrogen content ⁇ 3ppm, and its tensile strength is greater than or equal to twice the tensile strength at the preset stress In the case of immersion in 1mol/L hydrochloric acid for 300 hours, delayed cracking will not occur.
  • the excellent performance of the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention can meet the needs of industry, is suitable for the manufacture of automobile safety structural parts, and has good promotion and application value and prospects.
  • the delayed crack resistant electrogalvanized super dual-phase steel of the present invention adopts reasonable composition design and continuous casting process to make the inside of the steel plate, especially the surface layer, free of TiN, which is beneficial to reducing the accumulation of hydrogen in the inside of the steel plate and improving the delayed cracking performance of the steel.
  • a combination of high temperature soaking + medium temperature tempering is adopted.
  • high temperature soaking causes more austenite transformation to occur, and more martensite is obtained during the subsequent rapid cooling, which ultimately ensures higher strength before tempering; through the use of medium and low temperature tempering
  • Treatment and control of relevant process parameters not only help reduce the hardness of martensite, but also effectively avoid the precipitation of coarse martensite, so that the yield ratio of the material is moderate.
  • tempering if the tempering temperature used is too low, it is not conducive to reducing the hardness of the martensite; if the tempering temperature is too high, the martensite will decompose and the final strength will be lower than 980MPa.
  • the combination of high-temperature soaking and medium-temperature tempering of the present invention effectively ensures that the produced delayed-cracking-resistant electrogalvanized super-strength dual-phase steel has excellent delayed-cracking resistance and low initial hydrogen content.
  • Table 1 lists the mass percentages of various chemical elements in the steel grades corresponding to the delayed cracking resistant electrogalvanized super dual-phase steels of Examples 1-6 and the steels of Comparative Examples 1-14.
  • Hot rolling control the cast slab to soak at a temperature of 1200 ⁇ 1260°C; then roll, control the final rolling temperature to 840 ⁇ 900°C, cool it at a rate of 20 ⁇ 70°C/s after rolling; then carry out coiling ,
  • the coiling temperature is 580 ⁇ 630°C, after coiling, the heat preservation cover is used for heat preservation for 1-5 hours;
  • Annealing heating at a heating rate of 3-10°C/s to an annealing soaking temperature of 780-820°C, annealing time of 40-200s, and then rapid cooling at a rate of 30-80°C/s, the beginning of rapid cooling
  • the temperature is 650 ⁇ 730°C;
  • Tempering temperature is 200 ⁇ 280°C, and tempering time is 100 ⁇ 400s;
  • Double-sided electro-galvanization the weight of the single-sided coating is 10-100g/m 2 .
  • Table 2-1 and Table 2-2 list the specific process parameters of the delayed-cracking resistant electrogalvanized super duplex steel of Example 1-6 and the steel of Comparative Example 1-14.
  • Table 3 lists the performance test results of the delayed crack-resistant electrogalvanized super dual-phase steel of Examples 1-6 and the steel of Comparative Examples 1-14.
  • the performance test method refers to the GB/T 13239-2006 low-temperature tensile test method for metallic materials, prepares standard specimens, performs static stretching on a tensile testing machine, and obtains the corresponding stress-strain curve. After data processing, the yield strength and resistance are finally obtained. Tensile strength and elongation at break parameters.
  • the measurement method of hydrogen content Heat the sample to a certain temperature, and use a hydrogen analyzer to measure the concentration of hydrogen released with the temperature change (increase) to determine the initial hydrogen content in the steel.
  • each embodiment of the present invention has ultra-high strength and delayed cracking performance that is significantly better than that of the comparable steel grades of the same level.
  • the preset stress is greater than or equal to twice the tensile strength After immersing in 1mol/L hydrochloric acid for 300 hours, no delayed cracking occurred.
  • the excellent performance of the electro-galvanized super dual-phase steel resistant to delayed cracking of the present invention can meet the needs of industry, is suitable for the manufacture of automobile safety structural parts, and has good promotion and application value and prospects.

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Abstract

本发明公开了一种耐延迟开裂的电镀锌超强双相钢，其基体组织为铁素体+回火马氏体，含有质量百分比如下的化学元素：C：0.07-0.1％，Si：0.05-0.3％，Mn：2.0-2.6％，Cr：0.2-0.6％，Mo：0.1-0.25％，Al：0.02-0.05％，Nb：0.02-0.04％，V：0.06-0.2％。本发明还公开了耐延迟开裂的电镀锌超强双相钢的制造方法，包括步骤：冶炼和连铸、热轧、冷轧、退火、回火、平整和电镀。本发明耐延迟开裂的电镀锌超强双相钢不仅有较好的力学性能，还具有优异的耐延迟开裂性和较低初始氢含量。

Description

一种耐延迟开裂的电镀锌超强双相钢及其制造方法 技术领域
本发明涉及一种金属材料及其制造方法，尤其涉及一种电镀锌超强双相钢及其制造方法。
背景技术
随着汽车工业出于汽车减重和安全性的需要，市场对强度更高的钢板需求量越来越多。而其中双相钢由于具有低屈服强度、高抗拉强度以及高的初始加工硬化速率等优良的性能在汽车零部件生产中得到了广泛使用。目前市场上强度等级需求主要以80公斤、100公斤级的为主，出于防腐的要求，目前汽车工业较多采用镀锌钢板，但此类钢板普遍存在延迟开裂问题。
延迟断裂是指在静止应力作用下的材料，经过一定时间后突然脆性破坏的一种现象。这种现象是材料与环境应力相互作用而发生地一种脆化，是氢导致材质恶化的一种形态。延迟断裂现象是妨碍超高强钢应用的一个主要因素，它大体上可分为以下两类：
(1)主要是由外部环境侵入的氢(外氢)引起的延迟断裂。如桥梁等使用的螺栓，在潮湿空气、雨水等环境中长期暴露而发生延迟断裂。
(2)酸洗、电镀处理等制造过程中侵入钢中的氢(内氢)引起的延迟断裂。如电镀螺栓等在加载后，经过几小时或几天的较短时间后而发生延迟断裂。
前者一般是由于在长期暴露过程中发生腐蚀，腐蚀坑处腐蚀反应生成的氢侵入而引起的；而后者是由于制造过程如酸洗、电镀处理时侵入钢中的氢在应力的作用下向应力集中处集中而引起的。
公开号为CN107148486B，公开日为2019年1月8日，名称为“高强度钢板、高强度热镀锌钢板、高强度热镀铝钢板和高强度电镀锌钢板、以及它们的制造方法”的中国专利文献，公开了一种电镀锌高强钢的制造方法，其化学成分为：C：0.030％以上且0.250％以下、Si：0.01％以上且3.00％以下、Mn：2.60％以上且4.20％以下、P：0.001％以上且0.100％以下、S：0.0001％以上且0.0200％以下、N：0.0005％ 以上且0.0100％以下和Ti：0.005％以上且0.200％以下、余量由Fe和不可避免的杂质构成。该钢坯加热至1100℃以上且1300℃以下，在750℃以上且1000℃以下的精轧出口侧温度下进行热轧，在300℃以上且750℃以下进行卷取，接着，通过酸洗除去氧化皮，在Ac1相变点+20℃以上且Ac1相变点+120℃以下的温度范围内保持600秒以上且21600秒以下，以30％以上的压下率进行冷轧，然后，在Ac1相变点以上且Ac1相变点+100℃以下的温度范围内保持20秒以上900秒以下，进行冷却，接着，实施电镀锌处理。
公开号为CN106282790B，公开日为2018年4月3日，名称为“一种电镀锌用超深冲冷轧钢板及其生产方法”的中国专利文献，公开了一种电镀锌用超深冲冷轧钢板的制造方法，其化学成分为：C≤0.002％，Si≤0.030％，Mn：0.06％～0.15％，P≤0.015％，S≤0.010％，Als：0.030％～0.050％，Ti：0.040～0.070％，N≤0.0040％，余量为Fe以及不可避免的杂质。所述冷轧钢板的生产方法，包括以下步骤：(1)铁水预处理；(2)转炉冶炼；(3)合金微调站；(4)RH炉精炼；(5)连铸；(6)热轧；(7)冷轧；(8)连续退火；(9)平整；本发明能够提高电镀锌钢板的表面质量，保证电镀锌钢板具有良好板型。所述冷轧钢板的力学性能为：屈服强度为120～180MPa，抗拉强度高于260MPa。
公开号为CN1419607A，公开日为2003年5月21日，名称为“高强度双相薄钢板和高强度双相电镀薄钢板及其制造方法”的中国专利文献，公开了一种抗拉强度600～650MPa级双相钢板及制造方法，其化学成分为：0.01～0.08％C、不超过2％Si、不超过3.0％Mn、0.01～0.5％V，V与C满足0.5×C/12≤V/51≤3×C/12，余量为Fe以及不可避免的杂质。该钢板加热至1250℃并均热，然后在900℃的精轧机输送温度下进行三道次轧制，随后进行650℃×1小时的保温处理。接着以70℃/s的压缩率对薄钢板进行冷轧，以获得厚度为1.2mm的冷轧薄钢板。接着在850℃下进行再结晶退火60秒并以30℃/s的冷却速率冷却，随后进行电镀处理。
由此可见，上述现有专利文献涉及到的产品抗拉强度等级均小于980MPa，或者基体为热冲压钢，基于此，期望获得一种耐延迟开裂的电镀锌超高强双相钢，以满足工业上的需求。
发明内容
本发明的目的之一在于提供一种耐延迟开裂的电镀锌超强双相钢，针对超高强 度钢易发生延迟开裂的特点，本发明耐延迟开裂的电镀锌超强双相钢采用合理的成分设计，通过碳、硅、锰以及铌、钒、铬、钼等微合金的合理设计和工艺配合，使获得钢具有优异耐延迟开裂性以及超高的强度。该耐延迟开裂的电镀锌超强双相钢屈服强度≥550MPa，抗拉强度≥980MPa，断后伸长率≥12％，起始氢含量≤3ppm、优选≤2ppm，其在预置应力大于等于一倍抗拉强度的情况下，以1mol/L的盐酸浸泡300小时不发生延迟开裂。在优选的实施方案中，该耐延迟开裂的电镀锌超强双相钢在预置应力为抗拉强度1.2倍的情况下，以1mol/L的盐酸浸泡300小时不发生延迟开裂。本发明所述的耐延迟开裂的电镀锌超强双相钢的优异性能可以满足工业上的需求，用于汽车安全结构件的制造，具有良好的推广应用价值和前景。
为了实现上述目的，本发明提供了一种耐延迟开裂的电镀锌超强双相钢，其基体组织为铁素体+回火马氏体，所述耐延迟开裂的电镀锌超强双相钢除了Fe以外还含有质量百分比如下的下述化学元素：
C：0.07-0.1％，Si：0.05-0.3％，Mn：2.0-2.6％，Cr：0.2-0.6％，Mo：0.1-0.25％，Al：0.02-0.05％，Nb：0.02-0.04％，V：0.06-0.2％。
进一步地，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，其各化学元素质量百分比为：
C：0.07-0.1％，Si：0.05-0.3％，Mn：2.0-2.6％，Cr：0.2-0.6％，Mo：0.1-0.25％，Al：0.02-0.05％，Nb：0.02-0.04％，V：0.06-0.2％，余量为Fe和其他不可避免的杂质。
在本发明所述的耐延迟开裂的电镀锌超强双相钢中，各化学元素的设计原理如下所述：
C：在本发明所述的耐延迟开裂的电镀锌超强双相钢中，C是固溶强化元素，是材料获得高强度的保证。但是，需要注意的是，钢中含C量越高，马氏体越硬，发生延迟开裂的倾向越大。因此产品设计时，尽量选择低碳的设计，在本发明所述的耐延迟开裂的电镀锌超强双相钢中控制C的质量百分比在0.07-0.1％之间。
Si和Al：在本发明所述的耐延迟开裂的电镀锌超强双相钢中，Si和Al元素能提高马氏体的抗回火性能，可以抑制Fe 3C的析出和长大，从而使回火时，形成的析出物以ε碳化物为主。此外，需要说明的是，Al还是脱氧元素，其可以在钢中起到脱氧作用。因此，在本发明所述的耐延迟开裂的电镀锌超强双相钢中控制Si的质量百分比在0.05-0.3％之间，控制Al的质量百分比在0.02-0.05％之间。
Mn：在本发明所述的耐延迟开裂的电镀锌超强双相钢中，Mn是强烈提高奥氏体淬透性的元素，其可以通过形成更多的马氏体从而有效提高钢的强度。因此，在本发明所述的耐延迟开裂的电镀锌超强双相钢中控制Mn的质量百分比在2.0-2.6％之间。
Cr：在本发明所述的耐延迟开裂的电镀锌超强双相钢中，Cr可以有效提高马氏体的抗回火能力，对延迟开裂的改善十分有益，在本发明所述的耐延迟开裂的电镀锌超强双相钢中控制Cr的质量百分比在0.2-0.6％之间。
Mo：在本发明所述的耐延迟开裂的电镀锌超强双相钢中，添加适量的Mo元素可以有利于形成弥散分布的细小析出物，有利于分散氢的聚集。Mo元素在钢中可以形成大量的MoC析出物，有利于分散氢在局部区域的聚集，对钢的延迟开裂改善十分有益。因此，在本发明所述的耐延迟开裂的电镀锌超强双相钢中控制Mo的质量百分比在0.1-0.25％之间。
Nb：在本发明所述的耐延迟开裂的电镀锌超强双相钢中，Nb元素是碳氮化物析出元素，可以细化晶粒和析出碳氮化物，提高材料的强度，同时共格的微合金析出物有利于分散氢的聚集，对延迟开裂有利。因此，在本发明所述的耐延迟开裂的电镀锌超强双相钢中控制Nb的质量百分比在0.02-0.04％之间。
V：在本发明所述的耐延迟开裂的电镀锌超强双相钢中，V可以起到细化晶粒的作用，同时共格的微合金析出物有利于分散氢的聚集。因此，在本发明所述的耐延迟开裂的电镀锌超强双相钢中控制V的质量百分比在0.06-0.2％之间。
进一步地，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，其还含有0.0015-0.003％的B元素。
在本发明所述的技术方案中，本发明所述的耐延迟开裂的电镀锌超强双相钢中还可以含有少量的B元素，B作为强淬透性元素，适量的B可以提高钢的淬透性，促进马氏体的形成。
进一步地，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，其中不可避免的杂质包括P、S和N元素，其含量控制为下述各项的至少其中之一：P≤0.012％，S≤0.003％，N≤0.005％。
上述技术方案中，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，P、S和N均是钢中不可避免的杂质元素，在钢中P、S和N元素含量越低越好。S易形成MnS夹杂物，会严重影响扩孔率；P元素会降低钢的韧性，对延迟开裂不利；钢中N 元素含量过高，容易导致板坯表面裂纹，大大影响钢的性能。因此，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，控制P的质量百分比为P≤0.012％，控制S的质量百分比为S≤0.003％，控制N的质量百分比为N≤0.005％。
进一步地，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，所述回火马氏体的相比例(体积比)＞50％。
进一步地，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，所述基体组织中弥散析出了大量的细小的碳化物颗粒，所述碳化物颗粒包括MoC、VC、Nb(C,N)，所述碳化物颗粒均以共格形式分布于基体组织中。
进一步地，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，上述碳化物颗粒的尺寸≤60nm。
进一步地，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，所述回火马氏体中还含有共格分布的ε碳化物。
进一步地，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，其性能满足下述各项的至少其中之一：屈服强度≥550MPa，抗拉强度≥980MPa，断后伸长率≥12％，起始氢含量≤3ppm；在预置应力大于等于一倍抗拉强度的情况下，以1mol/L的盐酸浸泡300小时不发生延迟开裂。
进一步地，在本发明所述的耐延迟开裂的电镀锌超强双相钢中，其性能满足下述各项：屈服强度≥550MPa，抗拉强度≥980MPa，断后伸长率≥12％，起始氢含量≤3ppm；在预置应力大于等于一倍抗拉强度的情况下，以1mol/L的盐酸浸泡300小时不发生延迟开裂。
进一步地，本发明所述的耐延迟开裂的电镀锌超强双相钢的屈强比在0.55-0.70的范围内。
相应地，本发明的另一目的在于提供一种耐延迟开裂的电镀锌超强双相钢的制造方法，采用该制造方法制得的耐延迟开裂的电镀锌超强双相钢的屈服强度≥550MPa，抗拉强度≥980MPa，断后伸长率≥12％，起始氢含量≤3ppm、优选≤2ppm，在预置应力大于等于一倍抗拉强度的情况下，以1mol/L的盐酸浸泡300小时不发生延迟开裂。
为了实现上述目的，本发明提出了上述的耐延迟开裂的电镀锌超强双相钢的制造方法，包括步骤：
(1)冶炼和连铸；
(2)热轧；
(3)冷轧；
(4)退火：以3-10℃/s的加热速度升温到退火均热温度780～820℃、优选790-810℃，退火时间为40～200s、优选40-160s，然后以30～80℃/s、优选35-80℃/s的速度快速冷却，快速冷却的开始温度为650～730℃；
(5)回火：回火温度为200～280℃、优选210-270℃，回火时间为100～400s、优选120-300s；
(6)平整；
(7)电镀。
在本发明所述的耐延迟开裂的电镀锌超强双相钢的制造方法中，在连续退火加热时，通过采用中低温回火处理，对相关工艺参数进行控制，不仅有利于降低马氏体的硬度，还可以有效避免粗大颗粒马氏体的析出，对钢的延迟开裂性能十分有利。
进一步地，在本发明所述的制造方法中，在步骤(1)中，连铸过程中控制连铸拉速为0.9-1.5m/min。
在上述技术方案中，在本发明所述的制造方法中，在步骤(1)中连铸可以采用大水量二冷模式进行。
进一步地，在本发明所述的制造方法中，在步骤(2)中，控制铸坯以1200～1260℃、优选1210-1245℃的温度均热；然后轧制，控制终轧温度为840～900℃，轧后以20～70℃/s的速度冷却；然后进行卷取，卷取温度为580～630℃，卷取后进行保温处理或缓冷处理。优选地，保温1-5小时，或以3-5℃/s的冷却速度进行缓冷。
在本发明所述的耐延迟开裂的电镀锌超强双相钢的制造方法中，在所述步骤(2)中，为保证轧制负荷的稳定，控制加热温度在1200℃以上，同时为防止氧化烧损的增大，控制加热温度的上限为1260℃，因此，最终控制铸坯以1200～1260℃的温度均热。
此外，需要说明的是，在步骤(2)中，热轧卷取后保温或卷取后缓冷，有利于弥散析出物的充分析出，各类弥散分布的析出物有利于吸附少量氢，分散氢的分布，避免氢的聚集，有利于抗延迟开裂。
进一步地，在本发明所述的制造方法中，在步骤(3)中，控制冷轧压下率为45～65％。
上述方案中，在所述步骤(3)中，在控制冷轧压下率为45～65％。冷轧前，可 以通过酸洗去除钢板表面氧化铁皮。
进一步地，在本发明所述的制造方法中，在步骤(6)中，控制平整压下率≤0.3％。
在本发明上述方案中，在所述步骤(6)中，为保证钢板的平整度，需要进行一定的平整量，然而过大的平整量会使得钢的屈服强度上升较多。因此，在本发明所述的制造方法中，控制平整压下率≤0.3％。
在本发明上述方案中，可采用常规的电镀锌的方法实施所述步骤(7)。优选地，进行双面镀，且单面的镀层重量在10-100g/m 2的范围内。
本发明所述的耐延迟开裂的电镀锌超强双相钢及其制造方法相较于现有技术具有如下所述的优点以及有益效果：
本发明所述的耐延迟开裂的电镀锌超强双相钢采用合理的成分设计，通过碳、硅、锰以及铌、钒、铬、钼等微合金的合理设计和工艺配合，使获得钢具有优异耐延迟开裂性以及超高的强度。该耐延迟开裂的电镀锌超强双相钢屈服强度≥550MPa，抗拉强度≥980MPa，断后伸长率≥12％，起始氢含量≤3ppm，其在预置应力大于等于一倍抗拉强度的情况下，以1mol/L的盐酸浸泡300小时不发生延迟开裂。本发明所述的耐延迟开裂的电镀锌超强双相钢的优异性能可以满足工业上的需求，适用于汽车安全结构件的制造，具有良好的推广应用价值和前景。
本发明的耐延迟开裂的电镀锌超强双相钢采用合理成分设计和连铸工艺使得钢板内部尤其是表层无TiN，对减轻氢在钢板内部的聚集有利，有利于提高钢的延迟开裂性能。
在本发明所述的制造方法中，采用高温均热+中温回火相结合的方式。在连续退火加热时，高温均热使得发生较多的奥氏体转变，在随后的快速冷却时得到更多的马氏体，最终保证回火前有更高的强度；通过采用中低温回火处理，对相关工艺参数进行控制，不仅有利于降低马氏体的硬度，还可以有效避免粗大颗粒马氏体的析出，使得材料的屈强比适中，另一方面对钢的延迟开裂性能十分有利。回火时，若采用的回火温度太低，不利于降低马氏体硬度；若回火温度太高，马氏体发生分解，最终强度低于980MPa。采用本发明的高温均热+中温回火相结合的方式有效地保证了制得的耐延迟开裂的电镀锌超强双相钢具有优异的耐延迟开裂性和较低的初始氢含量的特性。
具体实施方式
下面将结合具体的实施例对本发明所述的耐延迟开裂的电镀锌超强双相钢及其制造方法做进一步的解释和说明，然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例1-6和对比例1-14
表1列出了实施例1-6的耐延迟开裂的电镀锌超强双相钢和对比例1-14钢对应的钢种中各化学元素质量百分比。
表1(wt％，余量为Fe和其他除了P、S以及N以外的不可避免的杂质)
Figure PCTCN2021095802-appb-000001
本发明所述实施例1-6的耐延迟开裂的电镀锌超强双相钢和对比例1-14的钢均采用以下步骤制得：
(1)冶炼和连铸：在连铸过程中控制连铸拉速为0.9-1.5m/min，连铸采用大水量二冷模式进行；
(2)热轧：控制铸坯以1200～1260℃的温度均热；然后轧制，控制终轧温度为840～900℃，轧后以20～70℃/s的速度冷却；然后进行卷取，卷取温度为580～630℃，卷取后采用保温罩进行保温1-5小时；
(3)冷轧：控制冷轧压下率为45～65％；
(4)退火：以3-10℃/s的加热速度升温到退火均热温度780～820℃，退火时间 为40～200s，然后以30～80℃/s的速度快速冷却，快速冷却的开始温度为650～730℃；
(5)回火：回火温度为200～280℃，回火时间为100～400s；
(6)平整：控制平整压下率≤0.3％；
(7)双面电镀锌，单面镀层重量为10-100g/m 2。
需要说明的是，实施例1-6的耐延迟开裂的电镀锌超强双相钢的化学成分和相关工艺参数均满足本发明设计规范控制要求。对比例1-6的钢化学成分均存在未能满足本发明设计的要求的参数；对比例7-14对应的M钢种的化学成分虽然满足本发明设计要求，但是相关工艺参数均存在未能满足本发明设计规范的参数。
表2-1和表2-2列出了实施例1-6的耐延迟开裂的电镀锌超强双相钢和对比例1-14钢的具体工艺参数。
表2-1
Figure PCTCN2021095802-appb-000002
Figure PCTCN2021095802-appb-000003
表2-2
Figure PCTCN2021095802-appb-000004
将实施例1-6的耐延迟开裂的电镀锌超强双相钢和对比例1-14钢进行各项性能测试，所得的测试结果列于表3中。
表3列出了实施例1-6的耐延迟开裂的电镀锌超强双相钢和对比例1-14钢的性能测试结果。性能测试方法参照GB/T 13239-2006金属材料低温拉伸试验方法，制 备标准试样，在拉伸试验机上进行静态拉伸，得到相应应力-应变曲线，经过数据处理，最终得到屈服强度、抗拉强度和断裂延伸率参数。
氢含量的测量方法：将样品加热至一定温度，利用氢分析仪测量通过随温度变化(升高)释放出的氢的浓度，从而判断钢中的起始氢含量。
表3
Figure PCTCN2021095802-appb-000005
注：钢板在一定内应力水平下浸泡在1mol/L的盐酸中300小时的结果：Ο表示未开裂，X表示开裂。
由表3可看出，本发明各实施例的屈服强度均≥550MPa，抗拉强度均≥980MPa，断后伸长率均≥12％，起始氢含量均≤3ppm。各实施例的耐延迟开裂的电镀锌超强双相钢均具有超高的强度和明显优于同等级别的对比钢种的延迟开裂性能，其在预 置应力大于等于一倍抗拉强度的情况下，以1mol/L的盐酸浸泡300小时不发生延迟开裂。本发明所述的耐延迟开裂的电镀锌超强双相钢的优异性能可以满足工业上的需求，适用于汽车安全结构件的制造，具有良好的推广应用价值和前景。
需要说明的是，本发明的保护范围中现有技术部分并不局限于本申请文件所给出的实施例，所有不与本发明的方案相矛盾的现有技术，包括但不局限于在先专利文献、在先公开出版物，在先公开使用等等，都可纳入本发明的保护范围。此外，本案中各技术特征的组合方式并不限本案权利要求中所记载的组合方式或是具体实施例所记载的组合方式，本案记载的所有技术特征可以以任何方式进行自由组合或结合，除非相互之间产生矛盾。
还需要注意的是，以上所列举的实施例仅为本发明的具体实施例。显然本发明不局限于以上实施例，随之做出的类似变化或变形是本领域技术人员能从本发明公开的内容直接得出或者很容易便联想到的，均应属于本发明的保护范围。

Claims (15)

  1. 一种耐延迟开裂的电镀锌超强双相钢，其特征在于，其基体组织为铁素体+回火马氏体，所述耐延迟开裂的电镀锌超强双相钢除了Fe以外还含有质量百分比如下的下述化学元素：
    C：0.07-0.1％，Si：0.05-0.3％，Mn：2.0-2.6％，Cr：0.2-0.6％，Mo：0.1-0.25％，Al：0.02-0.05％，Nb：0.02-0.04％，V：0.06-0.2％。
  2. 如权利要求1所述的耐延迟开裂的电镀锌超强双相钢，其特征在于，其各化学元素质量百分比为：
    C：0.07-0.1％，Si：0.05-0.3％，Mn：2.0-2.6％，Cr：0.2-0.6％，Mo：0.1-0.25％，Al：0.02-0.05％，Nb：0.02-0.04％，V：0.06-0.2％，余量为Fe和其他不可避免的杂质。
  3. 如权利要求1或2所述的耐延迟开裂的电镀锌超强双相钢，其特征在于，其还含有0.0015-0.003％的B元素。
  4. 如权利要求2所述的耐延迟开裂的电镀锌超强双相钢，其特征在于，其中不可避免的杂质包括P、S和N元素，其含量控制为下述各项的至少其中之一：P≤0.012％，S≤0.003％，N≤0.005％。
  5. 如权利要求1或2所述的耐延迟开裂的电镀锌超强双相钢，其特征在于，所述回火马氏体的相比例＞50％。
  6. 如权利要求1或2所述的耐延迟开裂的电镀锌超强双相钢，其特征在于，所述基体组织中析出了细小弥散的碳化物颗粒，所述碳化物颗粒包括MoC、VC、Nb(C,N)，所述碳化物颗粒均以共格形式分布于基体组织中。
  7. 如权利要求6所述的耐延迟开裂的电镀锌超强双相钢，其特征在于，所述碳化物颗粒的尺寸≤60nm。
  8. 如权利要求1或2所述的耐延迟开裂的电镀锌超强双相钢，其特征在于，所述回火马氏体中还含有共格分布的ε碳化物。
  9. 如权利要求1或2所述的耐延迟开裂的电镀锌超强双相钢，其特征在于，其性能满足下述各项的至少其中之一：屈服强度≥550MPa，抗拉强度≥980MPa，断后伸长率≥12％，起始氢含量≤3ppm；在预置应力大于等于一倍抗拉强度的情况下，以1mol/L的盐酸浸泡300小时不发生延迟开裂。
  10. 一种如权利要求1-9中任意一项所述的耐延迟开裂的电镀锌超强双相钢的制造方法，其特征在于，包括步骤：
    (1)冶炼和连铸；
    (2)热轧；
    (3)冷轧；
    (4)退火：以3-10℃/s的加热速度升温到退火均热温度780～820℃，退火时间为40～200s，然后以30～80℃/s的速度快速冷却，快速冷却的开始温度为650～730℃；
    (5)回火：回火温度为200～280℃，回火时间为100～400s；
    (6)平整；
    (7)电镀。
  11. 如权利要求10所述的制造方法，其特征在于，在步骤(1)中，连铸过程中控制连铸拉速为0.9-1.5m/min。
  12. 如权利要求10所述的制造方法，其特征在于，在步骤(2)中，控制铸坯以1200～1260℃的温度均热；然后轧制，控制终轧温度为840～900℃，轧后以20～70℃/s的速度冷却；然后进行卷取，卷取温度为580～630℃，卷取后进行保温处理。
  13. 如权利要求10所述的制造方法，其特征在于，在步骤(3)中，控制冷轧压下率为45～65％。
  14. 如权利要求10所述的制造方法，其特征在于，在步骤(6)中，控制平整压下率≤0.3％。
  15. 如权利要求10所述的制造方法，其特征在于，步骤(2)中，控制铸坯以1210～1245℃的温度均热；步骤(4)中，以3～10℃/s的加热速度升温到退火均热温度790～810℃，退火时间为40～160s，然后以35～80℃/s的速度快速冷却，快速冷却的开始温度为650～730℃；步骤(5)中，回火温度为210～270℃，回火时间为120～300s。
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