CN104278194A - High-strength high-plasticity cold-rolled steel plate for automobiles and production method thereof - Google Patents

High-strength high-plasticity cold-rolled steel plate for automobiles and production method thereof Download PDF

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Publication number
CN104278194A
CN104278194A CN201310285053.8A CN201310285053A CN104278194A CN 104278194 A CN104278194 A CN 104278194A CN 201310285053 A CN201310285053 A CN 201310285053A CN 104278194 A CN104278194 A CN 104278194A
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temperature
cold
steel plate
plasticity
rolling
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CN104278194B (en
Inventor
王旭
刘仁东
王科强
郭金宇
徐荣杰
孙建伦
林利
徐鑫
喻振华
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Angang Steel Co Ltd
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Angang Steel Co Ltd
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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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • 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

Abstract

The invention discloses a high-strength high-plasticity cold-rolled steel plate for automobiles and a production method thereof. The high-strength high-plasticity cold-rolled steel plate comprises, by weight, 0.25-0.35% of C, 0.8-1.2% of Si, 2.0-2.5% of Mn, less than or equal to 0.02% of P, less than or equal to 0.005% of S, 0.5-1.0% of Al, 0.001-0.002% of B and the balance Fe and unavoidable impurities. The production method comprises smelting, continuous casting, hot rolling, pickling, cold rolling and continuous annealing. A continuous annealing heating temperature is in a range of 800-850 DEG C, thermal insulation time is in a range of 150-180s, a cooling rate is greater than or equal to 50 DEG C/s, a quenching temperature is in a range of 250-280 DEG C, a partition temperature is in a range of 350-400 DEG C, partition time is in a range of 300-600s and after partition, the product is cooled to a room temperature at a cooling rate greater than or equal to 50 DEG C/s.

Description

A kind of automobile cold-rolled steel plate and production method thereof with high-strength high-plasticity
Technical field
The invention belongs to cold rolled automobile steel making field, relate to a kind of tensile strength and be greater than 980MPa, high-strength high-plasticity cold-rolled steel sheet and production method thereof that unit elongation is greater than 20%.
Background technology
Automotive industry, through the development in century more than one, becomes the mainstay industry of Chinese national economy gradually.After entering 21 century, materials used in auto manufacturing there occurs wide variation, and from the overall development of Europe, the United States, Deng state materials used in auto manufacturing, due to the requirement of automotive light weight technology, the consumption of steel is in minimizing, and the consumption of powder metal, non-ferrous metal and plastics is in increase.But in order to improve vehicle safety, increase active and passive security measure again, this will increase the weight of automobile.The effective means solving this contradiction adopts AHSS exactly, as dual phase steel (DP), transformation induced plasticity steel (TRIP), twinning-induced plasticity steel (TWIP), containing B ultrasonic high-strength steel etc.Iron and steel circle through for many years with the technological cooperation of car industry at steel lightweight vehicle body, demonstrate the leading material that ferrous materials remains future automobile use, but intension there occurs wide variation, develop into based on high tensile steel plate and hot-dip galvanizing sheet steel with mild steel and common cold-reduced sheet for main by original, wherein, high tensile steel plate will be accounted for 14-45%(100-294 kilogram/car of car weight by current per car usage quantity) bring up to 30-70% in the future.
Patent CN102409252A discloses a kind of super high tensile cold-rolled steel plate and manufacture method thereof, design mix is 0.05-0.08%C, 0.10-0.40%Si, 0.50-1.0%Mn, 0.008-0.030%P, S≤0.006%, 0.08-0.20%Ni, 0.20-0.55%Cu, 0.30-0.60%Cr, 0.015-0.045%Al, 0.06-0.13%Ti, and surplus is Fe.Its yield strength can reach more than 700MPa, but tensile strength is seldom greater than 900MPa, and alloying element kind is more, and content is higher.
Patent CN102534373A discloses a kind of the super-high strength cold rolled steel band and the manufacture method thereof that are applicable to rolling formation, design mix is 0.13-0.17%C, 0.2-0.4%Si, 0.5-0.8%Mn, 0.015-0.003%B, P≤0.010%, S≤0.003%, 0.004-0.006%N, 0.025-0.05%Ti, 0.02-0.04%Al, 0.0025-0.0055%Ca, and all the other are Fe.Its tensile strength is at more than 980MPa, but unit elongation is only about 10%, and with the addition of the microalloy elements such as B, Ti, Ca, and smelting process is wayward.
Patent CN101871078A discloses a kind of super-high strength cold rolled steel and manufacture method thereof, design mix is 0.08-0.16%C, 0.1-0.4%Si, 1.6-2.2%Mn, P≤0.01%, S≤0.003%, 0.02-0.04%Al, N≤0.005%, 0.1-0.3%Cr, B/N:0.3-0.7.In order to improve the cutting ability of steel plate, the basis of above-mentioned chemical composition also added in Se and Bi one or both, wherein the addition of Se is the addition of 0.01-0.03%, Bi is 0.02-0.04%.
Patent CN101363102A discloses a kind of TRIP steel sheet for high strength cold rolled continuous annealing and preparation method thereof, design mix is 0.1-0.4%C, 0.5-2.5%Si, 0.5-2.5%Mn, 0.01-0.10%Nb, 0.01-0.10%Ti, 0.1-1.0%Cu, 0.1-1.0%Ni, P≤0.03%, S≤0.02%, and surplus is iron.Utilize Nb, Ti to separate out tiny carbonitride, and realize the raising of intensity by adding Cu, Ni.
In recent years, American scholar Speer etc. develop on basis at the TRIP steel containing Mn-Si, after high-carbon and middle carbon silicon containing steel are quenched, isothermal is carried out again in the certain temperature that Ms point is above, carbon is made to be dispensed to residual austenite by martensite, thus obtain the room temperature texture be made up of martensite and residual austenite two-phase, obtain higher intensity and plasticity cooperation.This process quilt is called the heat treated novel process of martensite steel sections (Q-P:quenching and partitioning).
In published cold rolling high strength steel plate patent, tensile strength reaches more than 980MPa, and person is little, and ubiquity unit elongation is lower, and it is more that alloying element adds kind, and addition is comparatively large, the shortcoming that smelting cost is high, difficulty is large.And for novel Q-P thermal treatment process, need in theory steel plate to be heated to more than Ac3 point, temperature is higher, and energy-output ratio is larger.
Summary of the invention
The object of the present invention is to provide one to have good strength plasticity to coordinate, tensile strength >=980MPa, the high strength cold-rolled automobile steel of unit elongation >=20% and production method thereof.
Q-P heat treatment process in the present invention is: first a certain temperature be heated to by steel between Ac1 and Ac3 is incubated, and makes its partial austenitizing, realizes the first time enrichment of carbon in austenite structure.Then be chilled to a certain temperature between Ms (martensite start) point (Ms) and exit temperature (Mf) with the cooling rate of >=50 DEG C/s, make austenite fraction change martensite into.The partition temperature being warmed up to Ms point subsequently above is incubated, and makes carbon from martensite to the austenite diffusion do not changed, and complete the rich carbon of second time of residual austenite, thus improve its room temperature stability, making it at room temperature can stable existence.Finally be quickly cooled to room temperature, obtain the heterogeneous structure of ferrite, martensite and residual austenite.
The automobile cold-rolled steel plate chemical composition of high-strength high-plasticity provided by the invention is by weight percentage: C:0.25-0.35%, Si:0.8-1.2%, Mn:2.0-2.5%, P :≤0.02%, S :≤0.005%, Al:0.5-1.0%, B:0.001-0.002%, surplus is Fe and inevitable impurity.
C:C is one of the most effective strengthening element of martensitic matrix, and it is solid-solution in austenite, expands austenitic area, greatly improve stabilization of austenite, the C curve of ferrite and bainite transformation is moved to right, postpones ferrite and bainite transformation temperature, and reduce Ms point temperature.The too low meeting of carbon content makes the stability of residual austenite decline, but the too high meeting of carbon content makes to occur twin in martensite, reduces the plasticity of steel, toughness and weldability.Therefore application claims C content is between 0.25-0.35%.
Si:Si is non-carbide forming element, and the solubleness in carbide is extremely low, exists, improved intensity and the cold deformation cementation index of steel by solution strengthening with sosoloid form.In partition isothermal process of the present invention, it can strongly inhibited Fe 3the formation of C, makes the rich carbon of austenite do not changed, thus greatly improves stabilization of austenite, can at room temperature remain.In addition, Si can also remarkable reinforced ferrite, but higher Si content can worsen hot rolling performance and the Coating performance of steel plate, produces more surface imperfection.Therefore the Si content in the present invention is 0.8-1.2%.
Mn:Mn is one of effective solution strengthening element, adds Mn and can reduce martensite transformation temperature Ms, increase the content of residual austenite.Mn is little to the Toughness of steel plate simultaneously, when containing the Mn of 1.5-2.5% in steel, effectively can improve the decomposition drag of residual austenite.Mn too high levels, can cause serious component segregation, forms banded structure, affects the mechanical property of steel plate, and the Mn content of therefore the present invention's selection is in 2.0-2.5% scope.
P, S:P, S are relict element, and P easily causes steel plate center segregation, the impelling strength of havoc steel, and are unfavorable for hot-work and the weldability of steel plate; S easily and Mn form non-metallic inclusion, make clod wash and the reaming degradation of steel plate, therefore both all should control at lower level as far as possible, i.e. P≤0.02%, S≤0.005%.
Al:Al is used for deoxidation, the same with Si, is also non-carbide forming element, can strongly inhibited Fe 3the formation of C, makes the rich carbon of residual austenite.Although the solid solution strengthening effect of Al is weaker than Si, in the present invention, the side effect that Al unit usually reduces silicon can be added.Al can also form AlN with N element, effectively crystal grain thinning, and therefore application claims Al content is between 0.5-1.0%.
The growing up of ferrite crystal grain when B:B can stop annealing, and can separate out fast at grain boundaries thus strengthen crystal boundary, suppression P is in the segregation of grain boundaries.Meanwhile, B contributes to the hardening capacity improving steel plate, does not need too high cooling rate also can ensure armor plate strength after annealing.Too high B will obviously reduce the plasticity of steel plate, and as deposited strength is too high, therefore its content of application claims controls between 0.001-0.002%.
A kind of automobile cold-rolled steel plate with high-strength high-plasticity of the present invention, its technological process of production is: smelting → continuous casting → hot rolling → pickling → cold rolling → continuous annealing
(1) smelt according to design mix, i.e. C:0.25-0.35%, Si:0.8-1.2%, Mn:2.0-2.5%, P :≤0.02%, S :≤0.005%, Al:0.5-1.0%, B:0.001-0.002%, surplus is Fe and inevitable impurity, and continuous casting becomes slab.
(2) hot rolling: slab heating temperature is 1200 ~ 1250 DEG C, insulation more than 180min; Hot rolling start rolling temperature is for being greater than 1100 DEG C, and finishing temperature is 870 ~ 950 DEG C; Coiling temperature is 600 ~ 650 DEG C.
(3) pickling and cold rolling: hot-rolled sheet carries out cold rolling after conventional pickling, and cold rolling draft controls between 60 ~ 70%.
(4) continuous annealing: continuous annealing realizes committed step of the present invention, Heating temperature is 800 ~ 850 DEG C, soaking time is 150-180s, rate of cooling is >=50 DEG C/s, quenching temperature is 250 ~ 280 DEG C, partition temperature is 350 ~ 400 DEG C, and the partition time is 300 ~ 600s, is chilled to room temperature afterwards with the cooling rate of >=50 DEG C/s.
The automobile cold-rolled steel plate of high-strength high-plasticity provided by the present invention is C-Si-Mn alloy system, and chemical composition is simple, reasonable, does not add valuable or rare alloy element, and smelting technology controls easy, with low cost.The speed of cooling that continuous annealing process requires is only >=50 DEG C/s, requires low to connecting the capacity of equipment of moving back unit, avoids the problems such as high temperature cools the deformed steel strip that brings fast and internal stress is higher simultaneously.Heterogeneous structure, intensity and the plasticity no-float of ferrite, martensite and residual austenite is obtained under room temperature.Tensile strength is greater than 980MPa, and unit elongation is greater than 20%, is applicable to being applied to manufacturing automobile structure or stiffener, meets automobile industry minimizing requirement, wide market.
Accompanying drawing explanation
Fig. 1 is the transmission electron microscope film photo of embodiment 1.
Embodiment
Embodiment chemical composition is as shown in table 1:
Table 1 chemical composition (wt%)
Embodiment C Si Mn P S Al B Fe
1 0.28 1.11 2.15 0.015 0.0031 0.73 0.0013 Surplus
2 0.31 1.18 2.48 0.010 0.0025 0.59 0.0011 Surplus
3 0.30 1.02 2.25 0.013 0.0022 0.87 0.0015 Surplus
4 0.32 0.85 2.12 0.015 0.0037 0.91 0.0018 Surplus
5 0.26 0.92 2.36 0.011 0.0042 0.80 0.0016 Surplus
6 0.33 1.09 2.09 0.012 0.0019 0.66 0.0018 Surplus
Embodiment rolling technological parameter is as shown in table 2:
Table 2 rolling technological parameter
Embodiment continuous annealing process parameter is as shown in table 3:
Table 3 continuous annealing process parameter
The mechanical property of embodiment steel plate is as shown in table 4:
The mechanical property of table 4 steel plate
Embodiment Rp 0.2（MPa） Rm（MPa） A（%）
1 653 1037 21.5
2 628 1047 21.0
3 669 1041 20.5
4 658 1057 21.5
5 653 1053 22.0
6 654 1045 21.0
Fig. 1 is the transmission electron microscope film photo of embodiment 1, is organized as ferrite, martensite and residual austenite.

Claims (2)

1. one kind has the automobile cold-rolled steel plate of high-strength high-plasticity, it is characterized in that: chemical composition is by weight percentage: C:0.25-0.35%, Si:0.8-1.2%, Mn:2.0-2.5%, P :≤0.02%, S :≤0.005%, Al:0.5-1.0%, B:0.001-0.002%, surplus is Fe and inevitable impurity.
2. an automobile cold-rolled Plate Production method with high-strength high-plasticity according to claim 1, comprises smelting → continuous casting → hot rolling → pickling → cold rolling → continuous annealing; It is characterized in that: slab heating temperature is 1200 ~ 1250 DEG C, insulation more than 180min; Hot rolling start rolling temperature is for being greater than 1100 DEG C, and finishing temperature is 870 ~ 950 DEG C; Coiling temperature is 600 ~ 650 DEG C; Hot-rolled sheet carries out cold rolling after conventional pickling, and cold rolling draft controls between 60 ~ 70%; Continuous annealing Heating temperature is 800 ~ 850 DEG C, and soaking time is 150-180s, and rate of cooling is >=50 DEG C/s, and quenching temperature is 250 ~ 280 DEG C, and partition temperature is 350 ~ 400 DEG C, and the partition time is 300 ~ 600s, is chilled to room temperature afterwards with the cooling rate of >=50 DEG C/s.
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Cited By (10)

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Publication number Priority date Publication date Assignee Title
JP2017053001A (en) * 2015-09-09 2017-03-16 新日鐵住金株式会社 Galvanized steel sheet, galvannealed steel sheet, and their production methods
CN106811698A (en) * 2015-12-02 2017-06-09 鞍钢股份有限公司 A kind of high strength steel plate and its manufacture method based on tissue precise controlling
JP2019505690A (en) * 2015-12-21 2019-02-28 アルセロールミタル Method for producing a high strength steel sheet having improved ductility and formability and the resulting steel sheet
CN109477182A (en) * 2016-08-03 2019-03-15 株式会社神户制钢所 High-strength steel sheet and its manufacturing method
CN109694992A (en) * 2017-10-20 2019-04-30 鞍钢股份有限公司 A kind of tensile strength is greater than the quenching partition steel and its production method of 1500MPa
CN110475891A (en) * 2017-03-30 2019-11-19 杰富意钢铁株式会社 Hot pressed member and its manufacturing method
CN111394658A (en) * 2020-04-22 2020-07-10 马鞍山钢铁股份有限公司 980 MPa-grade cold-rolled Q & P steel suitable for conventional continuous annealing production line and manufacturing method thereof
CN111455282B (en) * 2020-05-11 2021-03-16 武汉钢铁有限公司 Quenching distribution steel with tensile strength more than or equal to 1500MPa produced by adopting short process and method
CN113388773A (en) * 2021-05-21 2021-09-14 鞍钢股份有限公司 1.5GPa grade high-formability hydrogen-embrittlement-resistant ultrahigh-strength automobile steel and preparation method thereof
CN113718168A (en) * 2020-05-25 2021-11-30 宝山钢铁股份有限公司 High-strength cold-rolled steel plate and manufacturing method thereof

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CN101932744A (en) * 2008-01-31 2010-12-29 杰富意钢铁株式会社 High-strength hot-dip galvanized steel sheet with excellent processability and process for producing the same
WO2013018722A1 (en) * 2011-07-29 2013-02-07 新日鐵住金株式会社 High-strength zinc-plated steel sheet and high-strength steel sheet having superior moldability, and method for producing each
CN103160735A (en) * 2011-12-14 2013-06-19 鞍钢股份有限公司 Ultrahigh strength cold-rolled steel sheet for automobile and production method thereof

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CN101487096A (en) * 2009-02-19 2009-07-22 北京科技大学 Low-alloy high-strength C-Mn-Al Q & P steel and method of manufacturing the same
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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2017053001A (en) * 2015-09-09 2017-03-16 新日鐵住金株式会社 Galvanized steel sheet, galvannealed steel sheet, and their production methods
CN106811698A (en) * 2015-12-02 2017-06-09 鞍钢股份有限公司 A kind of high strength steel plate and its manufacture method based on tissue precise controlling
JP2019505690A (en) * 2015-12-21 2019-02-28 アルセロールミタル Method for producing a high strength steel sheet having improved ductility and formability and the resulting steel sheet
CN109477182B (en) * 2016-08-03 2021-06-18 株式会社神户制钢所 High-strength steel sheet and method for producing same
CN109477182A (en) * 2016-08-03 2019-03-15 株式会社神户制钢所 High-strength steel sheet and its manufacturing method
CN110475891A (en) * 2017-03-30 2019-11-19 杰富意钢铁株式会社 Hot pressed member and its manufacturing method
CN110475891B (en) * 2017-03-30 2021-03-12 杰富意钢铁株式会社 Hot-pressed member and method for manufacturing same
CN109694992A (en) * 2017-10-20 2019-04-30 鞍钢股份有限公司 A kind of tensile strength is greater than the quenching partition steel and its production method of 1500MPa
CN111394658A (en) * 2020-04-22 2020-07-10 马鞍山钢铁股份有限公司 980 MPa-grade cold-rolled Q & P steel suitable for conventional continuous annealing production line and manufacturing method thereof
CN111455282B (en) * 2020-05-11 2021-03-16 武汉钢铁有限公司 Quenching distribution steel with tensile strength more than or equal to 1500MPa produced by adopting short process and method
CN113718168A (en) * 2020-05-25 2021-11-30 宝山钢铁股份有限公司 High-strength cold-rolled steel plate and manufacturing method thereof
CN113388773A (en) * 2021-05-21 2021-09-14 鞍钢股份有限公司 1.5GPa grade high-formability hydrogen-embrittlement-resistant ultrahigh-strength automobile steel and preparation method thereof
CN113388773B (en) * 2021-05-21 2022-07-22 鞍钢股份有限公司 1.5GPa grade high-formability hydrogen-embrittlement-resistant ultrahigh-strength automobile steel and preparation method thereof

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