CN101781739A - Automobile cold-rolled dual-phase steel with tensile strength of 500 MPa - Google Patents
Automobile cold-rolled dual-phase steel with tensile strength of 500 MPa Download PDFInfo
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Abstract
The invention relates to automobile ferrite-martensite cold-rolled dual-phase steel with tensile strength of 500 MPa. The automobile cold-rolled dual-phase steel with tensile strength of 500 MPa comprises the following chemical components in percentage by weight: 0.05 to 0.2 percent of C, 0.02 to 0.049 percent of Si, 0.5 to 2.0 percent of Mn, 0.1 to 0.5 percent of Cr, 0.01 to 0.1 percent of Als, 0.003 to 0.01 percent of P, 0.003 to 0.01 percent of S, 0.003 to 0.01 percent of N, and the balance of Fe and inevitable impurities. After a steel plate is rolled by a conventional cold-rolled dual-phase steel hot rolling mill and a cold rolling mill, the mechanical properties of the steel plate comprise that: Rp0.2 is between 300 and 350 MPa, Rm is between 520 and 5,600 MPa, A80mm is between 27 and 32 percent, n is between 0.18 and 0.19, and BH2 is between 40 and 55 MPa. The steel has the advantages of low cost, stable process and good forming property, thereby ensuring that the steel plate has excellent surface quality and completely meets the requirements of automobile manufacturer.
Description
Technical field
The present invention relates to automobile steel, the automobile that specifically belongs to tensile strength and be the 500MPa level is with ferrite and martensite cold-rolled biphase steel.
Background technology
Along with the continuous development of body lightening and improving constantly of passenger safety requirement, car manufacturing enterprise more and more adopts the above advanced high-strength steel of intensity rank 500MPa level, and the consumption of at present external high-grade car high-strength steel has reached more than 70%.Dual phase steel becomes iron and steel enterprise's high-strength steel hot of research and development in view of it has good intensity and good plasticity.At present external iron and steel enterprise and some domestic iron and steel enterprises have all carried out the exploitation of the dual phase steel of different stage.
The patent Query Result of dual phase steel shows that iron and steel enterprise mainly adopts Si, Mn system at the composition design aspect of dual phase steel at present, adds the requirement that alloying elements such as proper C r, V, Nb, Mo, Ti, B satisfy varying strength simultaneously both at home and abroad.And Si content general requirement is 0.4%～1.0% in the composition of these dual phase steels design, even higher.For example the Si-Mn-Cr-Mo on probation of U.S. motor corporation is that the composition of 500MPa level dual phase steel is C=0.06%, Si=1.35%, and Mn=0.09%, Cr=0.50%, Mo=0.35, alloying element content height such as Cr, Mo, cost of alloy increases greatly; The dual phase steel patent main component of U.S. Iron And Steel Company application is C=0.02%～0.2%, Al=0.01%～0.15%, Si≤0.5%, Mn=0.8%～2.4%, Cr=0.03%～1.5%, Mo=0.03%～1.5%, alloying element content height such as Cr, Mo, cost of alloy increases greatly; The Si-Mn-V of certain Iron And Steel Company's exploitation of Europe is that the composition of 500MPa level dual phase steel is C=0.12%, Si=0.50%, Mn=1.25%, V=0.1%; " a kind of tensile strength 540MPa level dual phase sheet steel and manufacture method thereof " patent design mix of domestic certain university is: C=0.05%～0.08%, Si=0.20%～0.4%, Mn=1.00%～1.30%; The dual phase steel composition of domestic certain Iron And Steel Company's exploitation is designed to C=0.05%～0.13%, Si=0.80%～1.2%, Mn=1.9%～2.3%.Contrast can be found, the high silicon composition design of the many employings of the composition of cold-rolled biphase steel design at present both at home and abroad.Actual industrial production both at home and abroad shows that too high Si content will cause steel plate to produce in process of production such as surface quality problems such as hot-rolled sheet surface red phosphorus phenomenon, galvanized sheet surface plating leakages, thereby causes the production difficulty to strengthen and the quality product reduction; The surface quality defect of steel plate can cause detrimentally affect to the surface quality of user's finished product simultaneously.Simultaneously,, cause the production cost of steel plate to increase greatly, reduced the economy of product owing to added high price alloys such as Mo, V in the part steel plate.
Summary of the invention
The objective of the invention is to overcome above-mentioned deficiency, a kind of Si content in the steel that passes through to reduce on the basis of C-Mn steel is provided, the an amount of automobile cold-rolled dual phase steel of 500MPa level that adds the Cr alloy, its tensile strength height, yield tensile ratio is low, and obdurability matches, and punching performance is good, initial manufacture cementation index height can be avoided the surface quality problems of the automobile steel that causes because of silicone content is too high in the actual industrial production.
Realize the technical measures of above-mentioned purpose:
Automobile cold-rolled dual-phase steel with tensile strength of 500 MPa, its chemical composition and weight percent are: C:0.05%～0.2%, Si:0.02%～0.049%, Mn:0.5%～2.0%, Cr:0.1%～0.5%, Als:0.01%～0.1%, P:0.003%～0.01%, S:0.003%～0.01%, N:0.003%～0.01%, all the other are Fe and unavoidable impurities.
Its optimization: the weight percent of C is: 0.05%～0.15%.
Its optimization: the weight percent of Cr is: 0.15%～0.3%.
Its optimization: the weight percent of Mn is: 1.0%～1.8%.
The mechanism of action of each alloy ingredient is as follows among the present invention:
C: being the most effective strengthening element, is to form martensitic principal element, and carbon content has determined the hardness and the martensitic pattern of dual phase steel in the steel; But, guarantee that steel has high unit elongation and good weldability, require lower carbon content, so the weight percent of C is controlled at 0.05%～0.20% low scope among the present invention.
Mn: belong to typical austenite stabilizer element, significantly improve the hardening capacity of steel, and play the effect of solution strengthening and refinement ferrite crystal grain, can significantly postpone perlitic transformation and bainite transformation.But Mn when high manganese content is being postponed perlitic transformation, also can postpone ferritic separating out as the element that enlarges the austenitic area; And the too low perlitic transformation that causes easily of manganese content, so Mn weight percentage of the present invention is controlled at 0.5%～2.0%.
Si: ferritic solution strengthening element, quicken carbon to austenitic poly-partially, the solid solution carbon in the ferrite is had remove and cleaning action, help to improve the ductility of dual phase steel.But, reduce the silicone content in the steel, so Si weight percentage of the present invention is controlled at 0.02%～0.049% for fear of because of the Si too high levels influences plate surface quality at the refractory oxide that surface of steel plate forms as far as possible.
Cr: middle strong carbide forming element, significantly improve the hardening capacity of steel, can postpone perlitic transformation and bainite transformation strongly, and enlarge and batch window.Though Cr is weak solution strengthening element, can increase austenitic cold energy power excessively, thereby thinning microstructure plays strengthening effect.So Cr weight percent content of the present invention is controlled at 0.1%～0.5%.
Als:Al role in dual phase steel is similar to Si, and while Al also can form AlN and separate out, and plays certain crystal grain thinning effect.Because silicone content is low in the dual phase steel of the present invention, so the existence of small amount of aluminum, under the prerequisite of proof strength performance, the ductility of dual phase steel is improved.The Al weight percent content is controlled at 0.01%～0.1% among the present invention.
P, S: detrimental impurity is to the detrimentally affect of the punching performance of steel in the steel in order to reduce, and P, the S content in the steel is controlled in strictness.
The present invention compared with prior art, its characteristics: because that the Si alloy content is gone up in composition design is few, having improved high silicon is a series of surface quality problems that cause because of silicon oxidation in the dual phase steel production process.Have the tensile strength height on the mechanical property, yield tensile ratio is low, and strength and toughness matches, and the impact briquetting performance is good, initial manufacture cementation index height, and have good collision energy-absorbing, be applicable to collision safety spare and the high-strength structural safety part of making vehicle body.Simultaneously, cost of alloy of the present invention is low, and the preparation method is simple, is fit to suitability for industrialized production.
Embodiment
Be described in detail below:
Experiment condition of the present invention: adopt the 50Kg vacuum oven to test the smelting of steel; Adopt conventional cold-rolled biphase steel hot rolling mill and cold rolling mill to carry out the rolling of steel plate, obtain the thick chill attitude cold-reduced sheet of 1.5mm.
The chemical ingredients of specific embodiment of the invention steel is stated table 1 as follows.
Table 1: the chemical ingredients of specific embodiment of the invention steel (wt%)
| Embodiment number | ??C | ??Si | ??Mn | ??Cr | ??P | ??S | ??Als |
| ??1 | ??0.05 | ??0.025 | ??2.00 | ??0.20 | ??0.017 | ??0.005 | ??0.010 |
| ??2 | ??0.08 | ??0.032 | ??0.95 | ??0.50 | ??0.011 | ??0.005 | ??0.025 |
| ??3 | ??0.11 | ??0.038 | ??1.80 | ??0.10 | ??0.014 | ??0.006 | ??0.038 |
| ??4 | ??0.12 | ??0.041 | ??1.00 | ??0.35 | ??0.016 | ??0.005 | ??0.052 |
| ??5 | ??0.06 | ??0.049 | ??1.40 | ??0.45 | ??0.025 | ??0.010 | ??0.066 |
| ??6 | ??0.20 | ??0.045 | ??0.50 | ??0.10 | ??0.009 | ??0.006 | ??0.079 |
| ??7 | ??0.15 | ??0.020 | ??1.23 | ??0.15 | ??0.022 | ??0.008 | ??0.091 |
| ??8 | ??0.10 | ??0.035 | ??1.60 | ??0.20 | ??0.020 | ??0.004 | ??0.100 |
The hot dip process simulation test machine of the German IWATANI company of the test steel plate of embodiment through introducing carries out annealing test, and sample is quickly cooled to room temperature with 30 ℃/second and above speed of cooling after the slow cooling to 650 ℃ behind 780～820 ℃ of insulation 100s; Adopt the mechanics tensile testing machine that the mechanical property of steel plate is checked, adopt DIN EN 10002-2 standard test specimen.
Yield strength R to the dual phase steel product of eight embodiment of the present invention
P0.2(MPa), tensile strength R
m(MPa), yield tensile ratio R
P0.2/Rm, unit elongation A
80mm%, work hardening exponent n
10-UEValue, baking hardening value BH
2(MPa) etc. mechanical property detects, and the results are shown in Table 2.
Table 2: embodiment of the invention steel product mechanical property detected result:
| Embodiment number | ??R p0.2??(MPa) | ??R m??(MPa) | ??R p0.2/R m | ??A 80mm??％ | ??n 10-UE | ??BH 2??(MPa) |
| ??1 | ??300 | ??520 | ??0.57 | ??27 | ??0.19 | ??46 |
| ??2 | ??325 | ??525 | ??0.61 | ??30 | ??0.19 | ??51 |
| ??3 | ??310 | ??535 | ??0.58 | ??32 | ??0.18 | ??40 |
| ??4 | ??330 | ??530 | ??0.62 | ??28 | ??0.18 | ??52 |
| ??5 | ??335 | ??520 | ??0.64 | ??30 | ??0.19 | ??50 |
| ??6 | ??340 | ??540 | ??0.62 | ??29 | ??0.18 | ??55 |
| Embodiment number | ??R p0.2??(MPa) | ??R m??(MPa) | ??R p0.2/R m | ??A 80mm??％ | ??n 10-UE | ??BH 2??(MPa) |
| ??7 | ??345 | ??545 | ??0.63 | ??29 | ??0.19 | ??50 |
| ??8 | ??350 | ??560 | ??0.62 | ??28 | ??0.19 | ??48 |
Be the mechanical property that the present invention manufactures experimently dual phase steel annealing sample: R
P0.2=300～350MPa, R
m=520～5600MPa, A
80mm=27%～32%, n=0.18～0.19, BH
2=40～55MPa.
The performance comparison of 500MPa level dual phase steel is as shown in table 3 in dual phase steel of the present invention and national standard and the European standard.
Table 3: the performance comparison of 500MPa level dual phase steel in the present invention and national standard and the European standard
| Standard category | ??R p0.2??MPa | ??R m??MPa | ??A 80mm??％ | ??n 10-UE | ??BH 2??MPa |
| Dual phase steel of the present invention | ??300～350 | ??≥500 | ??≥27 | ??≥0.17 | ??≥40 |
| ??GB/T2564.2-2006 | ??300～400 | ??≥500 | ??≥24 | ??- | ??- |
| ??prEN10336：2004 | ??290～370 | ??≥500 | ??≥24 | ??≥0.15 | ??≥30 |
| ??SEW097-2：2000 | ??300～350 | ??≥500 | ??≥24 | ??≥0.15 | ??≥30 |
Contrast finds that each index of the mechanical property of dual phase steel of the present invention all is higher than various countries' standard far away to its performance demands.
Adopt opticmicroscope that the microstructure of embodiments of the invention dual phase steel is observed discovery, the duplex structure that it is organized as typical ferrite+island martensite body, organizing grain fineness number is 10～11 grades.Adopt imager that the martensite degree in the tissue is analyzed discovery, the martensite degree in the 500MPa level dual phase steel of the present invention is about 10%～16%.
Experiment showed, 500MPa level dual phase steel of the present invention, cost of alloy is low, and technology stability is good, the product strength height, plasticity is good, and plate surface quality is good, satisfy the requirement of automobile production producer fully, can be widely used in vehicle body collision safety spare and inner structural members, had good market outlook.
Claims (4)
1. automobile cold-rolled dual-phase steel with tensile strength of 500 MPa, its chemical composition and weight percent are: C:0.05%～0.2%, Si:0.02%～0.049%, Mn:0.5%～2.0%, Cr:0.1%～0.5%, Als:0.01%～0.1%, P:0.003%～0.01%, S:0.003%～0.01%, N:0.003%～0.01%, all the other are Fe and unavoidable impurities.
2. automobile cold-rolled dual-phase steel with tensile strength of 500 MPa as claimed in claim 1 is characterized in that: the weight percent of C is: 0.05%～0.15%.
3. automobile cold-rolled dual-phase steel with tensile strength of 500 MPa as claimed in claim 1 is characterized in that: the weight percent of Cr is: 0.15%～0.3%.
4. automobile cold-rolled dual-phase steel with tensile strength of 500 MPa as claimed in claim 1 is characterized in that: the weight percent of Mn is: 1.0%～1.8%.
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Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101942603A (en) * | 2010-09-28 | 2011-01-12 | 北京科技大学 | 600 MPa-grade ultra-low-silicon cold-rolled hot-galvanized dual-phase steel and preparation process thereof |
| CN102703815A (en) * | 2012-06-19 | 2012-10-03 | 东北大学 | 600 MPa-grade hot-rolled dual-phase steel and preparation method thereof |
| CN102732791A (en) * | 2012-06-07 | 2012-10-17 | 河北钢铁股份有限公司邯郸分公司 | Production method of cold-rolled dual phase steel with tensile strength of 450MPa |
| CN103938070A (en) * | 2014-04-10 | 2014-07-23 | 马钢(集团)控股有限公司 | Steel plate and preparation method thereof |
| CN104313460A (en) * | 2014-10-13 | 2015-01-28 | 河北钢铁股份有限公司邯郸分公司 | 500MPa-grade cold rolling dual-phase steel and production method thereof |
| CN104328349A (en) * | 2014-11-14 | 2015-02-04 | 武汉钢铁(集团)公司 | High-strength medium-carbon low-silicon aluminum cold-rolled dual-phase steel and production method |
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| CN107267726A (en) * | 2017-06-06 | 2017-10-20 | 武汉钢铁有限公司 | The manufacture method of 450MPa grades of cold-rolled biphase steels of tensile strength |
| CN107267727A (en) * | 2017-06-06 | 2017-10-20 | 武汉钢铁有限公司 | The manufacture method of 500MPa grades of automobile exterior panel zn-fe alloy coating dual phase sheet steels |
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| CN1782116A (en) * | 2004-11-29 | 2006-06-07 | 宝山钢铁股份有限公司 | 800MPa cold rolled and hot zinc plated double phase steel and its producing method |
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Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN101942603A (en) * | 2010-09-28 | 2011-01-12 | 北京科技大学 | 600 MPa-grade ultra-low-silicon cold-rolled hot-galvanized dual-phase steel and preparation process thereof |
| CN102732791A (en) * | 2012-06-07 | 2012-10-17 | 河北钢铁股份有限公司邯郸分公司 | Production method of cold-rolled dual phase steel with tensile strength of 450MPa |
| CN102703815A (en) * | 2012-06-19 | 2012-10-03 | 东北大学 | 600 MPa-grade hot-rolled dual-phase steel and preparation method thereof |
| CN103938070B (en) * | 2014-04-10 | 2017-04-12 | 马钢(集团)控股有限公司 | Steel plate and preparation method thereof |
| CN103938070A (en) * | 2014-04-10 | 2014-07-23 | 马钢(集团)控股有限公司 | Steel plate and preparation method thereof |
| CN104313460A (en) * | 2014-10-13 | 2015-01-28 | 河北钢铁股份有限公司邯郸分公司 | 500MPa-grade cold rolling dual-phase steel and production method thereof |
| CN104328349B (en) * | 2014-11-14 | 2016-08-17 | 武汉钢铁(集团)公司 | The carbon system cold-rolled dual phase steel of low sial and production method in a kind of high intensity |
| CN104328349A (en) * | 2014-11-14 | 2015-02-04 | 武汉钢铁(集团)公司 | High-strength medium-carbon low-silicon aluminum cold-rolled dual-phase steel and production method |
| CN104593677A (en) * | 2015-01-19 | 2015-05-06 | 唐山钢铁集团有限责任公司 | Production process of heavy gauge hot-rolled dual-phase steel DP600 |
| CN107267726A (en) * | 2017-06-06 | 2017-10-20 | 武汉钢铁有限公司 | The manufacture method of 450MPa grades of cold-rolled biphase steels of tensile strength |
| CN107267727A (en) * | 2017-06-06 | 2017-10-20 | 武汉钢铁有限公司 | The manufacture method of 500MPa grades of automobile exterior panel zn-fe alloy coating dual phase sheet steels |
| CN108517468A (en) * | 2018-05-24 | 2018-09-11 | 山东钢铁集团日照有限公司 | A kind of economical cold-rolled biphase steel and its production method of steel multistage |
| CN108754307A (en) * | 2018-05-24 | 2018-11-06 | 山东钢铁集团日照有限公司 | A method of producing the economical cold rolling DP780 steel of different yield strength ranks |
| CN108754307B (en) * | 2018-05-24 | 2020-06-09 | 山东钢铁集团日照有限公司 | Method for producing economical cold-rolled DP780 steel with different yield strength grades |
| CN112391580A (en) * | 2020-11-09 | 2021-02-23 | 河钢股份有限公司承德分公司 | Titanium-reinforced 500 MPa-grade galvanized sheet hot-rolled base material and production method thereof |
| CN115074637A (en) * | 2022-06-25 | 2022-09-20 | 上海交通大学 | Ultrahigh-strength high-toughness superfine-structure low-carbon low-alloy steel and preparation method thereof |
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Open date: 20100721 |