CN105420605A - Ultralow-yield-ratio cold-rolled dual-phase steel and manufacturing method thereof - Google Patents
Ultralow-yield-ratio cold-rolled dual-phase steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention belongs to the technical field of steel materials, and relates to an ultralow-yield-ratio cold-rolled dual-phase steel and a manufacturing method thereof. Internal control chemical components of the dual-phase steel comprise 0.13%-0.18% of C, 0.30%-0.60% of Si, 1.7%-2.0% of Mn, 0.02%-0.070% of Al, 0.02%-0.05% of Nb and the balance Fe and other inevitable impurities. Simple chemical component design is adopted, the hot-rolling deformation heat treatment TMCP and the flexible continuous annealing process are combined to obtain a microscopic structure with fine grain ferrite, island martensite and 5%-7% of retained austenite, and therefore the uniform deformation capacity of materials is increased while the strong plasticity of the cold-rolled dual-phase steel is improved. The ultralow-yield-ratio cold-rolled dual-phase steel has the beneficial effects that good stamping performance, low process sensitivity and the ultralow yield ratio YS/TS which is smaller than or equal to 0.51 are achieved, springback generated after stamping can be reduced, and later deep machining of the automobile industry is facilitated.
Description
Technical field
The invention belongs to steel material technical field, in particular, provide a kind of ultralow yield tensile ratio cold-rolled biphase steel DP780 and manufacture method thereof, punching performance is excellent, microstructure is controlled by flexible continuous annealing process parameter, thus while the strong plasticity of raising cold-rolled biphase steel, obtain ultralow yield tensile ratio, be beneficial to the deep processing of follow-up automobile industry.
Background technology
In recent years, along with increasingly sharpening of global energy and ecocrisis, energy-saving and emission-reduction have become the important topic that contemporary automotive Design and manufacture faces.What simultaneously the development of Vehicle mass reduction and passenger safety required improves constantly, 800MPa and other ultrahigh-strength steel of higher level are more and more applied in intermediate car structural part and stiffener, to reach energy-saving and emission-reduction and to improve complete automobile collision security impact.And cold-rolled biphase steel because of its have that yield strength is low, tensile strength is high, work hardening capacity is strong, breaking elongation and uniform elongation greatly, the plurality of advantages such as easily stamping, good plasticity and toughness coupling, the extremely favor of automotive industry circle.In " ULSAB " project that 1994-1998 years implement, the rate of utilization of the high tensile steel plate on car body and advanced High Strength Steel Plate reaches 90%, and wherein the rate of utilization of dual phase steel is 22%.(FSV) project that at the beginning of 2011, IISI also been proposed " following steel vehicle body ", the rate of utilization of high-strength steel and AHSS reaches 97%, and the rate of utilization of dual phase steel then reaches 31%.In recent years, international automobile manufacturer is in vehicle newly developed, the ratio of application ultra-high strength steel plate reaches about 20%, vehicle of winning international prize high tensile steel plate usage ratio is generally about 70%, and domestic Europe, the United States, system of Japan and Korea S. and independent brand new model high tensile steel plate employing rate also increase year by year.
The principal feature of 800MPa level cold-rolled biphase steel in chemical composition is low-carbon and low-alloy both at home and abroad at present.Main alloy element is based on Si, Mn, according to production technique and service requirements difference, also add the elements such as appropriate Cr, Mo, V, Nb, constituting with Si-Mn system, Si-Mn-Cr system, Si-Mn-Nb system, Si-Mn-V system, Mn-Mo system, Si-Mn-Cr-V system and Mn-Si-Cr-Mo is main dual phase steel series.But Mo element is expensive, production cost is high, wherein Si-Mn-Cr system is most widely used, but adding of Cr alloying element makes process window narrower, add the difficulty of technology controlling and process in production process, require higher to capacity of equipment and level of control, the impact of fluctuation on final performance of technique is larger, this is disadvantageous to impact briquetting, is unfavorable for suitability for industrialized production.Si-Mn system hardening capacity is poor, connects and moves back rapid cooling section cooling rate not, thus easily there is a small amount of bainite, affect forming property.Add the precipitation strength effect that Nb, V produce, while increase tensile strength, yield strength also significantly increases simultaneously.In order to control yield strength and reduce resilience, need to improve and optimize continuous annealing process parameter, thus best mechanical property could be obtained.The patent about cold-rolled biphase steel DP780 retrieved by sci-tech novelty-search is as follows:
Table 1 both at home and abroad DP780 patent contrasts with the present invention
The present invention is compared with other inventions of announcing (table 1), and composition is simple, and the low manganese of low-carbon (LC) adds a small amount of Nb.Process window is wide, and containing a small amount of remaining entity difficult to understand in tissue, reduces yield tensile ratio, improve rebound performance and punching performance, improve the over-all properties of dual phase steel.
Summary of the invention
The object of the present invention is to provide a kind of ultralow yield tensile ratio cold-rolled biphase steel DP780 and manufacture method thereof.Achieve low cost, low yield strength, low yield strength ratio, high-elongation and forming property good.
The present invention adopts simple chemical composition design, in conjunction with hot rolling thermomechanical treatment TMCP technique, flexible continuous annealing process obtain fine ferrite grain, island-like martensite and 5 ~ 7% the microstructure of residual austenite, thus yield tensile ratio is reduced while the strong plasticity of raising cold-rolled biphase steel, be convenient to follow-up impact briquetting.
The present invention adopts phase transformation strengthening to be main when Composition Design, in conjunction with the complex intensifying mode of solution strengthening, refined crystalline strengthening, precipitation strength.By analyzing the effect of each main alloy element and the impact on transformation behavior, consider the factors such as easy-formation, low resilience, high-strength plasticity, good welding property, low cost when Composition Design simultaneously.Cold-rolled biphase steel DP780 containing residual austenite of the present invention mainly considers that the alloying element added has C, Si, Mn, Al, Nb etc.Internal control chemical composition C0.13 ~ 0.18% of this 780MPa level good stamping performance, low process sensitivity, ultralow yield tensile ratio (YS/TS≤0.5) cold-rolled biphase steel DP780, Si0.30 ~ 0.60%, Mn1.7 ~ 2.0%, Al0.02%-0.070%, Nb0.02 ~ 0.05%, surplus is Fe and other inevitable impurity.Smelt into qualified strand.
Common process is adopted during cold-rolled biphase steel hot rolling of the present invention, steel billet is heated to 1150 ~ 1250 DEG C with stove, insulation 1.5 ~ 3h, carry out hot rolling subsequently, it is 1050 ~ 1100 DEG C that roughing start rolling temperature controls, it is 950 ~ 1000 DEG C that finish rolling start rolling temperature controls, and finish rolling finishing temperature control is 850 ~ 880 DEG C, and oiler temperature control is 640 ~ 680 DEG C.
Cold-rolled biphase steel plate carries out pickling, cold rolling, and cold rolling accumulation draft 50 ~ 70%, is rolled into the steel plate that thickness is 0.8-1.5mm, but is not limited thereto thickness;
Cold-rolled biphase steel plate carries out continuous annealing: in continuous annealing process, first at 780-840 DEG C of temperature, isothermal keeps 90 ~ 120s, through the slow cooling time of 20 ~ 30s, progressively cool to 680 ~ 740 DEG C, then cooling rate is controlled within the scope of 45≤Vc≤66 DEG C/s, be quickly cooled to martensite point below Ms, about 270-330 DEG C, continues isothermal at such a temperature and keeps 300-450s; Whole deepfreeze temperature is 100 ~ 170 DEG C, and the time is 100 ~ 130s, is then chilled to room temperature.
Finished product aligning unit elongation≤1.0%;
The microstructure characteristic of cold-rolled biphase steel is, ferrite (α)+martensite (M) becomes ferrite (α)+martensite (M)+5 ~ 7% residual austenite (RA.), the plasticity obtained while obtaining high strength and ultralow yield tensile ratio.
The mechanical property of dual phase steel annealed sample: wherein Rel=389 ~ 435MPa, Rm=830 ~ 882MPa, YS/TS=0.44 ~ 0.51, A
50=20 ~ 22.3%, Agt=11.5 ~ 15.5%, n=0.17 ~ 0.21, r=0.68 ~ 0.98.Yield tensile ratio is all in the lower scope of 0.4 ~ 0.51, and the Mechanical Fluctuation of each embodiment steel is little, and annealing process susceptibility is not strong, and process window is wide, is suitable for suitability for industrialized production.
Adopt opticmicroscope to carry out observation to the microstructure of embodiments of the invention cold-rolled biphase steel to find, it is organized as the duplex structure of typical ferrite+island-like martensite+a small amount of residual austenite, organizes grain fineness number to be 11 ~ 12 grades.
Embodiment and accompanying drawing display, cold-rolled biphase steel of the present invention has high, the ultralow yield tensile ratio of initial manufacture cementation index, avoid strain cracking and the excellent punching performance such as piece surface is wrinkling, vehicle body collision safety part and inner structural members can be widely used in, and reach loss of weight, reduce discharging energy-conservation effect.Along with the development of automotive light weight technology, this steel has good market outlook.
Major technique innovative point of the present invention is as follows:
1. present method composition system is simple, and C-Si-Mn set member basis adopts Nb microalloy treatment; Suitable crystal grain thinning while improving the martensite content in steel, ensures that dual phase steel DP780 has good comprehensive mechanical property.
2. present method is by flexible continuous annealing process technology, introduce a certain amount of (about 5 ~ 7%) residual austenite, make two-phase steel organization become ferrite (α)+martensite (M)+residual austenite (RA.) from traditional ferrite (α)+martensite (M).There is TRIP effect under utilizing the residual austenite of 5 ~ 7% to be organized in stress, the processability and rebound performance improving material is played an important role.
3. annealing process susceptibility is not strong, and two-phase region annealing temperature can reach the requirement of mechanical property in 780-840 DEG C of wide temperature range, and process window is wide, is suitable for suitability for industrialized production.
4. DP780 of the present invention has the performance characteristics such as ultralow yield tensile ratio, high elongation rate, high-strain hardening ability, high n-value, each side high comprehensive performance.Wherein Rel=389 ~ 435MPa, Rm=830 ~ 882MPa, YS/TS=0.44 ~ 0.51, A
50=20 ~ 22.3%, Agt=11.5 ~ 15.5%, n=0.17 ~ 0.21, r=0.68 ~ 0.98.
Accompanying drawing explanation
Metallographic pattern (500 ×) when Fig. 1 is sample critical annealing temperature Ta=780 DEG C after the corrosion of nitric acid alcohol.
Colour metallograpy pattern (500 ×) when Fig. 2 is sample critical annealing temperature Ta=780 DEG C.
Colour metallograpy pattern (500 ×) when Fig. 3 is sample critical annealing temperature Ta=800 DEG C.
Residual austenite SEM pattern and distribution (paralympic size about 1.3 μm) when Fig. 4 is critical annealing temperature Ta=780 DEG C.
Residual austenite SEM pattern and distribution (paralympic size about 0.7 μm when Fig. 5 is critical annealing temperature Ta=820 DEG C; ).
The photo ((wherein red is BCC phase: 98.4%, and blueness is FCC phase (i.e. residual austenite RA): 2.3%)) of the residual austenite Entropy density deviation figure that EBSD measures when Fig. 6 is annealing temperature 820 DEG C.
Fig. 7 is the content of residual austenite under different annealing temperature condition.
Embodiment
Embodiment 1:
The DP780 level cold-rolled biphase steel of trial-production, owing to being introduce a small amount of residual austenite in the microstructure of essential characteristic at ferrite matrix and martensite island, thus ensure that while intensity rank reaches similar Iron And Steel Company level, unit elongation A
50stablize and bring up to more than 20% (A
80>=18%), ultralow yield tensile ratio 0.44 ~ 0.45.Its method of manufacturing technology is as follows:
1) smelt also continuous casting and become base, the component of strand and weight percent content: C:0.16%, Mn:1.81%, Si:0.47%, Al:0.058%, P:0.0069%, S:0.0038%, Nb0.04%, surplus is Fe and inevitable impurity;
2) carry out hot rolling to after strand conventional heating, rolling adds up pressure 86%, hot-rolled finished product thickness 5.0mm, controls finishing temperature at 850 ~ 880 DEG C;
3) batch, control coiling temperature at 670 DEG C;
4) conventional pickling is carried out;
5) carry out cold rolling, controlling cold rolling accumulative draft is 70%, is rolled into the steel plate that thickness is 1.5mm;
6) carry out continuous annealing, control annealing temperature at 760 ~ 840 DEG C, annealing time 90 ~ 120 seconds;
7) under slow cooling speed is 3 ~ 6 DEG C/s, 680 ~ 720 DEG C are cooled to;
8) cool fast, speed of cooling controls 45≤Vc≤60 DEG C/s, and cooling temperature is at 270 ~ 330 DEG C;
9) Wetted constructures is carried out, overaging temperature 280 ~ 320 DEG C, overaging time 410 ~ 420s;
10) with the cooling rate slow cooling of 5 DEG C/s to 170 DEG C;
11) adopt cooling by water to room temperature.
Embodiment 2:
1) smelt also continuous casting and become base, the component of strand and weight percent content: C:0.13%, Mn:1.7%, Si:0.43%, Al:0.04%, P:0.0068%, S:0.0079%, N:0.0043%, Nb0.028%, surplus is Fe and inevitable impurity;
2) carry out hot rolling to after strand conventional heating, rolling adds up pressure 90%, hot-rolled finished product thickness 4.5mm, controls finishing temperature at 850 ~ 880 DEG C;
3) batch, control coiling temperature at 670 DEG C;
4) conventional pickling is carried out;
5) carry out cold rolling, controlling cold rolling accumulative draft is 66.7%, is rolled into the steel plate that thickness is 1.5mm;
6) carry out continuous annealing, control annealing temperature at 800 ~ 840 DEG C, annealing time 90 ~ 120 seconds;
7) under slow cooling speed is 3 ~ 5 DEG C/s, 700 ~ 740 DEG C are cooled to;
8) cool fast, speed of cooling controls at 60 ~ 66 DEG C/s, and cooling temperature is at 300 ~ 330 DEG C;
9) Wetted constructures is carried out, overaging temperature 300 ~ 320 DEG C, overaging time 420s;
10) with the cooling rate slow cooling of 5 DEG C/s to 170 DEG C;
11) adopt cooling by water to room temperature.
The actual mechanical property of table 2 the present invention
The microstructure of DP800 forms (xrd method), paralympic size about 0.7 ~ 1.3 μm primarily of 40 ~ 60% ferrites, 35 ~ 53% martensites, 5 ~ 7% residual austenites.Table 2 is the actual mechanical properties of the present invention.More conventional 0.54 ~ 0.65 low of dual phase steel yield tensile ratio (0.44 ~ 0.51) of the present invention, A
80unit elongation, higher than the unit elongation about 4 ~ 5% of common process, is easy to deep processing and impact briquetting.
Main result
The present invention mainly adopts simple chemical composition design, in conjunction with obtain under hot rolling thermomechanical treatment TMCP technique, wider flexible continuous annealing process window considerations fine ferrite grain, island-like martensite and 5 ~ 7% the microstructure of residual austenite, thus ensure that and reach similar Iron And Steel Company level, unit elongation A at intensity rank
50stablize and bring up to more than 20%.The DP800 simultaneously developed has the performance characteristics such as ultralow yield tensile ratio (YS/TS=0.44 ~ 0.51), higher n value, Mechanical Fluctuation scope be little, thus yield strength and yield tensile ratio is reduced while the strong plasticity of raising cold-rolled biphase steel, be convenient to follow-up impact briquetting.
Claims (2)
1. a ultralow yield tensile ratio cold-rolled biphase steel, is characterized in that: chemical composition is C0.13 ~ 0.18%, Si0.30 ~ 0.60%, Mn1.7 ~ 2.0%, Al0.02%-0.070%, Nb0.02 ~ 0.05%, and surplus is Fe and other inevitable impurity;
The microstructure of cold-rolled biphase steel: ferrite α+martensite M becomes ferrite α+martensite M+5 ~ 7% residual austenite RA;
The mechanical property of dual phase steel annealing: wherein Rel=389 ~ 435MPa, Rm=830 ~ 882MPa, YS/TS=0.44 ~ 0.51, A50=20 ~ 22.3%, Agt=11.5 ~ 15.5%, n=0.17 ~ 0.21, r=0.68 ~ 0.98; Yield tensile ratio is all in 0.44 ~ 0.51 scope.
2. a manufacture method for ultralow yield tensile ratio cold-rolled biphase steel according to claim 1, adopts common process during cold-rolled biphase steel hot rolling; It is characterized in that,
(1) steel billet is heated to 1150 ~ 1250 DEG C with stove, insulation 1.5 ~ 3h, carries out hot rolling subsequently, it is 1050 ~ 1100 DEG C that roughing start rolling temperature controls, it is 950 ~ 1000 DEG C that finish rolling start rolling temperature controls, and finish rolling finishing temperature control is 850 ~ 880 DEG C, and oiler temperature control is 640 ~ 680 DEG C;
(2) cold-rolled biphase steel plate carries out pickling, cold rolling, and cold rolling accumulation draft 50 ~ 70%, is rolled into the steel plate that thickness is 0.8-1.5mm;
(3) cold-rolled biphase steel plate carries out continuous annealing: in continuous annealing process, first at 780-840 DEG C of temperature, isothermal keeps 90 ~ 120s, through the slow cooling time of 20 ~ 30s, progressively cool to 680 ~ 740 DEG C, then cooling rate is controlled within the scope of 45≤Vc≤66 DEG C/s, be quickly cooled to martensite point below Ms, about 270-330 DEG C, continues isothermal at such a temperature and keeps 300-450s; Whole deepfreeze temperature is 100 ~ 170 DEG C, and the time is 100 ~ 130s, is then chilled to room temperature;
Finished product aligning unit elongation≤1.0%;
The microstructure of cold-rolled biphase steel: ferrite α+martensite M becomes ferrite α+martensite M+5 ~ 7% residual austenite RA,
The mechanical property of dual phase steel annealing: wherein Rel=389 ~ 435MPa, Rm=830 ~ 882MPa, YS/TS=0.44 ~ 0.51, A50=20 ~ 22.3%, Agt=11.5 ~ 15.5%, n=0.17 ~ 0.21, r=0.68 ~ 0.98; Yield tensile ratio is all in 0.44 ~ 0.51 scope.
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| CN106755867A (en) * | 2016-12-01 | 2017-05-31 | 首钢总公司 | A kind of hot dip galvanized dual phase steel surface treatment method |
| CN107058869A (en) * | 2017-05-22 | 2017-08-18 | 钢铁研究总院 | Ultralow yield tensile ratio 980MPa grades of cold-rolled biphase steels and its manufacture method |
| 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 |
| CN109328240A (en) * | 2016-07-01 | 2019-02-12 | 株式会社Posco | The high-strength steel sheet and its manufacturing method of low yield strength ratio characteristic and excellent in low temperature toughness |
| CN109371317A (en) * | 2018-09-25 | 2019-02-22 | 邯郸钢铁集团有限责任公司 | A kind of 1000MPa grades of ultrafast cold cold-rolled biphase steel plate and preparation method thereof |
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| CN111826507A (en) * | 2020-06-19 | 2020-10-27 | 华菱安赛乐米塔尔汽车板有限公司 | Ultrahigh-yield-ratio steel and production process thereof |
| CN113737086A (en) * | 2020-05-27 | 2021-12-03 | 宝山钢铁股份有限公司 | Economical 780 MPa-grade cold-rolled annealed dual-phase steel and manufacturing method thereof |
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000355735A (en) * | 1999-06-15 | 2000-12-26 | Nippon Steel Corp | Hot rolled high strength steel sheet small in variation of material and excellent in workability and its production |
| US20100000634A1 (en) * | 2006-11-14 | 2010-01-07 | Salzgitter Flachstahl Gmbh | Process for producing a steel strip comprising a relatively high strength dual phase steel |
| CN104862597A (en) * | 2015-05-27 | 2015-08-26 | 钢铁研究总院 | Method for improving elongation of cold-rolled dual-phase steel by utilizing retained austenite |
-
2015
- 2015-11-30 CN CN201510860653.1A patent/CN105420605A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2000355735A (en) * | 1999-06-15 | 2000-12-26 | Nippon Steel Corp | Hot rolled high strength steel sheet small in variation of material and excellent in workability and its production |
| US20100000634A1 (en) * | 2006-11-14 | 2010-01-07 | Salzgitter Flachstahl Gmbh | Process for producing a steel strip comprising a relatively high strength dual phase steel |
| CN104862597A (en) * | 2015-05-27 | 2015-08-26 | 钢铁研究总院 | Method for improving elongation of cold-rolled dual-phase steel by utilizing retained austenite |
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| CN109328240B (en) * | 2016-07-01 | 2022-05-17 | 株式会社Posco | High-strength steel sheet having low yield ratio characteristics and excellent low-temperature toughness, and method for manufacturing same |
| CN106755867A (en) * | 2016-12-01 | 2017-05-31 | 首钢总公司 | A kind of hot dip galvanized dual phase steel surface treatment method |
| CN107058869A (en) * | 2017-05-22 | 2017-08-18 | 钢铁研究总院 | Ultralow yield tensile ratio 980MPa grades of cold-rolled biphase steels and its manufacture method |
| CN107058869B (en) * | 2017-05-22 | 2019-05-31 | 钢铁研究总院 | Ultralow yield tensile ratio 980MPa grades of cold-rolled biphase steels and its manufacturing method |
| CN109794729A (en) * | 2017-11-16 | 2019-05-24 | 上海汇众汽车制造有限公司 | The production method of 800MPa high intensity torsion beam crossbeam |
| 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 |
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| CN109371317A (en) * | 2018-09-25 | 2019-02-22 | 邯郸钢铁集团有限责任公司 | A kind of 1000MPa grades of ultrafast cold cold-rolled biphase steel plate and preparation method thereof |
| CN109536851A (en) * | 2019-01-24 | 2019-03-29 | 本钢板材股份有限公司 | A kind of cold rolling quenching partition steel plate and preparation method thereof |
| CN109988969A (en) * | 2019-04-01 | 2019-07-09 | 山东钢铁集团日照有限公司 | A kind of cold rolling Q&P1180 steel and its production method with different yield tensile ratios |
| CN109988969B (en) * | 2019-04-01 | 2021-09-14 | 山东钢铁集团日照有限公司 | Cold-rolled Q & P1180 steel with different yield ratios and production method thereof |
| CN113737086A (en) * | 2020-05-27 | 2021-12-03 | 宝山钢铁股份有限公司 | Economical 780 MPa-grade cold-rolled annealed dual-phase steel and manufacturing method thereof |
| CN111826507B (en) * | 2020-06-19 | 2021-12-03 | 华菱安赛乐米塔尔汽车板有限公司 | Production process of steel with ultrahigh yield ratio |
| CN111826507A (en) * | 2020-06-19 | 2020-10-27 | 华菱安赛乐米塔尔汽车板有限公司 | Ultrahigh-yield-ratio steel and production process thereof |
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| CN115522131B (en) * | 2022-10-13 | 2023-12-05 | 武汉科技大学 | 1000 MPa-grade hot-rolled dual-phase steel and preparation method and application thereof |
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Application publication date: 20160323 |