CN104357740A - High-strength low-carbon high silicon manganese molybdenum niobium system cold-rolled dual phase steel and production method thereof - Google Patents
High-strength low-carbon high silicon manganese molybdenum niobium system cold-rolled dual phase steel and production method thereof Download PDFInfo
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- CN104357740A CN104357740A CN201410644803.0A CN201410644803A CN104357740A CN 104357740 A CN104357740 A CN 104357740A CN 201410644803 A CN201410644803 A CN 201410644803A CN 104357740 A CN104357740 A CN 104357740A
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention provides high-strength low-carbon high silicon manganese molybdenum niobium system cold-rolled dual phase steel. The steel comprises the following components in percentage by weight: 0.06-0.10 percent of C, 1.51-2.0 percent of Si, 1.5-2.5 percent of Mn, 0.01-0.10 percent of Mo, 0.01-0.05 percent of Nb, less than 0.005 percent of S, less than 0.01 percent of P and less than 0.01 percent of N. The preparation method comprises the following steps: melting, continuously casting into a blank, conventionally heating the casting blank, and carrying out hot rolling; reeling; conventionally pickling and carrying out cold rolling; annealing and galvanizing; slowly cooling; overaging and cooling to room temperature. According to the dual phase steel, by adopting the low-carbon high-silicon, the purity of ferrite can be improved, and the extensibility of steel can be effectively improved; and a proper amount of molybdenum, niobium and other microalloys are added to compound and enhance, so that the strength of steel is guaranteed. The proportion of the second phase of the dual phase steel and the microscopic appearance of the second martensite can be effectively guaranteed by high-temperature annealing and low-temperature overaging treatment, so that the strength of a steel sheet can be effectively guaranteed. On the premise that the safety of a vehicle is not reduced, the tensile strength of the steel is increased to over 800MPa, and the ductility A80mm is more than 18 percent, and the development requirement for light weight and high enhancement of vehicles can be met.
Description
Technical field
The present invention relates to a kind of automobile steel and production method, belong to a kind of high strength low-carbon height silicomanganese system cold-rolled dual phase steel of molybdenum niobium and production method particularly.
Background technology
Dual phase steel is a kind of advanced high-strength steel based on phase transformation strengthening, and microtexture adds tough martensite by the ferrite of high ductility and formed.Unique weave construction defines the premium properties features such as the yield-point of dual phase steel in mechanical property is low, intensity is high, initial manufacture hardening rate is high and strength and ductility is worked good, the features such as high intensity and work hardening exponent, low yield strength ratio and good bake hardenability, have become the New Type Punching Steel that a kind of intensity high formability is good.
Because dual phase steel combines the requirement that intensity is high, plasticity is good of automobile high-strength steel, be therefore widely used in structural part and the safety member of Hyundai Motor manufacture, to improve vehicle body security and to realize body lightening.Research finds, is ensureing that under the prerequisite that vehicle safety does not reduce, the intensity of material brings up to 600MPa from 200MPa, then automobile can realize loss of weight about 13%.Along with automotive light weight technology designs the enforcement with development and ultralight steel car body research project, with dual phase steel be the novel high-strength automobile steel [4-8] of representative development & application research be widely applied and development, and product strength rank also constantly promotes, wherein have with DP600, DP800 consumption maximum.
For dual phase steel, Composition Design is very important link, and it plays decisive role to the acquisition of the design of post annealed speed of cooling and second-phase martensitic phase.Carbon and manganese are the main alloying elements of dual phase steel, in order to meet different annealing process designs and different requirement of strength, Si, Cr, Mo, Al, Ti and Nb are also frequent to be added as alloying element independence or compound, to meet the overall design requirements of production technique and mechanical property.
Along with the raising of intensity, in order to obtain high strength, while constantly increasing steel grade carbon content, the additions such as the alloying element in steel such as Si, Mn, Mo, Nb, Cr need constantly to increase.But along with the continuous increase of alloy content, while realizing Mechanical Properties of Dual Phase Steels, the unit elongation of steel plate reduces greatly.For example traditional 800MPa Mechanical Properties of Dual Phase Steels is when intensity is greater than 800MPa, and its unit elongation is only 14% ~ 17%, greatly have impact on the comprehensive forming property of steel plate.Therefore, in high strength dual phase steel R&D process, while paying close attention to intensity raising, the forming property particularly unit elongation index of steel plate should be paid close attention to simultaneously.As through retrieval, Chinese Patent Application No. is the patent documentation of CN201110409715.9, it discloses a kind of dual phase steel and the production method thereof with high strength and high-ductility, the chemical component weight per-cent of described dual phase steel is: C:0.07% ~ 0.19%, Si:0.10% ~ 0.50%, Mn:1.00% ~ 2.30%, P :≤0.020%, S≤0.015%, N≤0.008%, Al:0.02% ~ 0.07%, Mo :≤0.40%, Nb :≤0.06%; Chinese Patent Application No. is the patent documentation of CN201110071272.7, it is disclosed that a kind of 800MPa level cold-rolled biphase steel and manufacture method thereof, described chemical component weight per-cent is: C:0.10 ~ 0.18%, Si:0.03 ~ 0.19%, Mn:2.6 ~ 3.0%, Als:0.01 ~ 0.04%, Cr:0.15 ~ 0.9%.
The present invention, on the basis considering armor plate strength and forming property, by the employing low-carbon (LC) of novelty, the design of high silicon, adds appropriate Mo, Nb simultaneously and carries out microalloying, successfully develop a kind of 800MPa level cold-rolled biphase steel cold-reduced sheet of high-elongation.
The applicant has carried out a kind of 800MPa level cold-rolled biphase steel laboratory study of low carbon and high silicon manganese molybdenum niobium system, result shows, the present invention can be used for the processing and manufacturing of the multiple forming mode part of automobile, can meet the requirement of domestic automobile lightweight and raising security, its economic benefit and social benefit are very remarkable.
Summary of the invention
The present invention is directed to the up to standard but unit elongation present situation causing part forming scarce capacity on the low side of current conventional 800MPa dual phase steel intensity, providing a kind of by adopting the design of low carbon and high silicon manganese molybdenum niobium set member, successfully developing unit elongation A
80mmthe 800MPa level low carbon and high silicon manganese system cold-rolled dual phase steel of molybdenum niobium of>=18% and production method.
Realize the technical measures of above-mentioned purpose:
The system cold-rolled dual phase steel of a kind of high strength low-carbon height silicomanganese molybdenum niobium, its component and weight percent content are: C:0.06% ~ 0.10%, Si:1.51% ~ 2.0%, Mn:1.5% ~ 2.5%, Mo:0.01% ~ 0.10%, Nb:0.01% ~ 0.05%, S<0.005%, P<0.01%, N<0.01%, and surplus is Fe and inevitable impurity.
Preferably: C:0.073% ~ 0.092%, Si:1.51% ~ 1.8%, Mn:1.8% ~ 2.4%, Mo:0.05% ~ 0.10%, Nb:0.03% ~ 0.05%.
Produce the method for the system cold-rolled dual phase steel of a kind of high strength low-carbon height silicomanganese molybdenum niobium, its step:
1) become base and routine to carry out hot rolling to after strand heating through smelting, continuous casting, wherein, control finish rolling finishing temperature at 800 ~ 900 DEG C;
2) batch, control coiling temperature at 560 ~ 640 DEG C;
3) cold rolling after conventional pickling, control its total reduction 65% ~ 70%;
4) carry out zinc-plated front annealing, control its soaking holding temperature at 800-850 DEG C, annealing time is 180 ~ 240s;
5) carry out slow cooling, be chilled to 650-680 DEG C; Then cool fast, under speed of cooling is greater than 25 DEG C/s, is cooled to 270-300 DEG C;
6) then within the scope of 260 ~ 290 DEG C, directly room temperature is cooled to after Wetted constructures.
The effect of each element in the present invention:
C: it is the most effective strengthening element, be form martensitic principal element, in steel, carbon content determines the hardness of dual phase steel and martensitic pattern; Carbon belongs to the strongest a kind of solution strengthening element, and increase the intensity that carbon content can significantly improve steel, meanwhile, carbon is also a kind of austenite stable element, effectively improves austenitic condensate depression.In the present invention, in order to ensure the unit elongation of experimental steel, therefore its scope is strict controlled in 0.06% ~ 0.10% scope.Preferably C is 0.08% ~ 0.10%.
Mn: it belongs to typical austenite stabilizer element, significantly improves the hardening capacity of steel, and plays the effect of solution strengthening and fining ferrite grains, can significantly postpone perlitic transformation and bainite transformation.But Mn is as the element expanding γ phase region.In the present invention, when Mn content higher than 2.5% time, its postponement perlitic transformation while, also can postpone ferritic precipitation; And when Mn content lower than 1.5% time, easily cause perlitic transformation again.Therefore its scope is strict controlled in 1.5% ~ 2.5%.Preferably Mn is in 1.8% ~ 2.4% scope.
Si: it is ferritic solution strengthening element, it accelerates carbon to austenitic segregation, have " removing " and " purification " to act on to the solid solution carbon in ferrite, when reducing gap solution strengthening and can suppress to cool, the generation of thick carbide, improves the ductility of dual phase steel.In order to improve the unit elongation of dual phase steel, present invention employs the design of high silicon.But when its content higher than 2.0% time, the oxidation of serious surface enrichment so that hot rolling surface can be caused to worsen, lower than 1.51% time, can to reduction product intensity.Preferably it is 1.51% ~ 1.8%.
Mo: consider alloy strengthening effect, preferably it is at 0.05% ~ 0.10%.
Nb: consider alloy strengthening effect, preferably it is 0.03% ~ 0.05%.
Why the present invention adopts high temperature annealing, low temperature Wetted constructures technique in process, and it ensures ratio and the martensitic microscopic appearance of second-phase of dual phase steel second-phase effectively, thus effectively ensure that the intensity of steel plate.
The present invention compared with prior art, adopts low carbon and high silicon, can improve ferritic purity, thus effectively improve the extensibility of steel; Add the microalloies such as appropriate molybdenum, niobium simultaneously and carry out complex intensifying, ensure that the strength property of steel.By adopting high temperature annealing, low temperature Wetted constructures technique, effectively ensure ratio and the martensitic microscopic appearance of Section 2 of dual phase steel second-phase, thus effectively ensure that the intensity of steel plate, ensureing under the prerequisite that vehicle safety does not reduce, its tensile strength is increased to 800MPa and more than, unit elongation A
80mm>=18%, meet automotive light weight technology, the demand for development of high strengthening.
Embodiment
Below the present invention is described in detail:
Table 1 is the chemical composition value list of various embodiments of the present invention and comparative example;
Table 2 is the main technologic parameters list of various embodiments of the present invention and comparative example;
Table 3 is various embodiments of the present invention and the list of comparative example Performance Detection situation.
Various embodiments of the present invention are produced according to following steps:
1) become base and routine to carry out hot rolling to after strand heating through smelting, continuous casting, wherein, control finish rolling finishing temperature at 800 ~ 900 DEG C;
2) batch, control coiling temperature at 560 ~ 640 DEG C;
3) cold rolling after conventional pickling, control its total reduction 65% ~ 70%;
4) carry out zinc-plated front annealing, control its soaking holding temperature at 800-850 DEG C, annealing time is 180 ~ 240s;
5) carry out slow cooling, be chilled to 650-680 DEG C; Then cool fast, under speed of cooling is greater than 25 DEG C/s, is cooled to 270-300 DEG C;
6) then within the scope of 260 ~ 290 DEG C, directly room temperature is cooled to after Wetted constructures.
The chemical composition value list (wt%) of table 1. various embodiments of the present invention and comparative example
The main technologic parameters of table 2. various embodiments of the present invention and comparative example
Note: the value in table 1 and table 2 is not one-to-one relationship, is only citing.
Table 3. various embodiments of the present invention and the list of comparative example Performance Detection situation
As can be seen from Table 3, production technique adaptability of the present invention is good, good mechanical performance, and has good high strength galvanized steel.
Above-described embodiment is only the best and exemplifies, and is not the restriction to embodiments of the present invention.
Claims (3)
1. the system cold-rolled dual phase steel of high strength low-carbon height silicomanganese molybdenum niobium, its component and weight percent content are: C:0.06% ~ 0.10%, Si:1.51% ~ 2.0%, Mn:1.5% ~ 2.5%, Mo:0.01% ~ 0.10%, Nb:0.01% ~ 0.05%, S<0.005%, P<0.01%, N<0.01%, and surplus is Fe and inevitable impurity.
2. the system cold-rolled dual phase steel of a kind of high strength low-carbon height silicomanganese molybdenum niobium as claimed in claim 1, is characterized in that: its component and weight percent content are: C:0.073% ~ 0.092%, Si:1.51% ~ 1.8%, Mn:1.8% ~ 2.4%, Mo:0.05% ~ 0.10%, Nb:0.03% ~ 0.05%, S<0.005%, P<0.01%, N<0.01%.
3. the method for the system cold-rolled dual phase steel of a kind of high strength low-carbon height silicomanganese molybdenum niobium described in production claim 1, its step:
1) become base and routine to carry out hot rolling to after strand heating through smelting, continuous casting, wherein, control finish rolling finishing temperature at 800 ~ 900 DEG C;
2) batch, control coiling temperature at 560 ~ 640 DEG C;
3) cold rolling after conventional pickling, control its total reduction 65% ~ 70%;
4) carry out zinc-plated front annealing, control its soaking holding temperature at 800-850 DEG C, annealing time is 180 ~ 240s;
5) carry out slow cooling, be chilled to 650-680 DEG C; Then cool fast, under speed of cooling is greater than 25 DEG C/s, is cooled to 270-300 DEG C;
6) then within the scope of 260 ~ 290 DEG C, directly room temperature is cooled to after Wetted constructures.
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| CN201410644803.0A CN104357740B (en) | 2014-11-14 | 2014-11-14 | A kind of high strength low-carbon height silicomanganese system cold-rolled dual phase steel of molybdenum niobium and production method |
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| CN201410644803.0A CN104357740B (en) | 2014-11-14 | 2014-11-14 | A kind of high strength low-carbon height silicomanganese system cold-rolled dual phase steel of molybdenum niobium and production method |
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| CN104357740A true CN104357740A (en) | 2015-02-18 |
| CN104357740B CN104357740B (en) | 2016-06-01 |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105296852A (en) * | 2015-11-24 | 2016-02-03 | 西安三维应力工程技术有限公司 | Welding steel pipe for automobile transmission shaft and manufacturing method of welding steel pipe |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002080931A (en) * | 2000-09-07 | 2002-03-22 | Nippon Steel Corp | High strength cold rolled steel sheet and high strength plated steel sheet having excellent workability and spot weldability and method for producing the same |
| JP2005213603A (en) * | 2004-01-30 | 2005-08-11 | Jfe Steel Kk | High workability high strength cold rolled steel plate and its manufacturing method |
| JP2010111891A (en) * | 2008-11-04 | 2010-05-20 | Sumitomo Metal Ind Ltd | Cold rolled steel sheet, surface treated steel sheet, and method for producing the same |
| CN102605240A (en) * | 2011-12-09 | 2012-07-25 | 首钢总公司 | High-strength and high-plasticity dual-phase steel and manufacturing method thereof |
| JP2012229457A (en) * | 2011-04-25 | 2012-11-22 | Jfe Steel Corp | High strength electroseamed steel pipe and method for producing the same |
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- 2014-11-14 CN CN201410644803.0A patent/CN104357740B/en not_active Expired - Fee Related
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002080931A (en) * | 2000-09-07 | 2002-03-22 | Nippon Steel Corp | High strength cold rolled steel sheet and high strength plated steel sheet having excellent workability and spot weldability and method for producing the same |
| JP2005213603A (en) * | 2004-01-30 | 2005-08-11 | Jfe Steel Kk | High workability high strength cold rolled steel plate and its manufacturing method |
| JP2010111891A (en) * | 2008-11-04 | 2010-05-20 | Sumitomo Metal Ind Ltd | Cold rolled steel sheet, surface treated steel sheet, and method for producing the same |
| JP2012229457A (en) * | 2011-04-25 | 2012-11-22 | Jfe Steel Corp | High strength electroseamed steel pipe and method for producing the same |
| CN102605240A (en) * | 2011-12-09 | 2012-07-25 | 首钢总公司 | High-strength and high-plasticity dual-phase steel and manufacturing method thereof |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105296852A (en) * | 2015-11-24 | 2016-02-03 | 西安三维应力工程技术有限公司 | Welding steel pipe for automobile transmission shaft and manufacturing method of welding steel pipe |
| CN105296852B (en) * | 2015-11-24 | 2017-03-29 | 西安三维应力工程技术有限公司 | Welded still pipe used for vehicle transmission shaft and its manufacture method |
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