CN109023149A - Low 980MPa grade cold-rolled biphase steel and its manufacturing method are required producing line cooling capacity - Google Patents
Low 980MPa grade cold-rolled biphase steel and its manufacturing method are required producing line cooling capacity Download PDFInfo
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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
- C22C38/18—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
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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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
Low 980MPa grade cold-rolled biphase steel and its manufacturing method are required the invention discloses a kind of pair of producing line cooling capacity, belong to steelmaking technical field.It is made of each chemical constituent of following mass percent: C:0.14~0.17%, Si:0.10~0.30%, Mn:1.8~2.2%, P≤0.012%, Cr:0.4~0.6%, Alt:0.02~0.07%, Nb:0.01~0.02%, B:0.0005~0.002%, S≤0.005%, N≤0.005%, surplus are Fe and inevitable impurity.According to above-mentioned chemical constituent by smelting, block technique, and it heating of plate blank, hot rolling, batches, pickling, cold rolling and continuous annealing process, in continuous annealing process, controlling annealing temperature is 800~820 DEG C, slow cooling section 8 DEG C/s of cooling rate <, it is 620~640 DEG C that slow cooling section, which terminates temperature, and it is 300~320 DEG C that rapid cooling section, which terminates temperature, rapid cooling section cooling rate 30 DEG C/s of <, overaging temperature are 270~310 DEG C.Chemical constituent and technique according to the invention carry out preparing dual phase steel, not high to the rapid cooling rate request in production producing line, can be used for conventional common producing line.
Description
Technical field
The present invention relates to the manufacturing methods of high strength cold-rolled dual phase steel, belong to steelmaking technical field, more particularly to one kind
Low 980MPa grade cold-rolled biphase steel and its manufacturing method are required producing line cooling capacity.
Background technique
With automobile industry development, demand of the market to small displacement, low energy consumption automobile is increasingly improved.According to statistics, automobile matter
Every mitigation 10% is measured, fuel consumption can reduce by 3~7%.The considerations of for cost, the energy, safety, environment etc., automobile is light
Quantization is the developing direction of Hyundai Motor industry.Steel material for accounting for vehicle gross weight 55~70% carries out performance optimization and liter
Grade, plays an important role in automotive light weight technology process.In order to achieve the purpose that material upgrades, high-intensitive, high-performance is pursued
The trend of design and research as automobile steel.Dual phase steel (DP steel) is met the tendency of as the advanced high-strength vehicle of the first generation with steel
And give birth to, gradually it is applied on vehicle structure and part at home.
The main product of cold-rolled biphase steel application at present is 450~780MPa rank, especially 590 and 780MPa rank
Product is widely used in production body structural member since its intensity is high, forming property is considerable compared to traditional high-strength steel.And with
Light-weighted continuous upgrading, 980MPa grades of cold-rolled biphase steels in future automobile with will gradually obtain high volume applications on material,
It is cooling to producing line at present since its intensity superelevation, produced on-site stability control difficulty are big, and according to dual phase steel formation basic theory
The energy line of force is more demanding, generally requires and is produced on super-high strength steel industrial siding, and the country only has a small number of steel mills and has batch life
Production capacity power.
Wuhan Iron and Steel Plant is limited to only have common automobile board assembly line at present, does not build up dedicated superelevation Johnson & Johnson producing line, existing company
Cooling rate is less than 30 DEG C/s under normal circumstances for annealing production line, with the continuous increasing of the 980MPa grades of cold-rolled biphase steel market demands
Add, it is urgently to be resolved that the super-high strength steel product of high quality this project how is produced in current producing line.Producing line cooling rate is low,
Mean that product alloying component needs to do special designing, for example increases certain alloys if to obtain a large amount of martensitic structure
A constituent content, while also to take into account cost factor, in addition, also to be designed with alloy in the formulation of technique and producing line situation be done
Match.Therefore, the demand for market and producing line are practical, and the limited exploitation for having carried out 980MPa grades of cold-rolled biphase steels of Wuhan Iron and Steel Plant is developed,
Design of Chemical Composition, the preparation process control technology of this steel grade are successfully grasped.
Some iron and steel enterprises and research institution both domestic and external have also carried out the research work of high strength cold-rolled two-phase steel product,
To meet the needs of auto industry.As Chinese invention patent application (application publication number: CN101348885A, apply publication date:
A kind of 1000MPa grade cold rolling hot dip galvanizing dual phase steel and its manufacturing method 2009-1-21) are disclosed, cold rolling hot dip galvanizing height is belonged to
Strong steel plate technical field.The chemical component mass percent of cold rolling hot dip galvanizing dual phase steel: C:0.06~0.18%, Si≤
0.1%, Mn:1.2~2.5%, Mo:0.05~0.5%, Cr:0.05~0.6%, Al:0.005~0.05%, Nb:0.01~
0.06%, Ti:0.01~0.05%, P≤0.02%, S≤0.01%, N≤0.005%；Surplus is iron and inevitably miscellaneous
Matter.The present invention replaces Si using Cr, Mo, to expand austenite+ferrite two-phase section, improves the harden ability of dual phase steel.Together
When, crystal grain is refined to improve the intensity, toughness of steel by addition Nb, Ti, makes steel that there is good solderability, usability, intensity
Rank can achieve 1000MPa or more, but the application production is hot rolling Galvanized Dual Phase Steel.
For another example Chinese invention patent application (application publication number: CN102828119A applies for publication date: 2012-12-19) is public
A kind of high flexure type 980MPa grades of cold-rolled biphase steels and its preparation process are opened, the weight percent of steel plate chemical analysis are as follows: C:
0.03~0.20%, Si:0.20~0.80%, Mn:1.2~2.2%, Cr:0.2~1.0%, Nb:0.02~0.15%, S <
0.015%, P < 0.020%, Als:0.02~0.15%, surplus are Fe and inevitable impurity.Its preparation process: slab adds
Hot temperature is 1180~1250 DEG C, and roughing start rolling temperature is 1150~1050 DEG C, and finishing temperature is 1020~980 DEG C, and finish rolling is opened
Rolling temperature is 940~1000 DEG C, and finishing temperature is 750~920 DEG C, and coiling temperature is 520~700 DEG C；Hot rolled plate is through overpickling
Cold rolling afterwards, cold rolling reduction ratio are 45~80%；Flat cold-rolled sheet annealing temperature is 740~840 DEG C, and soaking time is 60~200s,
Fast speed of cooling is 25~40 DEG C/s, and overaging temperature is 170~400 DEG C, and the overaging time is 120~500s.Present invention preparation
Steel plate 990~1210MPa of tensile strength, elongation 10.1~18.9%, yield tensile ratio 0.42~0.53, n value 0.23~0.32,
0.5~1.5mm of minimum bending radius.For another example (application publication number: CN101768695A, application are open for Chinese invention patent application
Day: 2010-07-07) disclose a kind of 1000MPa grade Ti micro-alloying ultra-fine grained cold rolling dual phase steel and its preparation process.Steel
Chemical component and mass percentage content are as follows: C:0.03~0.20%, Si:0.20~0.80%, Mn:1.2~2.0%, Ti:
0.03~0.15%, S < 0.015%, P < 0.020%, Als:0.02~0.15%, surplus Fe.This method is with C-Si-
Mn-Ti is that basic alloy system reduces and is produced into using cheap Ti without adding the alloying elements such as Cr, Mo, Nb, V
This,, can be by martensite island under conditions of fast speed of cooling is less than 50 DEG C/s in continuous annealing by flexible continuous annealing process
Size Control at 1~2 μm or increase to 5 μm or so, to obtain three kinds of different types of dual phase steels: high strength type (Rm=
980~1200MPa, A50=10~13%), high-ductility type (Rm=980~1100MPa, A50=14~18%) and it is comprehensive
(Rm=980~1150MPa, A50=12~15%), yield tensile ratio is 0.47~0.65.However the product of this two pieces application documents
It is relatively high to rapid cooling rate request, therefore have higher requirement to the cooling capacity of producing line, it is suitble to stronger in cooling capacity
It is produced in producing line.
Summary of the invention
In order to solve the above technical problems, requiring low 980MPa grade cold rolling the invention discloses a kind of pair of producing line cooling capacity
Dual phase steel and its manufacturing method, the dual phase steel of the high intensity are applicable to generally produce producing line.
To achieve the above object, the invention discloses a kind of pair of producing line cooling capacities to require low 980MPa grade cold rolling double
Xiang Gang is made of: C:0.14~0.17%, Si:0.10~0.30%, Mn:1.8 each chemical constituent of following mass percent
~2.2%, P≤0.012% (does not include zero), Cr:0.4~0.6%, Alt:0.02~0.07%, Nb:0.01~0.02%,
B:0.0005~0.002%, S≤0.005% (including zero), N≤0.005% (including zero), surplus is for Fe and inevitably
Impurity.
Above-mentioned Alt indicates full aluminium, is exactly the total content of aluminium.
Further, in the chemical constituent, the mass percent of C is 0.15~0.16%.
Preferably, in the chemical constituent, the mass percent of C is 0.15%.
Preferably, in the chemical constituent, the mass percent of C is 0.155%.
Preferably, in the chemical constituent, the mass percent of C is 0.16%.
Further, in the chemical constituent, the mass percent of Si is 0.15~0.25%.
Preferably, in the chemical constituent, the mass percent of Si is 0.15%.
Preferably, in the chemical constituent, the mass percent of Si is 0.20%.
Preferably, in the chemical constituent, the mass percent of Si is 0.25%.
Further, in the chemical constituent, the mass percent of B is 0.0006~0.001%.
Preferably, in the chemical constituent, the mass percent of B is 0.0006%.
Preferably, in the chemical constituent, the mass percent of B is 0.0007%.
Preferably, in the chemical constituent, the mass percent of B is 0.0008%.
Preferably, in the chemical constituent, the mass percent of B is 0.0009%.
Preferably, in the chemical constituent, the mass percent of B is 0.001%.
Further, in the chemical constituent, the mass percent of Cr is 0.40%.
Further, in the chemical constituent, the mass percent of Cr is 0.45%.
Further, in the chemical constituent, the mass percent of Cr is 0.50%.
Further, in the chemical constituent, the mass percent of Cr is 0.55%.
Further, in the chemical constituent, the mass percent of Cr is 0.60%.
Further, in the chemical constituent, the mass percent of Nb is 0.010%.
Further, in the chemical constituent, the mass percent of Nb is 0.015%.
Further, in the chemical constituent, the mass percent of Nb is 0.020%.
The effect of each chemical constituent is illustrated below:
Carbon (C): C element can significantly improve the intensity of steel, and especially in dual phase steel, content of the C in martensite is direct
Martensite intensity is influenced, and then influences the tensile strength of steel, but the carbon content in steel is excessively high totally unfavorable to forming property,
The welding performance of material can be deteriorated.Therefore its content is limited to 0.12~0.17% range, and preferably 0.15~0.16%.
Silicon (Si): Si element has catharsis to ferrite matrix in dual phase steel, inhibits the formation of carbide, promotees simultaneously
It is spread into C from ferrite matrix to austenite, but excessive Si element will lead to iron scale in hot rolling production process and remove
Not to the utmost the problems such as.So its content is limited to 0.10~0.30% range, and preferably 0.15~0.25%.
Manganese (Mn): Mn element can play the role of expanding austenitic area, and improve the intensity of steel, but higher manganese content meeting
Steel-making is adversely affected with continuous casting process, it is contemplated that steel need intensity rank to be achieved, its content is limited to 1.8~
2.2%.
Phosphorus (P): P element belongs to control element in the present invention, and content requirement is low, considers its synthesis shadow to Steel Properties
It rings, is limited to 0.012% or less.
Aluminium (Al): Al element is added as deoxidier in the present invention, guarantees the pure of molten steel, but excessive aluminium contains
Amount will form alumina inclusion.The Alt content comprehensively considered in steel is controlled 0.02~0.07%.
Chromium (Cr): Cr element can play the role of expanding austenitic area, reduce the temperature of austenitizing, ensure martensite
Forming amount comprehensively considers on the influence of the performance of steel, and content range is controlled 0.4~0.6%.
Niobium (Nb): Nb element is that annealing recrystallization process can be effectively hindered in dual phase steel, the tissue of fining ferrite,
To improve ferrite matrix hardness and strength, high-yield strength is realized, niobium can also be such that the diffusion path of C and alloying element becomes
It is short, be conducive to the diffusion of C and alloying element.But niobium is relatively valuable, considers cost of alloy, and content is limited to 0.01~
0.02%.
Sulphur (S): S element belongs to control element in steel of the present invention, and the lower content the better, therefore sulfur content in steel is controlled
Below 0.005%.
Nitrogen (N): N element is harmful element in steel, influences the forming property of steel.Therefore its content is controlled 0.005%
Below.
Boron (B): B element can effectively improve the harden ability of steel, and the addition of B element can be used to further make " C curve "
It moves to right, martensite can be generated by ensureing under cooling rate low in annealing process, but B addition excessively can make steel brittleness in crystal boundary segregation
Increase.Therefore its content is controlled 0.0005~0.002%, and preferably 0.0006~0.001%.
The above-mentioned manufacturing method for requiring producing line cooling capacity low 980MPa grade cold-rolled biphase steel, including according to describedization
Learn component by smelting, block technique, further include heating of plate blank, hot rolling, batch, pickling, cold rolling and continuous annealing process,
In the continuous annealing process, control annealing temperature is 800~820 DEG C, and slow cooling section cooling rate < 8 DEG C/s, slow cooling section terminates temperature and is
620~640 DEG C, it is 300~320 DEG C, rapid cooling section cooling rate 30 DEG C/s of < that rapid cooling section, which terminates temperature, and overaging temperature is 270~310
℃。
Further, in the continuous annealing process, rapid cooling 25 DEG C/s of section cooling rate <, smooth elongation percentage 0.3~0.5%.
Further, the rapid cooling section cooling rate is 20 DEG C/s.
Preferably, in the continuous annealing process, slow cooling section cooling rate is 6 DEG C/s.
Further, the slab heating temperature is 1270~1330 DEG C, and finishing temperature is 880~920 DEG C, batches temperature
Degree is 630~670 DEG C.
Further, the cold rolling reduction ratio is 55~65%, under the cold rolling reduction ratio, is conducive to product tissue and property
The uniformity of energy.
The control principle of each processing step is illustrated below:
In continuous annealing process, control annealing temperature is 800~820 DEG C, and the advantage of the temperature range is based on above-mentioned
Ingredient and preceding procedure technology obtain reasonable ferrite and austenite two-phase proportion, require to beat for the subsequent product final performance that meets
Lower basis.
Meanwhile it is 620~640 DEG C that slow cooling section, which terminates temperature, it is 300~320 DEG C that rapid cooling section, which terminates temperature, and is controlled slow
Cold section of cooling rate < 8 DEG C/s, rapid cooling section cooling rate 30 DEG C/s of <, the in this process Volume fraction of ferrite and martensite two-phase
The available accurate control of example, to realize the matching of intensity.
In addition, overaging temperature is 270~310 DEG C in annealing process, at this stage, the structure of martensite has been obtained surely
It is fixed, be conducive to the tensile strength for further improving dual phase steel.
The beneficial effects are mainly reflected as follows as follows:
Chemical constituent according to the invention carries out preparing dual phase steel, not to the rapid cooling rate request in production producing line
Height can be used for conventional common producing line, meanwhile, about 40% is contained in the heterogeneous microstructure for the dual phase steel that the present invention is prepared
The ferrite of volume fraction+about 60% volume fraction martensite ensure that the yield strength of product is 550~730MPa, resist
Tensile strength is higher than 980MPa, elongation (A80mm) it is not less than 9%.
Detailed description of the invention
Fig. 1 is the metallographic structure figure of dual phase steel of the present invention.
Specific embodiment
In order to better explain the present invention, below in conjunction with the specific embodiment main contents that the present invention is furture elucidated, but
The contents of the present invention are not limited solely to following embodiment.
Embodiment 1
It present embodiments provides a kind of pair of producing line cooling capacity and requires low 980MPa grade cold-rolled biphase steel, by following quality
The chemical constituent of percentage is constituted: C:0.141%, Si:0.23%, Mn:1.91%, P:0.009%, Cr:0.46%, Alt:
0.04%, Nb:0.02%, B:0.0008%, S:0.003%, N:0.0022%, surplus are Fe and inevitable impurity.
The production method of above-mentioned dual phase steel, its step are as follows:
In hot rolling technology slab heating temperature be 1270~1282 DEG C, 892~901 DEG C of finishing temperature, coiling temperature 639~
657 DEG C, cold rolling reduction ratio 62%, 805~812 DEG C of annealing temperature in annealing process, slow cooling section terminates 629~637 DEG C of temperature,
Rapid cooling section terminates 301~315 DEG C of temperature, and slow cooling section cooling rate is 6 DEG C/s, and rapid cooling section cooling rate is 25 DEG C/s, and overaging temperature 289~
300 DEG C, smooth elongation percentage 0.42~0.50%.
The results are shown in Table 3 for the mechanical properties test for the dual phase steel that the present embodiment is prepared, wherein steel plate is prepared
With a thickness of 1.0mm, yield strength Rp0.2=559MPa, tensile strength Rm=992MPa, elongation A80mm=12%.
Metallographic structure figure as shown in Figure 1, the microstructure of dual phase steel manufactured in the present embodiment are mainly martensite and iron
Ferritic tissue, and ferritic volume fraction is about 40%, the volume fraction of martensite is about 60%, reasonable body between two-phase
Fraction ensure that the mechanical property of dual phase steel.
Low 980MPa grade cold-rolled biphase steel is required producing line cooling capacity provided by embodiment 2~6, by institute in table 1
The chemical constituent for the mass percent listed constitutes (surplus is Fe and inevitable impurity).Its production stage and embodiment 1
It is essentially identical, the difference is that the processing parameter that table 2 is listed.
The comparative example (%) of 1 1~embodiment of the embodiment of the present invention 6 of table
The processing parameter list of 2 1~embodiment of the embodiment of the present invention 6 of table
Mechanical properties test the results list of 3 1~embodiment of the embodiment of the present invention 6 of table
By above-mentioned table 1, table 2 and table 3 it is found that the present invention is by the suitable alloying component of control and combines corresponding production
Technique such as hot rolling application cooling controlling and rolling controlling process, acid are rolled using compared with heavy reduction, and annealing process uses intercritical annealing, passes through control
The critical process point such as rapid cooling outlet temperature, overaging temperature, so that can prepare intensity rank in routinely production producing line and be
980MPa grades or so of dual phase steel is not needed using super-high strength steel production line；Meanwhile the product that the present invention is prepared is used for
When producing body of a motor car high-strength structure part, gained part strength is high, high-quality, and good lightweight can be played to body structure
Effect has significant Social benefit and economic benefit.
Above embodiments are only best citing, rather than a limitation of the embodiments of the present invention.Except above-described embodiment
Outside, there are also other embodiments by the present invention.All technical solutions formed using equivalent substitution or equivalent transformation, all fall within the present invention
It is required that protection scope.
Claims (9)
1. a kind of pair of producing line cooling capacity requires low 980MPa grade cold-rolled biphase steel, it is characterised in that: by following quality percentage
Each chemical constituent of ratio forms: C:0.14~0.17%, Si:0.10~0.30%, Mn:1.8~2.2%, P≤0.012%,
Cr:0.4~0.6%, Alt:0.02~0.07%, Nb:0.01~0.02%, B:0.0005~0.002%, S≤0.005%, N
≤ 0.005%, surplus is Fe and inevitable impurity.
2. requiring producing line cooling capacity low 980MPa grade cold-rolled biphase steel according to claim 1, it is characterised in that: institute
It states in chemical constituent, the mass percent of C is 0.15~0.16%.
3. requiring producing line cooling capacity low 980MPa grade cold-rolled biphase steel according to claim 1, it is characterised in that: institute
It states in chemical constituent, the mass percent of Si is 0.15~0.25%.
4. requiring producing line cooling capacity low 980MPa grade cold-rolled biphase steel according to claim 1, it is characterised in that: institute
It states in chemical constituent, the mass percent of B is 0.0006~0.001%.
5. the manufacturing method of low 980MPa grade cold-rolled biphase steel is required producing line cooling capacity described in a kind of Claims 1 to 4,
Including passing through smelting, block technique according to the chemical constituent, it is characterised in that: further include heating of plate blank, hot rolling, volume
It takes, pickling, cold rolling and continuous annealing process, in the continuous annealing process, control annealing temperature is 800~820 DEG C, slow cooling section
Cooling rate < 8 DEG C/s, it is 620~640 DEG C that slow cooling section, which terminates temperature, and it is 300~320 DEG C that rapid cooling section, which terminates temperature, rapid cooling section cooling rate <
30 DEG C/s, overaging temperature is 270~310 DEG C.
6. the manufacturing method of low 980MPa grade cold-rolled biphase steel is required producing line cooling capacity according to claim 5,
Be characterized in that: in the continuous annealing process, rapid cooling section cooling rate 25 DEG C/s of <, smooth elongation percentage is 0.3~0.5%.
7. the manufacturing method of low 980MPa grade cold-rolled biphase steel is required producing line cooling capacity according to claim 6,
Be characterized in that: the rapid cooling section cooling rate is 20 DEG C/s.
8. requiring producing line cooling capacity low 980MPa grade cold-rolled biphase steel according to any one of claim 5~7
Manufacturing method, it is characterised in that: the slab heating temperature be 1270~1330 DEG C, finishing temperature be 880~920 DEG C, volume
Taking temperature is 630~670 DEG C.
9. requiring producing line cooling capacity low 980MPa grade cold-rolled biphase steel according to any one of claim 5~7
Manufacturing method, it is characterised in that: the cold rolling reduction ratio be 55~65%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810673252.9A CN109023149B (en) | 2018-06-26 | 2018-06-26 | 980 MPa-grade cold-rolled dual-phase steel with low requirement on cooling capacity of production line and manufacturing method thereof |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810673252.9A CN109023149B (en) | 2018-06-26 | 2018-06-26 | 980 MPa-grade cold-rolled dual-phase steel with low requirement on cooling capacity of production line and manufacturing method thereof |
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| Publication Number | Publication Date |
|---|---|
| CN109023149A true CN109023149A (en) | 2018-12-18 |
| CN109023149B CN109023149B (en) | 2020-09-04 |
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| CN201810673252.9A Active CN109023149B (en) | 2018-06-26 | 2018-06-26 | 980 MPa-grade cold-rolled dual-phase steel with low requirement on cooling capacity of production line and manufacturing method thereof |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110512056A (en) * | 2019-09-20 | 2019-11-29 | 本钢板材股份有限公司 | A kind of continuous annealing furnace overaging section strip steel heating means |
| CN111455266A (en) * | 2020-02-17 | 2020-07-28 | 本钢板材股份有限公司 | 980 MPa-grade low-yield cold-rolled dual-phase steel and preparation method thereof |
| CN114525448A (en) * | 2022-01-19 | 2022-05-24 | 邯郸钢铁集团有限责任公司 | 780 MPa-grade reinforced forming hot-dip galvanized dual-phase steel and manufacturing method thereof |
| WO2022206913A1 (en) * | 2021-04-02 | 2022-10-06 | 宝山钢铁股份有限公司 | Dual-phase steel and hot-dip galvanized dual-phase steel having tensile strength greater than or equal to 980mpa and method for manufacturing same by means of rapid heat treatment |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04235253A (en) * | 1990-12-28 | 1992-08-24 | Kawasaki Steel Corp | Ultrahigh strength cold rolled steel sheet having good bendability and impact property and its manufacture |
| JP2004263270A (en) * | 2003-03-04 | 2004-09-24 | Jfe Steel Kk | Ultrahigh-strength cold-rolled steel sheet excellent in hardenability and its production method |
| CN102828119A (en) * | 2011-06-14 | 2012-12-19 | 鞍钢股份有限公司 | High-bending 980 MPa-grade cold-rolled dual-phase steel and preparation process thereof |
| CN103882320A (en) * | 2012-12-21 | 2014-06-25 | 鞍钢股份有限公司 | High-strength cold-rolled steel sheet having excellent stretch flangeability and spot weldability, and method for producing same |
| 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 |
-
2018
- 2018-06-26 CN CN201810673252.9A patent/CN109023149B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04235253A (en) * | 1990-12-28 | 1992-08-24 | Kawasaki Steel Corp | Ultrahigh strength cold rolled steel sheet having good bendability and impact property and its manufacture |
| JP2004263270A (en) * | 2003-03-04 | 2004-09-24 | Jfe Steel Kk | Ultrahigh-strength cold-rolled steel sheet excellent in hardenability and its production method |
| CN102828119A (en) * | 2011-06-14 | 2012-12-19 | 鞍钢股份有限公司 | High-bending 980 MPa-grade cold-rolled dual-phase steel and preparation process thereof |
| CN103882320A (en) * | 2012-12-21 | 2014-06-25 | 鞍钢股份有限公司 | High-strength cold-rolled steel sheet having excellent stretch flangeability and spot weldability, and method for producing same |
| 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 |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110512056A (en) * | 2019-09-20 | 2019-11-29 | 本钢板材股份有限公司 | A kind of continuous annealing furnace overaging section strip steel heating means |
| CN111455266A (en) * | 2020-02-17 | 2020-07-28 | 本钢板材股份有限公司 | 980 MPa-grade low-yield cold-rolled dual-phase steel and preparation method thereof |
| WO2022206913A1 (en) * | 2021-04-02 | 2022-10-06 | 宝山钢铁股份有限公司 | Dual-phase steel and hot-dip galvanized dual-phase steel having tensile strength greater than or equal to 980mpa and method for manufacturing same by means of rapid heat treatment |
| EP4317515A4 (en) * | 2021-04-02 | 2024-10-02 | Baoshan Iron & Steel | Dual-phase steel and hot-dip galvanized dual-phase steel having tensile strength greater than or equal to 980mpa and method for manufacturing same by means of rapid heat treatment |
| CN114525448A (en) * | 2022-01-19 | 2022-05-24 | 邯郸钢铁集团有限责任公司 | 780 MPa-grade reinforced forming hot-dip galvanized dual-phase steel and manufacturing method thereof |
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| CN109023149B (en) | 2020-09-04 |
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