CN109280854A - 980MPa grades of low-carbon cold rolling dual phase steels and preparation method thereof - Google Patents

980MPa grades of low-carbon cold rolling dual phase steels and preparation method thereof Download PDF

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CN109280854A
CN109280854A CN201811429155.1A CN201811429155A CN109280854A CN 109280854 A CN109280854 A CN 109280854A CN 201811429155 A CN201811429155 A CN 201811429155A CN 109280854 A CN109280854 A CN 109280854A
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dual phase
cold rolling
low
carbon cold
preparation
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邝春福
郑之旺
周三保
张劲超
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Pangang Group Panzhihua Iron and Steel Research Institute Co Ltd
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Pangang Group Panzhihua Iron and Steel Research Institute Co Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • 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
    • C21D2211/005—Ferrite
    • 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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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The present invention relates to 980MPa grades of low-carbon cold rolling dual phase steels and preparation method thereof, belong to automobile high-strength steel technical field.Present invention solves the technical problem that being that existing 980MPa grades of cold-rolled biphase steel high production cost, production difficulty are big.Strong dual phase steel of cold rolling low cost superelevation of the present invention and preparation method thereof, its chemical component mass percent is C:0.05~0.10%, Si:0.30~0.70%, Mn:2.00~2.50%, Cr:0.40~0.80%, Al:0.01~0.06% controls molten iron V content in converter, and then hot rolling, acid roll, annealing process obtains 980MPa grades of low-carbon cold rolling dual phase steels.Mechanical Properties of Dual Phase Steels and forming property of the invention is excellent, and cost advantage is obvious, has significant economic benefit and social benefit.

Description

980MPa grades of low-carbon cold rolling dual phase steels and preparation method thereof
Technical field
The invention belongs to automobile high-strength steel technical fields, and in particular to 980MPa grades of low-carbon cold rolling dual phase steels and its preparation Method.
Background technique
With the development of automotive light weight technology technology, automobile steel develops towards high-strength steel direction has become inexorable trend.It is double Phase steel has the characteristics that low yield strength, high-tensile and excellent plasticity, becomes automobile first choice high-strength steel, and dosage is estimated It will be more than 70% in the advanced high-strength steel of automobile.With the continuous release of internal vapor sweep production capacity, the competition in high-strength steel market Also more and more fierce, the dual phase steel of low-cost and high-performance has become the target that each enterprise is pursued, and receives great attention.
Patent document CN102828119A discloses high flexure type 980MPa grades of cold-rolled biphase steels and preparation process, preferably Chemical component percentage are as follows: C:0.17~0.19%, Si:0.50~0.70%, Mn:1.80~2.00%, Cr:0.30~ 0.60%, Nb:0.04~0.06%, surplus are Fe and inevitable impurity；Delayed by 740-840 DEG C of heat preservation, 640-760 DEG C Cold, 170-400 DEG C of Wetted constructures have obtained the cold-rolled biphase steel that tensile strength is greater than 980MPa.Although by its chemistry at Divide and the cold-rolled biphase steel of production method preparation has excellent mechanical property, but its welding performance (higher carbon content) and height roll Difficulty (Nb inhibits Austenite Dynamic Recrystallization) processed is its main weakness.Carbon content is higher so that under cold-rolled biphase steel welding performance Drop, finally necessarily affects extensive use of the dual phase steel on automobile.
Patent document CN102586688A discloses a kind of dual phase sheet steel and its manufacturing method, chemical component percentage Are as follows: C:0.07~0.098%, Si:0.10~0.40%, Mn:1.95~2.20%, Cr:0.30~0.60%, Al:0.015~ 0.055%, Nb:0.015~0.04%, Ti:0.015~0.04%, Mo:0.20~0.40%, P≤0.015%, S≤ 0.004%, N≤0.005%, surplus are Fe and inevitable impurity；By 780-820 DEG C of heat preservation, 650-700 DEG C of slow cooling, 200-300 DEG C of Wetted constructures have obtained the cold-rolled biphase steel that tensile strength is greater than 980MPa.Although passing through the excellent of chemical component Change, reduces carbon content so that welding performance improves, however to produce containing microalloy elements such as a large amount of Nb, Ti and Mo Cost obviously increases.In addition, in the hot rolling, the effects of C, Nb, Mo compound inhibition austenite recrystallization, so that hot rolling difficulty It significantly improves.
Patent document CN102517492A discloses a kind of preparation side of dual phase steel of deep-draw containing vanadium through sub- temperature annealing Method, chemical component percentage are as follows: C:0.01~0.10%, Si:1.00-2.00%, Mn:0.10~1.00%, V:0.02~ 0.08%, P:0.01~0.10%, S≤0.01%, surplus are Fe and inevitable impurity；It is moved back by 750~800 DEG C of sub- temperature Fire, 800~850 DEG C of heat preservations, 20~50 DEG C/s rapid cooling, methods of 250~300 DEG C of overaging obtain tensile strength and are greater than 600MPa, r value are greater than 1.4 cold-rolled biphase steel.The invention is mainly to be conducive to the effect of the fixed C atom of V, to obtain high-strength The cold-rolled biphase steel of degree, high r value.However, this method needs twice annealing, production cycle long, industrialized production effect is seriously affected Rate.
Summary of the invention
Present invention solves the technical problem that being that existing 980MPa grades of cold-rolled biphase steel high production cost, production difficulty are big.
Technical proposal that the invention solves the above-mentioned problems is to provide 980MPa grades of low-carbon cold rolling dual phase steels, chemical component matter Measure percentage are as follows: C:0.05~0.10%, Si:0.30~0.70%, Mn:2.00~2.50%, Cr:0.40~0.80%, Al: 0.01~0.06%, V:0.05~0.15%, P≤0.020%, S≤0.010%, N≤0.006%, surplus are Fe and can not keep away Exempt from impurity.
Preferably, the present invention provides 980MPa grades of low-carbon cold rolling dual phase steels, and chemical component mass percent is C:0.06 ~0.08%, Si:0.40~0.60%, Mn:2.20~2.50%, Cr:0.60~0.80%, Al:0.02~0.05%, V: 0.05~0.10%, P≤0.015%, S≤0.005%, N≤0.005%；Surplus is Fe and inevitable impurity.
Wherein, the microstructure of dual phase steel is mainly made of ferrite and martensite.
Wherein, dual phase steel yield strength is 570~650MPa, and tensile strength is 1000~1080MPa, elongation (A80) be 10.0~15.0%.
The present invention also provides the preparation method of 980MPa grades of low-carbon cold rolling dual phase steels, include the following steps: according to above-mentioned double Phase steel chemical composition mass percent is smelted, and V content is controlled in converter, slab is cast as after smelting, then hot rolling, Acid rolls, annealing process, obtains 980MPa grades of low-carbon cold rolling dual phase steels.
Wherein, hot rolling includes heating, roughing, finish rolling and batches.
Wherein, in course of hot rolling, heating temperature is 1200~1300 DEG C, and finish rolling start rolling temperature is 1000~1100 DEG C, essence Rolling finishing temperature is 850~950 DEG C, and coiling temperature is 600~700 DEG C.
Wherein, acid rolls for cold rolling after pickling, and cold rolling reduction ratio is 40~70%.
Wherein, annealing temperature is 800~850 DEG C, slowly cools to 700~750 DEG C from annealing temperature, is quickly cooled down immediately To 200~300 DEG C of overaging temperature, it is finally cooled to room temperature, smooth 0.20~0.50%.
Further, annealing temperature is 800~850 DEG C, is cooled to 700~750 DEG C from 800~850 DEG C with 2~5 DEG C/s, 200~300 DEG C of overaging temperature are cooled to 30~80 DEG C/s immediately, is finally cooled to room temperature, smooth 0.20~0.50%.
Beneficial effects of the present invention:
1, low-carbon cold rolling dual phase steel yield strength provided by the invention be 570~650MPa, tensile strength be 1000~ 1080MPa, elongation (A80) it is 10.0~15.0%, microstructure is mainly made of ferrite and martensite, is had good Mechanical property, welding performance and forming property；
2, low-carbon cold rolling dual phase steel of the present invention is free of expensive Nb, Mo, and smelting process controls V content in converter, Production cost reduces；
3, it is not added with the microalloy element that Nb etc. improves hot rolling deformation drag, production difficulty reduces.
Detailed description of the invention
Fig. 1 is the continuous annealing process schematic diagram of low-carbon cold rolling dual phase steel of the present invention；
Fig. 2 is the microstructure morphology of low-carbon cold rolling dual phase steel of the present invention.
Specific embodiment
The present invention provide 980MPa grade low-carbon cold rolling dual phase steels, chemical component mass percent for C:0.05~ 0.10%, Si:0.30~0.70%, Mn:2.00~2.50%, Cr:0.40~0.80%, Al:0.01~0.06%, V:0.05 ~0.15%, P≤0.020%, S≤0.010%, N≤0.006%, surplus are Fe and inevitable impurity.
Preferably, the present invention provides 980MPa grades of low-carbon cold rolling dual phase steels, and chemical component mass percent is C:0.06 ~0.08%, Si:0.40~0.60%, Mn:2.20~2.50%, Cr:0.60~0.80%, Al:0.02~0.05%, V: 0.05~0.10%, P≤0.015%, S≤0.005%, N≤0.005%；Surplus is Fe and inevitable impurity.
C determines the intensity, plasticity and forming property of steel plate as one of most important component of dual phase steel.C is steel material The most apparent element of solid solution strengthening effect in material, solid solution C content increases by 0.1% in steel, and about 450MPa can be improved in intensity.C contains When measuring too low, the stability and martensite hardenability of austenite decline, and lead to low strength, are generally not less than in dual phase steel 0.02%；When C content is excessively high, the plasticity and welding performance of dual phase steel decline, and are generally not more than 0.20% in dual phase steel.Therefore, C content of the present invention is 0.05~0.10%, preferably 0.06~0.08%.
Si can be solid-solution in the intensity that steel is improved in ferrite and austenite, and effect is only second to C, P, compared with Mn, Cr, Ti and Ni Equal elements are strong；Si can also inhibit the precipitation of carbide in ferrite, be enriched with solid solution C atom sufficiently into austenite, thus Improve its stability.However, the scale on surface that Si is formed in heating furnace is difficult to remove when Si too high levels, increase Dephosphorization difficulty.Therefore, Si content of the present invention is 0.30~0.70%, preferably 0.40~0.60%.
Mn is common solution strengthening element in good deoxidier and desulfurizing agent and steel, general not low in dual phase steel In 1.20%.Mn can both form a variety of carbide in conjunction with C and play the role of precipitation strength, and also dissolving in enhances solid solution in matrix Strengthening effect.Mn easily forms high melting compound MnS in conjunction with S, so that the hot-short phenomenon due to caused by FeS is eliminated or weakens, Improve the hot-working character of steel.Stabilization of austenite can be improved in Mn, moves to right C curve, to significantly reduce facing for martensite Boundary's cooling rate.Therefore, Mn content is 2.00~2.50%, preferably 2.20~2.50% in the present invention.
Cr can significantly postpone pearlite and bainite transformation, and austenite is made sufficiently to be changed into martensitic structure, to obtain Obtain higher tensile strength.Since Cr has apparent cost advantage compared with Mo, so largely making an addition to cold rolling and hot galvanizing two-phase In steel.Therefore, in the present invention, Cr content is 0.30~0.80%, preferably 0.60~0.80%.
V mainly exists in the form of VC in dual phase steel, has the function of that significant crystal grain refinement and intergranular precipitation are strengthened.In heat In cooling procedure after rolling, VC provides a large amount of nucleation sites for ferrite crystal grain, so that ferrite crystal grain obviously refines.In cold rolling During annealing heating, undissolved VC particle can be with pinning ferrite grain boundaries, to play the role of refining crystal grain；Annealing temperature When increasing to two-phase section, VC solution temperature is lower, therefore is completely dissolved in matrix, while being dissolved C atom and being enriched with into austenite To improve its stability；In annealing process, the VC in ferrite will be precipitated again, to produce apparent precipitation strength.Cause This, in the present invention, V content is 0.05~0.15%, preferably 0.05~0.10%.
Al is deoxidier common in steel, while can form AlN pinning crystal boundary, to play the role of refining crystal grain； In addition, Al is similar to Si effect, Carbide Precipitation can be inhibited, to make the sufficiently rich carbon of austenite.Therefore, Al contains in the present invention Amount is 0.01~0.06%, preferably 0.02~0.05%.
In the design of chemical component, the present invention using low C guarantee cold-rolled biphase steel superior weldability energy, higher Mn, Cr substitutes Mo to reduce its production cost；Come fining ferrite and martensitic crystal grains with trace V, at the same VC disperse educt play it is heavy The effect that shallow lake is strengthened.
The present invention also provides the preparation method of 980MPa grades of low-carbon cold rolling dual phase steels, according to above-mentioned two-phase steel chemical composition into Row smelt, V content is controlled in converter, slab is cast as after smelting, then hot rolling, acid roll, annealing process, obtain 980MPa Grade low-carbon cold rolling dual phase steel.
Specifically, it can carry out in accordance with the following steps:
(1) smelting procedure: being smelted according to above-mentioned designed chemical component, and is controlled V content in converter and (passed through Control V content in original molten iron), then it is cast as slab；
(2) hot-rolled process: obtaining hot rolled coil after heating, dephosphorization, roughing, finish rolling and section cooling for slab, wherein Finish rolling start rolling temperature is 1000~1100 DEG C, and finish rolling finishing temperature is 850~950 DEG C, and coiling temperature is 600~700 DEG C；
(3) acid rolls process: by above-mentioned hot rolled coil, cold rolling becomes cold-rolled thin steel strip after overpickling, and wherein cold rolling reduction ratio is 40~70%；
(4) by above-mentioned cold-rolled thin steel strip after continuous annealing, required cold-rolled biphase steel steel continuous annealing process: is made Plate；Wherein annealing temperature is 800~850 DEG C, slowly cools to 700~750 DEG C of rapid cooling start temperature from annealing temperature, immediately fastly Speed is cooled to 200~300 DEG C of overaging temperature, and slow cooling rate CR1 is 2~5 DEG C/s, and rapid cooling rate CR2 is 30~80 DEG C/s, It is finally cooled to room temperature, smooth 0.20~0.50%.
The present invention will be further explained by the following examples and explanation.
Low-carbon cold rolling dual phase steel DP1 and DP2 is prepared according to the method for the present invention respectively in embodiment 1 and embodiment 2, specifically Steps are as follows:
(1) pass through smelting process, be prepared for the dual phase steel slab of chemical component percentage as shown in table 1 below；
1 two-phase steel chemical composition (wt.%) of table
Number C Si Mn P S Als Cr V N
DP1 0.06 0.60 2.20 0.015 0.003 0.035 0.80 0.05 0.0036
DP2 0.08 0.40 2.50 0.014 0.002 0.044 0.60 0.10 0.0038
(2) slab is obtained into hot rolled coil after heating, dephosphorization, hot rolling and section cooling, wherein finish rolling start rolling temperature is 1000~1100 DEG C, finish rolling finishing temperature is 850~950 DEG C, and coiling temperature is 600~700 DEG C, and specific hot-rolled process parameter is such as Shown in the following table 2；
2 dual phase steel hot rolling main technologic parameters of table
Number Heating temperature/DEG C Final rolling temperature/DEG C Finishing temperature/DEG C Coiling temperature/DEG C Hot rolled thickness/mm
DP1 1240 1060 850~900 600~650 4.0
DP2 1240 1080 900~950 650~700 3.0
(3) by after hot rolled coil pickling, it is cold rolled to Thin Strip Steel, wherein the cold rolling reduction ratio of DP1 and DP2 is respectively 55.0% He 60.0%；
(4) required product is made in cold-rolled thin steel strip after continuous annealing process is handled, wherein annealing temperature be 800~ 850 DEG C, 700~750 DEG C of rapid cooling start temperature are slowly cooled to from annealing temperature, is quickly cooled to overaging temperature 200 immediately ~300 DEG C, slow cooling rate CR1 is 2~5 DEG C/s, and rapid cooling rate CR2 is 30~80 DEG C/s, is finally cooled to room temperature, smooth 0.20~0.50%, annealing process schematic diagram is as shown in Figure 1, specific cold rolled annealed technological parameter is as shown in table 3.
The cold rolled annealed main technologic parameters of table 3
Number Annealing temperature/DEG C Slow cooling temperature/DEG C Overaging temperature/DEG C Rapid cooling rate/DEG C/s
DP1 800 700 200 41
DP2 850 750 300 54
The cold-rolled biphase steel microstructure that is prepared through above-mentioned technique as shown in Fig. 2, its mechanical property and the prior art pair Than as shown in table 4 below.
4 present invention of table is compared with existing cold-rolled biphase steel mechanical property
Number Yield strength/MPa Tensile strength/MPa Elongation A80/ % Yield tensile ratio
DP1 586 1014 14.6 0.58
DP2 625 1072 11.2 0.58
CN 102828119A 447 1000 12.6 0.45
CN 102586688A 600 1023 14.0 0.59
The result shows that cold-rolled biphase steel microstructure prepared by the present invention is made of tiny ferrite and martensite, Yield strength (570~650MPa) and yield tensile ratio (≤0.60) are lower, tensile strength (1000-1080MPa) and elongation (10.0-15.0%) is higher.Low-carbon cold rolling dual phase steel is not added with the expensive microalloy element such as Mo, Nb, so cost advantage is obvious, C content reduction simultaneously makes it have excellent forming property and welding performance.

Claims (10)

1.980MPa grades of low-carbon cold rolling dual phase steels, it is characterised in that: its chemical component mass percent is C:0.05~0.10%, Si:0.30~0.70%, Mn:2.00~2.50%, Cr:0.40~0.80%, Al:0.01~0.06%, V:0.05~ 0.15%, P≤0.020%, S≤0.010%, N≤0.006%, surplus are Fe and inevitable impurity.
2. 980MPa grades of low-carbon cold rolling dual phase steel according to claim 1, it is characterised in that: its chemical component quality percentage Than for C:0.06~0.08%, Si:0.40~0.60%, Mn:2.20~2.50%, Cr:0.60~0.80%, Al:0.02~ 0.05%, V:0.05~0.10%, P≤0.015%, S≤0.005%, N≤0.005%；Surplus is Fe and inevitable miscellaneous Matter.
3. 980MPa grades of low-carbon cold rolling dual phase steel according to claim 1 or 2, it is characterised in that: the dual phase steel it is micro- Tissue is seen mainly to be made of ferrite and martensite.
4. described in any item 980MPa grades of low-carbon cold rolling dual phase steels according to claim 1~3, it is characterised in that: the two-phase Steel yield strength is 570~650MPa, and tensile strength is 1000~1080MPa, and elongation is 10.0~15.0%.
The preparation method of 5.980MPa grades of low-carbon cold rolling dual phase steels, it is characterised in that include the following steps: according to claim 1 or Chemical component mass percent described in 2 is smelted, and V content is controlled in converter, slab is cast as after smelting, then through heat Roll, acid rolls, annealing process, obtain 980MPa grades of low-carbon cold rolling dual phase steels.
6. the preparation method of 980MPa grades of low-carbon cold rolling dual phase steel according to claim 5, it is characterised in that: the hot rolling Including heating, roughing, finish rolling and batch.
7. the preparation method of 980MPa grades of low-carbon cold rolling dual phase steel according to claim 5 or 6, it is characterised in that: described In course of hot rolling, finish rolling start rolling temperature is 1000~1100 DEG C, and finish rolling finishing temperature is 850~950 DEG C, coiling temperature 600 ~700 DEG C.
8. according to the preparation method of the described in any item 980MPa grades of low-carbon cold rolling dual phase steels of claim 5~7, feature exists In: cold rolling after the acid rolls for pickling, cold rolling reduction ratio are 40~70%.
9. according to the preparation method of the described in any item 980MPa grades of low-carbon cold rolling dual phase steels of claim 5~8, feature exists In: the annealing temperature is 800~850 DEG C, slowly cools to 700~750 DEG C from 800~850 DEG C, was quickly cooled to immediately 200~300 DEG C of aging temp, it is finally cooled to room temperature, smooth 0.20~0.50%.
10. according to the preparation method of the described in any item 980MPa grades of low-carbon cold rolling dual phase steels of claim 5~9, feature exists Be 800~850 DEG C in: the annealing temperature, be cooled to 700~750 DEG C from 800~850 DEG C with 2~5 DEG C/s, immediately with 30~ 80 DEG C/s is cooled to 200~300 DEG C of overaging temperature, is finally cooled to room temperature, and smooth 0.20~0.50%.
CN201811429155.1A 2018-11-27 2018-11-27 980MPa grades of low-carbon cold rolling dual phase steels and preparation method thereof Pending CN109280854A (en)

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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
CN111979489A (en) * 2020-09-07 2020-11-24 鞍钢股份有限公司 780 MPa-grade high-plasticity cold-rolled DH steel and preparation method thereof
CN112322975A (en) * 2020-10-27 2021-02-05 北京首钢股份有限公司 Steel for ultrahigh-strength cold-rolled carriage plate and manufacturing method thereof
CN113957221A (en) * 2021-10-21 2022-01-21 山东钢铁集团日照有限公司 Preparation method and application of DP980 cold-hardened steel strip
CN114535810A (en) * 2022-04-07 2022-05-27 攀钢集团攀枝花钢铁研究院有限公司 980 MPa-grade cold-rolled dual-phase steel with low yield ratio and welding method of acid rolling process thereof
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CN110093491A (en) * 2019-05-17 2019-08-06 中冶赛迪工程技术股份有限公司 A kind of cold-rolled galvanized duplex steel and its manufacturing method
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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
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CN113957221B (en) * 2021-10-21 2023-11-24 山东钢铁集团日照有限公司 Preparation method and application of DP980 chilled steel strip
CN114535810A (en) * 2022-04-07 2022-05-27 攀钢集团攀枝花钢铁研究院有限公司 980 MPa-grade cold-rolled dual-phase steel with low yield ratio and welding method of acid rolling process thereof
CN114535810B (en) * 2022-04-07 2024-07-12 攀钢集团攀枝花钢铁研究院有限公司 980 MPa-grade low-yield-ratio cold-rolled dual-phase steel and welding method for acid rolling process thereof

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Application publication date: 20190129