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CN109518080A - Strong dual phase steel of cold rolling low cost superelevation and preparation method thereof - Google Patents

Strong dual phase steel of cold rolling low cost superelevation and preparation method thereof Download PDF

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Publication number
CN109518080A
CN109518080A CN201811427852.3A CN201811427852A CN109518080A CN 109518080 A CN109518080 A CN 109518080A CN 201811427852 A CN201811427852 A CN 201811427852A CN 109518080 A CN109518080 A CN 109518080A
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China
Prior art keywords
phase steel
cold
rolling
strength
temperature
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CN201811427852.3A
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Inventor
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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Priority to CN201811427852.3A priority Critical patent/CN109518080A/en
Publication of CN109518080A publication Critical patent/CN109518080A/en
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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
    • C21D8/0221—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
    • 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
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

本发明涉及冷轧低成本超高强双相钢及其制备方法，属于汽车用高强钢技术领域。本发明解决的技术问题是现有1180MPa级冷轧双相钢生产成本高、生产难度大。本发明提供冷轧低成本超高强双相钢及其制备方法，化学成分质量百分比为C：0.12～0.17％，Si：0.10～0.60％，Mn：2.00～2.50％，Al：0.01～0.06％，Cr：0.30～0.80％，在转炉中控制铁水V含量，然后经热轧、酸轧、退火工艺得到冷轧超高强双相钢。本发明的冷轧超高强双相钢力学性能和成形性能优良，成本优势明显，具有显著的经济效益和社会效益。

The invention involves cold rolling and low -cost super high -strength double -phase steel and its preparation methods, which belongs to the field of high -strength steel technology for automobiles. The technical problem solved by the present invention is that the current 1180MPA -class cold -rolled double -phase steel has a high production cost and difficult production. The invention provides a cold-rolled low-cost ultra-high-strength dual-phase steel and a preparation method thereof. The mass percentage of the chemical composition is C: 0.12-0.17%, Si: 0.10-0.60%, Mn: 2.00-2.50%, Al: 0.01-0.06%, CR: 0.30 ～ 0.80 %, control the iron V content in the turntable, and then get cold rolled high -strength double -phase steel through hot rolling, acid rolling, and annealing process. The cold -rolled high -strength double -phase steel mechanical performance and forming performance of the invention are excellent, the cost advantage is obvious, and it has significant economic and social benefits.

Description

Strong dual phase steel of cold rolling low cost superelevation and preparation method thereof
Technical field
The invention belongs to automobile high-strength steel technical fields, and in particular to the strong dual phase steel of cold rolling low cost superelevation 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 CN 102021483A discloses a kind of tensile strength 1200MPa grades of cold-rolled biphase steels and preparation method, Its preferred chemical component percentage are as follows: C:0.19~0.21%, Si:0.70~0.90%, Mn:1.90~2.10%, Cr:0.01 ~0.02%, Nb:0.02~0.04%, surplus are Fe and inevitable impurity；By 820-860 DEG C of heat preservation, 710 DEG C of slow cooling, 45~55 DEG C/s rapid cooling, 240-320 DEG C of Wetted constructures have obtained the cold-rolled biphase steel that tensile strength is greater than 1200MPa.Although There is excellent mechanical property by cold-rolled biphase steel prepared by above-mentioned chemical component and production method, but higher C content and Si content causes welding performance poor, and adding micro Nb leads to high hot rolling load, and it is extensive on automobile to necessarily affect dual phase steel Using.
Patent document CN 102021482A discloses a kind of cold-rolled galvanized duplex steel and its manufacturing method, chemistry at Divide percentage are as follows: C:0.095~0.12%, Si:0.80~0.12%, Mn:1.90~2.50%, Cr:0.40~0.60%, Nb:0.005~0.025%, Mo:0.04~0.30%, surplus are Fe and inevitable impurity；Pass through 760-840 DEG C of heat preservation, 1 ~40 DEG C/s rapid cooling, 450-465 DEG C of hot galvanizing have obtained the hot dip galvanized dual phase steel that tensile strength is greater than 1180MPa.Although passing through This method is prepared for the qualified strong dual phase steel of superelevation, however dual phase steel needs to add the expensive microalloy element such as Nb, Mo, not only makes Production cost obviously increases, while in the hot rolling, the effects of Nb inhibits austenite recrystallization, so that hot rolling difficulty is obvious It improves.
Summary of the invention
Present invention solves the technical problem that being that existing 1180MPa 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 the strong dual phase steel of cold rolling low cost superelevation, chemical component matter Measure percentage are as follows: C:0.12~0.17%, Si:0.10~0.60%, Mn:2.00~2.50%, Al:0.01~0.06%, Cr: 0.30~0.80%, V:0.05~0.20%, P≤0.015%, S≤0.005%, N≤0.006%, surplus are Fe and can not keep away Exempt from impurity.
Preferably, the present invention provides the strong dual phase steel of cold rolling low cost superelevation, chemical component mass percent are as follows: C:0.13 ~0.16%, Si:0.30~0.60%, Mn:2.20~2.50%, Al:0.02~0.05%, Cr:0.50~0.80%, V: 0.05~0.10%, P≤0.015%, S≤0.010%, N≤0.005%, surplus are 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 850-950MPa, tensile strength 1200-1300MPa, elongation 5.0- 10.0%.
The present invention also provides the preparation method of the strong dual phase steel of cold rolling low cost superelevation, 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 the strong dual phase steel of cold rolling low cost superelevation.
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 40~60%.
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, the strong dual phase steel yield strength of cold rolling low cost superelevation provided by the invention is 850-950MPa, and tensile strength is 1200-1300MPa, elongation 5.0-10.0%, microstructure are mainly made of ferrite and martensite, have good power Learn performance, welding performance and forming property；
2, the strong two-phase of cold rolling low cost superelevation of the present invention is free of expensive Nb, Mo, and smelting process controls V in converter Content, production cost reduce；
3, the present invention is not added with the microalloy element that Nb etc. improves hot rolling deformation drag, and production difficulty reduces.
Detailed description of the invention
Fig. 1 is the continuous annealing process schematic diagram of cold-rolled biphase steel of the present invention；
Fig. 2 is the microstructure morphology of cold-rolled biphase steel of the present invention.
Specific embodiment
The present invention provides the strong dual phase steel of cold rolling low cost superelevation, chemical component mass percent are as follows: and C:0.12~ 0.17%, Si:0.10~0.60%, Mn:2.00~2.50%, Al:0.01~0.06%, Cr:0.30~0.80%, V:0.05 ~0.20%, P≤0.015%, S≤0.005%, N≤0.006%, surplus are Fe and inevitable impurity.
Preferably, the present invention provides the strong dual phase steel of cold rolling low cost superelevation, chemical component mass percent are as follows: C:0.13 ~0.16%, Si:0.30~0.60%, Mn:2.20~2.50%, Al:0.02~0.05%, Cr:0.50~0.80%, V: 0.05~0.10%, P≤0.015%, S≤0.010%, N≤0.005%, surplus are 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 be C:0.12~0.17%, preferably 0.13~0.16%.
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 0.10~0.60%%, preferably 0.30~0.60%.
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.
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%.
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 or hot galvanizing two-phase In steel.Therefore, in the present invention, Cr content is 0.30~0.80%, preferably 0.50~0.80%.
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 0.05~0.20%, preferably 0.05~0.10%.
In the design of chemical component, the present invention uses higher C, Mn, Cr content to guarantee the stability of cold rolling austenite And harden ability, to obtain the martensite of high-volume fractional；Using trace V come fining ferrite and martensitic crystal grains, while VC Disperse educt plays the effect of precipitation strength, while resistant to hydrogen can be improved and cause delayed fracture property.
The present invention also provides the preparation method of the strong dual phase steel of cold rolling low cost superelevation, 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, it is low to obtain cold rolling The strong dual phase steel of cost superelevation.
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 Heating temperature is 1200~1300 DEG C, and finish rolling start rolling temperature is 1000~1100 DEG C, and finish rolling finishing temperature is 850~950 DEG C, volume Taking 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 40~60%；
(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 be 800~850 DEG C, from annealing temperature with 2~5 DEG C/s slowly cool to rapid cooling start temperature 700~ 750 DEG C, it is quickly cooled to 200~300 DEG C of overaging temperature immediately, slow cooling rate CR1 is 2~5 DEG C/s, rapid cooling rate CR2 For 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.
Embodiment 1 and embodiment 2 respectively according to the method for the present invention be prepared the strong dual phase steel DP1 of cold rolling low cost superelevation and DP2, the specific 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 0.13 0.60 2.50 0.010 0.005 0.02 0.50 0.05 0.004
DP2 0.16 0.30 2.20 0.012 0.003 0.05 0.80 0.10 0.004
(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 1250 1070 850~900 600~650 2.50
DP2 1250 1080 900~950 650~700 3.00
(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 52.0% He 50.0%；
(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 57
DP2 850 750 300 42
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 862 1203 9.1 0.71
DP2 925 1287 6.7 0.72
CN 102021483A 665 1219 9.5(A50) 0.55
CN 102021482A 691 1210 11.4(A50) 0.57
The result shows that cold-rolled biphase steel microstructure prepared by the present invention is made of tiny ferrite and martensite, Yield strength (850-950MPa) is lower, and tensile strength (1200-1300MPa) and elongation (5.0-10.0%) are higher.Cold rolling The inexpensive strong dual phase steel of superelevation so cost advantage is obvious, while having excellent forming without the expensive microalloy element such as Mo, Nb Performance.

Claims (10)

1.冷轧低成本超高强双相钢，其特征在于：其化学成分质量百分比为C：0.12～0.17％，Si：0.10～0.60％，Mn：2.00～2.50％，Al：0.01～0.06％，Cr：0.30～0.80％，V：0.05～0.20％，P≤0.015％，S≤0.005％，N≤0.006％，余量为Fe及不可避免杂质。1. Cold-rolled low-cost ultra-high-strength dual-phase steel, characterized in that: the mass percentage of its chemical composition is C: 0.12-0.17%, Si: 0.10-0.60%, Mn: 2.00-2.50%, Al: 0.01-0.06%, Cr: 0.30-0.80%, V: 0.05-0.20%, P≤0.015%, S≤0.005%, N≤0.006%, and the balance is Fe and unavoidable impurities. 2.根据权利要求1所述的冷轧低成本超高强双相钢，其特征在于：其化学成分质量百分比为C：0.13～0.16％，Si：0.30～0.60％，Mn：2.20～2.50％，Al：0.02～0.05％，Cr：0.50～0.80％，V：0.05～0.10％，P≤0.015％，S≤0.010％，N≤0.005％，余量为Fe及不可避免杂质。2. The cold-rolled low-cost ultra-high-strength dual-phase steel according to claim 1, characterized in that: its chemical composition mass percentage is C: 0.13-0.16%, Si: 0.30-0.60%, Mn: 2.20-2.50%, Al: 0.02-0.05%, Cr: 0.50-0.80%, V: 0.05-0.10%, P≤0.015%, S≤0.010%, N≤0.005%, and the balance is Fe and unavoidable impurities. 3.根据权利要求1或2所述的冷轧低成本超高强双相钢，其特征在于：所述双相钢的微观组织主要由铁素体和马氏体组成。3. The cold-rolled low-cost ultra-high-strength dual-phase steel according to claim 1 or 2, characterized in that: the microstructure of the dual-phase steel is mainly composed of ferrite and martensite. 4.根据权利要求1～3任一项所述的冷轧低成本超高强双相钢，其特征在于：所述双相钢屈服强度为850-950MPa，抗拉强度为1200-1300MPa，伸长率为5.0-10.0％。4. The cold-rolled low-cost ultra-high-strength dual-phase steel according to any one of claims 1-3, characterized in that: the yield strength of the dual-phase steel is 850-950MPa, the tensile strength is 1200-1300MPa, and the elongation The rate is 5.0-10.0%. 5.冷轧低成本超高强双相钢的制备方法，其特征在于包括如下步骤：根据权利要求1或2所述的化学成分质量百分比进行冶炼，在转炉中控制V含量，冶炼后铸造成板坯，然后经热轧、酸轧、退火工艺，得到冷轧低成本超高强双相钢。5. The preparation method of cold-rolled low-cost ultra-high-strength dual-phase steel, which is characterized in that it includes the following steps: smelting according to the mass percentage of the chemical composition described in claim 1 or 2, controlling the V content in the converter, and casting into plates after smelting The billet is then subjected to hot rolling, acid rolling, and annealing processes to obtain cold-rolled low-cost ultra-high-strength dual-phase steel. 6.根据权利要求5所述的冷轧低成本超高强双相钢的制备方法，其特征在于：所述热轧包括加热、粗轧、精轧和卷取。6. The method for preparing cold-rolled low-cost ultra-high-strength dual-phase steel according to claim 5, wherein the hot rolling includes heating, rough rolling, finish rolling and coiling. 7.根据权利要求5或6所述的冷轧低成本超高强双相钢的制备方法，其特征在于：所述热轧过程中，加热温度为1200～1300℃，精轧开轧温度为1000～1100℃，精轧终轧温度为850～950℃，卷取温度为600～700℃。7. The method for preparing cold-rolled low-cost ultra-high-strength dual-phase steel according to claim 5 or 6, characterized in that: in the hot rolling process, the heating temperature is 1200-1300°C, and the finishing rolling start temperature is 1000°C ~1100°C, finishing rolling temperature is 850~950°C, coiling temperature is 600~700°C. 8.根据权利要求5～7任一项所述的冷轧低成本超高强双相钢的制备方法，其特征在于：所述酸轧为酸洗后冷轧，冷轧压下率为40～60％。8. The method for preparing cold-rolled low-cost ultra-high-strength dual-phase steel according to any one of claims 5 to 7, characterized in that: the acid rolling is cold rolling after pickling, and the cold rolling reduction rate is 40-40. 60%. 9.根据权利要求5～8任一项所述的冷轧低成本超高强双相钢的制备方法，其特征在于：所述退火温度为800～850℃，从800～850℃缓慢冷却至700～750℃，随即快速冷却至过时效温度200～300℃，最后冷却至室温，平整0.20～0.50％。9. The method for preparing cold-rolled low-cost ultra-high-strength dual-phase steel according to any one of claims 5-8, characterized in that: the annealing temperature is 800-850°C, slowly cooled from 800-850°C to 700°C ~750°C, then rapidly cooled to the overaging temperature of 200~300°C, and finally cooled to room temperature, leveling 0.20~0.50%. 10.根据权利要求5～9任一项所述的冷轧低成本超高强双相钢的制备方法，其特征在于：所述退火温度为800～850℃，从800～850℃以2～5℃/s冷却至700～750℃，随即以30～80℃/s冷却至过时效温度200～300℃，最后冷却至室温，平整0.20～0.50％。10. The method for preparing cold-rolled low-cost ultra-high-strength dual-phase steel according to any one of claims 5-9, characterized in that: the annealing temperature is 800-850°C, and the temperature ranges from 800-850°C at 2-5 °C/s cooling to 700-750 °C, then cooling at 30-80 °C/s to overaging temperature 200-300 °C, and finally cooling to room temperature, leveling 0.20-0.50%.
CN201811427852.3A 2018-11-27 2018-11-27 Strong dual phase steel of cold rolling low cost superelevation and preparation method thereof Pending CN109518080A (en)

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