CN112760554A - High-strength steel with excellent ductility and manufacturing method thereof - Google Patents

High-strength steel with excellent ductility and manufacturing method thereof Download PDF

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CN112760554A
CN112760554A CN201910998434.8A CN201910998434A CN112760554A CN 112760554 A CN112760554 A CN 112760554A CN 201910998434 A CN201910998434 A CN 201910998434A CN 112760554 A CN112760554 A CN 112760554A
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strength steel
less
ductility
steel
cooling
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陈孟
钟勇
汪水泽
李旭飞
王利
毛新平
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Baoshan Iron and Steel Co Ltd
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Baoshan Iron and Steel Co Ltd
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Priority to PCT/CN2020/122085 priority patent/WO2021078111A1/en
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • 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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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • 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
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
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    • 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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    • 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
    • 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

Abstract

The invention discloses high-strength steel with excellent ductility, which comprises the following chemical elements in percentage by mass: c: 0.15-0.25 wt%; si: 1.00-2.00 wt%; mn: 1.50-3.00 wt%; al: 0.03-0.06 wt%; the balance being Fe and other unavoidable impurities. Further, the present invention also discloses a method for producing the high-strength steel excellent in ductility, comprising the steps of: (1) smelting and sheet billet continuous casting: wherein the thickness of the plate blank at the outlet end of the continuous casting is controlled to be 55-60 mm; (2) heating; (3) hot rolling: the thickness of the oxide skin on the surface of the hot-rolled steel strip is less than or equal to 5 mu m, and the (FeO + Fe) in the oxide skin on the surface of the hot-rolled steel strip3O4) Less than or equal to 40wt percent; (4) acid washing or acid washing plus cold rolling; (5) and (5) continuously annealing.

Description

High-strength steel with excellent ductility and manufacturing method thereof
Technical Field
The invention relates to a steel grade and a manufacturing method thereof, in particular to high-strength steel and a manufacturing method thereof.
Background
In recent years, automobile lightweight technology represented by automobile body lightweight provides powerful support for development of 'energy conservation, emission reduction, safety and economy' of automobiles. The advanced high-strength steel reduces the thickness of the steel plate by improving the strength of the steel plate, and simultaneously keeps excellent forming performance, so that the high-strength steel is the most comprehensive competitive material for vehicle body light weight at present and is also the direction of key attention of steel mills and main engine plants.
Advanced high-strength steels based on the transformation induced plasticity (TRIP) effect have good ductility while maintaining high strength. From the microstructure, the TRIP steel is composed of ferrite, bainite and residual austenite, the phase structure limits further improvement of the strength, and the strength of the TRIP steel can be continuously improved by replacing the bainite with the martensite as a main strengthening phase. For advanced high-strength steel based on the TRIP effect, the main factors determining the ductility are the form, volume fraction and stability of the retained austenite in the steel, which are closely related to the size and carbon content of the retained austenite.
In order to ensure the strength and the ductility of the steel plate, the existing advanced high-strength steel is mainly based on carbon-manganese steel components, and more alloy elements such as Cr, Mo, Nb, Ti, B and the like are added, so that the material cost is increased, and the manufacturability of steelmaking, hot rolling and cold rolling is difficult.
For example: chinese patent publication No. CN106574342A, published as 2017, 4 and 19, entitled "high-strength steel sheet and method for producing same, and method for producing high-strength galvanized steel sheet" discloses a high-strength steel sheet. In the technical solution disclosed in this patent document, the manufacturing method is: heating a steel billet meeting the composition conditions to 1100-1300 ℃, keeping the temperature of a finish rolling outlet side at 800-1000 ℃, keeping the average coiling temperature at 450-Ac 1 for 900-36000 s after pickling, carrying out cold rolling at a reduction ratio of more than 30%, heating the steel plate to 820-950 ℃ for primary annealing, cooling to below Ms temperature at an average cooling speed of more than 15 ℃/s till 500 ℃, heating to 740-840 ℃ for secondary annealing, cooling to 150-350 ℃ at a cooling speed of 1-15 ℃/s, reheating to 350-550 ℃ and keeping the temperature for more than 10 s. It should be noted that, in the technical solution disclosed in the patent document, heating and rolling are required, and two annealing treatments are adopted, so that the production process is complicated, and the manufacturing cost is increased, thereby greatly limiting the application of the method in the field of automobiles.
Another example is: chinese patent publication No. CN104245971A, published 24/12/2014, entitled "high-strength cold-rolled steel sheet and method for producing the same", discloses a high-strength cold-rolled steel sheet. In the technical solution disclosed in this patent document, the components are: 0.1 to 0.3 percent of C, 0.4 to 1.0 percent of Si, 2.0 to 3.0 percent of Mn, less than or equal to 0.6 percent of Cr, 1.0 to 1.8 percent of Si +0.8Al + Cr, 0.2 to 0.8 percent of Al, less than 0.1 percent of Nb, less than 0.3 percent of Mo, less than 0.2 percent of Ti, less than 0.1 percent of V, less than 0.5 percent of Cu, less than 0.5 percent of Ni, less than or equal to 0.01 percent of S, less than or equal to 0.02 percent of P, less than or equal to 0.02 percent of N, less than 0.005 percent of B, less than 0.005 percent of Ca, less than 0.005 percent of Mg, less than 0.005 percent of REM. The microstructure (vol%) was: 5 to 20 percent of retained austenite, more than or equal to 80 percent of bainite, bainitic ferrite and tempered martensite, less than or equal to 10 percent of polygonal ferrite and less than or equal to 20 percent of martensite-austenite component. It should be noted that, because the steel type component related to the technical proposal needs to add a certain amount of Cr and Mo, although the tensile strength is more than or equal to 980MPa, the elongation at time is only about 14%, and the advantages of the steel for automobile parts, such as cost and formability, are not obvious.
For another example: international patent document No. WO2018/116155, published as 2018, 6/28, entitled "HIGH-STRENGTH COLD ROLLED steel STEEL SHEET HAVING HIGH formed into excellent ROLLED steel OF MANUFACTURING thermal" discloses a HIGH-STRENGTH COLD ROLLED steel sheet having HIGH formability. In the technical solution disclosed in this patent document, the components are: 0.19 to 0.24 percent of C, 1.9 to 2.2 percent of Mn, 1.4 to 1.6 percent of Si, 0.01 to 0.06 percent of Al, 0.2 to 0.5 percent of Cr, less than or equal to 0.02 percent of P, less than or equal to 0.003 percent of S, and one or more of the following components: 0.0010 to 0.06 percent of Nb, 0.001 to 0.08 percent of Ti, 0.001 to 0.1 percent of V, 0.001 to 0.005 percent of Ca, and the balance of Fe and inevitable impurities. It should be noted that the steel grade according to this technical solution has a tensile strength of not less than 1150MPa, an elongation of not less than 13%, and a hole expansion ratio of not less than 30%, and is not suitable as an automotive steel with very strict cost control requirements because it contains a large amount of Cr, Nb, and Ti elements, although it has a high tensile strength.
Disclosure of Invention
An object of the present invention is to provide a high-strength steel having excellent ductility, which is designed using simple components and ensures the strength and ductility of a steel sheet by making full use of the rule of influence of C, Si and Mn on the phase transition of a material.
In order to achieve the above object, the present invention provides a high strength steel with excellent ductility, which comprises the following chemical elements by mass percent:
C：0.15～0.25wt％；
Si：1.00～2.00wt％；
Mn：1.50～3.00wt％；
Al：0.03～0.06wt％；
the balance being Fe and other unavoidable impurities.
In the technical scheme, the common carbon-silicon-manganese steel component design is adopted, and the influence rule of C, Si and Mn elements on the phase change of the material is fully utilized, so that the unification of high strength and high ductility of the high-strength steel is realized, and a steel plate product with excellent performance is finally obtained. The design principle of each chemical element is specifically as follows:
c: in the high-strength steel with excellent ductility, the solubility of C in austenite is much higher than that in ferrite, so that the incubation period before austenite transformation can be prolonged, and the Ms temperature can be reduced. The higher the mass percentage of C, the more the fraction of the retained austenite, the higher the enrichment degree of C in the retained austenite during the partitioning, which is beneficial to enhancing the stability of the retained austenite, generating the TRIP effect and improving the ductility of the material. C is also the most basic solid-solution strengthening element in steel. However, too high a mass percentage of C may reduce the weldability of the steel. Further, when the mass percentage of C in the steel exceeds 0.25%, more twin crystals are likely to occur after quenching, increasing crack sensitivity. Accordingly, in the high-strength steel excellent in ductility according to the present invention, the mass percentage of C is controlled to 0.15 to 0.25 wt%.
Si: in the high-strength steel excellent in ductility according to the present invention, the solubility of Si in carbides is extremely low, and cementite formation is strongly suppressed during the partitioning treatment, so that carbon enrichment into retained austenite is promoted, and the stability of retained austenite is improved. However, too high a mass percentage of Si reduces high temperature plasticity of steel and increases hot rolling defect incidence, and at the same time, a high mass percentage of Si forms stable oxides on the surface of steel sheet and reduces wettability of steel sheet. Based on this, the mass percentage of Si in the high-strength steel having excellent ductility according to the present invention is controlled to be 1.00 to 2.00 wt%.
Mn: in the high-strength steel with excellent ductility, Mn can expand an austenite phase region, reduce Ac3, Ms and Mf points, improve austenite stability and steel hardenability, reduce critical transformation rate, facilitate the storage of retained austenite to room temperature, and simultaneously, Mn can also play a solid solution strengthening effect in the steel. However, too high mass% of Mn aggravates the tendency of grain coarsening, reduces the plasticity and toughness of steel, and deteriorates corrosion resistance and weldability. However, when the mass percentage of Mn is too low, a ferrite-pearlite band structure is generated at a low cooling rate due to segregation. Based on this, the mass percentage of Mn in the high-strength steel excellent in ductility according to the present invention is controlled to be 1.50 to 3.00 wt%.
Al: in the high-strength steel excellent in ductility according to the present invention, when Al exists in a solid solution state, the stacking fault energy is increased, thereby suppressing cementite precipitation and γ -to-martensite transformation, and improving the austenite stability. And Al and C, N form fine and dispersed insoluble particles to refine grains, but Al has a weaker strengthening effect than Si and a weaker ability to stabilize austenite than Si. In addition, the mass percentage of Al is too high, a large amount of oxide inclusions are easily formed, and the continuous casting of steel making is not facilitated. Therefore, the mass percentage of Al is controlled to be 0.03 to 0.06 wt% in the high strength steel having excellent ductility according to the present invention.
Further, in the high-strength steel excellent in ductility according to the present invention, the chemical elements thereof satisfy at least one of the following in mass percent:
C：0.17～0.23wt％；
Si：1.4～1.8wt％；
Mn：1.8～2.3wt％。
further, the high-strength steel excellent in ductility according to the present invention further contains at least one of the following elements:
Cr≤0.5wt％；
Mo≤0.5wt％；
Nb≤0.05wt％；
Ti≤0.05wt％；
V≤0.05wt％；
B≤0.001wt％。
the above Cr, Mo, Nb, Ti, V and B can further improve the properties of the high strength steel of the present invention. For example: cr and Mo can improve the hardenability of steel and adjust the strength of the steel, but Cr can be enriched on the surface of a steel plate to influence the welding performance, and the high mass percent of Mo leads to the increase of the cold rolling deformation resistance of the steel. Another example is: the Nb, Ti and V elements can form fine carbides with C to promote the structure refinement, but the formation of the fine carbides is not beneficial to the enrichment of C into the retained austenite and the stabilization of the retained austenite. For another example: the main function of B is to improve the hardenability of the steel, B is easy to be segregated in austenite grain boundaries and delays the transformation from austenite to ferrite, a small amount of B is added into the steel to play an obvious role, and the steel strength is increased due to the over-high mass percentage of B, which is not beneficial to obtaining good shaping. Therefore, the mass percent of B can be controlled to be less than or equal to 0.001 percent.
In addition, the addition of the above elements increases the cost of the material, and in the technical scheme of the invention, at least one of the above elements can be preferably added in consideration of the combination of performance and cost control.
Still further, in the high strength steel excellent in ductility according to the present invention, each chemical element satisfies at least one of the following:
Cr≤0.25wt％；
Mo≤0.25wt％；
Nb≤0.025wt％；
Ti≤0.02wt％；
V≤0.02wt％。
further, in the high strength steel excellent in ductility according to the present invention, among other unavoidable impurities: p is less than or equal to 0.015 wt%, S is less than or equal to 0.012 wt%, and N is less than or equal to 0.008 wt%.
In the above scheme, P, S, N is an impurity, wherein P can play a solid solution strengthening role, inhibit carbide formation and contribute to improving the stability of retained austenite, but the content of P is too high in mass percentage, which weakens grain boundaries, increases material brittleness and deteriorates welding performance, that is, the positive effect of P is weaker than the negative effect thereof, therefore, the mass percentage of P is preferably controlled to be less than or equal to 0.015 wt%. As for N, since too high a mass percentage of N causes difficulty in steel making and continuous casting and is not favorable for inclusion control, it is preferable to control the mass percentage of N to 0.008 wt% or less.
Further, in the high-strength steel excellent in ductility according to the present invention, the microstructure is 30% to 50% of ferrite, 40% to 60% of martensite and retained austenite.
Further, in the high strength steel excellent in ductility according to the present invention, the ratio of crystal grains of 10 μm or less in ferrite is 80% or more, and the ratio of crystal grains of 5 μm or less is 50% or more.
Further, in the high-strength steel excellent in ductility according to the present invention, wherein the average grain size of the retained austenite is 2 μm or less; and/or the average C content in the retained austenite is more than or equal to 1.1 wt%.
Further, in the high-strength steel with excellent ductility, the yield strength is 550-850 MPa, the tensile strength is 900-1100 MPa, the uniform elongation is not less than 13%, and the elongation at break is 18-28%.
Accordingly, another object of the present invention is to provide a method for manufacturing the above-described high-strength steel excellent in ductility, by using a thin slab continuous casting process in combination with an acid pickling or acid rolling process, and obtaining the high-strength steel excellent in ductility after continuous annealing. The manufacturing method is simple in production, and the elongation of the obtained high-strength steel is obviously improved under the condition of the same strength.
In order to achieve the above object, the present invention provides a method for producing the above high-strength steel having excellent ductility, comprising the steps of:
(1) smelting and sheet billet continuous casting: wherein the thickness of the plate blank at the outlet end of the continuous casting is controlled to be 55-60 mm;
(2) heating;
(3) hot rolling: the thickness of the oxide skin on the surface of the hot-rolled steel strip is less than or equal to 5 mu m, and the (FeO + Fe) in the oxide skin on the surface of the hot-rolled steel strip3O4)≤40wt％；
(4) Acid washing or acid washing plus cold rolling;
(5) and (3) continuous annealing: annealing at 800-920 ℃, and slowly cooling to 680-750 ℃ at a cooling rate of 3-10 ℃/s to obtain ferrite in a certain proportion; then quickly cooling to 220-320 ℃, wherein the cooling speed is 50-1000 ℃/s, so that the austenite is partially transformed into martensite; then heating to 360-460 ℃, preserving the heat for 100-500 s, and finally cooling to room temperature.
In the technical scheme of the invention, because the thin slab continuous casting is adopted in the step (1), a rough rolling process can be omitted, and the hot rolling deformation is reduced, so that the performance of the steel plate in the subsequent step (4) and the step (5) is ensured. In addition, because the thin slab continuous casting is adopted in the step (1), the heat of the slab can be fully utilized, and the energy consumption required by heating is reduced, so that a more uniform ferrite or ferrite + pearlite structure is obtained, a certain amount of fine-grained ferrite is kept in the finished product microstructure in the step 5), and the uniformity of the structure is improved.
In the step (3), the thickness of the scale on the surface of the hot-rolled steel strip is controlled to be less than or equal to 5 mu m, and the (FeO + Fe) in the scale on the surface of the hot-rolled steel strip is controlled to be3O4) 40 wt.% or less, it is possible to facilitate the subsequent step (4) and has an important influence on the properties of the steel sheet obtained after the continuous annealing because: in the technical scheme of the invention, FeO and Fe3O4Specific to Fe2O3Is more difficult to be pickled, and when the thickness of the oxide scale on the surface of the hot rolled steel strip and the (FeO + Fe) in the oxide scale on the surface of the hot rolled steel strip are controlled3O4) The pickling effect can be improved by less than or equal to 40 wt%, the pickled plate can be used for directly and continuously supporting the surface of the pickled plate, the pickled plate can be directly subjected to continuous annealing, the deformation amount of a hot-rolled structure is small, and the pearlite and the ferrite are used as main parts of a steel plate structure, so that the material strength can be reduced under the same continuous annealing condition, the structure is more uniform, and the excellent ductility is obtained.
In the step (5), a homogenized austenite structure or austenite + ferrite structure can be formed by controlling the annealing temperature; then slowly cooling to 680-750 ℃ at a cooling speed of 3-10 ℃/s to further adjust the content of ferrite in the tissue and improve the shaping of the material; then cooling to 220-320 ℃ (namely between Ms and Mf) at the speed of 50-1000 ℃/s, wherein the austenite is partially transformed into martensite, and the steel is ensured to have higher strength; and (3) heating to 360-460 ℃ and preserving heat for 100-500 seconds to distribute carbon in martensite and austenite to form a certain amount of residual austenite rich in carbon, and stably keeping the residual austenite to room temperature.
Because the high-strength steel adopts high-carbon and high-manganese design and ferrite grain refinement, the size of the high-strength steel is further refined while nucleation points of austenite reverse phase transformation are increased in the continuous annealing process, and the average grain size of residual austenite stably kept at room temperature can be less than or equal to 2 mu m; the average C content in the retained austenite is more than or equal to 1.1 percent. In addition, due to the adoption of the high-Si design, martensite formed by rapid cooling is not decomposed basically in the distribution process, so that the content of the martensite in the structure is ensured, and the strength of the steel is ensured.
Further, in the manufacturing method of the present invention, in the step (1), the continuous casting drawing speed is controlled to be 2 to 5 m/min.
Further, in the manufacturing method of the present invention, in the step (2), the slab is heated to 1200 to 1250 ℃.
Further, in the manufacturing method of the present invention, in the step (3), the finishing temperature is controlled to 860 to 930 ℃, and the coiling temperature is controlled to 450 to 600 ℃.
Further, in the manufacturing method according to the present invention, in the step (4), when the pickling and cold rolling step is adopted, the deformation amount is controlled to be 30% to 70%.
Further, in the manufacturing method of the present invention, in the step (5), the continuous annealing process is controlled to satisfy at least one of the following conditions:
the annealing temperature is 820-870 ℃;
slowly cooling to 700-730 ℃ at a cooling speed of 3-10 ℃/s;
rapidly cooling to 280-320 ℃;
after quick cooling, heating to 400-430 ℃, and keeping the temperature for 180-300 s;
and controlling the volume content of hydrogen in the reducing atmosphere in the continuous annealing furnace to be 10-15%.
Compared with the prior art, the high-strength steel with excellent ductility and the manufacturing method thereof have the following advantages and beneficial effects:
the high-strength steel provided by the invention is based on carbon-silicon-manganese steel, no expensive alloy element is added, and the high-strength cold-rolled steel plate with excellent ductility is obtained by optimizing the proportion of carbon, silicon and manganese.
The manufacturing method provided by the invention is simple in production process, the elongation of the obtained high-strength steel can be obviously improved under the condition of the same strength, the high-strength steel has a better application prospect in automobile safety structural parts, and the high-strength steel is particularly suitable for manufacturing vehicle structural parts and safety parts which are complex in shape and have high requirements on forming performance, such as A/B columns, longitudinal beams, door impact bars, bumpers and the like.
Drawings
FIG. 1 is a photograph showing the microstructure of the high-strength steel of example 12.
FIG. 2 is a photograph of the phase composition EBSD of the high strength steel of example 12.
Detailed Description
The high strength steel excellent in ductility and the method for manufacturing the same according to the present invention will be further explained and explained with reference to the drawings and specific examples, however, the explanation and explanation do not unduly limit the technical solution of the present invention.
Examples 1 to 36 and comparative examples 1 to 3
The high strength steels of examples 1-36, which are excellent in ductility, were prepared by the following steps:
(1) smelting and continuous thin slab casting were carried out according to the chemical composition shown in table 1: the thickness of the plate blank at the continuous casting outlet end is controlled to be 55-60 mm, and the drawing speed of the continuous casting blank is controlled to be 2-5 m/min.
(2) Heating: heating the plate blank to 1200-1250 ℃.
(3) Hot rolling: the thickness of the oxide skin on the surface of the hot rolled steel strip is less than or equal to 5 mu m, and the surface of the hot rolled steel strip(FeO + Fe) in oxide scale3O4) Not more than 40 wt%, controlling the finishing rolling temperature to be 860-930 ℃, and controlling the coiling temperature to be 450-600 ℃.
(4) Acid washing or acid washing plus cold rolling: when the steps of pickling and cold rolling are adopted, the deformation is controlled to be 30-70%.
(5) And (3) continuous annealing: annealing at 800-920 ℃, and slowly cooling to 680-750 ℃ at a cooling rate of 3-10 ℃/s to obtain ferrite in a certain proportion; then quickly cooling to 220-320 ℃, wherein the cooling speed is 50-1000 ℃/s, so that the austenite is partially transformed into martensite; then heating to 360-460 ℃, preserving the heat for 100-500 s, and finally cooling to room temperature.
It should be noted that, in some preferred embodiments, in step (5), the parameter may be further controlled to satisfy at least one of the following:
the annealing temperature is 820-870 ℃;
slowly cooling to 700-730 ℃ at a cooling speed of 3-10 ℃/s;
rapidly cooling to 280-320 ℃;
after quick cooling, heating to 400-430 ℃, and keeping the temperature for 180-300 s;
and controlling the volume content of hydrogen in the reducing atmosphere in the continuous annealing furnace to be 10-15%.
And comparative examples 1-3 were made using conventional processes.
Table 1 shows the mass percentages of the chemical elements of the high-strength steels excellent in ductility of examples 1 to 36 and the comparative steels of comparative examples 1 to 3.
Table 1 (wt%, balance Fe and unavoidable impurities other than P, S and N)
Figure BDA0002240517890000091
Tables 2-1 and 2-2 show specific process parameters of the high strength steels excellent in ductility of examples 1-36 and the comparative steels of comparative examples 1-3.
Table 2-1.
Figure BDA0002240517890000092
Figure BDA0002240517890000101
Table 2-2.
Figure BDA0002240517890000102
Figure BDA0002240517890000111
Table 3 shows the results of mechanical property tests of the high strength steels excellent in ductility of examples 1 to 36 and the comparative steels of comparative examples 1 to 3.
Table 3.
Figure BDA0002240517890000112
Figure BDA0002240517890000121
As can be seen from Table 3, the high-strength steels having excellent ductility of examples 1 to 36 of the present invention have excellent ductility surfaces while maintaining the strength, and have a yield strength of 550 to 850MPa, a tensile strength of 900 to 1100MPa, a uniform elongation of not less than 13%, and an elongation at break of 18 to 28%.
Table 4 microstructure observation results of high strength steels excellent in ductility of examples 1 to 36.
Table 4.
Figure BDA0002240517890000131
As can be seen from tables 3 and 4, the microstructures of the high strength steels excellent in ductility of examples 1 to 36 of the present application were 30 to 50% of ferrite, 40 to 60% of martensite and retained austenite, wherein in the ferrite, the grains of 10 μm or less account for 80% or more, the grains of 5 μm or less account for 50% or more, and the average grain size of the retained austenite was 2 μm or less; and/or the average C content in the retained austenite is more than or equal to 1.1 wt%. Thus, it was demonstrated that the high strength steels of the embodiments of the present application, which are excellent in ductility, can have excellent ductility while having high strength because they have a certain amount of fine-grained ferrite and good uniformity of structure.
FIG. 1 is a photograph showing the microstructure of the high-strength steel of example 12. FIG. 2 is a photograph of the phase composition EBSD of the high strength steel of example 12.
As can be seen from fig. 1 and 2, the microstructure of the high strength steel of example 12 is 30 to 50% of ferrite, 40 to 60% of martensite, and retained austenite, wherein in the ferrite, grains of 10 μm or less account for 80% or more, grains of 5 μm or less account for 50% or more, and the average grain size of the retained austenite is 2 μm or less; and/or the average C content in the retained austenite is more than or equal to 1.1 wt%.
In conclusion, the high-strength steel provided by the invention is based on carbon-silicon-manganese steel, does not add any expensive alloy element, and obtains the high-strength cold-rolled steel plate with excellent ductility by optimizing the proportion of carbon, silicon and manganese.
The manufacturing method provided by the invention is simple in production process, the elongation of the obtained high-strength steel can be obviously improved under the condition of the same strength, the high-strength steel has a better application prospect in automobile safety structural parts, and the high-strength steel is particularly suitable for manufacturing vehicle structural parts and safety parts which are complex in shape and have high requirements on forming performance, such as A/B columns, longitudinal beams, door impact bars, bumpers and the like.
It should be noted that the prior art in the protection scope of the present invention is not limited to the examples given in the present application, and all the prior art which is not inconsistent with the technical scheme of the present invention, including but not limited to the prior patent documents, the prior publications and the like, can be included in the protection scope of the present invention.
In addition, the combination of the features in the present application is not limited to the combination described in the claims of the present application or the combination described in the embodiments, and all the features described in the present application may be freely combined or combined in any manner unless contradictory to each other.
It should also be noted that the above-mentioned embodiments are only specific embodiments of the present invention. It is apparent that the present invention is not limited to the above embodiments and similar changes or modifications can be easily made by those skilled in the art from the disclosure of the present invention and shall fall within the scope of the present invention.

Claims (15)

1. A high-strength steel with excellent ductility is characterized by comprising the following chemical elements in percentage by mass:
C：0.15～0.25wt％；
Si：1.00～2.00wt％；
Mn：1.50～3.00wt％；
Al：0.03～0.06wt％；
the balance being Fe and other unavoidable impurities.
2. The high strength steel excellent in ductility according to claim 1, characterized in that the chemical elements thereof satisfy at least one of the following in mass percent:
C：0.17～0.23wt％；
Si：1.4～1.8wt％；
Mn：1.8～2.3wt％。
3. the high strength steel excellent in ductility according to claim 1 or 2, further comprising at least one of the following elements:
Cr≤0.5wt％；
Mo≤0.5wt％；
Nb≤0.05wt％；
Ti≤0.05wt％；
V≤0.05wt％；
B≤0.001wt％。
4. the high strength steel excellent in ductility according to claim 3, wherein each chemical element satisfies at least one of the following:
Cr≤0.25wt％；
Mo≤0.25wt％；
Nb≤0.025wt％；
Ti≤0.02wt％；
V≤0.02wt％。
5. the high strength steel having excellent ductility according to claim 1, characterized in that, among other unavoidable impurities: p is less than or equal to 0.015 wt%, S is less than or equal to 0.012 wt%, and N is less than or equal to 0.008 wt%.
6. The high-strength steel having excellent ductility according to claim 1, wherein the microstructure is 30 to 50% of ferrite, 40 to 60% of martensite and retained austenite.
7. The high-strength steel excellent in ductility according to claim 6, wherein the ferrite contains not less than 80% and not more than 50% of grains having a size of not more than 10 μm.
8. The high strength steel excellent in ductility according to claim 6, wherein the average grain size of the retained austenite is 2 μm or less; and/or the average C content in the retained austenite is more than or equal to 1.1 wt%.
9. The high-strength steel having excellent ductility according to claim 1, characterized in that the yield strength is 550 to 850MPa, the tensile strength is 900 to 1100MPa, the uniform elongation is not less than 13%, and the elongation at break is 18 to 28%.
10. The method of manufacturing a high strength steel having excellent ductility according to any one of claims 1 to 9, characterized by comprising the steps of:
(1) smelting and sheet billet continuous casting: wherein the thickness of the plate blank at the outlet end of the continuous casting is controlled to be 55-60 mm;
(2) heating;
(3) hot rolling: the thickness of the oxide skin on the surface of the hot-rolled steel strip is less than or equal to 5 mu m, and the (FeO + Fe) in the oxide skin on the surface of the hot-rolled steel strip3O4)≤40wt％；
(4) Acid washing or acid washing plus cold rolling;
(5) and (3) continuous annealing: annealing at 800-920 ℃, and slowly cooling to 680-750 ℃ at a cooling rate of 3-10 ℃/s to obtain ferrite in a certain proportion; then quickly cooling to 220-320 ℃, wherein the cooling speed is 50-1000 ℃/s, so that the austenite is partially transformed into martensite; then heating to 360-460 ℃, preserving the heat for 100-500 s, and finally cooling to room temperature.
11. The manufacturing method according to claim 10, wherein in the step (1), the continuous casting drawing speed is controlled to 2 to 5 m/min.
12. The manufacturing method according to claim 10, wherein in the step (2), the slab is heated to 1200 to 1250 ℃.
13. The method according to claim 10, wherein in the step (3), the finishing temperature is controlled to 860 to 930 ℃ and the coiling temperature is controlled to 450 to 600 ℃.
14. The manufacturing method according to claim 10, wherein in the step (4), when the pickling + cold rolling step is adopted, the deformation amount is controlled to be 30% to 70%.
15. The manufacturing method according to claim 10, wherein in the step (5), the continuous annealing process is controlled to satisfy at least one of:
the annealing temperature is 820-870 ℃;
slowly cooling to 700-730 ℃ at a cooling speed of 3-10 ℃/s;
rapidly cooling to 280-320 ℃;
after quick cooling, heating to 400-430 ℃, and keeping the temperature for 180-300 s;
and controlling the volume content of hydrogen in the reducing atmosphere in the continuous annealing furnace to be 10-15%.
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