CN109355573B - One-steel multi-stage hot rolled steel plate based on carbon distribution technology and manufacturing method thereof - Google Patents
One-steel multi-stage hot rolled steel plate based on carbon distribution technology and manufacturing method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention belongs to the technical field of high-strength automobile hot rolled steel plates, and particularly relates to a one-steel multi-stage hot rolled steel plate based on a carbon distribution technology and a manufacturing method thereof. The chemical components of the one-steel multi-stage hot rolled steel plate are as follows in percentage by weight: 0.19-0.21% of C, 1.55-1.65% of Si, 1.55-1.65% of Mn, less than or equal to 0.008% of P, less than or equal to 0.003% of S and the balance of Fe. The method combines TMCP technology and Q & P concept, adopts two-stage control rolling, and then is cooled to 320-540 ℃ through an air cooling section and an ultra-fast cooling section, and then is coiled, and the carbon distribution process is realized by utilizing the coiling waste heat. According to the invention, low-cost low-carbon Si-Mn series steel is utilized, matrix structures with different strength levels are obtained by means of on-line quenching to a bainite region and a martensite region, 8-16% of residual austenite is obtained by utilizing a carbon distribution technology, the plasticity is further improved, one-steel multi-level control is realized, the tensile strength covers 850-1300 MPa levels, and the product of strength and elongation is more than 20 GPa%.
Description
Technical Field
The invention belongs to the technical field of high-strength automobile hot rolled steel plates, and particularly relates to a one-steel multi-stage hot rolled steel plate based on a carbon distribution technology and a manufacturing method thereof, wherein the one-steel multi-stage hot rolled steel plate comprises complex phase steel with tensile strength of 850MPa, 900MPa, 950MPa, 1000MPa, 1100MPa and 1300 MPa.
Background
With the increasingly prominent problems of energy and environment, the automobile industry is developing towards weight reduction and consumption reduction. AHSS (advanced high-strength steel) can fully meet the requirement of high strength of automobile steel while realizing energy conservation and emission reduction, and becomes a key research and development object of automobile materials. The quenching-partitioning (Q & P) concept is a process technology proposed by the professor Speer 2003 for producing a new generation of advanced automotive steels, under which a good match of strong plasticity is achieved with a structure of martensite and retained austenite.
At present, most scholars adopt a mode of increasing the content of alloy elements and performing off-line heat treatment to perform Q & P treatment so as to obtain more residual austenite, thereby improving the strength and plasticity of experimental steel. Therefore, the alloy has problems of high cost, complex process, and the like. Generally speaking, the research of the steel grade mainly takes low-carbon silicomanganese steel as a component, and the component has the characteristics of more phase change and easy control. Therefore, if the TMCP technology (controlled rolling and controlled cooling technology) is combined with the Q & P technology, the flexible control of the organization can be realized, so that the aim of one-steel multi-stage production is fulfilled, and the industrial application prospect is effectively expanded.
Chinese patent CN101775470A discloses a production process of complex phase Q & P steel, which is actually a two-step process for producing Q & P steel. Chinese patent CN103233161A discloses a low yield ratio high strength hot rolled Q & P steel and a manufacturing method thereof, but the carbon content in the chemical composition thereof is too high, deteriorating the welding performance of the material. Chinese patent CN103215516A discloses a 700 MPa-grade high-strength hot-rolled Q & P steel, but the structure of the steel is dominated by martensite, and the hot-rolled product has serious plate shape problem. In addition, the elongation is less than 15%, the formability is poor, and all the patents do not have research reports of producing high-strength steel by one steel in multiple stages based on quenching-partitioning technology.
Disclosure of Invention
The invention aims to provide a one-steel multi-stage hot rolled steel plate based on a carbon distribution technology and a manufacturing method thereof, which take low-carbon silicomanganese steel as a research object, do not add any other alloy elements, combine a TMCP technology with a Q & P concept, realize that the content of proeutectoid ferrite is adjustable, combine bainite zone quenching coiling distribution and martensite zone quenching coiling distribution, and finally obtain a complex phase structure of ferrite, martensite, bainite and residual austenite.
The technical scheme of the invention is as follows:
the carbon distribution technology-based one-steel multi-stage hot rolled steel plate comprises the following chemical components in percentage by weight: 0.19 to 0.21 percent of C, 1.55 to 1.65 percent of Si, 1.55 to 1.65 percent of Mn, less than or equal to 0.008 percent of P, less than or equal to 0.003 percent of S, and the balance of Fe.
The manufacturing method of the one-steel multi-stage hot rolled steel plate based on the carbon distribution technology specifically comprises the following steps:
1) smelting and casting
Smelting in a converter or an electric furnace according to chemical components, and casting into a billet;
2) heating and hot rolling
Heating the billet to 1190-1210 ℃, preserving heat for 1-1.5 h, carrying out rough rolling at the initial rolling temperature of 1180-1190 ℃ in an austenite complete recrystallization zone, and obtaining an intermediate billet with the accumulated deformation of 50-70%; when the temperature of the intermediate blank is reduced to 920-930 ℃, performing finish rolling for more than two times, wherein the finish rolling temperature is 870-880 ℃, and the accumulated deformation is 75-90%, so as to obtain a hot-rolled steel plate with the thickness of 3-4 mm;
3) on-line cooling
And cooling the finish-rolled steel plate to 740-870 ℃ through an air cooling section, then cooling to 320-540 ℃ through an ultra-fast cooling section, wherein the ultra-fast cooling speed is 100-150 ℃/s, finally performing simulated coiling, and slowly cooling to room temperature along with a furnace.
In the manufacturing method of the one-steel multi-stage hot rolled steel plate based on the carbon distribution technology, in the step 2), rough rolling is performed for 2-3 passes of deformation, and the pass deformation is controlled to be 20% -35%; the finish rolling is performed for 3-5 passes of deformation, and the pass deformation is controlled to be 15-30%.
According to the manufacturing method of the one-steel multi-stage hot rolled steel plate based on the carbon distribution technology, in the step 3), after the termination temperature of an air cooling section is 740-870 ℃, the steel plate is cooled to 320-540 ℃ through on-line water quenching, and the coiling cooling speed is 50-60 ℃/h.
The manufacturing method of the one-steel multi-stage hot rolled steel plate based on the carbon distribution technology comprises the steps of cooling the hot rolled steel plate to 860-870 ℃ in an air cooling section, then carrying out ultra-fast cooling to 320-350 ℃ and then coiling to obtain 1300 MPa-grade martensite-austenite complex phase steel, wherein the yield strength of the 1300 MPa-grade martensite-austenite complex phase steel is 1000-1120 MPa, the elongation after fracture is 13.75-15.5%, the volume fraction of retained austenite in a structure is 8-11%, and a hard phase is mainly martensite.
The manufacturing method of the one-steel multi-stage hot rolled steel plate based on the carbon distribution technology comprises the steps of cooling a rolled steel plate to 740-760 ℃ in an air cooling section, carrying out ultra-fast cooling to 320-385 ℃, and then coiling to obtain ferrite-martensite-austenite complex phase steel with the grades of 950MPa, 1000MPa and 1100MPa, wherein the yield strength is 490-560 MPa, the elongation after fracture is 20-27%, the volume fraction of ferrite in a structure is 32.1-40.2%, the volume fraction of residual austenite is 12-14%, and a hard phase is mainly martensite.
The manufacturing method of the one-steel multi-stage hot rolled steel plate based on the carbon distribution technology comprises the steps of cooling the hot rolled steel plate to 780-820 ℃ in an air cooling section, carrying out ultra-fast cooling to 530-540 ℃, and then coiling to obtain ferrite-bainite-austenite multiphase steel of 850MPa and 900MPa, wherein the yield strength of the steel is 445-650 MPa, the elongation after fracture is 30-32.4%, the volume fraction of ferrite in a structure is 15.4-26.3%, the volume fraction of residual austenite is 13.4-15.1%, and the hard phase is mainly bainite.
The design idea of the invention is as follows:
in the aspect of component design, the simplest low-carbon silicon manganese steel is used as a raw material, so that the low cost and the good welding performance are ensured, and a certain content of residual austenite can be effectively obtained through distribution. In the aspect of process control, a mode of combining TMCP technology and Q & P is adopted to realize controlled rolling, so that the prior austenite crystal grains are greatly refined, and the effect of fine grain strengthening is achieved; the ferrite content is regulated and controlled by controlling sectional cooling, so that the yield strength is adjustable; the tensile strength is adjustable by quenching to a bainite and martensite interval; and (4) obtaining the residual austenite stable at room temperature by coiling and residual heat distribution. Finally, based on the saving type components and the simplified process, one-steel multi-stage control is realized, and the obtained steel grade has excellent comprehensive mechanical properties and high strength level of tensile strength coverage series.
Compared with the prior art, the invention has the characteristics and beneficial effects that:
1. compared with the traditional low-alloy high-strength steel, the low-carbon silicon-manganese steel is not added with any precious metal elements such as Nb, V, Cu and the like, has no smelting difficulty and fully ensures the welding performance of the steel plate.
2. The invention is based on the carbon distribution technology, applies the TMCP technology to the development of hot-rolled high-strength steel, fully utilizes the comprehensive action of size effect and element distribution to stabilize the residual austenite, and ensures the plasticity of the steel plate. Meanwhile, sectional cooling is adopted, the traditional quenching temperature interval of the Q & P steel is changed, the adjustment of yield strength and tensile strength is realized, the purpose of one steel and multiple grades is achieved, a diversified selection approach is provided for enterprises, and the industrial application of the high-strength steel is expanded.
Drawings
FIG. 1 is a schematic view of the structure at room temperature in example 1.
FIG. 2 is a room temperature texture map of example 2.
FIG. 3 is a room temperature texture map of example 3.
FIG. 4 is a room temperature texture map of example 4.
FIG. 5 is a room temperature texture map of example 5.
FIG. 6 is a room temperature texture map of example 6.
Detailed Description
In the specific implementation process, the one-steel multi-stage hot rolled steel plate based on the carbon distribution technology and the manufacturing method thereof are as follows:
1) smelting and casting
The chemical components by weight percentage are as follows: 0.19-0.21% of C, 1.55-1.65% of Si, 1.55-1.65% of Mn, less than or equal to 0.008% of P, less than or equal to 0.003% of S and the balance of Fe, and smelting and casting the mixture into a billet.
2) Heating and hot rolling
Heating the steel billet obtained in the step 1) to 1190-1210 ℃, preserving heat for 1-1.5 h, and carrying out rough rolling at the initial rolling temperature of 1180-1190 ℃ (in an austenite complete recrystallization zone), wherein the accumulated deformation is 55%. And (3) carrying out multi-pass finish rolling when the temperature of the intermediate blank is reduced to 920-930 ℃ (in an austenite non-recrystallization region), wherein the final rolling temperature is 870-880 ℃, and the accumulated deformation is 78%, so as to obtain the hot-rolled steel plate with the thickness of 3-4 mm.
3) On-line cooling
And cooling the finish-rolled steel plate to 740-870 ℃ through an air cooling section, then cooling to 320-540 ℃ through an ultra-fast cooling section, wherein the ultra-fast cooling speed is 100-150 ℃/s, and finally coiling and slowly cooling to room temperature.
The present invention will be explained in further detail below by way of examples and figures.
Example 1
In this embodiment, the chemical compositions of the hot rolled steel sheet of one steel and multiple grades are as follows by weight percent: c: 0.19%, Si: 1.63%, Mn: 1.61%, P: 0.004%, S: 0.002%, and the balance Fe.
The production steps are as follows:
after smelting and forging, the billet is heated to 1200 ℃ and is kept warm for 1.5 h. Performing first-stage rolling at 1180 ℃ at the final rolling temperature of 1130 ℃, then performing second-stage rolling after air cooling to 920 ℃, wherein the final rolling temperature is 880 ℃, performing air cooling to 870 ℃, then performing water cooling to 340 ℃, performing furnace slow cooling, and cooling to room temperature for about 6 hours.
The performance indexes of the alloy are as follows through mechanical property detection: the yield strength is 1050MPa, the tensile strength is 1320MPa, the yield ratio is 0.80, the elongation after fracture is 15.5%, and the product of strength and elongation is 20.5 GPa%. As shown in fig. 1, the room-temperature structure is composed of martensite and retained austenite, and the volume fraction of the retained austenite is 10.3%.
Example 2
In this embodiment, the chemical compositions of the hot rolled steel sheet of one steel and multiple grades are as follows by weight percent: c: 0.20%, Si: 1.60%, Mn: 1.60%, P: 0.004%, S: 0.002%, and the balance Fe.
The production steps are as follows:
after smelting and forging, the billet is heated to 1210 ℃ and is kept warm for 1.5 h. Performing first-stage rolling at 1190 ℃, wherein the final rolling temperature is 1140 ℃, then performing second-stage rolling by air cooling to 920 ℃, wherein the final rolling temperature is 875 ℃, performing air cooling to 755 ℃, then performing water cooling to 320 ℃, performing furnace slow cooling, and cooling to room temperature for about 6 hours.
The performance indexes of the alloy are as follows through mechanical property detection: the yield strength is 530MPa, the tensile strength is 1140MPa, the yield ratio is 0.46, the elongation after fracture is 20.2 percent, and the product of strength and elongation is 23.03 GPa%. As shown in fig. 2, the room temperature structure is composed of ferrite, martensite, and retained austenite, wherein the volume fraction of ferrite is 34.2%, and the volume fraction of retained austenite is 12.1%.
Example 3
In this embodiment, the chemical compositions of the hot rolled steel sheet of one steel and multiple grades are as follows by weight percent: c: 0.21%, Si: 1.60%, Mn: 1.55%, P: 0.004%, S: 0.002%, and the balance Fe.
After smelting and forging, the billet is heated to 1200 ℃ and is kept warm for 1.5 h. Performing first-stage rolling at 1180 ℃ at the finish rolling temperature of 1135 ℃, then performing second-stage rolling by air cooling to 930 ℃, wherein the finish rolling temperature is 875 ℃, performing air cooling to 740 ℃, then performing water cooling to 335 ℃, performing furnace slow cooling, and cooling to room temperature for about 6.5 hours.
The performance indexes of the alloy are as follows through mechanical property detection: the yield strength is 490MPa, the tensile strength is 1040MPa, the yield ratio is 0.46, the elongation after fracture is 23.4%, and the product of strength and elongation is 24.33 GPa%. As shown in fig. 3, the room temperature structure is composed of ferrite, martensite, and retained austenite, wherein the volume fraction of ferrite is 40.2%, and the volume fraction of retained austenite is 13.2%.
Example 4
In this embodiment, the chemical compositions of the hot rolled steel sheet of one steel and multiple grades are as follows by weight percent: c: 0.19%, Si: 1.62%, Mn: 1.60%, P: 0.004%, S: 0.002%, and the balance Fe.
After smelting and forging, the billet is heated to 1200 ℃ and is kept warm for 1.5 h. Performing first-stage rolling at 1185 ℃ at the finish rolling temperature of 1135 ℃, then performing second-stage rolling by air cooling to 930 ℃, wherein the finish rolling temperature is 875 ℃, performing air cooling to 760 ℃, then performing water cooling to 385 ℃, performing furnace slow cooling, and cooling to room temperature for about 6.5 hours.
The performance indexes of the alloy are as follows through mechanical property detection: the yield strength is 560MPa, the tensile strength is 985MPa, the yield ratio is 0.57, the elongation after fracture is 26.5 percent, and the product of strength and elongation is 26.10 GPa%. As shown in fig. 4, the room temperature structure is composed of ferrite, martensite, and retained austenite, in which the volume fraction of ferrite is 32.1% and the volume fraction of retained austenite is 13.8%.
Example 5
In this embodiment, the chemical compositions of the hot rolled steel sheet of one steel and multiple grades are as follows by weight percent: c: 0.20%, Si: 1.60%, Mn: 1.62%, P: 0.004%, S: 0.002%, and the balance Fe.
After smelting and forging, the billet is heated to 1200 ℃ and is kept warm for 1.5 h. The first stage rolling is carried out at 1190 ℃, the final rolling temperature is 1135 ℃, then the air cooling is carried out to 925 ℃ for carrying out the second stage rolling, the final rolling temperature is 870 ℃, after the air cooling is carried out to 820 ℃, the water cooling is carried out to 540 ℃, furnace slow cooling is carried out, and the cooling is carried out to the room temperature for about 10 hours.
The performance indexes of the alloy are as follows through mechanical property detection: the yield strength is 650MPa, the tensile strength is 940MPa, the yield ratio is 0.69, the elongation after fracture is 30.0 percent, and the product of strength and elongation is 28.2 GPa%. As shown in fig. 5, the room temperature structure is composed of ferrite, bainite, and retained austenite, in which the volume fraction of ferrite is 15.4% and the volume fraction of retained austenite is 13.4%.
Example 6
In this embodiment, the chemical compositions of the hot rolled steel sheet of one steel and multiple grades are as follows by weight percent: c: 0.20%, Si: 1.61%, Mn: 1.60%, P: 0.004%, S: 0.002%, and the balance Fe.
After smelting and forging, the steel billet is heated to 1195 ℃, and heat preservation is carried out for 1.5 h. Performing first-stage rolling at 1180 ℃ at the finish rolling temperature of 1135 ℃, then performing second-stage rolling by air cooling to 920 ℃, wherein the finish rolling temperature is 875 ℃, performing air cooling to 780 ℃, then performing water cooling to 530 ℃, performing furnace slow cooling, and cooling to room temperature for about 10 hours.
The performance indexes of the alloy are as follows through mechanical property detection: the yield strength is 445MPa, the tensile strength is 880MPa, the yield ratio is 0.51, the elongation after fracture is 32.4%, and the product of strength and elongation is 28.5 GPa%. As shown in fig. 6, the room temperature structure is composed of ferrite, bainite, and retained austenite, in which the volume fraction of ferrite is 26.3% and the volume fraction of retained austenite is 15.1%.
The embodiment result shows that the TMCP technology and the Q & P concept are combined, two-stage controlled rolling is adopted, the temperature is cooled to 320-540 ℃ through an air cooling section and an ultra-fast cooling section, then coiling is carried out, and the carbon distribution process is realized by utilizing coiling waste heat. The hollow cooling section controls the content of ferrite, and the ultra-fast cooling speed is 100-150 ℃/s. The typical 1+ x structure type is finally obtained under the process condition, bainite or martensite is used as a matrix, ferrite in a specific proportion and 8-16% of residual austenite are added, and the steel has the characteristics of high strength and high plasticity. The tensile strength of the hot-rolled steel plate covers 850-1300 MPa, and the product of strength and elongation is more than 20 GPa%. The invention utilizes low-cost low-carbon Si-Mn series steel, obtains matrix structures with different strength levels by adopting a mode of on-line quenching to a bainite area and a martensite area, and obtains retained austenite by utilizing a carbon distribution technology, thereby further improving the plasticity and realizing multi-level control of one steel.
Claims (4)
1. The manufacturing method of the one-steel multi-stage hot rolled steel plate based on the carbon distribution technology is characterized in that the one-steel multi-stage hot rolled steel plate comprises the following chemical components in percentage by weight: 0.19-0.21% of C, 1.55-1.65% of Si, 1.55-1.65% of Mn, less than or equal to 0.008% of P, less than or equal to 0.003% of S and the balance of Fe;
the manufacturing method of the one-steel multi-stage hot rolled steel plate based on the carbon distribution technology specifically comprises the following steps:
1) smelting and casting
Smelting in a converter or an electric furnace according to chemical components, and casting into a billet;
2) heating and hot rolling
Heating the billet to 1190-1210 ℃, preserving heat for 1-1.5 h, carrying out rough rolling at the initial rolling temperature of 1180-1190 ℃ in an austenite complete recrystallization zone, and obtaining an intermediate billet with the accumulated deformation of 50-70%; when the temperature of the intermediate blank is reduced to 920-930 ℃, performing finish rolling for more than two times, wherein the finish rolling temperature is 870-880 ℃, and the accumulated deformation is 75-90%, so as to obtain a hot-rolled steel plate with the thickness of 3-4 mm;
3) on-line cooling
Cooling the finish-rolled steel plate to 740-870 ℃ through an air cooling section, then cooling to 320-540 ℃ through an ultra-fast cooling section, wherein the ultra-fast cooling speed is 100-150 ℃/s, finally performing simulated coiling, and slowly cooling to room temperature along with a furnace;
in the step 2), rough rolling is carried out for 2-3 passes of deformation, and the pass deformation is controlled to be 20% -35%; the finish rolling is carried out for 3-5 passes of deformation, and the pass deformation is controlled to be 15-30%;
in the step 3), after the termination temperature of the air cooling section is 740-870 ℃, the steel is cooled to 320-540 ℃ through online water quenching, and the coiling cooling speed is 50-60 ℃/h.
2. The method for manufacturing a one-steel multi-stage hot-rolled steel plate based on the carbon distribution technology according to claim 1, wherein the hot-rolled steel plate is air-cooled to 860 to 870 ℃, then ultra-fast cooled to 320 to 350 ℃, and then coiled to obtain 1300 MPa-grade martensite-austenite complex phase steel, the yield strength of the steel is 1000 to 1120MPa, the elongation after fracture is 13.75 to 15.5%, the volume fraction of retained austenite in the structure is 8 to 11%, and the hard phase is mainly martensite.
3. The method for manufacturing a one-steel multi-stage hot rolled steel sheet based on the carbon distribution technology as claimed in claim 1, wherein the rolled steel sheet is cooled to 740 to 760 ℃ in an air cooling section, then is cooled to 320 to 385 ℃ in an ultra-rapid cooling mode, and then is coiled, so that ferrite-martensite-austenite complex phase steel of 950MPa, 1000MPa, and 1100MPa grade is obtained, the yield strength is 490 to 560MPa, the elongation after fracture is 20 to 27%, the volume fraction of ferrite in the structure is 32.1 to 40.2%, the volume fraction of retained austenite is 12 to 14%, and the hard phase is mainly martensite.
4. The method for manufacturing a one-steel multi-stage hot-rolled steel plate based on the carbon distribution technology as claimed in claim 1, wherein the hot-rolled steel plate is air-cooled to 780-820 ℃, then ultra-fast cooled to 530-540 ℃, and then coiled to obtain ferrite-bainite-austenite complex phase steel of 850MPa and 900MPa, the yield strength of the steel is 445-650 MPa, the elongation after fracture is 30-32.4%, the volume fraction of ferrite in the structure is 15.4-26.3%, the volume fraction of retained austenite is 13.4-15.1%, and the hard phase is mainly bainite.
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