CN109371317B - 1000 MPa-grade ultra-fast cold-rolled dual-phase steel plate and preparation method thereof - Google Patents
1000 MPa-grade ultra-fast cold-rolled dual-phase steel plate and preparation 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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- 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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- 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
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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
- 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
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Abstract
The invention discloses a 1000 MPa-grade ultra-fast cold-rolled dual-phase steel plate and a preparation method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: c: 0.1-0.15%, Si: 0.3-0.9%, Mn: 1.6-2.2%, P is less than or equal to 0.015%, S is less than or equal to 0.008%, Als: 0.03-0.06%, Nb: 0.02-0.05%, N is less than or equal to 0.005%, and the balance is Fe and inevitable impurities; the preparation method comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling. According to the invention, through the Nb microalloying Cr-free and Mo-free component design, the hardenability and strength of the hot-rolled steel plate are reduced, and stable production by acid rolling is facilitated; the continuous annealing process is utilized for water cooling and ultra-fast cooling, the hardenability of the steel plate is improved, and the cold-rolled dual-phase steel with ferrite and martensite dual-phase structure morphology is obtained, and has uniform structure performance and excellent mechanical property.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to a 1000 MPa-grade ultrafast cold-rolled dual-phase steel plate and a preparation method thereof.
Background
With the development of modern automobiles in light weight directions such as weight reduction, energy conservation, high safety and the like, research and development of high-strength thin steel plates for automobiles are promoted. Dual phase steels have the advantages of low yield ratio, high initial work hardening rate, good combination of strength and ductility, etc., have been developed into high strength structural steels with good formability, and become one of the preferred steel grades for modern automotive steels.
The microstructure of a 1000MPa grade cold rolled dual phase steel consists mainly of a softer ferritic matrix and a small amount of hard martensitic phase. The dual-phase steel is advanced high-strength steel based on phase change strengthening, can be obtained by low-carbon steel through a critical zone heat treatment and controlled rolling process, has good strong plasticity matching and cold deformation performance due to the dual-phase composite structural state, and is widely applied to structural members, reinforcing members and anti-collision members, such as automobile bumpers, vehicle bottom cross members, rails, anti-collision rods, anti-collision rod reinforcing structural members and the like.
The invention patents related to 1000MPa grade cold rolling dual-phase steel with the publication numbers of 102586688A, 107043888A and 105132816A are searched by searching, and the components of the invention all contain Cr which is an element for improving hardenability, so that the hardenability of the steel plate in the hot rolling process can be improved, the strength of the hot rolled steel plate is higher, but the subsequent acid rolling production is not facilitated.
Therefore, the 1000 MPa-grade ultra-fast cold-rolled dual-phase steel plate without the Cr component system is developed, a certain amount of Nb element is added into the components, the important effects on phase change behavior, grain refinement, C enrichment in austenite and martensite nucleation are achieved, the hardenability and strength of the hot-rolled steel plate are reduced, the acid rolling production stability is improved, the steel plate forming performance is improved, and the product has a good market prospect.
Disclosure of Invention
The invention aims to solve the technical problem of providing a 1000 MPa-grade ultra-fast cold-rolled dual-phase steel plate and a preparation method thereof.
In order to solve the technical problems, the invention adopts the technical scheme that: a1000 MPa-grade ultra-fast cold-rolled dual-phase steel plate comprises the following chemical components in percentage by mass: c: 0.1-0.15%, Si: 0.3-0.9%, Mn: 1.6-2.2%, P is less than or equal to 0.015%, S is less than or equal to 0.008%, Als: 0.03-0.06%, Nb: 0.02-0.05%, N is less than or equal to 0.005%, and the balance is Fe and inevitable impurities.
The steel plate has the following yield strength: 600-800 MPa, tensile strength: 1000-1150 MPa, elongation: 10 to 18 percent.
The invention also provides a preparation method of the 1000 MPa-grade ultra-fast cold-rolled dual-phase steel plate, which comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling; in the annealing process, the rapid cooling section adopts water-cooling ultra-rapid cooling and rapidly cools to 50-60 ℃ at a cooling rate of 120-150 ℃/s.
The method adopts a continuous annealing process, heats the strip steel to 820-850 ℃ at a heating rate of 1-3 ℃/s, keeps the temperature for 120-150 s, then slowly cools the strip steel to 690-720 ℃ at 2-4 ℃/s, then adopts water cooling ultra-fast cooling, quickly cools the strip steel to 50-60 ℃ at a cooling rate of 120-150 ℃/s, and then heats the strip steel to 250 ℃ at a heating rate of 20-30 ℃/s for carrying out overaging treatment for 250-400 s.
The smelting process adopts converter smelting and an LF + RH duplex process.
In the continuous casting process, molten steel is continuously cast after smelting to obtain a continuous casting billet, and the continuous casting billet comprises the following chemical components in percentage by mass: c: 0.1-0.15%, Si: 0.3-0.9%, Mn: 1.6-2.2%, P is less than or equal to 0.015%, S is less than or equal to 0.008%, Als: 0.03-0.06%, Nb: 0.02-0.05%, N is less than or equal to 0.005%, and the balance is Fe and inevitable impurities.
According to the hot rolling process, a plate blank is heated to 1230-1270 ℃, the final rolling temperature is controlled to 880-910 ℃, and the plate blank is cooled to 600-650 ℃ through a laminar cooling system after rolling and coiled, wherein the cooling rate is 15-20 ℃/s. In the cold rolling process, the cold rolling reduction is controlled to be 50-60%.
The leveling process has the leveling elongation of 0.4-0.7%.
The invention has the following contents and functions of the elements:
c: carbon is an effective strengthening element and can greatly improve the strength of the steel. However, too high carbon content deteriorates the weldability of steel, and the solid solution strengthening causes an increase in strength and a decrease in plasticity. According to the invention, the C content is 0.1-0.15%, and the steel plate strength cannot be ensured if the C content is too low.
Si: silicon is a ferrite-forming element and is present mainly in solid solution in steel to perform a strengthening function. Si is a non-carbide forming element, can enlarge an alpha + gamma region in an Fe-C phase diagram, improve the transformation temperature from austenite to ferrite and promote the precipitation of ferrite. According to the invention, the Si content is selected to be 0.3-0.9%, and the surface quality problem is easily caused by too high Si content.
Mn: manganese is an austenite stabilizing element, has an obvious inhibiting effect on the recrystallization process of austenite, can fully utilize unrecrystallized control to roll refined grains by properly increasing the content of Mn, has a certain solid solution strengthening effect, and can improve the ductility and toughness. The Mn content is selected to be 1.6-2.2%.
Nb: niobium plays an important role in phase transformation behavior, grain refinement, C enrichment in austenite and nucleation of martensite. The content of Nb is selected to be 0.02-0.05%.
P: the impurity elements in the steel are required to be less than or equal to 0.015 percent.
S: the impurity elements in the steel are required to be less than or equal to 0.008 percent.
And Als: the alloy plays roles in deoxidizing and refining grains in steel, and the ALs content is required to be 0.03-0.06%.
N: the impurity elements in the steel are required to be less than or equal to 0.005 percent.
The 1000MPa grade ultra-fast cold-rolled dual-phase steel plate product of the invention is referred to GB/T20564.2-2017 in the standard; the product performance detection method is in standard reference GB/T228.1-2010.
Adopt the produced beneficial effect of above-mentioned technical scheme to lie in: 1. the invention reduces the hardenability and the strength of the hot-rolled steel plate by the Nb microalloying Cr-free and Mo-free component design, and is beneficial to the stable production of acid rolling. 2. The invention utilizes the continuous annealing process water cooling ultra-fast cooling to improve the hardenability of the steel plate, and the cold-rolled dual-phase steel with ferrite and martensite dual-phase structure morphology is obtained, and has uniform structure performance and excellent mechanical property.
Drawings
FIG. 1 is a metallographic structure diagram (1000 times) of a 1000MPa class ultrafast cold-rolled dual-phase steel sheet according to example 1;
FIG. 2 is a metallographic structure diagram (1000 times) of a 1000MPa class ultrafast cold-rolled dual-phase steel sheet according to example 2;
FIG. 3 is a metallographic structure drawing (1000 times) of a 1000MPa class ultrafast cold-rolled dual-phase steel sheet according to example 3;
FIG. 4 is a metallographic structure drawing (1000 times) of a 1000MPa class ultrafast cold-rolled dual-phase steel sheet according to example 4;
FIG. 5 is a metallographic structure drawing (1000 times) of a 1000MPa class ultrafast cold-rolled dual-phase steel sheet according to example 5;
FIG. 6 is a metallographic structure drawing (1000 times) of a 1000MPa class ultra-fast cold-rolled dual-phase steel sheet of example 6;
FIG. 7 is a metallographic structure drawing (1000 times) of a 1000MPa class ultra-fast cold-rolled dual-phase steel sheet according to example 7;
FIG. 8 is a metallographic structure drawing (1000 times) of a 1000MPa class ultra-fast cold-rolled dual-phase steel sheet according to example 8;
FIG. 9 is a metallographic structure drawing (1000 times) of a 1000MPa class ultra-fast cold-rolled dual-phase steel sheet according to example 9;
FIG. 10 is a metallographic structure drawing (1000 times) of a 1000MPa class ultra-fast cold-rolled dual-phase steel sheet of example 10. Detailed Description
The present invention will be described in further detail with reference to specific examples.
Example 1
The chemical components and the mass percentage of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate of the embodiment are shown in the table 1.
The preparation method of the 1000 MPa-level ultra-fast cold-rolled dual-phase steel plate comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling, and comprises the following specific process steps:
(1) smelting: adopting converter smelting and LF + RH duplex process;
(2) and (3) continuous casting process: continuously casting the smelted molten steel to obtain a continuous casting billet, wherein the chemical component composition and the mass percentage content of the continuous casting billet are shown in table 1;
(3) a hot rolling procedure: heating the plate blank to 1244 ℃, controlling the final rolling temperature to 880 ℃, cooling to 633 ℃ through a laminar cooling system after rolling, and coiling at a cooling rate of 15 ℃/s;
(4) a cold rolling procedure: the cold rolling reduction is controlled to be 53.8 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 829 ℃ at the heating rate of 1.0 ℃/s, the temperature is kept for 140s, then the strip steel is slowly cooled to 720 ℃ at the speed of 2 ℃/s, then the strip steel is rapidly cooled to 55 ℃ at the cooling rate of 134 ℃/s by adopting water-cooling ultra-rapid cooling, and then the strip steel is heated to 250 ℃ at the heating rate of 20 ℃/s for carrying out overaging treatment for 284 s;
(6) leveling: the flat elongation was 0.47%.
The mechanical properties of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in Table 2; the metallographic structure is shown in figure 1, and the structure is a ferrite + martensite dual-phase structure as can be seen from figure 1.
Example 2
The chemical components and the mass percentage of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate of the embodiment are shown in the table 1.
The preparation method of the 1000 MPa-level ultra-fast cold-rolled dual-phase steel plate comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling, and comprises the following specific process steps:
(1) smelting: adopting converter smelting and LF + RH duplex process;
(2) and (3) continuous casting process: continuously casting the smelted molten steel to obtain a continuous casting billet, wherein the chemical component composition and the mass percentage content of the continuous casting billet are shown in table 1;
(3) a hot rolling procedure: heating the plate blank to 1230 ℃, controlling the finishing temperature to 899 ℃, cooling to 618 ℃ through a laminar cooling system after rolling, and coiling at the cooling rate of 20 ℃/s;
(4) a cold rolling procedure: the cold rolling reduction rate is controlled at 50 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 834 ℃ at the heating rate of 1.8 ℃/s, the temperature is kept for 128s, then the strip steel is slowly cooled to 697 ℃ at 4 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 55 ℃ at the cooling rate of 120 ℃/s, and then the strip steel is heated to 250 ℃ at the heating rate of 30 ℃/s for overaging treatment for 343 s;
(6) leveling: the flat elongation was 0.51%.
The mechanical properties of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in Table 2; the metallographic structure is shown in FIG. 2, and the structure is a ferrite + martensite dual-phase structure as can be seen from FIG. 2.
Example 3
The chemical components and the mass percentage of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate of the embodiment are shown in the table 1.
The preparation method of the 1000 MPa-level ultra-fast cold-rolled dual-phase steel plate comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling, and comprises the following specific process steps:
(1) smelting: adopting converter smelting and LF + RH duplex process;
(2) and (3) continuous casting process: continuously casting the smelted molten steel to obtain a continuous casting billet, wherein the chemical component composition and the mass percentage content of the continuous casting billet are shown in table 1;
(3) a hot rolling procedure: heating the plate blank to 1247 ℃, controlling the finishing temperature at 892 ℃, cooling to 600 ℃ through a laminar cooling system after rolling, and coiling at a cooling rate of 17 ℃/s;
(4) a cold rolling procedure: the cold rolling reduction is controlled to be 53.3 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 820 ℃ at the heating rate of 1.8 ℃/s, the temperature is kept for 120s, then the strip steel is slowly cooled to 713 ℃ at the speed of 2.5 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 55 ℃ at the cooling rate of 141 ℃/s, and then the strip steel is heated to 250 ℃ at the heating rate of 26 ℃/s for overaging treatment for 250 s;
(6) leveling: the flat elongation was 0.40%.
The mechanical properties of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in Table 2; the metallographic structure is shown in FIG. 3, and the structure is a ferrite + martensite dual-phase structure as can be seen from FIG. 3.
Example 4
The chemical components and the mass percentage of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate of the embodiment are shown in the table 1.
The preparation method of the 1000 MPa-level ultra-fast cold-rolled dual-phase steel plate comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling, and comprises the following specific process steps:
(1) smelting: adopting converter smelting and LF + RH duplex process;
(2) and (3) continuous casting process: continuously casting the smelted molten steel to obtain a continuous casting billet, wherein the chemical component composition and the mass percentage content of the continuous casting billet are shown in table 1;
(3) a hot rolling procedure: heating the plate blank to 1246 ℃, controlling the finishing temperature to 890 ℃, cooling to 629 ℃ through a laminar cooling system after rolling, and coiling at the cooling rate of 18 ℃/s;
(4) a cold rolling procedure: the cold rolling reduction is controlled to be 55.6 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 828 ℃ at the heating rate of 1.6 ℃/s, the temperature is kept for 135s, then the strip steel is slowly cooled to 709 ℃ at the speed of 3.2 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 55 ℃ at the cooling rate of 129 ℃/s, and then the strip steel is heated to 250 ℃ at the heating rate of 24 ℃/s for overaging treatment for 311 s;
(6) leveling: the flat elongation was 0.58%.
The mechanical properties of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in Table 2; the metallographic structure is shown in FIG. 4, and the structure is a ferrite + martensite dual-phase structure as can be seen from FIG. 4.
Example 5
The chemical components and the mass percentage of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate of the embodiment are shown in the table 1.
The preparation method of the 1000 MPa-level ultra-fast cold-rolled dual-phase steel plate comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling, and comprises the following specific process steps:
(1) smelting: adopting converter smelting and LF + RH duplex process;
(2) and (3) continuous casting process: continuously casting the smelted molten steel to obtain a continuous casting billet, wherein the chemical component composition and the mass percentage content of the continuous casting billet are shown in table 1;
(3) a hot rolling procedure: heating the plate blank to 1247 ℃, controlling the finishing temperature to 902 ℃, cooling to 635 ℃ through a laminar cooling system after rolling, and coiling at the cooling rate of 17 ℃/s;
(4) a cold rolling procedure: the cold rolling reduction is controlled to be 55.6 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 832 ℃ at the heating rate of 2.2 ℃/s, kept warm for 139s, slowly cooled to 698 ℃ at 3.6 ℃/s, then water-cooled ultra-fast cooled, quickly cooled to 55 ℃ at the cooling rate of 134 ℃/s, and then heated to 250 ℃ at the heating rate of 29 ℃/s for overaging treatment for 299 s;
(6) leveling: the flat elongation was 0.57%.
The mechanical properties of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in Table 2; the metallographic structure is shown in FIG. 5, and the structure is shown as a ferrite + martensite dual-phase structure in FIG. 5.
Example 6
The chemical components and the mass percentage of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate of the embodiment are shown in the table 1.
The preparation method of the 1000 MPa-level ultra-fast cold-rolled dual-phase steel plate comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling, and comprises the following specific process steps:
(1) smelting: adopting converter smelting and LF + RH duplex process;
(2) and (3) continuous casting process: continuously casting the smelted molten steel to obtain a continuous casting billet, wherein the chemical component composition and the mass percentage content of the continuous casting billet are shown in table 1;
(3) a hot rolling procedure: heating the plate blank to 1250 ℃, controlling the finishing temperature to 895 ℃, cooling to 623 ℃ through a laminar cooling system after rolling, and coiling at the cooling rate of 16 ℃/s;
(4) a cold rolling procedure: the cold rolling reduction is controlled to be 56.5 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 850 ℃ at the heating rate of 2.3 ℃/s, the temperature is kept for 141s, then the strip steel is slowly cooled to 690 ℃ at 2.2 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 55 ℃ at the cooling rate of 143 ℃/s, and then the strip steel is heated to 250 ℃ at the heating rate of 24 ℃/s for overaging for 355 s;
(6) leveling: the flat elongation was 0.62%.
The mechanical properties of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in Table 2; the metallographic structure is shown in FIG. 6, and the structure is a ferrite + martensite dual-phase structure as can be seen from FIG. 6.
Example 7
The chemical components and the mass percentage of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate of the embodiment are shown in the table 1.
The preparation method of the 1000 MPa-level ultra-fast cold-rolled dual-phase steel plate comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling, and comprises the following specific process steps:
(1) smelting: adopting converter smelting and LF + RH duplex process;
(2) and (3) continuous casting process: continuously casting the smelted molten steel to obtain a continuous casting billet, wherein the chemical component composition and the mass percentage content of the continuous casting billet are shown in table 1;
(3) a hot rolling procedure: heating the plate blank to 1267 ℃, controlling the finishing rolling temperature at 910 ℃, cooling to 638 ℃ through a laminar cooling system after rolling, and coiling at the cooling rate of 18 ℃/s;
(4) a cold rolling procedure: the cold rolling reduction is controlled to be 55.9 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 837 ℃ at the heating rate of 3 ℃/s, the temperature is kept for 140s, then the strip steel is slowly cooled to 708 ℃ at the speed of 2.7 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 55 ℃ at the cooling rate of 138 ℃/s, and then the strip steel is heated to 250 ℃ at the heating rate of 23 ℃/s for overaging 369 s;
(6) leveling: the flat elongation was 0.54%.
The mechanical properties of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in Table 2; the metallographic structure is shown in FIG. 7, and the structure is a ferrite + martensite dual-phase structure as can be seen from FIG. 7.
Example 8
The chemical components and the mass percentage of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate of the embodiment are shown in the table 1.
The preparation method of the 1000 MPa-level ultra-fast cold-rolled dual-phase steel plate comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling, and comprises the following specific process steps:
(1) smelting: adopting converter smelting and LF + RH duplex process;
(2) and (3) continuous casting process: continuously casting the smelted molten steel to obtain a continuous casting billet, wherein the chemical component composition and the mass percentage content of the continuous casting billet are shown in table 1;
(3) a hot rolling procedure: heating the plate blank to 1253 ℃, controlling the final rolling temperature to 893 ℃, cooling to 641 ℃ through a laminar cooling system after rolling, and coiling at the cooling rate of 19 ℃/s;
(4) a cold rolling procedure: the cold rolling reduction is controlled to be 54.8 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 826 ℃ at the heating rate of 1.9 ℃/s, is slowly cooled to 711 ℃ at the speed of 3.8 ℃/s after being kept warm for 150s, is rapidly cooled to 55 ℃ at the cooling rate of 150 ℃/s by adopting water-cooling ultra-rapid cooling, and is heated to 250 ℃ at the heating rate of 21 ℃/s for overaging treatment for 400 s;
(6) leveling: the flat elongation was 0.7%.
The mechanical properties of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in Table 2; the metallographic structure is shown in FIG. 8, and the structure is a ferrite + martensite dual-phase structure as can be seen from FIG. 8.
Example 9
The chemical components and the mass percentage of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate of the embodiment are shown in the table 1.
The preparation method of the 1000 MPa-level ultra-fast cold-rolled dual-phase steel plate comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling, and comprises the following specific process steps:
(1) smelting: adopting converter smelting and LF + RH duplex process;
(2) and (3) continuous casting process: continuously casting the smelted molten steel to obtain a continuous casting billet, wherein the chemical component composition and the mass percentage content of the continuous casting billet are shown in table 1;
(3) a hot rolling procedure: heating the plate blank to 1270 ℃, controlling the final rolling temperature to 901 ℃, cooling to 637 ℃ by a laminar cooling system after rolling, and coiling at a cooling rate of 17 ℃/s;
(4) a cold rolling procedure: the cold rolling reduction rate is controlled at 60 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 834 ℃ at the heating rate of 2.2 ℃/s, the temperature is kept for 135s, then the strip steel is slowly cooled to 705 ℃ at 3.5 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 55 ℃ at the cooling rate of 136 ℃/s, and then the strip steel is heated to 250 ℃ at the heating rate of 26 ℃/s for overaging treatment for 340 s;
(6) leveling: the flat elongation was 0.46%.
The mechanical properties of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in Table 2; the metallographic structure is shown in FIG. 9, and the structure is a ferrite + martensite dual-phase structure as can be seen from FIG. 9.
Example 10
The chemical components and the mass percentage of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate of the embodiment are shown in the table 1.
The preparation method of the 1000 MPa-level ultra-fast cold-rolled dual-phase steel plate comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and leveling, and comprises the following specific process steps:
(1) smelting: adopting converter smelting and LF + RH duplex process;
(2) and (3) continuous casting process: continuously casting the smelted molten steel to obtain a continuous casting billet, wherein the chemical component composition and the mass percentage content of the continuous casting billet are shown in table 1;
(3) a hot rolling procedure: heating the plate blank to 1247 ℃, controlling the finishing temperature to 886 ℃, cooling to 650 ℃ through a laminar cooling system after rolling, and coiling at the cooling rate of 19 ℃/s;
(4) a cold rolling procedure: the cold rolling reduction is controlled to be 54.7 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 832 ℃ at the heating rate of 2.5 ℃/s, the temperature is kept for 135s, then the strip steel is slowly cooled to 707 ℃ at 2.8 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 55 ℃ at the cooling rate of 141 ℃/s, and then the strip steel is heated to 250 ℃ at the heating rate of 23 ℃/s for overaging treatment for 333 s;
(6) leveling: the flat elongation was 0.55%.
The mechanical properties of the 1000MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in Table 2; the metallographic structure is shown in FIG. 10, and the structure is a ferrite + martensite dual-phase structure as shown in FIG. 10.
Chemical component composition and mass percentage content of ultra-fast cold-rolled dual-phase steel plate in 11000 MPa
The balance of the ingredients in table 1 were Fe and unavoidable impurities.
Mechanical properties of ultra-fast cold-rolled dual-phase steel plate in table 21000 MPa
As can be seen from Table 2, the 1000 MPa-grade ultra-fast cold-rolled dual-phase steel plate has excellent mechanical properties and tensile strength of more than 1000 MPa.
Although the present invention has been described in detail with reference to the above embodiments, it should be understood by those skilled in the art that: modifications and equivalents may be made thereto without departing from the spirit and scope of the invention and it is intended to cover in the claims the invention as defined in the appended claims.
Claims (6)
1. The 1000 MPa-grade ultra-fast cold-rolled dual-phase steel plate is characterized by comprising the following chemical components in percentage by mass: c: 0.1-0.15%, Si: 0.3-0.9%, Mn: 1.6-2.2%, P is less than or equal to 0.015%, S is less than or equal to 0.008%, Als: 0.03-0.06%, Nb: 0.02-0.05%, N is less than or equal to 0.005%, and the balance is Fe and inevitable impurities, wherein the yield strength of the steel plate is as follows: 600-800 MPa, tensile strength: 1000-1150 MPa, elongation: 10-18%; the steel plate is prepared by the following method: comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and flattening; in the hot rolling procedure, the rolled steel is cooled to 600-650 ℃ by a laminar cooling system and coiled, and the cooling rate is 15-20 ℃/s; the annealing process comprises the steps of adopting a continuous annealing process, heating the strip steel to 820-850 ℃ at a heating rate of 1-3 ℃/s, preserving heat for 120-150 s, then slowly cooling to 690-720 ℃ at 2-2.8 ℃/s, then adopting water-cooling ultra-fast cooling, rapidly cooling to 50-60 ℃ at a cooling rate of 120-150 ℃/s, and then heating to 250 ℃ at a heating rate of 20-30 ℃/s for overaging treatment for 250-400 s.
2. The method for preparing the 1000 MPa-grade ultrafast cold-rolled dual-phase steel plate according to claim 1, wherein the preparation method comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and flattening; in the hot rolling procedure, the rolled steel is cooled to 600-650 ℃ by a laminar cooling system and coiled, and the cooling rate is 15-20 ℃/s; the annealing process comprises the steps of adopting a continuous annealing process, heating the strip steel to 820-850 ℃ at a heating rate of 1-3 ℃/s, preserving heat for 120-150 s, then slowly cooling to 690-720 ℃ at 2-2.8 ℃/s, then adopting water-cooling ultra-fast cooling, rapidly cooling to 50-60 ℃ at a cooling rate of 120-150 ℃/s, and then heating to 250 ℃ at a heating rate of 20-30 ℃/s for overaging treatment for 250-400 s.
3. The method for preparing the 1000 MPa-grade ultrafast cold-rolled dual-phase steel plate according to claim 2, wherein the smelting process adopts converter smelting and an LF + RH duplex process.
4. The method for preparing the 1000 MPa-grade ultra-fast cold-rolled dual-phase steel plate according to the claim 2 or 3, characterized in that the hot rolling process is to heat the plate blank to 1230-1270 ℃, and the final rolling temperature is controlled to 880-910 ℃.
5. The method for preparing the 1000 MPa-grade ultrafast cold-rolled dual-phase steel plate according to claim 4, wherein in the cold rolling process, the cold rolling reduction rate is controlled to be 50-60%.
6. The method for preparing the 1000 MPa-grade ultrafast cold-rolled dual-phase steel plate according to claim 5, wherein the flattening elongation of the flattening process is 0.4-0.7%.
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| CN113308649B (en) * | 2021-05-14 | 2022-10-18 | 唐山钢铁集团有限责任公司 | Low-yield-ratio 1000 MPa-grade cold-rolled dual-phase strip steel and production method thereof |
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003247045A (en) * | 2001-10-03 | 2003-09-05 | Kobe Steel Ltd | Dual-phase steel sheet having excellent stretch flange formability and production method thereof |
| CN101363099A (en) * | 2008-09-11 | 2009-02-11 | 北京科技大学 | Cold rolled dual-phase sheet steel with 1000MPa grade tensile strength and preparation method thereof |
| CN102605240A (en) * | 2011-12-09 | 2012-07-25 | 首钢总公司 | High-strength and high-plasticity dual-phase steel and manufacturing method thereof |
| US20120255654A1 (en) * | 2009-08-31 | 2012-10-11 | Hyundai Hysco | Dual phase steel sheet and method of manufacturing the same |
| CN104862597A (en) * | 2015-05-27 | 2015-08-26 | 钢铁研究总院 | Method for improving elongation of cold-rolled dual-phase steel by utilizing retained austenite |
| CN105420605A (en) * | 2015-11-30 | 2016-03-23 | 钢铁研究总院 | Ultralow-yield-ratio cold-rolled dual-phase steel and manufacturing method thereof |
-
2018
- 2018-09-25 CN CN201811115404.XA patent/CN109371317B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003247045A (en) * | 2001-10-03 | 2003-09-05 | Kobe Steel Ltd | Dual-phase steel sheet having excellent stretch flange formability and production method thereof |
| CN101363099A (en) * | 2008-09-11 | 2009-02-11 | 北京科技大学 | Cold rolled dual-phase sheet steel with 1000MPa grade tensile strength and preparation method thereof |
| US20120255654A1 (en) * | 2009-08-31 | 2012-10-11 | Hyundai Hysco | Dual phase steel sheet and method of manufacturing the same |
| CN102605240A (en) * | 2011-12-09 | 2012-07-25 | 首钢总公司 | High-strength and high-plasticity dual-phase steel and manufacturing method thereof |
| CN104862597A (en) * | 2015-05-27 | 2015-08-26 | 钢铁研究总院 | Method for improving elongation of cold-rolled dual-phase steel by utilizing retained austenite |
| CN105420605A (en) * | 2015-11-30 | 2016-03-23 | 钢铁研究总院 | Ultralow-yield-ratio cold-rolled dual-phase steel and manufacturing method thereof |
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