CN109280857B - 1200 MPa-grade ultrafast cold-rolled dual-phase steel plate and preparation method thereof - Google Patents
1200 MPa-grade ultrafast cold-rolled dual-phase steel plate and preparation method thereof Download PDFInfo
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- 229910000885 Dual-phase steel Inorganic materials 0.000 title claims abstract description 65
- 238000002360 preparation method Methods 0.000 title claims abstract description 19
- 238000000034 method Methods 0.000 claims abstract description 91
- 238000001816 cooling Methods 0.000 claims abstract description 87
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 79
- 239000010959 steel Substances 0.000 claims abstract description 79
- 238000000137 annealing Methods 0.000 claims abstract description 53
- 238000009749 continuous casting Methods 0.000 claims abstract description 47
- 230000008569 process Effects 0.000 claims abstract description 41
- 238000003723 Smelting Methods 0.000 claims abstract description 40
- 238000005097 cold rolling Methods 0.000 claims abstract description 39
- 238000005098 hot rolling Methods 0.000 claims abstract description 27
- 239000000126 substance Substances 0.000 claims abstract description 26
- 239000012535 impurity Substances 0.000 claims abstract description 9
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 4
- 238000010438 heat treatment Methods 0.000 claims description 42
- 238000005096 rolling process Methods 0.000 claims description 26
- 230000009467 reduction Effects 0.000 claims description 12
- 229910000859 α-Fe Inorganic materials 0.000 abstract description 16
- 229910000734 martensite Inorganic materials 0.000 abstract description 14
- 229910045601 alloy Inorganic materials 0.000 abstract description 3
- 239000000956 alloy Substances 0.000 abstract description 3
- 239000000203 mixture Substances 0.000 description 11
- 238000005266 casting Methods 0.000 description 10
- 239000010936 titanium Substances 0.000 description 8
- 239000011572 manganese Substances 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 6
- 238000004519 manufacturing process Methods 0.000 description 5
- 229910000746 Structural steel Inorganic materials 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 239000002253 acid Substances 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910017112 Fe—C Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
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- 238000005272 metallurgy Methods 0.000 description 1
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- 238000012986 modification Methods 0.000 description 1
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- 238000010587 phase diagram Methods 0.000 description 1
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- 238000003908 quality control method Methods 0.000 description 1
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- 230000003014 reinforcing effect Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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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
- C21D8/0242—Flattening; Dressing; Flexing
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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 discloses a 1200 MPa-grade ultrafast 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: 0.12-0.17%, Si: 0.3-0.6%, Mn: 2.0-2.4%, P is less than or equal to 0.015%, S is less than or equal to 0.008%, Als: 0.03-0.06%, Ti: 0.03-0.06%, 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, by means of Ti microalloying low alloy component design and continuous annealing process water cooling 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, the structure performance is uniform, the tensile strength reaches over 1200MPa, and the mechanical property is excellent.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to a 1200 MPa-grade ultrafast cold-rolled dual-phase steel plate and a preparation method thereof.
Background
The 1200MPa grade cold rolling dual-phase steel has the advantages of low yield ratio, high initial work hardening rate, good matching of strength and ductility and the like, has been developed into high-strength structural steel with good formability, the microstructure of the high-strength structural steel mainly comprises a softer ferrite matrix and a small amount of hard martensite phase, the steel can be obtained by low alloy steel through a critical zone heat treatment and controlled rolling process, and the dual-phase composite structural state enables the high-strength structural steel to have good strong plasticity matching and cold deformation performance, so that the high-strength structural steel is widely applied to structural members, reinforcing members and anti-collision members.
As the 1200 MPa-grade cold-rolled dual-phase steel is high enough in strength, more alloy elements are often required to be added in the traditional process components, so that the production process difficulty of various links such as smelting, hot rolling, acid rolling and the like is increased, the stable production of the steel is not facilitated, and the production cost is high.
The invention patent of a cold-rolled dual-phase steel plate with 103556048A tensile strength of 1200MPa and a preparation method thereof is searched by searching, and is characterized in that the cold-rolled dual-phase steel plate comprises the following chemical components in percentage by weight: c: 0.19 to 0.21%, Si: 0.7-0.9%, Mn: 1.9-2.1%, Cr: 0.01 to 0.02%, Nb: 0.02-0.04%, P is less than or equal to 0.005%, S is less than or equal to 0.003%, and the balance is Fe and inevitable impurities. The steel has the advantages that the tensile strength is more than 1200MPa, the grain size reaches 2-3 mu m, the yield ratio is 0.5-0.6, the elongation is more than 8%, and the volume fraction of martensite is 58-68%. The problem with this steel is that C, Si weight percent is high, which is detrimental to welding and surface quality control.
Disclosure of Invention
The invention aims to solve the technical problem of providing a 1200 MPa-grade ultrafast cold-rolled dual-phase steel plate and a preparation method thereof. The invention adopts a low-carbon Cr-free and Mo-free component system, reduces the hardenability and strength of the hot-rolled steel plate, improves the acid rolling production stability, obtains the low-cost ultrahigh-strength dual-phase steel with good performance by an ultrafast cooling process and combining a controlled rolling and controlled cooling technology, and has better market prospect.
In order to solve the technical problems, the invention adopts the technical scheme that: a1200 MPa-grade ultrafast cold-rolled dual-phase steel plate comprises the following chemical components in percentage by mass: c: 0.12-0.17%, Si: 0.3-0.6%, Mn: 2.0-2.4%, P is less than or equal to 0.015%, S is less than or equal to 0.008%, Als: 0.03-0.06%, Ti: 0.03-0.06%, 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: 820 to 950MPa, tensile strength: 1200-1350 MPa, elongation: 5 to 10 percent.
The invention also provides a preparation method of the 1200 MPa-grade ultrafast 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 procedure, the fast cooling section adopts water-cooling ultra-fast cooling, and the temperature is fast cooled to 50-60 ℃ at a cooling rate of 130-150 ℃/s.
According to the annealing process, a continuous annealing process is adopted, strip steel is heated to 810-840 ℃ at the heating rate of 1-3 ℃/s, the temperature is kept for 120-150 s, then the strip steel is slowly cooled to 700-730 ℃ at the speed of 2-4 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 50-60 ℃ at the cooling rate of 130-150 ℃/s, and then the strip steel is heated to 250 ℃ at the heating rate of 20-30 ℃/s for overaging treatment for 200-400 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: 0.12-0.17%, Si: 0.3-0.6%, Mn: 2.0-2.4%, P is less than or equal to 0.015%, S is less than or equal to 0.008%, Als: 0.03-0.06%, Ti: 0.03-0.06%, 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 1220-1260 ℃, the final rolling temperature is controlled to 850-880 ℃, and the plate blank is cooled to 580-630 ℃ through a laminar cooling system after rolling, and is 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 0.3-0.6%.
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 0.12-0.17%, 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 0.3-0.6%, 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 2.0-2.4%.
Ti: the titanium can form TiN with nitrogen to prevent austenite grains from growing in heating and refine original grains in initial rolling. Ti (CN) particles precipitated in an austenite high-temperature region during rolling can retard the recrystallization process of austenite, ferrite grains are finally refined, and a trace amount of Ti is added into steel to refine the grains and improve the strength. The Ti content is selected to be 0.03-0.06%.
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 1200 MPa-level ultrafast cold-rolled dual-phase steel plate product standard of the invention refers to GB/T20564.2-2017; 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 Ti microalloying without Cr and Mo components, and is beneficial to 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 obtains the low-cost cold-rolled dual-phase steel with ferrite and martensite dual-phase structure morphology, and the cold-rolled dual-phase steel has uniform structure performance and excellent mechanical property.
Drawings
FIG. 1 is a metallographic structure drawing (1000 times) of a 1200MPa class ultrafast cold-rolled dual phase steel sheet according to example 1;
FIG. 2 is a metallographic structure drawing (1000 times) of a 1200MPa class ultrafast cold-rolled dual-phase steel sheet according to example 2;
FIG. 3 is a metallographic structure drawing (1000 times) of a 1200MPa class ultrafast cold-rolled dual-phase steel sheet according to example 3;
FIG. 4 is a metallographic structure drawing (1000 times) of a 1200MPa class ultrafast cold-rolled dual-phase steel sheet according to example 4;
FIG. 5 is a metallographic structure drawing (1000 times) of a 1200MPa class ultrafast cold-rolled dual-phase steel sheet according to example 5;
FIG. 6 is a metallographic structure drawing (1000 times) of a 1200MPa class ultra-fast cold-rolled dual-phase steel sheet according to example 6;
FIG. 7 is a metallographic structure drawing (1000 times) of a 1200MPa class ultra-fast cold-rolled dual-phase steel sheet according to example 7;
FIG. 8 is a metallographic structure drawing (1000 times) of a 1200MPa class ultra-fast cold-rolled dual-phase steel sheet according to example 8;
FIG. 9 is a metallographic structure drawing (1000 times) of a 1200MPa class ultra-fast cold-rolled dual-phase steel sheet according to example 9;
FIG. 10 is a metallographic structure drawing (1000 times) of a 1200MPa class ultra-fast cold-rolled dual-phase steel sheet according to example 10.
Detailed Description
The invention is described in further detail below with reference to the figures and specific examples.
Example 1
The chemical components and the mass percentage of the 1200MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in the table 1.
The preparation method of the 1200 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 1220 ℃, controlling the finishing temperature to be 850 ℃, cooling to 630 ℃ through a laminar cooling system after rolling, and coiling at the 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 810 ℃ at the heating rate of 1.0 ℃/s, the temperature is kept for 150s, then the strip steel is slowly cooled to 720 ℃ at the speed of 2 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 55 ℃ at the cooling rate of 130 ℃/s, and then the strip steel is heated to 250 ℃ at the heating rate of 20 ℃/s for overaging treatment for 400 s;
(6) leveling: the flat elongation was 0.6%.
The mechanical properties of the 1200MPa grade ultrafast 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 1200MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in the table 1.
The preparation method of the 1200 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 1260 ℃, controlling the final rolling temperature to 880 ℃, cooling to 580 ℃ through a laminar cooling system after rolling, and coiling at a 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 120s, then the strip steel is slowly cooled to 707 ℃ at 4 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 55 ℃ at the cooling rate of 150 ℃/s, and then the strip steel is heated to 250 ℃ at the heating rate of 30 ℃/s for overaging treatment for 200 s;
(6) leveling: the flat elongation was 0.3%.
The mechanical properties of the 1200MPa grade ultrafast 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 1200MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in the table 1.
The preparation method of the 1200 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 862 ℃, cooling to 600 ℃ 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 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 130s, then the strip steel is slowly cooled to 725 ℃ 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 0.4%.
The mechanical properties of the 1200MPa grade ultrafast 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 1200MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in the table 1.
The preparation method of the 1200 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 1236 ℃, controlling the final rolling temperature to 860 ℃, cooling to 609 ℃ through a laminar cooling system after rolling, and coiling at a 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 139 ℃/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 0.5%.
The mechanical properties of the 1200MPa grade ultrafast 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 1200MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in the table 1.
The preparation method of the 1200 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 1227 ℃, controlling the finish rolling temperature to 872 ℃, cooling to 605 ℃ 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 55.6 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 836 ℃ at the heating rate of 2.2 ℃/s, kept warm for 139s, slowly cooled to 708 ℃ at 3.6 ℃/s, then water-cooled ultra-fast cooled, quickly cooled to 55 ℃ at the cooling rate of 144 ℃/s, and then heated to 250 ℃ at the heating rate of 29 ℃/s for overaging for 295 s;
(6) leveling: the flat elongation was 0.4%.
The mechanical properties of the 1200MPa grade ultrafast 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 1200MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in the table 1.
The preparation method of the 1200 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 at 865 ℃, cooling to 613 ℃ 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 830 ℃ at the heating rate of 2.3 ℃/s, the temperature is kept for 141s, then the strip steel is slowly cooled to 700 ℃ at the speed of 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 treatment for 255 s;
(6) leveling: the flat elongation was 0.6%.
The mechanical properties of the 1200MPa grade ultrafast 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 1200MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in the table 1.
The preparation method of the 1200 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 final rolling temperature to 880 ℃, cooling to 580 ℃ through a laminar cooling system after rolling, and coiling at a 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 728 ℃ at the speed of 2.7 ℃/s, then the strip steel is quickly cooled to 55 ℃ at the cooling rate of 138 ℃/s by adopting water-cooling ultra-quick cooling, and then the strip steel is heated to 250 ℃ at the heating rate of 23 ℃/s for overaging treatment for 376 s;
(6) leveling: the flat elongation was 0.5%.
The mechanical properties of the 1200MPa grade ultrafast 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 1200MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in the table 1.
The preparation method of the 1200 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 1236 ℃, controlling the finishing temperature to 865 ℃, cooling to 621 ℃ 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 350 s;
(6) leveling: the flat elongation was 0.4%.
The mechanical properties of the 1200MPa grade ultrafast 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 1200MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in the table 1.
The preparation method of the 1200 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 1260 ℃, controlling the final rolling temperature to 871 ℃, cooling to 625 ℃ 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 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 702 ℃ at 3.5 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 60 ℃ 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 360 s;
(6) leveling: the flat elongation was 0.5%.
The mechanical properties of the 1200MPa grade ultrafast 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 1200MPa grade ultra-fast cold-rolled dual-phase steel plate in the embodiment are shown in the table 1.
The preparation method of the 1200 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 1227 ℃, controlling the finishing temperature to 874 ℃, cooling to 590 ℃ 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 58.7 percent;
(5) and (3) annealing: the annealing mode adopts continuous annealing, the strip steel is heated to 840 ℃ at the heating rate of 2.5 ℃/s, the temperature is kept for 135s, then the strip steel is slowly cooled to 730 ℃ at the speed of 2.8 ℃/s, then water-cooling ultra-fast cooling is adopted, the strip steel is rapidly cooled to 50 ℃ 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 364 s;
(6) leveling: the flat elongation was 0.3%.
The mechanical properties of the 1200MPa grade ultrafast 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 with surface 11200 MPa
The balance of the ingredients in table 1 is Fe and unavoidable impurities.
Mechanical properties of ultra-fast cold-rolled dual-phase steel plate with surface 21200 MPa
As can be seen from Table 2, the 1200 MPa-grade ultra-fast cold-rolled dual-phase steel plate has excellent mechanical properties and the tensile strength of the steel plate reaches over 1200 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 1200 MPa-level ultra-fast cold-rolled dual-phase steel plate is characterized by comprising the following chemical components in percentage by mass: c: 0.12-0.17%, Si: 0.3-0.6%, Mn: 2.17-2.4%, P is less than or equal to 0.015%, S is less than or equal to 0.008%, Als: 0.03-0.06%, Ti: 0.03-0.06%, N: 0.003-0.005% of Fe and inevitable impurities as the rest; the steel plate yield strength is as follows: 820 to 950MPa, tensile strength: 1200-1350 MPa, elongation: 5-10%; the steel plate is prepared by the following method: comprises the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and flattening; the annealing process comprises the steps of adopting a continuous annealing process, heating the strip steel to 810-840 ℃ at a heating rate of 1-3 ℃/s, preserving heat for 120-150 s, then slowly cooling the strip steel to 700-730 ℃ at 2-4 ℃/s, then quickly cooling the strip steel to 50-60 ℃ at a cooling rate of 130-150 ℃/s by adopting water cooling and ultra-quick cooling at a quick cooling section, and then heating the strip steel to 250 ℃ at a heating rate of 20-30 ℃/s for carrying out overaging treatment for 200-400 s.
2. The method for preparing the 1200 MPa-grade ultrafast cold-rolled dual-phase steel plate is characterized by comprising the working procedures of smelting, continuous casting, hot rolling, cold rolling, annealing and flattening; the annealing process comprises the steps of adopting a continuous annealing process, heating the strip steel to 810-840 ℃ at a heating rate of 1-3 ℃/s, preserving heat for 120-150 s, then slowly cooling the strip steel to 700-730 ℃ at 2-4 ℃/s, then quickly cooling the strip steel to 50-60 ℃ at a cooling rate of 130-150 ℃/s by adopting water cooling and ultra-quick cooling at a quick cooling section, and then heating the strip steel to 250 ℃ at a heating rate of 20-30 ℃/s for carrying out overaging treatment for 200-400 s.
3. The method for preparing the 1200 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 preparation method of the 1200 MPa-grade ultrafast cold-rolled dual-phase steel plate according to claim 2 or 3, wherein in the hot rolling process, the plate blank is heated to 1220-1260 ℃, the final rolling temperature is controlled to 850-880 ℃, and the plate blank is cooled to 580-630 ℃ through a laminar cooling system after rolling, and is coiled, wherein the cooling rate is 15-20 ℃/s.
5. The method for preparing the 1200 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 1200 MPa-grade ultrafast cold-rolled dual-phase steel plate according to claim 5, wherein the flattening process has a flattening elongation of 0.3-0.6%.
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| CN110747405B (en) * | 2019-10-24 | 2021-09-14 | 邯郸钢铁集团有限责任公司 | One-thousand-megapascal-grade cold-rolled bainite steel plate suitable for rolling and preparation method thereof |
| CN113737087B (en) * | 2020-05-27 | 2022-07-19 | 宝山钢铁股份有限公司 | Ultrahigh-strength dual-phase steel and manufacturing method thereof |
| CN112481552A (en) * | 2020-11-11 | 2021-03-12 | 鞍钢股份有限公司 | 1000 MPa-grade cold-rolled sheet steel for automobiles and ultra-fast cooling production method |
| CN112481553A (en) * | 2020-11-11 | 2021-03-12 | 鞍钢股份有限公司 | 1000 MPa-grade automobile steel with good hardenability and ultra-fast cooling production method |
| 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 |
| CN117660846A (en) * | 2022-08-23 | 2024-03-08 | 宝山钢铁股份有限公司 | A 120kg cold-rolled low-alloy annealed dual-phase steel and its manufacturing method |
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