CN115418461A - Method for preparing dual-phase steel, complex-phase steel and steel continuous annealing plate for hot forming by using boron-containing steel - Google Patents
Method for preparing dual-phase steel, complex-phase steel and steel continuous annealing plate for hot forming by using boron-containing steel Download PDFInfo
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- 239000010959 steel Substances 0.000 title claims abstract description 178
- 238000000137 annealing Methods 0.000 title claims abstract description 119
- 238000000034 method Methods 0.000 title claims abstract description 42
- 229910000885 Dual-phase steel Inorganic materials 0.000 title claims abstract description 40
- 229910052796 boron Inorganic materials 0.000 title claims abstract description 22
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 title claims abstract description 18
- 238000001816 cooling Methods 0.000 claims abstract description 84
- 238000004519 manufacturing process Methods 0.000 claims abstract description 22
- 238000010438 heat treatment Methods 0.000 claims abstract description 20
- 238000005097 cold rolling Methods 0.000 claims abstract description 16
- 238000005098 hot rolling Methods 0.000 claims abstract description 11
- 238000005266 casting Methods 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 238000005096 rolling process Methods 0.000 claims description 18
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- 239000002253 acid Substances 0.000 claims description 3
- 238000002360 preparation method Methods 0.000 abstract description 5
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- 229910000859 α-Fe Inorganic materials 0.000 description 16
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- 229910001035 Soft ferrite Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
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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
- C21D8/0205—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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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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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
- C21D11/00—Process control or regulation for heat treatments
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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
- C21D11/00—Process control or regulation for heat treatments
- C21D11/005—Process control or regulation for heat treatments for cooling
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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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- 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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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C21D2211/00—Microstructure comprising significant phases
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
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Abstract
The invention discloses a method for preparing a continuous annealing plate by using boron-containing steel, which comprises the following steps: casting blank: controlling the components of the boron-containing steel according to the weight percentage: c: 0.065-0.125%, mn:1.6 to 2.5%, si:0.0003 to 0.25%, cr:0.0003 to 0.3%, nb:0.0003 to 0.024%, ti:0.015 to 0.04%, B:0.0003 to 0.005%, als:0.01 to 0.1 percent of Fe and inevitable impurities as the rest, and continuously casting the components after smelting into a plate blank; hot rolling; cold rolling; and (3) continuous annealing: the thin strip steel is processed by a continuous annealing production line to be made into at least one of a dual-phase steel continuous annealing plate, a complex-phase steel continuous annealing plate and a steel continuous annealing plate for hot forming, wherein the continuous annealing comprises the steps of heating the thin strip steel to 760-870 ℃ at the speed of 1-10 ℃/s, preserving heat for 1-5 min, cooling to 260-480 ℃ at the cooling speed of 10-50 ℃/s, preserving heat for 4-14 min, and cooling to room temperature, wherein annealing parameters are controlled based on the structure performance of the continuous annealing plate. The method is based on the same steel component, and realizes the preparation of 780 MPa-grade dual-phase steel, complex phase steel (steel for cold forming) and 1000 MPa-grade steel for hot forming by adjusting the technological parameters of continuous annealing.
Description
Technical Field
The invention belongs to the technical field of steel production, and particularly relates to a method for preparing a dual-phase steel, complex-phase steel and a steel continuous annealing plate for hot forming by using boron-containing steel with specific components.
Background
With the rapid development of science and technology, the development of automotive steel towards high strength has become an inevitable trend in order to reduce the weight of the automobile body and improve the safety performance of the automobile body. The low carbon of automotive manufacturing against the "dual carbon" background has become an important issue for industry development. At present, a plurality of steel parts related to a white automobile body are all made of steel plates with different components, different thicknesses and different performances. Dual phase steel (DP), one of the most widely used high strength steels, has a structure mainly composed of a relatively soft ferrite matrix and relatively high strength martensite, and has the performance characteristics of relatively low yield ratio, relatively high strength and the like, and is suitable for producing press-formed parts. On one hand, along with the promotion of light weight of automobiles, the preparation of high-end automobile parts puts forward the requirement of high reaming ratio, so that the complex phase steel (CP) taking bainite + ferrite + martensite + a small amount of austenite as the structure is developed and applied, and the common strength grade of the dual phase steel and the complex phase steel is 780MPa. On the other hand, the hot stamping forming technology is a novel forming technology for heating a steel plate blank or a preformed part blank to austenitizing temperature, quickly transferring the steel plate blank or the preformed part blank to a die through a mechanical arm after heat preservation for a certain time, then quickly stamping and forming the steel plate blank by a stamping machine, and quenching and maintaining the pressure in the die for a certain time to obtain an ultrahigh-strength stamping part. In a high temperature state, the steel plate is in an austenitizing state, the strength is about 200MPa, the plasticity is high, the steel plate is firstly formed under a small press pressure and then hardened into a martensite structure, the contradiction between the strength and the formability is perfectly solved, and the hot forming steel is gradually applied in recent years. A more typical strength rating currently required for high strain-to-break hot formed steel (PHS) components is 1000MPa. The production of various steel grades with different components increases the difficulty of optimizing process parameters in various working procedures such as metallurgy, inclusion control, mechanical property and the like; meanwhile, the existence of a plurality of component steel grades makes the forming, connecting and coating links in automobile manufacturing extremely complicated, and manufacturers almost need to set corresponding production specifications for various steel grades with various thicknesses; scrap sorting/recycling/reuse of scrapped bodies becomes a challenge.
CN 109930068A discloses an 800 MPa-grade ultrathin specification cold-rolled dual-phase steel and a preparation method thereof, wherein the cold-rolled dual-phase steel comprises the following chemical components in percentage by weight: c:0.07 to 0.13%, mn:0.80 to 1.70%, si:0.10 to 0.40%, als:0.060 to 0.15%, P: less than or equal to 0.015 percent, S: less than or equal to 0.0020%, N: less than or equal to 0.004%, cr: 0.20-0.50%, ca: 0.0005-0.0025%, less than or equal to 0.002% of T [ O ], and the balance of Fe and inevitable impurities. The coiling temperature of the steel grade is too low, so that the requirement on coiling equipment is high, two times of cold rolling are adopted, cover annealing is required, the process is complex, the cost is increased, and the production efficiency is low. From this composition, the hardenability is insufficient, and it is difficult to ensure the formation of all martensite and a large amount of bainite, and thus it cannot be used for the production of complex phase steel and steel for hot forming.
CN113584393A discloses a dual-phase steel with tensile strength of 780MPa and a production method thereof, and the dual-phase steel comprises the following chemical components in percentage by mass: c:0.06 to 0.10%, si:1.0% or less, mn + Cr:2.0% -2.8%, nb + Ti:0.03% -0.08%, als:0.02 to 0.08%, P:0.03% or less, S:0.008% or less, N: less than 0.006%, and the balance Fe and inevitable impurities. The yield ratio of the dual-phase steel is controlled by adopting the conventional microalloying component design, heat treatment process and structure design and the step design of the total reduction rate, and the yield ratio of the produced dual-phase steel with the tensile strength of 780MPa reaches 0.65-0.80. However, the steel grade using the expensive Mo element with the content of 0.1% is high in cost, and in addition, the hardenability is insufficient in view of the components, so that the generation of full martensite and a large amount of bainite is difficult to ensure, and the steel grade cannot be used for the preparation of complex phase steel and hot forming steel.
Therefore, how to efficiently and conveniently meet various requirements of automobile body structure design becomes an urgent technical problem to be solved in the field of steel production.
Disclosure of Invention
In order to solve the technical problems in the prior art, the invention provides a method for preparing a dual-phase steel, complex-phase steel and steel continuous annealing plate for hot forming by using boron-containing steel with specific components. The method is based on the same steel component, and realizes the preparation of 780MPa grade dual-phase steel, complex phase steel (steel for cold forming) and 1000MPa grade steel for hot forming by adjusting the technological parameters of continuous annealing.
According to the present invention, there is provided a method for manufacturing a continuous annealing plate using boron-containing steel, comprising the steps of:
casting blank: controlling the components of the boron-containing steel according to the weight percentage: c:0.065 to 0.125%, mn:1.6 to 2.5%, si:0.0003 to 0.25%, cr:0.0003 to 0.3%, nb:0.0003 to 0.024%, ti:0.015 to 0.04%, B:0.0003 to 0.005%, als:0.01 to 0.1 percent of Fe and inevitable impurities as the rest, and continuously casting the components after smelting into a plate blank;
hot rolling: heating, dephosphorizing, roughly rolling, finely rolling, laminar cooling and coiling the plate blank to obtain a hot-rolled coil;
cold rolling: the hot rolled coil is cold-rolled into thin strip steel by an acid continuous rolling production line;
and (3) continuous annealing: the thin strip steel is processed by a continuous annealing production line to be made into at least one of a dual-phase steel continuous annealing plate, a complex-phase steel continuous annealing plate and a steel continuous annealing plate for hot forming, wherein the continuous annealing comprises the steps of heating the thin strip steel to 760-870 ℃ at the speed of 1-10 ℃/s, preserving heat for 1-5 min, cooling to 260-480 ℃ at the cooling speed of 10-50 ℃/s, preserving heat for 4-14 min, and cooling to room temperature, wherein annealing parameters are controlled based on the structure performance of the continuous annealing plate.
According to one embodiment of the invention, the rolling temperature of the finish rolling is 1070 to 1090 ℃, the rolling temperature of the finish rolling is 820 to 930 ℃, and the coiling temperature is 540 to 640 ℃ in the hot rolling process.
According to one embodiment of the invention, laminar cooling is performed by front-end cooling during hot rolling.
According to one embodiment of the invention, the cold rolling reduction is 45 to 75% during the cold rolling.
According to one embodiment of the invention, the continuous annealing comprises: heating the thin strip steel to 780-850 ℃ at the speed of 1-10 ℃/s, preserving heat for 1-5 min, cooling to 260-320 ℃ at the cooling speed of 10-50 ℃/s, preserving heat for 4-14 min, and cooling to room temperature to obtain the dual-phase steel continuous annealing plate.
According to one embodiment of the invention, the thin strip steel is cooled to 670-720 ℃ at the cooling speed of 1-8 ℃/s after heat preservation, then cooled to 270-300 ℃ at the cooling speed of 15-30 ℃/s, and cooled to room temperature after heat preservation for 4-14 min.
According to one embodiment of the present invention, the continuous annealing comprises: the continuous annealing comprises: heating the thin strip steel to 800-870 ℃ at the speed of 1-10 ℃/s, preserving heat for 1-5 min, cooling to 350-450 ℃ at the cooling speed of 10-50 ℃/s, preserving heat for 4-14 min, and cooling to room temperature to obtain the complex phase steel continuous annealing plate.
According to one embodiment of the invention, the thin strip steel is cooled to 650-720 ℃ at a cooling speed of 1-10 ℃/s after heat preservation, then cooled to 380-450 ℃ at a cooling speed of 10-30 ℃/s, and cooled to room temperature after heat preservation for 4-14 min.
According to one embodiment of the invention, the continuous annealing comprises: heating the thin strip steel to 760-830 ℃ at the speed of 1-10 ℃/s, preserving heat for 1-5 min, then cooling to 600-660 ℃ and 380-480 ℃ at the cooling speeds of 1-10 ℃/s and 10-35 ℃/s respectively, preserving heat for 4-14 min, and then cooling to room temperature to obtain the steel continuous annealing plate for hot forming.
According to one embodiment of the invention, the hot-forming steel continuous annealing plate is heated to 900-950 ℃, is insulated until austenitizing is completed, is transferred to a die to be formed and is quenched to be below 180 ℃, and then a hot-forming steel component is obtained.
Due to the adoption of the technical scheme, compared with the prior art, the invention has the following advantages:
1. according to the method, various derivative steel types (dual-phase steel, complex-phase steel and steel for hot forming) with excellent performance are flexibly obtained through continuous annealing production line adjustment based on the single-component boron-containing steel, and the complexity of various links such as design, purchase, production, manufacture and the like of the steel white body is effectively reduced;
2. the dual-phase steel, the complex-phase steel and the steel continuous annealing plate for hot forming prepared by the method can provide more excellent mechanical property than the existing steel grade, and effectively realize the light weight of the automobile.
Drawings
FIG. 1 is a flow chart of a method for preparing a dual phase steel, complex phase steel, hot forming steel continuous annealing plate from boron-containing steel according to the present invention;
FIG. 2 is a microstructure of a dual phase steel continuously annealed plate obtained in example 1;
FIG. 3 is a microstructure of the complex phase steel continuous annealing plate obtained in example 5;
FIG. 4 is a microstructure of a continuously annealed steel hot-formed plate obtained in example 12;
FIG. 5 shows a microstructure of the hot-stamping steel for hot-stamping obtained in example 12.
Detailed Description
In order to make the objects, technical solutions and advantages of the present invention more apparent, the present invention is further described in detail with reference to the following embodiments. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention.
The method for preparing the continuous annealing plate by using the boron-containing steel aims to obtain the 780MPa grade dual-phase steel continuous annealing plate, the complex phase steel continuous annealing plate and the steel continuous annealing plate for hot forming with excellent performance by adjusting the procedures of the conventional industrial continuous annealing production line on the basis of the same steel component. Wherein, the 1000-1300MPa class hot forming steel component with high breaking strain performance (large three-point bending angle of VDA 238-100) can be obtained after the hot forming steel continuous annealing plate is quenched by a hot processing production line process die. As shown in fig. 1, the method specifically includes the following steps:
casting blank
Controlling the components of the boron-containing steel according to the weight percentage: c: 0.065-0.125%, mn:1.6 to 2.5%, si:0.0003 to 0.25%, cr:0.0003 to 0.3%, nb:0.0003 to 0.024%, ti:0.015 to 0.04%, B:0.0003 to 0.005%, als:0.01 to 0.1 percent, and the balance of Fe and inevitable impurities, and continuously casting the components after smelting into a plate blank. Wherein, P, S and N are taken as inevitable impurity elements to meet the requirements of traditional steelmaking, and the specific content is not limited.
The components give full play to Nb microalloying, and a small amount of Nb is added to refine austenite grains, refine martensite Block (Packet) and martensite bundle (Block) units, provide fine grain reinforcement and improve toughness.
Boron (B) is an essential element, and is extremely effective in improving the hardenability of steel. The hardenability of this steel is not directly determined by the total B content added, but by the solid-solution B content that enhances hardenability. However, B has a strong tendency to bind to N, and the resultant BN does not have any effect on the improvement of hardenability, and this portion B is called ineffective B and is usually subjected to nitrogen fixation treatment with other strong nitride-forming elements (such as Ti and the like). The titanium element (Ti) mainly fixes the N element, and on one hand, tiN particles with the size of hundreds of nanometers precipitated in the high-temperature soaking process can effectively inhibit the growth of high-temperature austenite; on the other hand, ti consumes N element to avoid the formation of ineffective B compound BN to ensure the effectiveness of solid solution B for hardenability.
The boron-containing steel components of samples 1-4 are shown in table 1:
table 1 boron-containing steel components (wt.%) and
hot rolling
And heating, dephosphorizing, roughly rolling, finely rolling, carrying out laminar cooling and coiling on the plate blank to obtain a hot-rolled coil.
In the embodiment of the invention, the start rolling temperature of finish rolling in the hot rolling process is 1070-1090 ℃, the finish rolling temperature is 820-930 ℃, and the coiling temperature is 540-640 ℃. The laminar cooling can adopt a front section cooling mode.
The specific hot rolling process parameters of samples 1-4 are shown in table 2:
TABLE 2 Hot Rolling Process parameters
Cold rolling of steel
The hot rolled coil (2.5-4.0 mm) is further cold rolled into thin strip steel (0.8-1.8 mm). In the embodiment of the present invention, the cold rolling reduction in the cold rolling process is preferably set to 45 to 75%. In the examples of the present invention, samples 1 to 4 were subjected to a cold rolling process and then to continuous annealing, and the cold rolling reductions were 45%, 55%, 65%, and 75% in this order to continuously roll thin strip steel.
In an embodiment of the present invention, the cold rolling process may be performed by a continuous process in an acid continuous rolling mill train.
Continuous annealing
And processing the thin strip steel after cold rolling by a continuous annealing production line to prepare at least one of a dual-phase steel continuous annealing plate, a complex-phase steel continuous annealing plate and a steel continuous annealing plate for hot forming. Specifically, the continuous annealing comprises heating the thin strip steel to 760-870 ℃, keeping the temperature for 1-5 min, cooling to 260-480 ℃ at a cooling speed of 10-50 ℃/s, and naturally cooling to room temperature. Wherein the continuous annealing parameters are controlled based on the texture properties of the continuous annealing plate. That is, by controlling the continuous annealing parameters, at least one of the following steel materials can be obtained after the continuous annealing is completed: 1) A dual-phase steel continuous annealing plate having a microstructure composed of ferrite and martensite for subsequent cold working; 2) The complex phase steel continuous annealing plate with the microstructure composed of ferrite, bainite, martensite and a small amount of martensite island is used for subsequent cold processing; 3) The steel for hot forming continuously annealed sheet suitable for the hot forming step as the subsequent step may have a dual phase (ferrite + martensite or ferrite + pearlite) or a complex phase (ferrite, bainite, martensite, small amount of austenite).
In some embodiments of the present invention, the continuous annealing process may comprise: heating the thin strip steel to 780-850 ℃ at the speed of 1-10 ℃/s, preserving the heat for 1-5 min, cooling to 260-320 ℃ at the cooling speed of 10-50 ℃/s, and naturally cooling to room temperature to obtain the dual-phase steel continuous annealing plate. Preferably, the thin strip steel is cooled to 670-720 ℃ at the cooling speed of 1-8 ℃/s after heat preservation, then cooled to 270-300 ℃ at the cooling speed of 15-30 ℃/s, and cooled to room temperature after heat preservation for 4-14 min.
Under the alloy system, the low-cost 780MPa grade dual-phase steel continuous annealing plate obtained by adjusting the continuous annealing process has the yield strength of 440-550 MPa, the tensile strength of 800-880 MPa and the elongation A 80 13.0 to 22.0%, and the structure thereof is composed of ferrite and martensite.
In other embodiments of the present invention, the continuous annealing process may comprise: heating the thin strip steel to 800-870 ℃ at the speed of 1-10 ℃/s, preserving the heat for 1-5 min, cooling to 350-450 ℃ at the cooling speed of 10-50 ℃/s, and then cooling to room temperature to obtain the complex phase steel continuous annealing plate. Preferably, the thin strip steel is cooled to 650-720 ℃ at a cooling speed of 1-10 ℃/s after heat preservation, then cooled to 380-450 ℃ at a cooling speed of 10-30 ℃/s, and cooled to room temperature after heat preservation for 4-14 min.
Under the alloy system, the low-cost 780 MPa-grade complex phase steel continuous annealing plate obtained by adjusting the continuous annealing process has the yield strength of 580-680 MPa, the tensile strength of 760-850 MPa and the elongation A 80 12.0 to 19.0%, and the structure thereof is composed of bainite, ferrite and martensite.
In still other embodiments of the present invention, the continuous annealing process may comprise: heating the thin strip steel to 760-830 ℃ at the speed of 1-10 ℃/s, preserving heat for 1-5 min, then cooling to 600-660 ℃ and 380-480 ℃ at the cooling speeds of 1-10 ℃/s and 10-35 ℃/s respectively, preserving heat for 4-14 min, and then cooling to room temperature to obtain the steel continuous annealing plate for hot forming.
Thermoforming
Heating the continuous annealing plate of the steel for hot forming to 900-950 ℃, preserving heat until austenitizing is completed, then transferring the continuous annealing plate to a die for forming and quenching to below 180 ℃ to obtain the hot-formed steel member. Wherein, the time required for complete austenitizing of the continuous annealing plate of the steel for hot forming with the thickness of 1.4mm is about 220 to 330s, and the heat preservation time can be adjusted by the technicians in the field according to the actual size of the continuous annealing plate of the steel for hot forming.
The yield strength of the hot forming steel obtained by adjusting the hot stamping heat treatment process to quench the low-cost steel continuous annealing plate for hot forming under the alloy system is 810-1120 MPa, the tensile strength is 1000-1250 MPa, and the elongation A is 50 5.0 to 10.0 percent, the bending angle corresponding to the continuous annealing plate VDA238 to 100 with the thickness of 1.4mm under the maximum bending load is 90 to 140 degrees, and the quenching structure of the continuous annealing plate is composed of fresh martensite and tempered martensite or fresh martensite and tempered martensite and a certain amount of bainite.
The following are specific examples of the method for preparing a dual phase steel, a complex phase steel, a steel for hot forming continuous annealing plate according to the boron-containing steel of the present invention and specific process parameters thereof.
Example 1 (DP-1)
In this example, continuous annealing was performed on sample 1 to obtain a dual phase steel continuously annealed sheet DP-1.
Specifically, the cold-rolled thin strip steel is heated to 850 ℃ at the speed of 5 ℃/s, is kept warm for 5min, is cooled to 670 ℃ at the cooling speed of 1 ℃/s, is cooled to 305 ℃ at the cooling speed of 15 ℃/s, is kept warm for 14min and is cooled to the room temperature.
Fig. 2 shows the metallographic structure of the continuously annealed dual phase steel sheet obtained in this example, which was composed of ferrite + martensite and was typical of dual phase steels.
Example 2 (DP-2)
In this example, continuous annealing was performed on sample 2 to obtain a dual phase steel continuously annealed sheet DP-2.
Specifically, the cold-rolled thin strip steel is heated to 800 ℃ at the speed of 5 ℃/s, is kept warm for 3.5min, is cooled to 685 ℃ at the cooling speed of 5 ℃/s, is cooled to 290 ℃ at the cooling speed of 30 ℃/s, is kept warm for 8min and is cooled to room temperature.
Example 3 (DP-3)
In this example, continuous annealing was performed on the test piece 3 to obtain a dual phase steel continuously annealed sheet DP-3.
Specifically, the cold-rolled thin strip steel is heated to 820 ℃ at the speed of 5 ℃/s, is kept warm for 2.5min, is cooled to 720 ℃ at the cooling speed of 4 ℃/s, is cooled to 280 ℃ at the cooling speed of 40 ℃/s, is kept warm for 6.5min, and is cooled to room temperature.
Example 4 (DP-4)
In this example, continuous annealing was performed on the test piece 4 to obtain a dual phase steel continuously annealed sheet DP-4.
Specifically, the cold-rolled thin strip steel is heated to 810 ℃ at the speed of 5 ℃/s, is kept for 2.0min, is cooled to 700 ℃ at the cooling speed of 8 ℃/s, is cooled to 260 ℃ at the cooling speed of 50 ℃/s, and is kept for 5.5min and then is cooled to room temperature.
Example 5 (CP-1)
In this example, continuous annealing was performed on the sample 1 to obtain a complex phase steel continuous annealed sheet CP-1.
Specifically, the cold-rolled thin strip steel is heated to 800 ℃ at the speed of 2 ℃/s, is kept warm for 5min, is cooled to 670 ℃ at the cooling speed of 5 ℃/s, is cooled to 400 ℃ at the cooling speed of 20 ℃/s, is kept warm for 11min and is cooled to room temperature.
Fig. 3 shows the metallographic structure of the complex phase steel continuous annealing plate obtained in the present embodiment, which is composed of ferrite + bainite + martensite, and belongs to typical complex phase steel.
Example 6 (CP-2)
In this embodiment, continuous annealing was performed on the sample 2 to obtain the complex phase steel continuous annealed sheet CP-2.
Specifically, the cold-rolled thin strip steel is heated to 830 ℃ at the speed of 10 ℃/s, is kept for 3min, is cooled to 700 ℃ at the cooling speed of 3 ℃/s, is cooled to 350 ℃ at the cooling speed of 12 ℃/s, and is kept for 9min and then is cooled to room temperature.
Example 7 (CP-3)
In this embodiment, continuous annealing was performed on the test piece 3 to obtain a complex phase steel continuous annealed sheet CP-3.
Specifically, the cold-rolled thin strip steel is heated to 820 ℃ at the speed of 5 ℃/s, is kept warm for 3min, is cooled to 720 ℃ at the cooling speed of 1 ℃/s, is cooled to 450 ℃ at the cooling speed of 10 ℃/s, is kept warm for 9min and is cooled to room temperature.
Example 8 (CP-4)
In this embodiment, continuous annealing is performed on the sample 4 to obtain the complex phase steel continuous annealed sheet CP-4.
Specifically, the cold-rolled thin strip steel is heated to 870 ℃ at the speed of 7 ℃/s, is kept warm for 3min, is cooled to 685 ℃ at the cooling speed of 10 ℃/s, is cooled to 430 ℃ at the cooling speed of 25 ℃/s, is kept warm for 9min, and is cooled to the room temperature.
Embodiment 9 (PHS-CAL-1)
In this example, continuous annealing was performed on sample 1 to obtain a hot-formed steel continuous annealing plate PHS-CAL-1.
Specifically, the cold-rolled thin strip steel is heated to 830 ℃ at the speed of 5 ℃/s, is kept for 3min, is cooled to 630 ℃ at the cooling speed of 1 ℃/s, is cooled to 480 ℃ at the cooling speed of 10 ℃/s, is kept for 9min and is cooled to room temperature.
Further, the hot-forming steel continuous annealing plate PHS-CAL-1 is heated to 915 ℃, the temperature is kept for 250s until austenitizing is completed, and then the hot-forming steel continuous annealing plate is transferred to a die to be formed and quenched to 180 ℃ to obtain a hot-forming steel component PHS-1.
Embodiment 10 (PHS-CAL-2)
In this example, continuous annealing was performed on sample 2 to obtain a hot-formed steel continuous annealing sheet PHS-CAL-2.
Specifically, the cold-rolled thin strip steel is heated to 800 ℃ at the speed of 10 ℃/s, is kept warm for 3min, is cooled to 600 ℃ at the cooling speed of 3 ℃/s, is cooled to 380 ℃ at the cooling speed of 35 ℃/s, is kept warm for 9min and is cooled to room temperature.
Further, the hot-forming steel continuous annealing plate PHS-CAL-2 is heated to 900 ℃, is kept warm for 330 seconds until austenitizing is completed, and then is transferred to a die to be formed and quenched to 20 ℃ to obtain a hot-forming steel component PHS-2.
Embodiment 11 (PHS-CAL-3)
In this example, continuous annealing was performed on the sample 3 to obtain a hot-formed steel continuous annealing plate PHS-CAL-3.
Specifically, the cold-rolled thin strip steel is heated to 760 ℃ at the speed of 2 ℃/s, is kept warm for 3min, is cooled to 620 ℃ at the cooling speed of 5 ℃/s, is cooled to 400 ℃ at the cooling speed of 20 ℃/s, is kept warm for 9min and is cooled to room temperature.
Further, the hot-forming steel continuous annealing plate PHS-CAL-3 is heated to 950 ℃, is kept warm for 220s until austenitizing is completed, and then is transferred to a die to be formed and quenched to 20 ℃ to obtain a hot-forming steel component PHS-3.
Embodiment 12 (PHS-CAL-4)
In this example, continuous annealing was performed on the test piece 4 to obtain a hot-formed steel continuous annealing plate PHS-CAL-4.
Specifically, the cold-rolled thin strip steel is heated to 810 ℃ at the speed of 7 ℃/s, is kept for 3min, is cooled to 660 ℃ at the cooling speed of 10 ℃/s, is cooled to 420 ℃ at the cooling speed of 30 ℃/s, is kept for 9min and is cooled to room temperature.
Further, the hot-forming steel continuous annealing plate PHS-CAL-4 is heated to 930 ℃, kept warm for 280 seconds until austenitizing is completed, then transferred to a die for forming and quenched to 100 ℃, and the hot-forming steel component PHS-4 is obtained.
FIGS. 4 and 5 show the microstructures of the hot-formed steel annealed sheet PHS-CAL-4 (before hot forming) and the hot-formed steel PHS-4 (after hot forming) obtained in this example, respectively, in which the microstructure before hot forming was composed of ferrite + martensite, and the microstructure after hot forming was a martensite structure.
The mechanical properties of the dual-phase steel continuous annealing plate and the dual-phase steel continuous annealing plate obtained in examples 1 to 8 were measured, and the results are shown in table 3:
TABLE 3 mechanical properties of dual-phase steel continuous annealing plate and complex-phase steel continuous annealing plate
Mechanical property tests were carried out on the hot-formed steel continuous annealed sheets and hot-formed steels obtained in examples 9 to 12, and the results are shown in tables 4 to 5:
TABLE 4 mechanical properties of the hot-formed steel continuous annealing plate before hot stamping
| Numbering | Yield strength/MPa | Tensile strength/MPa | Elongation A 80 /％ |
| PHS-CAL-1 | 459 | 641 | 21.6 |
| PHS-CAL-2 | 467 | 656 | 19.8 |
| PHS-CAL-3 | 451 | 630 | 21.1 |
| PHS-CAL-4 | 520 | 836 | 15.5 |
TABLE 5 mechanical properties of hot-stamped (1.40 mm steel sheet) steel
The result shows that the dual-phase steel structure prepared by the continuous annealing production line has ferrite and martensite, the strength grade is 780MPa, and the dual-phase steel structure has better plasticity; the microstructure of the complex phase steel consists of ferrite, bainite and martensite, has good welding performance and high elongation, and meets the requirements of high strength and high elongation; meanwhile, the alloy component system is simultaneously suitable for preparing hot stamping formed steel and corresponding parts thereof, the structure before hot stamping is ferrite and cementite, ferrite + pearlite structure or ferrite + bainite + martensite, the structure after hot stamping is fresh martensite + self-tempered martensite or fresh martensite + self-tempered martensite + a small amount of bainite, the tensile strength is as high as 1000-1300MPa, the maximum bending angle of VDA238-100 representing the collision performance is 90-140 degrees, and the ductility and toughness of the alloy component system are far superior to the ductility and toughness (the bending angle is about 62 degrees) of a 22MnB5 steel continuous annealing plate after hot stamping.
The above examples only show the embodiments of the present invention, and the description thereof is specific and detailed, but not construed as limiting the scope of the present invention. It should be noted that various changes and modifications can be made by those skilled in the art without departing from the spirit of the invention, and these changes and modifications are all within the scope of the invention. Therefore, the protection scope of the present patent shall be subject to the appended claims.
Claims (10)
1. A method for preparing a continuous annealing plate by using boron-containing steel is characterized by comprising the following steps:
casting blank: controlling the components of the boron-containing steel according to the weight percentage: c: 0.065-0.125%, mn:1.6 to 2.5%, si:0.0003 to 0.25%, cr:0.0003 to 0.3%, nb:0.0003 to 0.024%, ti:0.015 to 0.04%, B:0.0003 to 0.005%, als:0.01 to 0.1 percent, and the balance of Fe and inevitable impurities, and continuously casting the components after smelting into a plate blank;
hot rolling: heating, dephosphorizing, roughly rolling, finely rolling, laminar cooling and coiling the plate blank to obtain a hot-rolled coil;
cold rolling: cold-rolling the hot-rolled coil into thin strip steel by an acid continuous rolling production line; thin strip steel
And (3) continuous annealing: the thin strip steel is processed by a continuous annealing production line to be made into at least one of a dual-phase steel continuous annealing plate, a complex-phase steel continuous annealing plate and a steel continuous annealing plate for hot forming, wherein the continuous annealing comprises the steps of heating the thin strip steel to 760-870 ℃ at a speed of 1-10 ℃/s, keeping the temperature for 1-5 min, cooling to 260-480 ℃ at a cooling speed of 10-50 ℃/s, keeping the temperature for 4-14 min, and cooling to room temperature, wherein annealing parameters are controlled based on the structure performance of the continuous annealing plate.
2. The method according to claim 1, wherein the hot rolling is performed at a finishing rolling start temperature of 1070 to 1090 ℃, a finishing rolling temperature of 820 to 930 ℃, and a coiling temperature of 540 to 640 ℃.
3. The method of claim 2, wherein the laminar cooling is performed by front-end cooling during the hot rolling.
4. The method of claim 1, wherein a cold rolling reduction in the cold rolling process is 45 to 75%.
5. The method of any one of claims 1-4, wherein the continuous annealing comprises: heating the thin strip steel to 780-850 ℃ at the speed of 1-10 ℃/s, preserving heat for 1-5 min, cooling to 260-320 ℃ at the cooling speed of 10-50 ℃/s, preserving heat for 4-14 min, and cooling to room temperature to obtain the dual-phase steel continuous annealing plate.
6. The method as claimed in claim 5, wherein the thin strip steel is cooled to 670-720 ℃ at a cooling rate of 1-8 ℃/s after heat preservation, then cooled to 270-300 ℃ at a cooling rate of 15-30 ℃/s, and cooled to room temperature after heat preservation for 4-14 min.
7. The method of any one of claims 1-4, wherein the continuous annealing comprises: heating the thin strip steel to 800-870 ℃ at the speed of 1-10 ℃/s, preserving heat for 1-5 min, cooling to 350-450 ℃ at the cooling speed of 10-50 ℃/s, preserving heat for 4-14 min, and cooling to room temperature to obtain the complex phase steel continuous annealing plate.
8. The method as claimed in claim 7, wherein the thin strip steel is cooled to 650-720 ℃ at a cooling rate of 1-10 ℃/s after heat preservation, then cooled to 380-450 ℃ at a cooling rate of 10-30 ℃/s, and cooled to room temperature after heat preservation for 4-14 min.
9. The method of any one of claims 1 to 4, wherein the continuous annealing comprises: heating the thin strip steel to 760-830 ℃ at the speed of 1-10 ℃/s, preserving heat for 1-5 min, then cooling to 600-660 ℃ and 380-480 ℃ at the cooling speeds of 1-10 ℃/s and 10-35 ℃/s respectively, preserving heat for 4-14 min, and then cooling to room temperature to obtain the steel continuous annealing plate for hot forming.
10. The method as claimed in claim 9, wherein the hot-formed steel continuous annealing plate is heated to 900 to 950 ℃, kept warm until austenitizing is completed, and then transferred to a die to be formed and quenched to 180 ℃ or less to obtain a hot-formed steel member.
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