CN114990432B - Hot rolled strip steel with tensile strength not lower than 1500MPa produced by TSR production line and method - Google Patents
Hot rolled strip steel with tensile strength not lower than 1500MPa produced by TSR production line and method Download PDFInfo
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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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0637—Accessories therefor
- B22D11/0697—Accessories therefor for casting in a protected atmosphere
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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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- 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
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Abstract
The hot rolled strip produced by adopting a TSR production line and having the tensile strength of more than or equal to 1500MPa comprises the following components in percentage by weight: c:0.20 to 0.25%, si:0.25 to 0.50%, mn: 1.30-2.00%, P is less than or equal to 0.01%, S is less than or equal to 0.01%, als:0.015 to 0.050%, cr: 0.4-1.0%, N is less than or equal to 0.005%, nb:0.016 to 0.035 percent or Ti:0.016 to 0.035 percent or V: 0.06-0.20 percent of one or more than two; the process comprises the following steps: conventional smelting and refining; casting into a blank; hot rolling; cooling; naturally cooling after coiling; and (5) cold forming after uncoiling and blanking. According to the invention, by adding Nb, ti or V or compounding, controlling Cr and Mo and adopting a TSR process, not only can the mechanical property be ensured, but also the repeated heating, multiple dephosphorization, multiple pass rolling and the like of the strip steel can be reduced, cold rolling and annealing can be cancelled, the energy consumption is reduced by more than 80%, the carbon dioxide emission reduction is reduced by more than 70%, and the surface roughness of the strip steel is reduced to within 1 mu m from 1.5-3 mu m.
Description
Technical Field
The invention relates to a steel and a manufacturing method thereof, and particularly belongs to a hot-rolled thin strip steel with the tensile strength of more than or equal to 1500MPa grade and the method for producing the hot-rolled thin strip steel with the tensile strength of 0.5-2.0 mm by adopting a double-roller thin strip casting and rolling (TSR) production line.
Background
The light weight of the automobile is an important technical approach for realizing green low-carbon development of the automobile industry. The high-strength steel is adopted for the lightweight design and manufacture of the vehicle body, so that the collision safety of the whole vehicle can be improved, and the oil consumption or the energy consumption can be reduced. In recent years, ultrahigh-strength steel with tensile strength of more than or equal to 1000MPa is popular with domestic and foreign automobile companies, and is widely applied to manufacturing of vehicle body safety structural members such as A/B columns, anti-collision beams, doorsills and the like.
The existing ultrahigh-strength steel for automobile body parts is divided into two types, namely hot forming (hot stamping, hot rolling and the like) thin strip steel and direct cold forming (stamping, rolling and the like) thin strip steel according to the production and processing modes of the ultrahigh-strength steel. The hot-forming thin strip steel utilizes the characteristic of small deformation resistance of a plate material in a high-temperature state and has the advantage of good forming performance; but because the product needs to heat the steel plate to a high temperature state for forming, the energy consumption is higher.
At present, the 1500 MPa-grade thin steel plate for automobiles at home and abroad takes martensite steel as a main raw material, and the production process route is generally as follows: molten steel smelting → continuous casting → cooling → casting blank heating → hot continuous rolling → cooling → coiling → uncoiling → acid pickling → cold rolling → coiling → uncoiling → heating → annealing → cooling → coiling. Such as Chinese patent publication Nos. CN 110684932, CN 111979470A and CN 113462978A. In the production process, raw materials need to repeatedly undergo processes such as uncoiling and coiling, heating and cooling treatment and the like in the processes such as hot rolling, cold rolling, annealing treatment and the like, and the defects of complex production process, high energy consumption, repeated processes and high production cost of the produced final thin steel plate are necessarily caused. The development of the ultrahigh-strength thin steel plate for direct cold forming with low energy consumption, high quality, short process and low cost is an urgent need of automobile users at home and abroad and a key research direction of steel enterprises.
Disclosure of Invention
The invention aims to overcome the defects of complex process, high energy consumption and low production efficiency in the prior art, and provides the hot rolled strip steel with the tensile strength of more than or equal to 1500MPa produced by adopting a TSR production line and the method, wherein on the premise of ensuring the strength level, the energy consumption can be reduced by more than 70%, the carbon dioxide emission can be reduced by more than 60%, the surface quality of the product can be improved, namely the thickness of the surface of the strip steel is reduced to be within 1 mu m from 1.5-3 mu m of the traditional hot rolling, and the production flow is further simplified.
The measures for realizing the aim are as follows:
the hot rolled strip steel with tensile strength not lower than 1500MPa produced by a TSR production line comprises the following components in percentage by weight: c:0.20 to 0.25%, si:0.25 to 0.50%, mn: 1.30-2.00%, P is less than or equal to 0.01%, S is less than or equal to 0.01%, als:0.015 to 0.050%, cr: 0.4-1.0%, N is less than or equal to 0.005%, nb: 0.016-0.035% or Ti: 0.016-0.035% or V: 0.06-0.20% of one or more of the above components, and the balance of Fe and inevitable impurities; the metallographic structure is full martensite.
Preferably: the weight percentage content of Cr is 0.46-0.95%.
Further, the method comprises the following steps: the weight percentage content of the added B is not more than 0.001 percent.
The production method of hot rolled strip steel with tensile strength of more than or equal to 1500MPa produced by a TSR production line comprises the following steps:
1) Conventionally smelting and refining to obtain molten steel with the components;
2) Casting into a blank: strip casting with a twin roll casting plant to obtain a cast strip, during which: controlling the molten steel to carry out thin strip continuous casting under the protection of conventional inert gas, wherein the thickness of a cast strip is 1.0-2.5 mm;
3) Hot rolling to the thickness of the product, and controlling the thickness of the product to be 0.5-2.0 mm; during the period: controlling single pass reduction rate at 20 to
60 percent, and the finishing temperature is 850-1000 ℃;
4) Cooling, namely cooling to the coiling temperature at a cooling speed of not less than 50 ℃/s by adopting laminar flow type or aerosol type cooling;
5) Coiling and then naturally cooling to room temperature; controlling the coiling temperature not to exceed 210 ℃;
6) And (5) cold forming after uncoiling and blanking.
Further, the method comprises the following steps: the hot rolled thin strip steel after coiling is not pickled before forming.
Preferably: the casting and rolling speed is 46-117 m/min.
Preferably: the coiling temperature is 150-206 ℃.
The action and mechanism of each element and the main process in the invention are as follows:
c: carbon is an essential element in steel and is also the most economical and effective strengthening element. The carbon content is designed to be lower, and the strength is reduced after hot stamping forming; however, too high a carbon content lowers the plasticity of the steel and is disadvantageous in weldability. Therefore, the control range of the percentage content of carbon in the invention is 0.20-0.25% from the aspects of economy and comprehensive performance.
Si: silicon is a solid-solution strengthening element, and is solid-dissolved in ferrite, which contributes to improvement in the strength of the base material and the hot-stamped material. With the increase of the silicon content, the strength of the steel is obviously improved, the plasticity is obviously reduced, and the welding performance is reduced. Therefore, the silicon content is controlled in the range of 0.25 to 0.50%.
Mn: manganese has a solid solution strengthening effect and is one of important elements for improving the strength of the material; however, the addition of manganese in an excessively high amount tends to be disadvantageous in weldability. Therefore, the upper limit of manganese is set to be 2.0 percent, and the content of the added manganese is 1.3 to 2.0 percent.
P: phosphorus is a harmful element in steel and is easy to cause center segregation of a casting blank. The steel is easy to be deviated to a grain boundary in the subsequent hot continuous rolling heating process, so that the brittleness of the steel is obviously increased. Meanwhile, the content is controlled to be below 0.01 percent based on the consideration of cost and without influencing the performance of steel.
S sulfur is a very harmful element. Sulfur in steel often exists in the form of sulfide of manganese, and this sulfide inclusion deteriorates toughness of steel and causes anisotropy of properties, so that the lower the sulfur content in steel, the better. The sulfur content in steel is controlled to be below 0.01% in consideration of the manufacturing cost.
And Als: aluminum is added for deoxidation, and when the content of Als is less than 0.015%, the effect thereof cannot be exerted; on the other hand, since addition of a large amount of aluminum easily forms alumina agglomerate inclusions, the aluminum content is controlled in the range of 0.015 to 0.050%.
Cr is an important element for improving the hardenability of steel, is dissolved into austenite to improve the stability of the austenite, and is beneficial to improving the hardenability of the steel to obtain a martensite structure; meanwhile, the chromium can improve the tempering stability of the steel. When the chromium content exceeds 1.0%, the hardenability is improved with a surplus, and a cast strip obtained by continuous casting is easy to generate surface cracks at a high drawing speed, so that strip breakage and steel leakage are caused or the surface quality of a product is influenced. Therefore, the chromium content in the present invention is controlled to 0.4 to 1.0%, and preferably the content of Cr is 0.46 to 0.95% by weight.
N can improve the strength of the steel; however, the bonding force of nitrogen with niobium and titanium is strong, and coarse niobium nitride and titanium nitride particles can be formed in the steel at high temperature, so that the plasticity and toughness of the steel are seriously damaged; in addition, higher nitrogen content increases the amount of micro-alloying elements needed to stabilize the nitrogen element, thereby increasing costs. Therefore, the content of nitrogen should be reduced as much as possible, and nitrogen is controlled to 0.005% or less in the present invention.
Nb, ti: niobium and titanium are strong C and N compound forming elements. A certain amount of niobium carbon and nitride can be formed by adding a small amount of niobium into the steel, so that austenite grains are prevented from growing and being refined, and the strength and the toughness of the steel after hot forming and quenching are greatly improved; the purpose of adding a small amount of titanium to the steel is to fix the N element in the steel and avoid the combination of B and N. However, excessive amounts of niobium and titanium combine with C to form coarse carbonitrides, thereby reducing the hardness and strength of the martensite after quenching of the test steel. Therefore, the total content is controlled to be in the range of 0.016 to 0.035%.
V is also a strong C and N compound forming element and can play a role in refining austenite grains, and a certain amount of niobium carbon and nitride can be formed by adding a small amount of vanadium into steel so as to prevent the austenite grains from growing, so that the size of a martensite lath after quenching is smaller, and the strength of the steel is greatly improved. Therefore, the content is controlled between 0.06 percent and 0.020 percent.
B is an element for strongly improving hardenability, and obvious influence can be caused by only adding a trace amount of boron, so that the hardenability can be improved by times, and other expensive metal elements are saved. The hardenability of the steel can be obviously improved by adding trace boron element into the steel. But the boron content is higher than 0.001 percent, and the cast strip obtained by continuous casting is easy to generate surface cracks at high drawing speed, thereby causing strip breakage and steel leakage or influencing the poor surface quality of products. Therefore, the boron content in the present invention is controlled to 0.001% or less.
According to the invention, the molten steel is controlled to carry out thin strip continuous casting under the protection of conventional inert gas, the thickness of the cast strip is 1.0-2.5 mm, and because of the thinner original thickness of the cast strip, the subsequent hot rolling reduction passes can be effectively reduced, and the production energy consumption is reduced; however, the thickness of the cast strip is too thin, and the strip is easy to break under the condition of high stretching of cast rolling, so that the continuity of production is influenced. The molten steel is controlled to carry out thin-strip continuous casting under the protection of conventional inert gas, so that the surface oxidation of the continuous casting thin strip can be avoided, the strip breakage caused by the pressing of oxides into the continuous casting thin strip is prevented, and the improvement of the surface quality of a product is facilitated.
The invention controls the single pass reduction rate to be 20-60% and the final rolling temperature to be 850-1000 ℃, and the larger hot rolling reduction rate can refine the grains of the strip steel and is beneficial to improving the strength of the material. However, the rolling reduction rate is too large, which is disadvantageous to controlling the plate shape and increases the rolling load; considering that the method only adopts single-pass hot rolling, the reduction rate is controlled within 60 percent to ensure that the shape and thickness precision of the product plate is controllable. In order to avoid the influence of mixed crystals in the hot rolling stage on the material performance, the finish rolling temperature cannot be lower than the cooling recrystallization temperature (Ar 3) 850 ℃ of high-temperature austenite; meanwhile, the surface oxidation thickness of the strip steel is increased along with the rise of the finish rolling temperature, so the finish rolling temperature is controlled within 1000 ℃.
The casting speed of 46-117 m/min is preferred in the present invention because the casting speed is related to the strip drawing speed and the steel production efficiency of the continuous casting. The high drawing speed is beneficial to improving the production efficiency, but molten steel can not be solidified in time in the double-stick casting machine easily, and the cast strip is broken to cause steel leakage; lower elongation will affect production efficiency, increase production cost, and at the same time will result in cold hardening of the cast strip, increase subsequent rolling load and energy consumption, and is detrimental to controlling strip shape.
The reason why the in-mold quenching is controlled to be cooled to below 210 ℃ at a quenching speed of not less than 50 ℃/s is that the steel sheet developed by the invention has a critical cooling speed and a critical finish temperature at which the steel sheet is converted into 100% martensite during the quenching treatment, otherwise the steel sheet cannot be sufficiently quenched to achieve the required strength. The cooling coiling temperature is preferably 150-208 ℃, because the plate belt preheating can be used for the self-tempering treatment of the plate temperature, the internal stress generated in quenching can be reduced or eliminated, and the plasticity of the strip steel is improved; meanwhile, the strip steel can utilize the waste heat to reduce the deformation resistance of the strip steel, so that the strip steel is convenient to curl.
Compared with the prior art, the Nb, ti and V are added compositely, elements such as Cr, B, mo and the like in the components are controlled, and the TSR short-flow process is adopted to produce the hot forming steel with the tensile strength of 1500MPa, so that the mechanical property of the hot forming steel can be ensured, the processes of repeatedly heating the steel in the production process, removing phosphorus for multiple times, rolling for multiple times and the like can be reduced, the cold rolling and annealing heat treatment processes can be cancelled, the energy consumption can be reduced by more than 80%, the carbon dioxide emission can be reduced by more than 70%, and the surface quality of the product, namely the thickness of the surface of the strip steel is reduced to be within 1 mu m from the traditional 1.5-3 mu m.
Drawings
FIG. 1 is a metallographic structure diagram of a steel sheet according to the present invention.
Detailed Description
The present invention is described in detail below:
table 1 is a list of chemical compositions for each example of the present invention and comparative example;
table 2 is a table of the main process parameters of each example of the present invention and comparative example;
table 3 is a table showing the results of the performance tests of the examples of the present invention and the comparative examples.
The production of each embodiment of the invention is carried out according to the following steps:
1) Conventionally smelting and refining to obtain molten steel with the components;
2) Casting to form a blank: strip casting with a twin roll casting plant to obtain a cast strip, during which: controlling the molten steel to perform strip continuous casting under the protection of conventional inert gas, and controlling the thickness of a cast strip to be 1.0-2.5 mm;
3) Hot rolling to the thickness of the product, and controlling the thickness of the product to be 0.5-2.0 mm; during the period: controlling the single-pass reduction rate at 20 to
60 percent, and the finishing temperature is 850-1000 ℃;
4) Cooling, namely cooling to the coiling temperature at a cooling speed of not less than 50 ℃/s by adopting laminar flow type or aerosol type cooling; 5) Coiling and then naturally cooling to room temperature; controlling the coiling temperature to be 150-208 ℃;
6) And (5) cold forming after uncoiling and blanking.
TABLE 1 chemical composition (wt.%) of inventive and comparative examples
TABLE 2 list of values of main process parameters of the examples and comparative examples of the present invention
TABLE 3 results of testing the properties of the inventive and comparative examples
As can be seen from the table 3, the tensile strength of the direct cold forming of the thin steel plate of the invention reaches the hot rolling thin steel plate of more than 1500MPa through the TSR double-roll thin strip casting and rolling process, which is far higher than the product strength of the existing TSR production line; the method has important significance for promoting the light weight level of the automobile and reducing the energy consumption and carbon emission in steel production.
The present embodiments are merely preferred examples, and are not intended to limit the scope of the present invention.
Claims (4)
1. The production method of hot rolled strip steel with tensile strength of more than or equal to 1500MPa produced by a TSR production line comprises the following steps:
the hot rolled strip steel with the tensile strength of more than or equal to 1500MPa produced by the TSR production line comprises the following components in percentage by weight: c:0.20 to 0.25%, si:0.42 to 0.50%, mn: 1.30-2.00%, P is less than or equal to 0.01%, S is less than or equal to 0.01%, als:0.041 to 0.050%, cr: 0.86-1.0%, N is less than or equal to 0.005%, nb:0.016 to 0.035 percent or Ti: 0.016-0.035% or V: 0.06-0.20% of one or more than two of the components are added in a composite way, and the balance is Fe and inevitable impurities; the metallographic structure is full martensite;
1) Conventionally smelting and refining to obtain molten steel of the components;
2) Casting into a blank: strip casting with a twin roll casting plant to obtain a cast strip, during which: controlling the molten steel to carry out thin strip continuous casting under the protection of conventional inert gas, wherein the thickness of a cast strip is 1.0-2.5 mm;
3) Hot rolling to the thickness of the product, and controlling the thickness of the product to be 0.5-2.0 mm; during the period: controlling the single-pass reduction rate to be 20-60% and the final rolling temperature to be 850-1000 ℃;
4) Cooling, adopting laminar flow or aerosol cooling, and cooling to the coiling temperature at the cooling speed of 50-85 ℃/s;
5) Coiling and naturally cooling to room temperature; controlling the coiling temperature not to exceed 210 ℃;
6) And (5) carrying out cold forming after uncoiling and blanking.
2. The production method of hot-rolled strip steel with tensile strength not lower than 1500MPa produced by the TSR production line according to claim 1, which is characterized in that: the hot rolled thin strip steel after coiling is not pickled before forming.
3. The production method of hot-rolled strip steel with tensile strength not lower than 1500MPa produced by the TSR production line according to claim 1, which is characterized in that: the casting and rolling speed is 46-117 m/min.
4. The production method of hot-rolled strip steel with tensile strength not lower than 1500MPa produced by the TSR production line according to claim 1, which is characterized in that: the coiling temperature is 150-208 ℃.
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| JP5020572B2 (en) * | 2006-08-31 | 2012-09-05 | 新日本製鐵株式会社 | High strength thin steel sheet with excellent delayed fracture resistance after forming |
| CN101603119B (en) * | 2009-07-03 | 2010-12-29 | 马景怡 | Method for manufacturing steel plate with high strength and high toughness by using hot-rolling coiled plate |
| CN102031456B (en) * | 2009-09-30 | 2013-07-03 | 鞍钢股份有限公司 | Steel plate for stamping and quenching and thermoforming method of steel plate |
| CN106399837B (en) * | 2016-07-08 | 2018-03-13 | 东北大学 | Hot press-formed steel, hot press-formed technique and hot press-formed component |
| CN112522573B (en) * | 2019-09-19 | 2022-06-21 | 宝山钢铁股份有限公司 | B-containing martensite steel strip and manufacturing method thereof |
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| CN111455282B (en) * | 2020-05-11 | 2021-03-16 | 武汉钢铁有限公司 | Quenching distribution steel with tensile strength more than or equal to 1500MPa produced by adopting short process and method |
| CN114214563B (en) * | 2021-12-07 | 2022-12-27 | 武汉科技大学 | High-toughness hot stamping steel rolled by sheet billet with Rm more than or equal to 1500MPa and production method |
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