CN111793777A - 1000 MPa-level hot-rolled high-strength corrosion-resistant dual-phase steel plate and preparation method thereof - Google Patents
1000 MPa-level hot-rolled high-strength corrosion-resistant dual-phase steel plate and preparation method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/02—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of sheets
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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
- C22C38/04—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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
Abstract
A 1000MPa grade high-strength hot-rolled corrosion-resistant dual-phase steel plate and a preparation method thereof; the steel plate comprises the following chemical components in percentage by mass: c: 0.10 to 0.25%, Si: 0.20 to 1.20%, Mn: 1.40-2.00%, Cr: 0.35-0.60%, Ni: 0.10-0.30%, Cu: 0.20 to 0.50%, Nb: 0.020 to 0.060%, Ti: 0.020 to 0.060%, Alt: 0.02-0.07%, P is less than or equal to 0.020%, S is less than or equal to 0.0050%, and the balance of Fe and inevitable residual impurity elements. The preparation method comprises the following steps: molten iron pretreatment → converter smelting → LF furnace refining → continuous casting → hot rolling. The invention realizes the tensile strength of the product to reach 1000MPa by applying the comprehensive effects of second-phase martensite reinforcement and assisting fine-grain reinforcement and precipitation reinforcement.
Description
Technical Field
The invention relates to a 1000 MPa-level hot-rolled high-strength corrosion-resistant dual-phase steel plate and a preparation method thereof, belonging to the technical field of hot-rolled automobile steel production.
Background
With the rapid development of the automobile industry in recent years, the dual-phase steel gradually receives attention from people by virtue of the advantages of good strength and toughness matching, low yield ratio, high collision energy absorption capacity and the like. Therefore, the dual-phase steel is very widely applied to automobile lightweight materials, for example, in the future FSV (future Steel vehicle) project of steel automobiles, the dual-phase steel occupies 31.3 percent.
Currently, due to the urgent need of environmental protection and energy saving, the research and development of ultra-high strength dual-phase steel is very important, and for common transportation structures, the development of a material with high strength, light weight and good corrosion resistance is urgently needed to increase the weight of single-time transportable goods and prolong the service life of the material. In order to meet the requirements of thinning and corrosion resistance of steel plates, the development of ultra-high strength hot-rolled corrosion resistant steel plates with tensile strength of 1000MPa or more is more and more favored by users, and the steel plates in the grade can effectively reduce the consumption of steel materials so as to reduce the manufacturing cost. In addition, the steel plate has good corrosion resistance, and is suitable for the development requirements of light weight of railway vehicles, containers and the like.
Disclosure of Invention
The invention aims to provide a 1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel plate and a preparation method thereof. The tensile strength of the product reaches 1000MPa by reasonable chemical composition design and the application of second-phase martensite reinforcement and the assistance of the comprehensive effects of fine-grain reinforcement and precipitation reinforcement. The technical scheme of the invention is as follows:
a1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel plate comprises the following chemical components in percentage by mass: c: 0.10 to 0.25%, Si: 0.20 to 1.20%, Mn: 1.40-2.00%, Cr: 0.35-0.60%, Ni: 0.10-0.30%, Cu: 0.20 to 0.50%, Nb: 0.020 to 0.060%, Ti: 0.020 to 0.060%, Alt: 0.02-0.07%, P is less than or equal to 0.020%, S is less than or equal to 0.0050%, and the balance of Fe and inevitable residual impurity elements.
The invention provides a preparation method of a 1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel plate, which comprises the following steps:
molten iron pretreatment → converter smelting → LF furnace refining → continuous casting → hot rolling;
hot rolling: the heating temperature is 1200-1250 ℃, the rough rolling is carried out in an austenite recrystallization region, the rough rolling stage adopts 5-7 passes, the thickness of an intermediate blank is 30-50 mm, the finish rolling is carried out in an austenite non-recrystallization region, the finish rolling stage adopts 7 passes, the finish rolling temperature is controlled at 810-860 ℃, and the thickness is reduced to the required thickness; adopting a sectional cooling process, and carrying out first-stage water cooling: the cooling rate is 10-50 ℃/S, and the temperature is reduced to 650-700 ℃; air cooling in the second stage: air cooling time is 4-10S; and (3) third-stage water cooling: cooling at 50-150 deg.c/S to 350 deg.c for coiling.
Further, the pretreatment of molten iron comprises: adding lime and fluorite into a hot metal tank filled with molten iron for desulfurization treatment, and adsorbing the treated product to the lime and the fluorite to be melted to form protective slag; wherein, the new ladle, the ladle bottom ladle with the weight of more than 2 tons, the return ladle and the residual molten steel are not allowed to be used for smelting the steel grade by 15 furnaces before newly opening the furnace, 1 st furnace after the large fettling furnace and the like.
Smelting in the converter: adding molten iron into a furnace containing nickel-containing raw materials, a copper plate and scrap steel, wherein S is less than or equal to 0.005%, and the thickness of slag is less than or equal to 30 mm; the end point avoids back blowing as much as possible and reduces the number of times of furnace turnover; the steel tapping hole is good and does not scatter flow. The argon blowing needs to avoid large-area exposure of molten steel.
And refining in the LF furnace: after the furnace is subjected to S removal, finely adjusting the components in the steel; 2m of Ca-Si wire per ton of steel (about Si increasing: 0.030%) is fed before weak stirring, the diameter of the Ca-Si wire is 12-13mm, the wire feeding speed is 200-250 m/min, and then the weak stirring time is 10-50 min.
The continuous casting is carried out; full-protection pouring and electromagnetic stirring are adopted, and hot charging or cold charging is adopted after the slab after continuous casting is cut.
The basic principle of the design of the content of each alloy element in the invention is as follows:
carbon: the most economical and effective strengthening elements are also main elements for improving hardenability and forming martensite, and the carbon content in the steel determines the strength and the martensite content of the dual-phase steel; the invention controls the content of C within the range of 0.10-0.25%.
Silicon: ferrite forming elements can effectively promote C to diffuse into austenite when the two-phase region is subjected to heat preservation and slow cooling, have a remarkable purification effect on ferrite, improve the purity of the ferrite in the dual-phase steel and improve the work hardening rate of the ferrite; therefore, the invention controls the Si content within the range of 0.20-1.20%.
Manganese: belongs to typical austenite stabilizing elements, can obviously improve the hardenability of steel, can obviously delay the transformation of pearlite and bainite, and reduces the critical cooling rate of martensite formation. The invention controls the Mn content within the range of 1.40-2.00%.
Chromium: the oxidation resistance of the steel can be obviously improved, the corrosion resistance of the steel is improved, and meanwhile, the yield ratio of the dual-phase steel can be reduced by adding a proper amount of Cr, the distribution of martensite is improved, and the elongation is further improved. The invention comprehensively considers the corrosion resistance, the impact toughness and the alloy cost of steel, but the Cr content is too high, and the Cr content is easy to generate complex FeMnCr carbide with Fe, Mn and C in the steel, and the forming performance of the steel is adversely affected, so the invention controls the Cr: 0.35 to 0.60 percent.
Nickel: the effective element of austenitizing can increase the Ac3 temperature of the steel grade, shift the C curve to the right, reduce the critical cooling speed of the steel, and improve the hardenability and strength of the steel without reducing the plasticity of the steel. In addition, Ni improves low-temperature toughness and fatigue resistance of steel and provides steel plates with certain corrosion resistance. The Ni content of the invention is controlled to be 0.10-0.30%.
Copper: the average corrosion depth and corrosion rate of the steel can be effectively reduced, and the corrosion resistance of the steel is improved. Meanwhile, as Cu and Cr are enriched in the rust layer, the density of the rust layer is increased, and the weight loss rate of the steel is obviously reduced. Meanwhile, the Ni/Cu ratio in the steel is generally controlled within the range of 1/2-2/3 in order to improve the surface quality of the hot rolled steel strip. The Cu content of the invention is controlled to be 0.20-0.50%
Niobium: the steel has obvious grain refining effect, and the hardenability of austenite can be obviously improved by solid solution of Nb in the steel; nb can promote the martensite to be refined and uniformly distributed while the ferrite grains are refined, thereby greatly improving the uniformity of the steel and improving the cold bending property of the steel. The content of Nb is controlled within the range of 0.020-0.060%.
Titanium: the method has two main functions in steel, namely, austenite grains are refined, and finally transformed ferrite and martensite are refined; and secondly, the nitrogen-fixing agent is combined with N element to form TiN, thereby playing a role in nitrogen fixation. The invention controls the Ti content within the range of 0.020-0.060%.
Aluminum: the most effective deoxidizing element, and meanwhile, Al is combined with N in the steel to form AlN, so that solid solution interstitial atoms in the steel are reduced, and the work hardening rate of the steel is improved; on the other hand, the AlN particles inhibit the growth of crystal grains and play a certain role in refining the crystal grains. However, as the content of Alt increases, the number of inclusions in the steel increases, and the size of the inclusions increases. Therefore, the invention controls the Alt content within the range of 0.02-0.07%.
Influence of the manufacturing process on the product of the invention:
smelting and refining treatment in a converter or an LF (ladle furnace): the method aims to ensure the basic component requirements of molten steel, remove harmful gases such as oxygen, nitrogen and hydrogen and harmful impurities such as P, S in the steel, and add necessary alloy elements such as carbon, manganese, silicon, chromium, niobium and aluminum to adjust the alloy elements.
Continuous casting: the internal components of the casting blank are ensured to be uniform, the surface quality is good, full-protection pouring and electromagnetic stirring are adopted in continuous casting, inclusions are reduced, Mn segregation is reduced, the quality of the casting blank is improved, and dendritic crystals are crushed; and hot charging or cold charging is adopted after the continuously cast slab is cut.
Hot rolling: in order to ensure that the alloy elements are fully dissolved in a solid solution and the austenite grains do not grow abnormally, the heating temperature is controlled to be 1200-1250 ℃, and the heat preservation time is more than or equal to 180 min. Rough rolling is carried out in an austenite recrystallization region, 5-7 passes are adopted in the rough rolling stage, the thickness of an intermediate blank is 30-50 mm, finish rolling is carried out in an austenite non-recrystallization region, 7 passes are adopted in the finish rolling stage, the finish rolling temperature is controlled at 810-860 ℃, and the blank is rolled to the required thickness. Adopting a sectional cooling process, and carrying out first-stage water cooling: the cooling rate is 10-50 ℃/S, and the temperature is reduced to 650-700 ℃; air cooling in the second stage: air cooling time is 4-10S; and (3) third-stage water cooling: cooling at 50-150 deg.c/S to 350 deg.c for coiling.
Compared with the prior art, the invention has the following advantages:
from the aspects of economy and light weight, the tensile strength of the product reaches 1000MPa by reasonable chemical composition design and application of second-phase martensite reinforcement and the combined action of fine-grain reinforcement and precipitation reinforcement, and the atmospheric corrosion resistance of the material is improved by reasonably adding alloy elements such as Cr, Ni, Cu and the like on the basis of the original chemistry; the atmospheric corrosion resistance index (I) is improved to 5.0-7.0 from 0.5 of low alloy steel.
Detailed Description
The invention will be further described with reference to specific embodiments, and the advantages and features of the invention will become apparent as the description proceeds. The examples are illustrative only and do not limit the scope of the present invention in any way. It will be understood by those skilled in the art that various changes in form and details may be made therein without departing from the spirit and scope of the invention, and that such changes and modifications may be made without departing from the spirit and scope of the invention.
Example 1: 1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel plate and preparation method thereof
A1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel plate comprises the following chemical components in percentage by mass: c: 0.15%, Si: 0.50%, Mn: 1.75%, Cr: 0.50%, Ni: 0.21%, Cu: 0.34%, Nb: 0.042%, Ti: 0.025%, Alt: 0.032%, P: 0.009%, S: 0.0011%, the balance being iron and unavoidable impurities.
The process flow comprises the following steps: molten iron pretreatment → smelting → LF furnace refining → continuous casting → hot rolling
The hot rolling step comprises: heating temperature of the strip steel: and at 1200 ℃, 7 passes are adopted in the rough rolling stage, the thickness of the intermediate blank is 32mm, the finish rolling is carried out in an austenite non-recrystallization region, 7 passes are adopted in the finish rolling stage, the finish rolling temperature is controlled at 830 ℃, and the rolling is carried out to 3.0 mm. Adopting a sectional cooling process, and carrying out first-stage water cooling: cooling to 690 ℃ at a cooling rate of 45 ℃/S; air cooling in the second stage: air cooling time is 6S; and (3) third-stage water cooling: cooling at 130 deg.C/S, and coiling at 230 deg.C.
The detection shows that the yield strength of the obtained 1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel product is 780MPa, the tensile strength is 1103MPa, and the elongation is 17.5%.
Example 2: 1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel plate and preparation method thereof
A1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel plate comprises the following chemical components in percentage by mass:
c: 0.13%, Si: 0.45%, Mn: 1.67%, Cr: 0.47%, Ni: 0.23%, Cu: 0.32%, Nb: 0.053%, Ti: 0.038%, Alt: 0.043%, P: 0.010%, S: 0.003%, and the balance iron and inevitable impurities.
The process flow comprises the following steps: molten iron pretreatment → smelting → LF furnace refining → continuous casting → hot rolling
The molten iron pretreatment: adding lime and fluorite into a hot metal tank filled with molten iron for desulfurization treatment, and adsorbing the treated product to the lime and the fluorite to be melted to form protective slag; wherein, the new ladle, the ladle bottom ladle with the weight of more than 2 tons, the return ladle and the residual molten steel are not allowed to be used for smelting the steel grade by 15 furnaces before newly opening the furnace, 1 st furnace after the large fettling furnace and the like.
Smelting in the converter: adding molten iron into a furnace containing nickel-containing raw materials, a copper plate and scrap steel, wherein S is less than or equal to 0.005%, and the thickness of slag is less than or equal to 30 mm; the end point avoids back blowing as much as possible and reduces the number of times of furnace turnover; the steel tapping hole is good and does not scatter flow. The argon blowing needs to avoid large-area exposure of molten steel.
And refining in the LF furnace: after the furnace is subjected to S removal, finely adjusting the components in the steel; 2m Ca-Si wires per ton of steel (about Si increase: 0.030%) are fed before weak stirring, the diameter of the Ca-Si wires is 12-13mm, the wire feeding speed is 230m/min, and then the weak stirring time is 30 min.
The continuous casting is carried out; full-protection pouring and electromagnetic stirring are adopted, and hot charging is adopted after the slab after continuous casting is cut.
The hot rolling step comprises: heating temperature of the strip steel: and at 1200 ℃, 7 passes are adopted in the rough rolling stage, the thickness of the intermediate blank is 32mm, the finish rolling is carried out in an austenite non-recrystallization region, 7 passes are adopted in the finish rolling stage, the finish rolling temperature is controlled at 830 ℃, and the rolling is carried out to 4.0 mm. Adopting a sectional cooling process, and carrying out first-stage water cooling: cooling to 690 ℃ at a cooling rate of 45 ℃/S; air cooling in the second stage: air cooling time is 7S; and (3) third-stage water cooling: cooling at 135 deg.C/S, cooling to 200 deg.C, and coiling.
The detection shows that the yield strength of the obtained 1000MPa grade high-strength hot-rolled corrosion-resistant dual-phase steel product is 690MPa, the tensile strength is 1054MPa, and the elongation is 17.0%.
Example 3: 1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel plate and preparation method thereof
A1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel plate comprises the following chemical components in percentage by mass:
c: 0.21%, Si: 1.12%, Mn: 1.85%, Cr: 0.38%, Ni: 0.18%, Cu: 0.38%, Nb: 0.04%, Ti: 0.045%, Alt: 0.035%, P: 0.011%, S: 0.002%, and the balance of iron and inevitable impurities.
The process flow comprises the following steps: molten iron pretreatment → smelting → LF furnace refining → continuous casting → hot rolling
The molten iron pretreatment: adding lime and fluorite into a hot metal tank filled with molten iron for desulfurization treatment, and adsorbing the treated product to the lime and the fluorite to be melted to form protective slag; wherein, the new ladle, the ladle bottom ladle with the weight of more than 2 tons, the return ladle and the residual molten steel are not allowed to be used for smelting the steel grade by 15 furnaces before newly opening the furnace, 1 st furnace after the large fettling furnace and the like.
Smelting in the converter: adding molten iron into a furnace containing nickel-containing raw materials, a copper plate and scrap steel, wherein S is less than or equal to 0.005%, and the thickness of slag is less than or equal to 30 mm; the end point avoids back blowing as much as possible and reduces the number of times of furnace turnover; the steel tapping hole is good and does not scatter flow. The argon blowing needs to avoid large-area exposure of molten steel.
And refining in the LF furnace: after the furnace is subjected to S removal, finely adjusting the components in the steel; 2m Ca-Si wires per ton of steel (about Si increase: 0.030%) are fed before weak stirring, the diameter of the Ca-Si wires is 12-13mm, the wire feeding speed is 230m/min, and then the weak stirring time is 30 min.
The continuous casting is carried out; full-protection pouring and electromagnetic stirring are adopted, and cold charging is adopted after the slab after continuous casting is cut.
The hot rolling step comprises: heating temperature of the strip steel: and at 1200 ℃, 7 passes are adopted in the rough rolling stage, the thickness of the intermediate blank is 32mm, the finish rolling is carried out in an austenite non-recrystallization region, 7 passes are adopted in the finish rolling stage, the finish rolling temperature is controlled at 830 ℃, and the rolling is carried out to 4.0 mm. Adopting a sectional cooling process, and carrying out first-stage water cooling: cooling to 690 ℃ at a cooling rate of 45 ℃/S; air cooling in the second stage: air cooling time is 7S; and (3) third-stage water cooling: cooling at 135 deg.C/S, cooling to 200 deg.C, and coiling.
The detection shows that the yield strength of the obtained 1000MPa grade high-strength hot-rolled corrosion-resistant dual-phase steel product is 690MPa, the tensile strength is 1065MPa, and the elongation is 16.5%.
Claims (7)
1. A1000 MPa-grade high-strength hot-rolled corrosion-resistant dual-phase steel plate is characterized by comprising the following chemical components in percentage by mass: c: 0.10 to 0.25%, Si: 0.20 to 1.20%, Mn: 1.40-2.00%, Cr: 0.35-0.60%, Ni: 0.10-0.30%, Cu: 0.20 to 0.50%, Nb: 0.020 to 0.060%, Ti: 0.020 to 0.060%, Alt: 0.02-0.07%, P is less than or equal to 0.020%, S is less than or equal to 0.0050%, and the balance of Fe and inevitable residual impurity elements.
2. The 1000MPa grade high-strength hot-rolled corrosion-resistant dual-phase steel plate according to claim 1, which is characterized by comprising the following chemical components in percentage by mass: c: 0.15%, Si: 0.50%, Mn: 1.75%, Cr: 0.50%, Ni: 0.21%, Cu: 0.34%, Nb: 0.042%, Ti: 0.025%, Alt: 0.032%, P: 0.009%, S: 0.0011%, the balance being iron and unavoidable impurities.
3. The preparation method of the 1000MPa grade high-strength hot-rolled corrosion-resistant dual-phase steel plate as claimed in claims 1-2, comprises the following steps:
molten iron pretreatment → converter smelting → LF furnace refining → continuous casting → hot rolling;
hot rolling: the heating temperature is 1200-1250 ℃, the rough rolling is carried out in an austenite recrystallization region, the rough rolling stage adopts 5-7 passes, the thickness of an intermediate blank is 30-50 mm, the finish rolling is carried out in an austenite non-recrystallization region, the finish rolling stage adopts 7 passes, the finish rolling temperature is controlled at 810-860 ℃, and the thickness is reduced to the required thickness; adopting a sectional cooling process, and carrying out first-stage water cooling: the cooling rate is 10-50 ℃/S, and the temperature is reduced to 650-700 ℃; air cooling in the second stage: air cooling time is 4-10S; and (3) third-stage water cooling: cooling at 50-150 deg.c/S to 350 deg.c for coiling.
4. The method according to claim 3, wherein the molten iron pretreatment: adding lime and fluorite into a hot metal tank filled with molten iron for desulfurization treatment, and adsorbing the treated product to the lime and the fluorite to be melted to form protective slag; wherein, the new ladle, the ladle bottom ladle with the weight of more than 2 tons, the return ladle and the residual molten steel are not allowed to be used for smelting the steel grade by 15 furnaces before newly opening the furnace, 1 st furnace after the large fettling furnace and the like.
5. The method according to claim 3, wherein the converter smelting comprises: molten iron is added into a furnace containing nickel-containing raw materials, a copper plate and scrap steel, wherein S is less than or equal to 0.005 percent, and the thickness of slag is less than or equal to 30 mm.
6. The method of claim 3, wherein the LF furnace refining: after the furnace is subjected to S removal, finely adjusting the components in the steel; feeding Ca-Si wires 2 m/ton steel before weak stirring, wherein the wire feeding speed is 200-250 m/min, and then, the weak stirring time is 10-50 min.
7. The manufacturing method according to claim 3, wherein the continuous casting adopts full-protection pouring and electromagnetic stirring, and the continuous cast slab is cut and then hot-packed or cold-packed.
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| CN112718859A (en) * | 2021-01-22 | 2021-04-30 | 山西太钢不锈钢股份有限公司 | Hot continuous rolling method for super duplex stainless steel coiled plate |
| CN114790532A (en) * | 2022-06-22 | 2022-07-26 | 江苏省沙钢钢铁研究院有限公司 | Alloy corrosion-resistant steel bar and preparation method thereof |
| CN116121642A (en) * | 2022-12-22 | 2023-05-16 | 本钢板材股份有限公司 | Steel with tensile strength of 1000MPa and preparation method and application thereof |
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| CN116121642A (en) * | 2022-12-22 | 2023-05-16 | 本钢板材股份有限公司 | Steel with tensile strength of 1000MPa and preparation method and application thereof |
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