CN113846270A - Production method of extra-thick ultrahigh-strength SX690DZ35 steel plate - Google Patents
Production method of extra-thick ultrahigh-strength SX690DZ35 steel plate 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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- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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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
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—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
The invention discloses a production method of an extra-thick ultrahigh-strength SX690DZ35 steel plate, which comprises the following chemical components in percentage by mass: 0.11 to 0.13 percent of C, 0.01 to 0.15 percent of Si, 0.95 to 1.20 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.005 percent of S, 0.03 to 0.05 percent of Nb, 0.02 to 0.04 percent of V, 0.50 to 0.60 percent of Mo, more than 0.45 and less than or equal to 0.55 percent of Cr, 2.7 to 3.4 percent of Ni, 0.2 to 0.3 percent of Cu, 0.020 to 0.050 percent of Als, less than 0.03 percent of Zr, less than 0.06 percent of Ce, and the balance of Fe and residual elements; the production method comprises the following steps: converter smelting, LF refining, VD vacuum degassing, die casting, heating, rolling, Acc controlled cooling and tempering. Through reasonable chemical component design and production process control, the developed steel plate has excellent performance indexes.
Description
Technical Field
The invention belongs to the technical field of thick plate production, and particularly relates to a production method of an extra-thick ultrahigh-strength SX690DZ35 steel plate.
Background
The ultra-thick and ultra-high strength SX690DZ35 steel plate is widely applied to industries of heavy machinery, hydropower construction and the like, and has the advantages of high required strength, good plasticity and toughness and easy welding.
The traditional Q690D high-strength steel has poor welding performance, unstable low-temperature impact and poor Z-direction performance, so that the application of the industry is restricted.
How to improve the welding performance, the low-temperature impact performance and the Z-direction performance on the premise of not influencing the strength, the plasticity and the toughness of the steel plate becomes a key technical problem to be solved urgently in the current metallurgical industry.
Disclosure of Invention
Aiming at the problems, the invention provides a production method of an extra-thick and ultrahigh-strength SX690DZ35 steel plate.
According to the technical scheme adopted when the extra-thick and ultrahigh-strength SX690DZ35 steel plate is produced, the thickness of the extra-thick and ultrahigh-strength SX690DZ35 steel plate is 100-350 mm, and the extra-thick and ultrahigh-strength SX DZ35 steel plate comprises the following chemical components in percentage by mass (unit, wt%): 0.11 to 0.13 percent of C, 0.01 to 0.15 percent of Si, 0.95 to 1.20 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.005 percent of S, 0.03 to 0.05 percent of Nb, 0.02 to 0.04 percent of V, 0.50 to 0.60 percent of Mo, more than 0.45 and less than or equal to 0.55 percent of Cr, 2.7 to 3.4 percent of Ni, 0.2 to 0.3 percent of Cu, 0.020 to 0.050 percent of Als, less than 0.03 percent of Zr, less than 0.06 percent of Ce, and the balance of Fe and residual elements; the carbon equivalent Ceq is less than or equal to 0.7, and the calculation formula is that Ceq is equal to C + Mn/6+ Si/24+ Ni/40+ Cr/5+ Mo/4+ V/14.
In the chemical composition setting, in order to ensure the strength, the ductility and the welding performance of the steel plate, the steel plate is designed to have low C and low Mn, and simultaneously, a proper amount of alloy elements such as Nb, V, Mo, Cr, Zr, Ni, Ce and the like are added. The content of C is increased, so that the toughness and brittleness transition temperature is obviously improved, meanwhile, the welding performance of the steel plate is seriously influenced by C, and in order to ensure good ductility and toughness and welding performance and ensure the hardenability of the steel plate, the content of C is controlled to be 0.11-0.13%; mn has an obvious effect on improving the strength and the hardenability of the steel plate, but the central segregation of the steel plate is aggravated due to the excessively high content of Mn, and meanwhile, the carbon equivalent and the welding crack sensitivity of the steel plate are improved, so that the comprehensive performance of the steel plate is influenced, and therefore, the content of Mn is controlled to be 0.95-1.20%; the Nb can effectively increase the recrystallization temperature of the steel plate in the controlled rolling process, prevent the crystal grains from growing, refine the crystal grains and improve the strength and toughness of the steel plate, so that the Nb content is controlled to be 0.03-0.05; chromium carbide serving as the finest carbide can be uniformly distributed in the steel, Mo can refine crystal grains of the steel, and the steel keeps enough strength and creep resistance at high temperature, and the chromium carbide and the Mo have positive effects on improving the strength and the hardenability of the steel plate, so that the content of Cr is controlled to be 0.45-0.55, and the content of Mo is controlled to be 0.5-0.6; zr and Ce have excellent deoxidation, denitrogenation and desulfurization effects, and can improve the corrosion resistance and refine crystal grains, so that Zr is controlled to be less than 0.03, Ce is controlled to be less than 0.06, Ni can improve the low-temperature toughness of the steel plate and simultaneously improve the hardenability and strength of the steel plate, and Cu can improve the corrosion resistance of the steel plate and reduce the limitation of the steel plate on the use environment.
In order to obtain the product, the production method adopted by the invention comprises the following steps: converter smelting, LF refining, VD vacuum degassing, die casting and casting, heating, rolling, stacking cooling, quenching and tempering heat treatment;
smelting in a converter: the tapping temperature of the converter is 1600-1650 ℃, the tapping P is less than or equal to 0.010 percent, the tapping C is less than or equal to 0.05 percent, and argon is blown in the whole tapping process;
secondly, LF refining: the initial refining temperature of LF is more than or equal to 1530 ℃, the white slag retention time is 10-30 min, and the final slag after refining is foamed white slag with good fluidity and proper viscosity; the LF leaving temperature is more than or equal to 1580 ℃;
③ VD vacuum degassing: vacuumizing for less than or equal to 10min, controlling the pressure maintaining time at less than or equal to 67Pa according to 15-25 min, and soft argon blowing time after vacuum breaking for less than or equal to 10 min;
molding: before die casting and pouring, the soft blowing and calming time is more than or equal to 2min, and the pouring temperature is controlled according to 1545-1570 ℃; the steel ingot cleaning and inspection adopts warm cleaning, the cleaning temperature is controlled to be above 80 ℃, the steel ingot is charged with the warm after the cleaning and inspection, and the charging temperature is controlled to be above 50 ℃;
heating: in the heating process, the preheating temperature is less than or equal to 1000 ℃, the heating speed is less than or equal to 50 ℃/h, the heating temperature is 1230-1300 ℃, the temperature of the heat preservation section is 1240-1280 ℃, and the overall heating time is 1.5-2.5 min/mm;
sixthly, rolling: the rolling process is carried out in two stages, wherein the rolling process is carried out in one stage by adopting high-temperature, low-speed and high-reduction rolling, the single-pass reduction is more than or equal to 25mm, so that the rolling force reaches the core part of a steel ingot, the deformation of the core part of the steel ingot is promoted, the defect pressing of looseness and the like is ensured, when the blank temperature is lower than 1000 ℃, the rolling process in the second stage is started, the single-pass reduction is more than or equal to 20mm, the rolling force reaches the 1/4 thickness position of the steel ingot, the deformation of the 1/4 thickness position of the steel ingot is promoted, and the aim of recrystallization of the core part and the 1/4 position is finally fulfilled, high-pressure water cooling is adopted in the rolling process, the surface temperature is reduced while the iron scale is removed, the surface hardness is improved, the penetration of the rolling reduction force is improved, the excessive growth of grains in the recrystallization process is avoided, more nucleation points are provided for refining austenite grains, and the final rolling temperature is 850-950 ℃; rapidly cooling after rolling to avoid crystal grain growth, controlling a banded structure, wherein the cooling speed is more than or equal to 1 ℃/S, the temperature of red return is less than or equal to 800 ℃, and then entering a slow pit for slow cooling;
and (c) cooling in a piling way: the temperature of the steel plate entering the slow cooling pit is more than or equal to 300 ℃, the upper surface and the lower surface of the steel plate are strictly forbidden to be exposed in the air, and the slow cooling time is more than 48 hours;
adjusting quality: quenching and tempering heat treatment are carried out on the steel plate, wherein the quenching temperature is 860 ℃ and 920 ℃, the heat preservation time is 2-4 min/mm, the steel plate is quickly cooled in water after heat preservation, the water inlet temperature is more than or equal to 700 ℃, and the final cooling temperature is less than or equal to 80 ℃; the tempering heat preservation temperature is 500-700 ℃, and the heat preservation time is 3.5-6 min/mm.
The beneficial effects of the above component design and process design are that by adopting the technical scheme, the welding performance of the steel plate can be effectively improved, the requirements of controlled cooling and heat treatment of the steel plate are reduced, and finally the mechanical property of the steel plate is ensured through tempering.
Detailed Description
The invention discloses a production method of an extra-thick and ultrahigh-strength SX690DZ35 steel plate, wherein the thickness of the steel plate is 100-350 mm, and the steel plate comprises the following chemical components in percentage by mass (unit, wt%): 0.11 to 0.13 percent of C, 0.01 to 0.15 percent of Si, 0.95 to 1.20 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.005 percent of S, 0.03 to 0.05 percent of Nb, 0.02 to 0.04 percent of V, 0.50 to 0.60 percent of Mo, more than 0.45 and less than or equal to 0.55 percent of Cr, 2.7 to 3.4 percent of Ni, 0.2 to 0.3 percent of Cu, 0.020 to 0.050 percent of Als, less than 0.03 percent of Zr, less than 0.06 percent of Ce, and the balance of Fe and residual elements; the carbon equivalent Ceq is less than or equal to 0.7, the calculation formula is Ceq ═ C + Mn/6+ Si/24+ Ni/40+ Cr/5+ Mo/4+ V/14, and the method is completed through the following steps:
smelting in a converter: the tapping temperature of the converter is 1600-1650 ℃, the tapping P is less than or equal to 0.010 percent, the tapping C is less than or equal to 0.05 percent, and argon is blown in the whole tapping process;
secondly, LF refining: the initial refining temperature of LF is more than or equal to 1530 ℃, the white slag retention time is 10-30 min, and the final slag after refining is foamed white slag with good fluidity and proper viscosity; the LF leaving temperature is more than or equal to 1580 ℃;
③ VD vacuum degassing: vacuumizing for less than or equal to 10min, controlling the pressure maintaining time at less than or equal to 67Pa according to 15-25 min, and soft argon blowing time after vacuum breaking for less than or equal to 10 min;
molding: before die casting and pouring, the soft blowing and calming time is more than or equal to 2min, and the pouring temperature is controlled according to 1545-1570 ℃; the steel ingot cleaning and inspection adopts warm cleaning, the cleaning temperature is controlled to be above 80 ℃, the steel ingot is charged with the warm after the cleaning and inspection, and the charging temperature is controlled to be above 50 ℃;
heating: in the heating process, the preheating temperature is less than or equal to 1000 ℃, the heating speed is less than or equal to 50 ℃/h, the heating temperature is 1230-1300 ℃, the temperature of the heat preservation section is 1240-1280 ℃, and the overall heating time is 1.5-2.5 min/mm;
sixthly, rolling: the rolling process is carried out in two stages, wherein the rolling process is carried out in one stage by adopting high-temperature, low-speed and high-reduction rolling, the single-pass reduction is more than or equal to 25mm, so that the rolling force reaches the core part of a steel ingot, the deformation of the core part of the steel ingot is promoted, the defect pressing of looseness and the like is ensured, when the blank temperature is lower than 1000 ℃, the rolling process in the second stage is started, the single-pass reduction is more than or equal to 20mm, the rolling force reaches the 1/4 thickness position of the steel ingot, the deformation of the 1/4 thickness position of the steel ingot is promoted, and the aim of recrystallization of the core part and the 1/4 position is finally fulfilled, high-pressure water cooling is adopted in the rolling process, the surface temperature is reduced while the iron scale is removed, the surface hardness is improved, the penetration of the rolling reduction force is improved, the excessive growth of grains in the recrystallization process is avoided, more nucleation points are provided for refining austenite grains, and the final rolling temperature is 850-950 ℃; rapidly cooling after rolling to avoid crystal grain growth, controlling a banded structure, wherein the cooling speed is more than or equal to 1 ℃/S, the temperature of red return is less than or equal to 800 ℃, and then entering a slow pit for slow cooling;
and (c) cooling in a piling way: the temperature of the steel plate entering the slow cooling pit is more than or equal to 300 ℃, the upper surface and the lower surface of the steel plate are strictly forbidden to be exposed in the air, and the slow cooling time is more than 48 hours;
and eighthly, quenching: the steel plate is subjected to heat preservation at 860-doped 920 ℃, the heat preservation time is 2-4 min/mm, the steel plate is subjected to heat preservation and then is rapidly cooled in water, the water inlet temperature is more than or equal to 700 ℃, and the final cooling temperature is less than or equal to 80 ℃;
ninthly, tempering heat treatment: the tempering heat preservation temperature is 500-700 ℃, and the heat preservation time is 3.5-6 min/mm.
Examples
The 100 mm-350 mm extra-thick and ultra-high strength SX690DZ35 steel plate with the chemical components shown in the following table 1 is obtained by the processes of converter smelting, LF refining, VD vacuum degassing, die casting and casting, steel ingot heating, rolling, controlled cooling, dump cooling, tempering and the like, wherein the process parameters and the mechanical properties are shown in the following tables 1 and 2.
Table 1 shows chemical compositions (Wt,%) of ultra-thick and ultra-high strength SX690DZ35 steel sheets of 100mm to 350mm
Table 2 shows mechanical properties of 100 mm-350 mm extra-thick and ultrahigh-strength SX690DZ35 steel plate
The method comprises the steps of trial production of 6, 9 and 3 extra-thick extra-high strength SX690DZ35 steel plates with the thickness of 150mm, 250mm and 300mm respectively, through reasonable chemical composition design and production process control, the yield strength 684-823MPa, the tensile strength 775-889MPa, the elongation 16-26, the impact absorption energy 133-294J at-20 ℃, the impact absorption energy 89-236J at-40 ℃ and the Z-direction performance 37-65 of the steel plates meet the design requirements.
Claims (1)
1. A production method of an extra-thick and ultrahigh-strength SX690DZ35 steel plate is characterized in that the thickness of the steel plate is 100-350 mm, and the steel plate comprises the following chemical components in percentage by mass (unit, wt%): 0.11 to 0.13 percent of C, 0.01 to 0.15 percent of Si, 0.95 to 1.20 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.005 percent of S, 0.03 to 0.05 percent of Nb, 0.02 to 0.04 percent of V, 0.50 to 0.60 percent of Mo, more than 0.45 and less than or equal to 0.55 percent of Cr, 2.7 to 3.4 percent of Ni, 0.2 to 0.3 percent of Cu, 0.020 to 0.050 percent of Als, less than 0.03 percent of Zr, less than 0.06 percent of Ce, and the balance of Fe and residual elements; the carbon equivalent Ceq is less than or equal to 0.7, and the calculation formula is
Ceq＝C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14；
The production method of the steel plate comprises the following production procedures: LF refining, VD vacuum degassing, die casting, heating, rolling, heap cooling and quenching and tempering heat treatment;
LF refining: the initial refining temperature of LF is more than or equal to 1530 ℃, the white slag retention time is 10-30 min, the final slag after refining is foamed white slag with good fluidity and proper viscosity, and the LF leaving temperature is more than or equal to 1580 ℃;
② VD vacuum degassing: vacuumizing for less than or equal to 10min, controlling the pressure maintaining time at less than or equal to 67Pa according to 15-25 min, and soft argon blowing time after vacuum breaking for less than or equal to 10 min;
third, die casting: before die casting and pouring, the soft blowing and calming time is more than or equal to 2min, and the pouring temperature is controlled according to 1545-1570 ℃; the steel ingot cleaning and inspection adopts warm cleaning, the cleaning temperature is controlled to be above 80 ℃, the steel ingot is charged with the warm after the cleaning and inspection, and the charging temperature is controlled to be above 50 ℃;
heating: in the heating process, the preheating temperature is less than or equal to 1000 ℃, the heating speed is less than or equal to 50 ℃/h, the heating temperature is 1230-1300 ℃, the temperature of the heat preservation section is 1240-1280 ℃, and the overall heating time is 1.5-2.5 min/mm;
rolling: the rolling process is carried out in two stages, wherein the initial rolling temperature of one stage is 1100-1180 ℃, the rolling is carried out at high temperature, low speed and high reduction, the single-pass reduction is more than or equal to 25mm, the rolling force reaches the core part of the steel ingot, the deformation of the core part of the steel ingot is promoted, the pressing of defects such as looseness is ensured, when the blank temperature is lower than 1000 ℃, the second-stage rolling is started, the single-pass reduction is more than or equal to 20mm, the rolling force reaches the thickness position of 1/4 of the steel ingot, the deformation of the 1/4 thickness position of the steel ingot is promoted, and the recrystallization of the core part and the 1/4 position is finally realized, high-pressure water cooling is adopted in the rolling process, the surface temperature is reduced while the iron scale is removed, the surface hardness is improved, the permeation of the force under the rolling pressure is improved, the excessive growth of grains in the recrystallization process is avoided, more nucleation points are provided for refining austenite grains, and the final rolling temperature is 850-950 ℃; after rolling, rapidly cooling at a cooling speed of more than or equal to 1 ℃/S and a re-reddening temperature of less than or equal to 800 ℃, and then entering a slow pit for slow cooling;
sixthly, cooling in a pile: the temperature of the steel plate entering the slow cooling pit is more than or equal to 300 ℃, the upper surface and the lower surface of the steel plate are strictly forbidden to be exposed in the air, and the slow cooling time is more than 48 hours;
and (c) hardening and tempering: quenching and tempering heat treatment are carried out on the steel plate, wherein the quenching temperature is 860 ℃ and 920 ℃, the heat preservation time is 2-4 min/mm, the steel plate is quickly cooled in water after heat preservation, the water inlet temperature is more than or equal to 700 ℃, and the final cooling temperature is less than or equal to 80 ℃; the tempering heat preservation temperature is 500-700 ℃, and the heat preservation time is 3.5-6 min/mm.
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN116200682A (en) * | 2022-12-14 | 2023-06-02 | 鞍钢股份有限公司 | High-strength high-toughness low Wen Haigong steel plate and manufacturing method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003266123A (en) * | 2002-03-12 | 2003-09-24 | Jfe Steel Kk | Method of forming high tensile strength steel sheet |
| CN103725986A (en) * | 2013-12-19 | 2014-04-16 | 江阴兴澄特种钢铁有限公司 | High-ductility Class F extra thick rack steel plate used at low temperature and manufacturing method of steel plate |
| CN104561772A (en) * | 2014-12-26 | 2015-04-29 | 南阳汉冶特钢有限公司 | Ultralow-temperature steel plate with thickness of 130-150 mm and production method for ultralow-temperature steel plate |
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- 2021-09-29 CN CN202111153999.XA patent/CN113846270A/en not_active Withdrawn
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003266123A (en) * | 2002-03-12 | 2003-09-24 | Jfe Steel Kk | Method of forming high tensile strength steel sheet |
| CN103725986A (en) * | 2013-12-19 | 2014-04-16 | 江阴兴澄特种钢铁有限公司 | High-ductility Class F extra thick rack steel plate used at low temperature and manufacturing method of steel plate |
| CN104561772A (en) * | 2014-12-26 | 2015-04-29 | 南阳汉冶特钢有限公司 | Ultralow-temperature steel plate with thickness of 130-150 mm and production method for ultralow-temperature steel plate |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116200682A (en) * | 2022-12-14 | 2023-06-02 | 鞍钢股份有限公司 | High-strength high-toughness low Wen Haigong steel plate and manufacturing method thereof |
| CN116200682B (en) * | 2022-12-14 | 2024-04-16 | 鞍钢股份有限公司 | High-strength high-toughness low Wen Haigong steel plate and manufacturing method thereof |
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Application publication date: 20211228 |