CA3157674A1 - An extra thick vessel steel plate with good low-temperature impact toughness at the center and a production method - Google Patents
An extra thick vessel steel plate with good low-temperature impact toughness at the center and a production methodInfo
- Publication number
- CA3157674A1 CA3157674A1 CA3157674A CA3157674A CA3157674A1 CA 3157674 A1 CA3157674 A1 CA 3157674A1 CA 3157674 A CA3157674 A CA 3157674A CA 3157674 A CA3157674 A CA 3157674A CA 3157674 A1 CA3157674 A1 CA 3157674A1
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- steel plate
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- cooling
- rolling
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 84
- 239000010959 steel Substances 0.000 title claims abstract description 84
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 14
- 238000005096 rolling process Methods 0.000 claims abstract description 31
- 238000000034 method Methods 0.000 claims abstract description 21
- 238000001816 cooling Methods 0.000 claims abstract description 18
- 230000008569 process Effects 0.000 claims abstract description 18
- 238000009749 continuous casting Methods 0.000 claims abstract description 16
- 238000010791 quenching Methods 0.000 claims abstract description 16
- 230000000171 quenching effect Effects 0.000 claims abstract description 16
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 10
- 238000005496 tempering Methods 0.000 claims abstract description 10
- 229910052739 hydrogen Inorganic materials 0.000 claims abstract description 6
- 238000009847 ladle furnace Methods 0.000 claims abstract description 6
- 239000000126 substance Substances 0.000 claims abstract description 6
- 238000003723 Smelting Methods 0.000 claims abstract description 5
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 238000007670 refining Methods 0.000 claims abstract description 5
- 238000010583 slow cooling Methods 0.000 claims abstract description 5
- FBPFZTCFMRRESA-JGWLITMVSA-N D-glucitol Chemical compound OC[C@H](O)[C@@H](O)[C@H](O)[C@H](O)CO FBPFZTCFMRRESA-JGWLITMVSA-N 0.000 claims abstract description 4
- 238000005266 casting Methods 0.000 claims abstract description 4
- 238000010438 heat treatment Methods 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 4
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 4
- 229910052802 copper Inorganic materials 0.000 claims abstract description 3
- 229910052742 iron Inorganic materials 0.000 claims abstract description 3
- 238000009849 vacuum degassing Methods 0.000 claims abstract 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 11
- 229910052758 niobium Inorganic materials 0.000 claims description 10
- 230000009467 reduction Effects 0.000 claims description 8
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 claims description 6
- 239000002184 metal Substances 0.000 claims description 3
- 229910052751 metal Inorganic materials 0.000 claims description 3
- 238000007664 blowing Methods 0.000 claims description 2
- 238000005516 engineering process Methods 0.000 claims description 2
- 230000001681 protective effect Effects 0.000 claims description 2
- 241000237519 Bivalvia Species 0.000 claims 1
- 235000020639 clam Nutrition 0.000 claims 1
- 238000006477 desulfuration reaction Methods 0.000 claims 1
- 230000023556 desulfurization Effects 0.000 claims 1
- 239000011261 inert gas Substances 0.000 claims 1
- 238000002791 soaking Methods 0.000 claims 1
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 229910052717 sulfur Inorganic materials 0.000 abstract description 3
- 239000000203 mixture Substances 0.000 abstract 1
- 238000002203 pretreatment Methods 0.000 abstract 1
- 229910052720 vanadium Inorganic materials 0.000 description 9
- 238000003466 welding Methods 0.000 description 6
- 229910000859 α-Fe Inorganic materials 0.000 description 5
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 238000010586 diagram Methods 0.000 description 3
- 239000001257 hydrogen Substances 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 238000001514 detection method Methods 0.000 description 2
- 125000004435 hydrogen atom Chemical group [H]* 0.000 description 2
- 238000007689 inspection Methods 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 230000035945 sensitivity Effects 0.000 description 2
- 238000003860 storage Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 238000009489 vacuum treatment Methods 0.000 description 2
- 229910000599 Cr alloy Inorganic materials 0.000 description 1
- 229910018651 Mn—Ni Inorganic materials 0.000 description 1
- 229910001257 Nb alloy Inorganic materials 0.000 description 1
- BPQQTUXANYXVAA-UHFFFAOYSA-N Orthosilicate Chemical compound [O-][Si]([O-])([O-])[O-] BPQQTUXANYXVAA-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000005587 bubbling Effects 0.000 description 1
- -1 carbon nitrides Chemical class 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 230000001788 irregular Effects 0.000 description 1
- 239000010410 layer Substances 0.000 description 1
- 239000003345 natural gas Substances 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Classifications
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/072—Treatment with gases
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- 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
-
- 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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Disclosed is an ultra-thick container steel plate with a good low-temperature impact toughness in the core, the ultra-thick container steel plate having a produced thickness of 60-100 mm and a chemical composition of 0.13-0.20% of C, Si: = 0.40%; 1.00-1.60% of Mn, P = 0.015%, S = 0.005%, 0.01-0.05% of Als, Nb + V + Ti = 0.080%, 0.20-0.50% of Ni, Cu = 0.30%, and H = 2 ppm, with the balance being Fe and inevitable impurity elements, which also satisfies CEV = 0.43% and 3 = w(Nb + V + Als)/w(Ti) = 8. The structure near the surface of the steel plate is tempered sorbite, and the structure at 1/4 and 1/2 of the plate thickness of the steel plate is bainite. The transverse impact energy -50°C KV2 at 1/4 of the plate thickness is = 150 J, and the transverse impact energy -50°C KV2 at 1/2 of the plate thickness is = 80 J. The manufacturing process therefor involves: pre-treatment of molten iron ? converter smelting ? ladle furnace refining ? vacuum degassing treatment ? continuous casting ? casting blank cooling with a cover ? casting blank heating ? controlled rolling ? controlled cooling ? stacking for slow cooling ? tempering. An online quenching process is also used to ensure that the steel plate has a good strength and toughness; furthermore, online quenching can significantly shorten the delivery cycle thereof.
Description
Specification An extra thick vessel steel plate with good low-temperature impact toughness at the center and a production method Technical field The invention belongs to the technical field of iron-based alloys.
Back2round art In recent years, various petrochemical and natural gas projects at home and abroad have been implemented one after another, and the demand for large reaction vessels or storage tanks has increased significantly. Quenching and tempering steel plates are more and more popular because of their good strength and toughness matching, especially as the equipment continues to develop towards large-scale and high parameter, so as to ensure the safe and stable operation of the equipment at the same time, good low temperature impact toughness and weldability at the center are particularly critical. To sum up, it has broad market prospects to develop vessel steel plates with easy welding and good low-temperature toughness at the center that can be mass and stably produced to meet the production of large-scale energy equipment.
Patent (CN107267857 A) applies for a 07MnNiMoDR steel plate and its on-line quenching production method. Its tensile strength is more than 630mpa, and its low-temperature impact toughness at -50 C is good, but the maximum thickness is only 50mm.
Patent (CN106350644 A) applies for a method of producing steel for storage tank by on-line quenching process, which realizes on-line quenching by using UFC + ACC
two-stage cooling mode. The produced steel plate has stable performance and good strength toughness matching, but does not mention the low-temperature impact toughness of the center of the steel plate.
Patent (CN106319376 B) applies for a new type of high-strength steel plate with low welding crack sensitivity. The 15-50mm thick steel plate produced by on-line quenching +
off-line tempering process has the characteristics of high strength and good weldability, but the impact test temperature is only -20 C. At the same time, there are many Nb and Cr Alloys added and the cost is high.
To sum up, most of the existing quenched and tempered high strength and toughness steel plates are produced by the traditional off-line quenching process. Even if the on-line quenching process is used, the thickness of the produced steel plates is less than 60mm, and the low-temperature impact toughness of the center is unstable, which cannot meet the needs of the development of chemical energy equipment to large-scale and high parameter.
Date Recue/Date Received 2022-04-11 Detailed description of the invention The invention provides an on-line quenching method for producing a 60-100mm thick extra thick steel plate with good low-temperature impact toughness at the center. The steel plate has the characteristics of stable structure, high strength, good low-temperature toughness at the center, easy welding, etc. The production method has the advantages of short process, relatively low cost and strong operability.
The technical scheme adopted by the invention to solve the above problems is:
an extra thick vessel steel plate with good low-temperature impact toughness at the center, and the production thickness of the steel plate reaches 60-100mm. According to the mass percentage, the chemical constitutions of the steel plate is as follows: C: 0.13-0.20%, Si: < 0.40%, Mn:
1.00-1.60%, P < 0.015%, S < 0.005%, Als: 0.01-0.05%, Nb + V + Ti < 0.080%, Ni:
0.20-0.50%, Cu < 0.30%, H < 2ppm, and the balance is Fe and unavoidable impurity elements.
At the same time, it meets the following requirements:
CEV=C+Mn/6+(Mo+V+Cr)/5+(Ni+Cu)/15<0.43%, 3<w (Nb+V+Als)/w (Ti)<8.
The microstructure near the surface of the steel plate is tempered sorbite, and the microstructure at 1/4 and 1/2 of the thickness of the steel plate is bainite.
Yield strength of steel plate? 400MPa, tensile strength Rm > 550MPa, elongation A? 22%, transverse impact energy at 1/4 of plate thickness -50 C KV2 > 150J; Transverse impact energy at 1/2 of plate thickness -50 C KV2 > 80J.
The limiting reasons of C, Si, Mn, P, s, Nb, Ni, V, Ti, H and other elements in the invention are described as follows:
C is the most economical element to improve the strength of steel plate, but too high content will reduce the plasticity and impact toughness, increase the sensitivity of welding crack, and it is easy to produce cracks in the welding process. In order to ensure that the base metal has good strength &toughness matching and weldability, the content of steel C in the invention is 0.13-0.20%.
Si can improve the strength of steel plate and welded joint. When the content of Si is greater than 0.45%, the toughness of steel plate and welded joint will be significantly reduced.
At the same time, the hard silicate inclusions formed are easy to cause surface defects of steel plate, and the content of Si is 0.10-0.40%.
Mn is a common element to improve the strength of steel plate. An appropriate amount of Mn can replace c to improve the strength and toughness of steel plate and welded joint.
With the increase of Mn content, the stability of austenite in steel can be improved, the critical cooling rate can be reduced, ferrite can be strengthened, and the hardenability can be significantly improved. At the same time, the speed of structural decomposition and transformation in the tempering process after quenching can be slowed down, and the stability of tempering structure can be improved. However, too high content will coarsen the grain of steel at high temperature and reduce the toughness and weldability of steel plate and welded joint, Therefore, the content of Mn in the steel of the invention is 1.00%-1.60%.
P and S as an impurity element is unavoidable in steel, but it is harmful to the machinability of steel plate, especially the low-temperature impact toughness.
The lower its content, the better. Therefore, the content of P in the steel of the invention is < 0.015%, and
Back2round art In recent years, various petrochemical and natural gas projects at home and abroad have been implemented one after another, and the demand for large reaction vessels or storage tanks has increased significantly. Quenching and tempering steel plates are more and more popular because of their good strength and toughness matching, especially as the equipment continues to develop towards large-scale and high parameter, so as to ensure the safe and stable operation of the equipment at the same time, good low temperature impact toughness and weldability at the center are particularly critical. To sum up, it has broad market prospects to develop vessel steel plates with easy welding and good low-temperature toughness at the center that can be mass and stably produced to meet the production of large-scale energy equipment.
Patent (CN107267857 A) applies for a 07MnNiMoDR steel plate and its on-line quenching production method. Its tensile strength is more than 630mpa, and its low-temperature impact toughness at -50 C is good, but the maximum thickness is only 50mm.
Patent (CN106350644 A) applies for a method of producing steel for storage tank by on-line quenching process, which realizes on-line quenching by using UFC + ACC
two-stage cooling mode. The produced steel plate has stable performance and good strength toughness matching, but does not mention the low-temperature impact toughness of the center of the steel plate.
Patent (CN106319376 B) applies for a new type of high-strength steel plate with low welding crack sensitivity. The 15-50mm thick steel plate produced by on-line quenching +
off-line tempering process has the characteristics of high strength and good weldability, but the impact test temperature is only -20 C. At the same time, there are many Nb and Cr Alloys added and the cost is high.
To sum up, most of the existing quenched and tempered high strength and toughness steel plates are produced by the traditional off-line quenching process. Even if the on-line quenching process is used, the thickness of the produced steel plates is less than 60mm, and the low-temperature impact toughness of the center is unstable, which cannot meet the needs of the development of chemical energy equipment to large-scale and high parameter.
Date Recue/Date Received 2022-04-11 Detailed description of the invention The invention provides an on-line quenching method for producing a 60-100mm thick extra thick steel plate with good low-temperature impact toughness at the center. The steel plate has the characteristics of stable structure, high strength, good low-temperature toughness at the center, easy welding, etc. The production method has the advantages of short process, relatively low cost and strong operability.
The technical scheme adopted by the invention to solve the above problems is:
an extra thick vessel steel plate with good low-temperature impact toughness at the center, and the production thickness of the steel plate reaches 60-100mm. According to the mass percentage, the chemical constitutions of the steel plate is as follows: C: 0.13-0.20%, Si: < 0.40%, Mn:
1.00-1.60%, P < 0.015%, S < 0.005%, Als: 0.01-0.05%, Nb + V + Ti < 0.080%, Ni:
0.20-0.50%, Cu < 0.30%, H < 2ppm, and the balance is Fe and unavoidable impurity elements.
At the same time, it meets the following requirements:
CEV=C+Mn/6+(Mo+V+Cr)/5+(Ni+Cu)/15<0.43%, 3<w (Nb+V+Als)/w (Ti)<8.
The microstructure near the surface of the steel plate is tempered sorbite, and the microstructure at 1/4 and 1/2 of the thickness of the steel plate is bainite.
Yield strength of steel plate? 400MPa, tensile strength Rm > 550MPa, elongation A? 22%, transverse impact energy at 1/4 of plate thickness -50 C KV2 > 150J; Transverse impact energy at 1/2 of plate thickness -50 C KV2 > 80J.
The limiting reasons of C, Si, Mn, P, s, Nb, Ni, V, Ti, H and other elements in the invention are described as follows:
C is the most economical element to improve the strength of steel plate, but too high content will reduce the plasticity and impact toughness, increase the sensitivity of welding crack, and it is easy to produce cracks in the welding process. In order to ensure that the base metal has good strength &toughness matching and weldability, the content of steel C in the invention is 0.13-0.20%.
Si can improve the strength of steel plate and welded joint. When the content of Si is greater than 0.45%, the toughness of steel plate and welded joint will be significantly reduced.
At the same time, the hard silicate inclusions formed are easy to cause surface defects of steel plate, and the content of Si is 0.10-0.40%.
Mn is a common element to improve the strength of steel plate. An appropriate amount of Mn can replace c to improve the strength and toughness of steel plate and welded joint.
With the increase of Mn content, the stability of austenite in steel can be improved, the critical cooling rate can be reduced, ferrite can be strengthened, and the hardenability can be significantly improved. At the same time, the speed of structural decomposition and transformation in the tempering process after quenching can be slowed down, and the stability of tempering structure can be improved. However, too high content will coarsen the grain of steel at high temperature and reduce the toughness and weldability of steel plate and welded joint, Therefore, the content of Mn in the steel of the invention is 1.00%-1.60%.
P and S as an impurity element is unavoidable in steel, but it is harmful to the machinability of steel plate, especially the low-temperature impact toughness.
The lower its content, the better. Therefore, the content of P in the steel of the invention is < 0.015%, and
- 2 -Date Recue/Date Received 2022-04-11 the content of S is < 0.005%.
Ni can significantly reduce the ductile & brittle transition temperature of steel, improve the low-temperature impact toughness, and reduce the tendency of billet surface cracks caused by the addition of Cu. However, Ni is expensive, and excessive addition will significantly increase the production cost of steel. Therefore, the content of Ni in the steel of the invention is 0.20-0.50%.
Nb and V can introduce a large number of high-density dislocation and distortion zones during rolling in the non-recrystallization zone, promote the formation of more transformation centers, and refine the austenite structure. At the same time, carbonitride is formed and precipitated in ferrite at austenite grain boundary, which can inhibit austenite recrystallization and prevent grain growth during rolling, so as to refine ferrite grains and improve the strength and toughness of steel. Ti can form high-temperature oxides and act as nucleation particles of acicular ferrite in welded joints, promote the formation of acicular ferrite and significantly improve the low-temperature impact toughness of welding heat affected zone. If too much is added, it will not only increase the cost, but also increase the amount and size of precipitates, which will reduce the toughness of steel, especially the center toughness.
Therefore, the steel Nb+V+Ti of the invention is < 0.08%, and the addition amount of Nb and V is not zero.
NB, V and Ti can be combined with C and N to produce carbonitride precipitation, so as to refine the grain. Due to the center segregation in the hardening process of the billet, TiN
precipitates mostly gather near the center of the billet, and the irregular shape of TiN
inclusions is unfavorable to the low-temperature impact toughness of the center of the steel plate. On the other hand, at the same temperature, the binding ability between Ti and N is stronger than Nb and V. Therefore, in the present specification, 3 < w (Nb + V
+ Als)/w (TI) is controlled to reduce the formation of TiN. Meanwhile, considering the expensive price of Nb and V, w (Nb+V+Als)/w (TI) < 8.
H hydrogen atoms are easy to diffuse in the billet. Under the action of hydrogen pressure, adjacent hydrogen bubbling cracks on different layers are connected with each other, thus forming a stepped center crack. Therefore, in order to ensure the low-temperature toughness of the center of the steel plate, the H of the invention steel is < 2ppm, and the continuous casting billet is subjected to hydrogen expansion treatment.
Another object of the invention is to provide a production method of the above vessel steel plate. The method comprises the following processes: hot metal pretreatment ¨>
converter smelting ¨> ladle furnace refining ¨> vacuum treatment ¨> continuous casting ¨>
billet cover cooling ¨> billet heating ¨> controlled rolling ¨> controlled cooling ¨> stack slow cooling ¨> tempering ¨> flaw detection ¨> performance inspection. The specific steps are as follows:
After the hot metal is pretreated by KR method, desulfurized and smelted in converter, it is refined in ladle furnace and vacuum treatment. After soft blowing for more than 15 minutes, it is smelted into high-purity molten steel. The whole process protective casting and soft reduction technology are used to cast the continuous casting billet on the continuous casting machine, and the billet is covered for slow cooling.
The continuous casting billet shall be heated to 1150-1200 C, the total furnace time shall not be less than 300min, and the holding time shall not be less than 90min.
After coming out of the furnace, the scale shall be removed by high-pressure water to remove the iron oxide
Ni can significantly reduce the ductile & brittle transition temperature of steel, improve the low-temperature impact toughness, and reduce the tendency of billet surface cracks caused by the addition of Cu. However, Ni is expensive, and excessive addition will significantly increase the production cost of steel. Therefore, the content of Ni in the steel of the invention is 0.20-0.50%.
Nb and V can introduce a large number of high-density dislocation and distortion zones during rolling in the non-recrystallization zone, promote the formation of more transformation centers, and refine the austenite structure. At the same time, carbonitride is formed and precipitated in ferrite at austenite grain boundary, which can inhibit austenite recrystallization and prevent grain growth during rolling, so as to refine ferrite grains and improve the strength and toughness of steel. Ti can form high-temperature oxides and act as nucleation particles of acicular ferrite in welded joints, promote the formation of acicular ferrite and significantly improve the low-temperature impact toughness of welding heat affected zone. If too much is added, it will not only increase the cost, but also increase the amount and size of precipitates, which will reduce the toughness of steel, especially the center toughness.
Therefore, the steel Nb+V+Ti of the invention is < 0.08%, and the addition amount of Nb and V is not zero.
NB, V and Ti can be combined with C and N to produce carbonitride precipitation, so as to refine the grain. Due to the center segregation in the hardening process of the billet, TiN
precipitates mostly gather near the center of the billet, and the irregular shape of TiN
inclusions is unfavorable to the low-temperature impact toughness of the center of the steel plate. On the other hand, at the same temperature, the binding ability between Ti and N is stronger than Nb and V. Therefore, in the present specification, 3 < w (Nb + V
+ Als)/w (TI) is controlled to reduce the formation of TiN. Meanwhile, considering the expensive price of Nb and V, w (Nb+V+Als)/w (TI) < 8.
H hydrogen atoms are easy to diffuse in the billet. Under the action of hydrogen pressure, adjacent hydrogen bubbling cracks on different layers are connected with each other, thus forming a stepped center crack. Therefore, in order to ensure the low-temperature toughness of the center of the steel plate, the H of the invention steel is < 2ppm, and the continuous casting billet is subjected to hydrogen expansion treatment.
Another object of the invention is to provide a production method of the above vessel steel plate. The method comprises the following processes: hot metal pretreatment ¨>
converter smelting ¨> ladle furnace refining ¨> vacuum treatment ¨> continuous casting ¨>
billet cover cooling ¨> billet heating ¨> controlled rolling ¨> controlled cooling ¨> stack slow cooling ¨> tempering ¨> flaw detection ¨> performance inspection. The specific steps are as follows:
After the hot metal is pretreated by KR method, desulfurized and smelted in converter, it is refined in ladle furnace and vacuum treatment. After soft blowing for more than 15 minutes, it is smelted into high-purity molten steel. The whole process protective casting and soft reduction technology are used to cast the continuous casting billet on the continuous casting machine, and the billet is covered for slow cooling.
The continuous casting billet shall be heated to 1150-1200 C, the total furnace time shall not be less than 300min, and the holding time shall not be less than 90min.
After coming out of the furnace, the scale shall be removed by high-pressure water to remove the iron oxide
- 3 -Date Recue/Date Received 2022-04-11 scale on the billet surface.
The austenitized continuous casting billet is rolled in two stages (controlled rolling, start rolling and finish rolling temperature shall be limited). The start rolling adopts small passes and large reduction. The start rolling temperature shall be controlled at 1020-1100 C, and the final rolling temperature shall be controlled at 1000-1060 C, so as to ensure the reduction rate of the last two passes? 15%; During the finish rolling, start rolling temperature shall be controlled at 880-920 C; after rolling, DQ+ACC two-stage cooling shall be adopted to achieve the purpose of on-line quenching. The water temperature of the steel plate shall be controlled at 840-880 C, and the cooling rate shall be controlled at 5-15 C/s.
After ACC, the surface temperature of the steel plate shall be 100-200 C, the steel plate shall be slowly cooled after being offline, and then tempered at 600-680 C. The steel plate shall be delivered after passing the flaw detection and performance inspection.
Compared with the existing arts, the invention has the advantages of:
1. In terms of constitution design, the contents of Nb, V, Ti and Als in the steel are controlled to reduce the formation of TiN unfavorable to low-temperature impact at the center.
At the same time, the carbon nitrides of Nb, V and Al play the role of pinning and refining billet grains; 2. Using the thickest continuous casting billet in China, the deformation in the rolling process is greatly increased. Combined with the differential temperature rolling process, the structure in the center of the steel plate is further refined to further lay the foundation for low-temperature impact toughness; 3. Online quenching is adopted to control the water temperature, so as to avoid the abnormal structure caused by too low or too high water temperature.
The C-Mn-Ni system is designed with Nb, V and other microalloying constitutions. After secondary refining and soft reduction of continuous casting billet, the molten steel is purer, ensuring the uniformity of subsequent steel plate properties, especially the low-temperature impact toughness of the center. The on-line quenching process is adopted to ensure that the steel plate has good strength toughness matching, significantly reduce the production cost, shorten the delivery time and it favors strong operability.
Description of the Attached Drawin2s Fig. 1 is a schematic diagram of tempered sorbite in the metallographic structure of the surface layer of a 90mm thick steel plate in the embodiment of the present invention;
Fig. 2 is a schematic diagram of bainite in 1/4 metallographic structure of 90mm thick steel plate in the embodiment of the present invention;
Fig. 3 is a schematic diagram of bainite in 1/2 metallographic structure of 90mm thick steel plate in the embodiment of the present invention.
Detailed description of embodiments The invention is described in further detail below in combination with the embodiments of the attached drawings. The embodiments described below are exemplary and are intended to explain the invention and cannot be understood as limitations on the invention. In addition, comparative examples are listed to highlight embodiments.
The austenitized continuous casting billet is rolled in two stages (controlled rolling, start rolling and finish rolling temperature shall be limited). The start rolling adopts small passes and large reduction. The start rolling temperature shall be controlled at 1020-1100 C, and the final rolling temperature shall be controlled at 1000-1060 C, so as to ensure the reduction rate of the last two passes? 15%; During the finish rolling, start rolling temperature shall be controlled at 880-920 C; after rolling, DQ+ACC two-stage cooling shall be adopted to achieve the purpose of on-line quenching. The water temperature of the steel plate shall be controlled at 840-880 C, and the cooling rate shall be controlled at 5-15 C/s.
After ACC, the surface temperature of the steel plate shall be 100-200 C, the steel plate shall be slowly cooled after being offline, and then tempered at 600-680 C. The steel plate shall be delivered after passing the flaw detection and performance inspection.
Compared with the existing arts, the invention has the advantages of:
1. In terms of constitution design, the contents of Nb, V, Ti and Als in the steel are controlled to reduce the formation of TiN unfavorable to low-temperature impact at the center.
At the same time, the carbon nitrides of Nb, V and Al play the role of pinning and refining billet grains; 2. Using the thickest continuous casting billet in China, the deformation in the rolling process is greatly increased. Combined with the differential temperature rolling process, the structure in the center of the steel plate is further refined to further lay the foundation for low-temperature impact toughness; 3. Online quenching is adopted to control the water temperature, so as to avoid the abnormal structure caused by too low or too high water temperature.
The C-Mn-Ni system is designed with Nb, V and other microalloying constitutions. After secondary refining and soft reduction of continuous casting billet, the molten steel is purer, ensuring the uniformity of subsequent steel plate properties, especially the low-temperature impact toughness of the center. The on-line quenching process is adopted to ensure that the steel plate has good strength toughness matching, significantly reduce the production cost, shorten the delivery time and it favors strong operability.
Description of the Attached Drawin2s Fig. 1 is a schematic diagram of tempered sorbite in the metallographic structure of the surface layer of a 90mm thick steel plate in the embodiment of the present invention;
Fig. 2 is a schematic diagram of bainite in 1/4 metallographic structure of 90mm thick steel plate in the embodiment of the present invention;
Fig. 3 is a schematic diagram of bainite in 1/2 metallographic structure of 90mm thick steel plate in the embodiment of the present invention.
Detailed description of embodiments The invention is described in further detail below in combination with the embodiments of the attached drawings. The embodiments described below are exemplary and are intended to explain the invention and cannot be understood as limitations on the invention. In addition, comparative examples are listed to highlight embodiments.
- 4 -Date Recue/Date Received 2022-04-11 The smelting chemical constitutions of this embodiment and the corresponding proportion is shown in Table 1 (wt%), and the rest is Fe and unavoidable impurity elements.
Table 1 Element C Si Mn P S Nb+V+Als Ti Ni H CEV (V+Nb+Als) /[Ti]
Embodime 0.13 0.20 1.50 0.005 0.001 0.084 0.015 0.35 0.0001 0.42 5.6 nt 1 Embodime 0.14 0.21 1.52 0.006 0.002 0.061 0.014 0.32 0.0001 0.42 4.4 nt 2 Comparati ye 0.16 0.25 1.40 0.012 0.006 0.030 0.018 0.45 0.0003 0.44 1.7 examples The above embodiment and comparative examples are smelted in the converter, deeply desulfurized and refined in the ladle furnace, degassed in the vacuum furnace and soft blown for more than 15 minutes to fully float and remove large particle inclusions, ensure uniform constitution and temperature, and then cast into continuous casting billet through light reduction and whole process protection. Two pieces of continuous casting billets are selected for finished product production.
The continuous casting billet is heated to 1150-1200 C, the total furnace time is >
300min, and the holding time is > 90min. After coming out of the furnace, the scale is removed by high-pressure water to remove the iron oxide scale on the billet surface; Then controlled rolling is carried out. The start rolling temperature is 1020-1100 C, the final rolling temperature is controlled at 1000-1060 C, and the reduction rate of the last two passes is > 15%; The start temperature of finish rolling shall be controlled at 880-920 C; After rolling, DQ+ACC two-stage cooling is adopted to achieve the purpose of on-line quenching.
The water temperature of the steel plate shall be controlled at 840-880 C, and the cooling rate shall be controlled at 5-15 C/s. After ACC, the surface temperature of the steel plate shall be 100-200 C, the steel plate shall be slowly cooled after being offline, and then tempered at 600-680 C.
Table 2 shows process parameters of the main rolling, controlled cooling and tempering of each embodiment and comparative examples.
Table 2 Steel Rough Finish DQ
. Outlet Temperi In plate and final rolling water Cooling Embodime . water ng furnace thickne rolling -start tempera rate nt temperat temperat time ss temperatu temperatur ture ( C/s) ure ( C) ure ( C) (min) (mm) re ( C) e ( C) ( C/s) Embodime nt 1 Embodime nt 2 Comparati ye 65 1026 908 826 10 158 650 180 examples 1
Table 1 Element C Si Mn P S Nb+V+Als Ti Ni H CEV (V+Nb+Als) /[Ti]
Embodime 0.13 0.20 1.50 0.005 0.001 0.084 0.015 0.35 0.0001 0.42 5.6 nt 1 Embodime 0.14 0.21 1.52 0.006 0.002 0.061 0.014 0.32 0.0001 0.42 4.4 nt 2 Comparati ye 0.16 0.25 1.40 0.012 0.006 0.030 0.018 0.45 0.0003 0.44 1.7 examples The above embodiment and comparative examples are smelted in the converter, deeply desulfurized and refined in the ladle furnace, degassed in the vacuum furnace and soft blown for more than 15 minutes to fully float and remove large particle inclusions, ensure uniform constitution and temperature, and then cast into continuous casting billet through light reduction and whole process protection. Two pieces of continuous casting billets are selected for finished product production.
The continuous casting billet is heated to 1150-1200 C, the total furnace time is >
300min, and the holding time is > 90min. After coming out of the furnace, the scale is removed by high-pressure water to remove the iron oxide scale on the billet surface; Then controlled rolling is carried out. The start rolling temperature is 1020-1100 C, the final rolling temperature is controlled at 1000-1060 C, and the reduction rate of the last two passes is > 15%; The start temperature of finish rolling shall be controlled at 880-920 C; After rolling, DQ+ACC two-stage cooling is adopted to achieve the purpose of on-line quenching.
The water temperature of the steel plate shall be controlled at 840-880 C, and the cooling rate shall be controlled at 5-15 C/s. After ACC, the surface temperature of the steel plate shall be 100-200 C, the steel plate shall be slowly cooled after being offline, and then tempered at 600-680 C.
Table 2 shows process parameters of the main rolling, controlled cooling and tempering of each embodiment and comparative examples.
Table 2 Steel Rough Finish DQ
. Outlet Temperi In plate and final rolling water Cooling Embodime . water ng furnace thickne rolling -start tempera rate nt temperat temperat time ss temperatu temperatur ture ( C/s) ure ( C) ure ( C) (min) (mm) re ( C) e ( C) ( C/s) Embodime nt 1 Embodime nt 2 Comparati ye 65 1026 908 826 10 158 650 180 examples 1
- 5 -Date Recue/Date Received 2022-04-11 Comparati ve 88 1034 896 832 9 182 640 270 examples 2 For the steel plate after heat treatment, take transverse samples at 1/4 and 1/2 of the plate thickness, process them into tensile samples and impact samples, and test the mechanical properties. See Table 3 for the test results.
Table 3 Steel Yield Impact at 1/2 of Tensile Elonga Impact at 1/4 of Embodim plate strength plate thickness strength tion plate thickness ent thickness ReL -50 CKV2 (J) Rm (MPa) A (%) -50 CKV2 (J) (mm) (MPa) Embodim 154 116 137 60 460 608 24.0 236 202 231 ent 1 Embodim 100 123 108 90 432 586 25.5 176 200 195 ent 2 Comparat 90 157 36 ive 65 425 578 27.5 167 188 202 examples Comparat 18 100 68 ive 88 411 562 26.0 166 217 169 examples It can be seen from Table 3 that the strength, elongation and impact toughness margin of the test steel plate are large in the embodiment of the invention, especially the impact energy at 1/2 of the plate thickness is more than 100J, while the impact energy at 1/2 of the plate thickness in the comparative example is unstable, and the lowest single value is only 18J.
The invention not only ensures that the steel has good strength and toughness, but also has stable low-temperature impact toughness of the center. The invention can be implemented in the medium and thick plate plant of metallurgical enterprises, has simple process flow, strong operability and low cost, and can be applied to the construction of large pressure vessels in petroleum, chemical and other industries.
Although the preferred embodiments of the invention have been described in detail above, it should be clearly understood that the invention may have various modifications and changes or those skilled in the art. Any modification, equivalent replacement, improvement, etc. made within the spirit and principles of the invention shall be included in the protection scope of the invention.
Table 3 Steel Yield Impact at 1/2 of Tensile Elonga Impact at 1/4 of Embodim plate strength plate thickness strength tion plate thickness ent thickness ReL -50 CKV2 (J) Rm (MPa) A (%) -50 CKV2 (J) (mm) (MPa) Embodim 154 116 137 60 460 608 24.0 236 202 231 ent 1 Embodim 100 123 108 90 432 586 25.5 176 200 195 ent 2 Comparat 90 157 36 ive 65 425 578 27.5 167 188 202 examples Comparat 18 100 68 ive 88 411 562 26.0 166 217 169 examples It can be seen from Table 3 that the strength, elongation and impact toughness margin of the test steel plate are large in the embodiment of the invention, especially the impact energy at 1/2 of the plate thickness is more than 100J, while the impact energy at 1/2 of the plate thickness in the comparative example is unstable, and the lowest single value is only 18J.
The invention not only ensures that the steel has good strength and toughness, but also has stable low-temperature impact toughness of the center. The invention can be implemented in the medium and thick plate plant of metallurgical enterprises, has simple process flow, strong operability and low cost, and can be applied to the construction of large pressure vessels in petroleum, chemical and other industries.
Although the preferred embodiments of the invention have been described in detail above, it should be clearly understood that the invention may have various modifications and changes or those skilled in the art. Any modification, equivalent replacement, improvement, etc. made within the spirit and principles of the invention shall be included in the protection scope of the invention.
- 6 -Date Recue/Date Received 2022-04-11
Claims (6)
1. An extra thick vessel steel plate with good low-temperature impact toughness at the center, characterized in that the chemical constitutions of the steel plate is: C: 0.13-0.20%, Si:
< 0.40%, Mn: 1.00-1.60%, P < 0.015%, s < 0.005%, Als: 0.01-0.05%, Nb + V + Ti < 0.080%, Ni: 0.20-0.50%, Cu < 0.30%, H < 2ppm, and the balance is Fe and unavoidable impurity elements. At the same time:
CEV=C+Mn/6+(Mo+V+Cr)/5+(Ni+Cu)/15<0.43%, 3<w (Nb+V+Als)/w (Ti)<8.
< 0.40%, Mn: 1.00-1.60%, P < 0.015%, s < 0.005%, Als: 0.01-0.05%, Nb + V + Ti < 0.080%, Ni: 0.20-0.50%, Cu < 0.30%, H < 2ppm, and the balance is Fe and unavoidable impurity elements. At the same time:
CEV=C+Mn/6+(Mo+V+Cr)/5+(Ni+Cu)/15<0.43%, 3<w (Nb+V+Als)/w (Ti)<8.
2. According to claim 1, the extra thick vessel steel plate with good low-temperature impact toughness at the center is characterized in that the thickness of the steel plate is 60-100mm.
3. According to claim 1, the extra thick vessel steel plate with good low-temperature impact toughness at the center is characterized in that the near surface of the steel plate is tempered sorbite, and the 1/4 and 1/2 of the thickness of the steel plate are bainite.
4. According to claim 1, the extra thick vessel steel plate with good low-temperature impact toughness at the center is characterized in that the yield strength of the steel plate is >
400MPa, the tensile strength Rm is > 550MPa, the elongation A is > 22%, and the transverse impact energy at 1/4 of the plate thickness is -50 C KV2 > 150J; Transverse impact energy at 1/2 of plate thickness -50 C KV2 > 80J.
400MPa, the tensile strength Rm is > 550MPa, the elongation A is > 22%, and the transverse impact energy at 1/4 of the plate thickness is -50 C KV2 > 150J; Transverse impact energy at 1/2 of plate thickness -50 C KV2 > 80J.
5. According to any one of claims 1-4, a method for production the extra thick vessel steel plate with good low-temperature impact toughness at the center is characterized in that the process flovv is: hot metal pretreatment ¨> converter smelting ladle furnace refining vacuum degassing treatment ¨> continuous casting ¨> billet covering & cooling ¨> billet heating ¨> controlled rolling ¨> controlled cooling ¨> stack slow cooling ¨>
tempering, Specific operation:
After KR pretreatment, desulfurization and converter smelting, the molten iron is refined in ladle furnace and vacuum treated, and smelted into high-purity molten steel after soft blowing for more than 15 minutes. The continuous casting billet is cast on the continuous casting machine by using the whole process inert gas protective casting and soft reduction technology, and the billet is covered for slow cooling;
The continuous casting billet shall be heated to 1150-1200 C, the holding time in the furnace shall not be less than 300min, and the soaking time shall not be less than 90min. After coming out of the furnace, the scale shall be descaled by high-pressure water to remove the iron oxide scale on the billet surface; Then carry out two-stage controlled rolling. The start rolling temperature is 1020-1100 C, the final rolling temperature is 1000-1060 C, and the reduction rate of the last tvvo passes of start rolling is > 15%; The starting temperature of finish rolling is 880-920 C; After rolling, DQ + ACC two-stage cooling is adopted to achieve the purpose of on-line quenching.
tempering, Specific operation:
After KR pretreatment, desulfurization and converter smelting, the molten iron is refined in ladle furnace and vacuum treated, and smelted into high-purity molten steel after soft blowing for more than 15 minutes. The continuous casting billet is cast on the continuous casting machine by using the whole process inert gas protective casting and soft reduction technology, and the billet is covered for slow cooling;
The continuous casting billet shall be heated to 1150-1200 C, the holding time in the furnace shall not be less than 300min, and the soaking time shall not be less than 90min. After coming out of the furnace, the scale shall be descaled by high-pressure water to remove the iron oxide scale on the billet surface; Then carry out two-stage controlled rolling. The start rolling temperature is 1020-1100 C, the final rolling temperature is 1000-1060 C, and the reduction rate of the last tvvo passes of start rolling is > 15%; The starting temperature of finish rolling is 880-920 C; After rolling, DQ + ACC two-stage cooling is adopted to achieve the purpose of on-line quenching.
6. According to claim 5, the production method of extra thick vessel steel plate with good low-temperature impact toughness at the center is characterized in that during cooling after rolling, the water temperature of the steel plate is controlled at 840-880 C, the cooling speed is controlled at 5-15 C/s, the water surface temperature of the steel plate is 100-200 C
Date Recue/Date Received 2022-04-11 after ACC cooling, the steel plate is slowly cooled after being offline, and then tempered, Tempering temperature: 600-680 C, tempering holding time: 180min-300min.
Date Recue/Date Received 2022-04-11
Date Recue/Date Received 2022-04-11 after ACC cooling, the steel plate is slowly cooled after being offline, and then tempered, Tempering temperature: 600-680 C, tempering holding time: 180min-300min.
Date Recue/Date Received 2022-04-11
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| PCT/CN2020/092872 WO2021179443A1 (en) | 2020-03-11 | 2020-05-28 | Ultra-thick container steel plate with good low-temperature impact toughness in core and manufacturing method therefor |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115354219A (en) * | 2022-07-06 | 2022-11-18 | 江阴兴澄特种钢铁有限公司 | SA516Gr70 steel plate with excellent high-temperature strength at 200-400 ℃ and manufacturing method thereof |
| CN115354219B (en) * | 2022-07-06 | 2023-09-15 | 江阴兴澄特种钢铁有限公司 | SA516Gr70 steel plate with excellent high-temperature strength at 200-400 ℃ and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN111363973A (en) | 2020-07-03 |
| CN111363973B (en) | 2021-06-18 |
| WO2021179443A1 (en) | 2021-09-16 |
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