EP3730655B1 - High strength steel plate and manufacturing method therefor - Google Patents
High strength steel plate and manufacturing method therefor Download PDFInfo
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- EP3730655B1 EP3730655B1 EP18891912.0A EP18891912A EP3730655B1 EP 3730655 B1 EP3730655 B1 EP 3730655B1 EP 18891912 A EP18891912 A EP 18891912A EP 3730655 B1 EP3730655 B1 EP 3730655B1
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- 229910000831 Steel Inorganic materials 0.000 title claims description 95
- 239000010959 steel Substances 0.000 title claims description 95
- 238000004519 manufacturing process Methods 0.000 title claims description 19
- 238000005096 rolling process Methods 0.000 claims description 27
- 230000007704 transition Effects 0.000 claims description 23
- 229910000734 martensite Inorganic materials 0.000 claims description 20
- 229910001563 bainite Inorganic materials 0.000 claims description 19
- 238000005496 tempering Methods 0.000 claims description 16
- 229910052804 chromium Inorganic materials 0.000 claims description 13
- 238000000034 method Methods 0.000 claims description 13
- 238000010791 quenching Methods 0.000 claims description 13
- 230000000171 quenching effect Effects 0.000 claims description 13
- 229910045601 alloy Inorganic materials 0.000 claims description 10
- 239000000956 alloy Substances 0.000 claims description 10
- 230000001186 cumulative effect Effects 0.000 claims description 8
- 239000012535 impurity Substances 0.000 claims description 7
- 238000003303 reheating Methods 0.000 claims description 7
- 229910052720 vanadium Inorganic materials 0.000 claims description 7
- 238000009863 impact test Methods 0.000 claims description 3
- 239000011651 chromium Substances 0.000 description 34
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 33
- 239000010955 niobium Substances 0.000 description 31
- 239000011572 manganese Substances 0.000 description 27
- 239000011575 calcium Substances 0.000 description 26
- 239000010949 copper Substances 0.000 description 26
- 239000010936 titanium Substances 0.000 description 22
- 230000000694 effects Effects 0.000 description 21
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 20
- 239000000203 mixture Substances 0.000 description 16
- 229910052757 nitrogen Inorganic materials 0.000 description 13
- 229910052748 manganese Inorganic materials 0.000 description 12
- 239000000463 material Substances 0.000 description 11
- 229910052710 silicon Inorganic materials 0.000 description 11
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 10
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 9
- 229910052799 carbon Inorganic materials 0.000 description 9
- 238000010438 heat treatment Methods 0.000 description 9
- 239000010703 silicon Substances 0.000 description 9
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 8
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 8
- 229910052782 aluminium Inorganic materials 0.000 description 8
- 229910052796 boron Inorganic materials 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 8
- 229910052750 molybdenum Inorganic materials 0.000 description 8
- 229910052698 phosphorus Inorganic materials 0.000 description 8
- 239000011574 phosphorus Substances 0.000 description 8
- 238000001953 recrystallisation Methods 0.000 description 8
- 229910052717 sulfur Inorganic materials 0.000 description 8
- 239000011593 sulfur Substances 0.000 description 8
- 229910052719 titanium Inorganic materials 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 7
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 7
- 229910052758 niobium Inorganic materials 0.000 description 7
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 7
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 6
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 6
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 6
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 6
- 229910052791 calcium Inorganic materials 0.000 description 6
- 229910052802 copper Inorganic materials 0.000 description 6
- 239000011733 molybdenum Substances 0.000 description 6
- 229910052759 nickel Inorganic materials 0.000 description 6
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 6
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 5
- 230000001965 increasing effect Effects 0.000 description 5
- 229910052718 tin Inorganic materials 0.000 description 5
- 238000009628 steelmaking Methods 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 3
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 238000012423 maintenance Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000004148 curcumin Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000004880 explosion Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- 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
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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
- C21D8/0247—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
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/44—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
-
- 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
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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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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present disclosure relates to a high strength steel plate and a manufacturing method therefor, and more particularly, to a high strength steel plate having excellent tensile strength and impact toughness, particularly suitable for a nuclear reactor containment container, and a manufacturing method therefor.
- a nuclear reactor containment vessel utilizes a steel material, and A516-70 steel produced by a normalizing process is mainly used as a thick steel plate material.
- A516-70 steel has insufficient tensile strength (about 500 Mpa) to ensure the nuclear power plant's safety, and, thus, a range of use thereof may be extremely limited. That is, since the A516-70 steel has relatively low tensile strength, when used to manufacture a nuclear reactor containment vessel, there may be a risk of damage or explosion due to the failure to withstand the high pressure inside. Accordingly, there may be an urgent need to develop a material suitable for a nuclear reactor containment container while having tensile strength of a certain level or more.
- Patent Document 1 discloses a high strength steel plate with improved tensile strength, which may be a high strength steel plate that may be used for a nuclear reactor containment vessel.
- the steel plate disclosed in Patent Document 1 has a level of tensile strength that may be used as a steel plate for a nuclear reactor containment vessel, but may not be suitable as a material for a nuclear reactor containment vessel due to deteriorations in low-temperature toughness and nil-ductility transition temperature properties.
- Patent document 2 discloses a high strength steel plate including, by weight: 0.03% to 0.20% C, 0.15% to 0.55% Si, 0.9% to 1.5% Mn, 0.001% to 0.05% Al, 0.030% or less P, 0.030% or less S, 0.30% or less Cr, 0.2% or less Mo, 0.6% or less Ni, 0.07% or less V, 0.04% or less Nb, 5 ppm to 50 ppm Ca, 0.005% to 0.025% Ti, 0.0020% to 0.0060% N, 0.0005% to 0.0020% B, the balance of F and unavoidable impurities.
- the steel plate may be formed of tempered martensite, and conditions for cooling and recrystallization controlled rolling are optimized so as to control an average grain size of a microstructure and an aspect ratio of structure grains.
- Patent Document 3 discloses a thick steel plate for a reactor storage container having a composition comprising, by mass, 0.05 to 0.15% C, 0.05 to 0.60% Si, 0.8 to 1.8% Mn, 0.020% or lower of P, 0.005% or lower of S, 0.005 to 0.080% Al and 0.0005 to 0.0050% N and further comprising one or more kinds selected from 0.50% or lower of Cu, 0.70% or lower of Ni, 0.50% or lower of Cr, 0.40% or lower of Mo, 0.07% or lower of V and 0.0003 to 0 .
- the microstructure in the 1/4 position of the plate thickness is made of tempered lower bainite and tempered martensite, and Tin an NRL drop hammer test in the 1/4 position of the plate thickness is -55°C or lower.
- a high strength steel plate having excellent tensile strength, low-temperature toughness, and nil-ductility transition temperature properties particularly suitable for a nuclear reactor containment container of a nuclear power plant, and a manufacturing method therefor, may be provided.
- a high strength steel plate includes, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfies relationships of Cu + Ni + Cr + Mo: 1.5% or less, Cr + Mo: 0.4% or less, V + Nb: 0.1% or less, and Ca/S: 1.0 or higher, and includes a microstructure of 30 to 60 area% of tempered martensite and 40 to 70 area% of tempered
- the tempered martensite may be included in 40 to 60 area% in the microstructure, and the tempered bainite may be included in 40 to 60 area% in the microstructure.
- a nil-ductility transition temperature of the steel plate may be -50°C or lower, wherein the nil-ductility transition temperature is a result value according to the drop-weight test transition temperature set by the ASTM E208-06 method.
- Tensile strength of the steel plate is 600 MPa or more.
- a method of manufacturing a high strength steel plate includes: reheating a steel slab at 1050 to 1250°C, the steel slab comprising, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfying relationships of Cu + Ni + Cr + Mo: 1.5% or less, Cr + Mo: 0.4% or less, V + Nb: 0.1% or less, and Ca/S: 1.0 or higher, rolling the slab in
- the austenizing may be performed for a time period of 1.6 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes).
- the tempering may be performed for a time period of 2.4 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes).
- a high strength steel plate securing a tensile strength of 600 MPa or more, a Charpy impact toughness of 300 J or more at -60°C, and a nil-ductility transition temperature of -50°C or lower, to be particularly suitable for a nuclear reactor containment container of a nuclear power plant, and a manufacturing method therefor, is provided.
- the present disclosure relates to a high strength steel plate and a manufacturing method therefor, and, hereinafter, preferred embodiments of the present disclosure will be described.
- Embodiments of the present disclosure may be modified in various forms, and the scope of the present disclosure should not be construed as being limited to embodiments to be described below. These embodiments may be provided to those skilled in the art to further detail the present disclosure.
- a high strength steel plate comprises, by weight: 0.05 to 0.2% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities.
- carbon (C) may be an effective element for securing strength
- the present disclosure limits a lower limit of the carbon (C) content to 0.05% to prevent a decrease in strength on a matrix phase.
- carbon (C) is excessively added, toughness and weldability may be deteriorated, making it unsuitable for use for a nuclear reactor containment container, and the present disclosure limits an upper limit of the carbon (C) content to 0.2%. Therefore, the carbon (C) content of the present disclosure is 0.05 to 0.2%, and a preferable carbon (C) content may be 0.08 to 0.15%.
- Silicon (Si) may be an element added for a deoxidation effect, a solid solution strengthening effect, and an impact transition temperature increasing effect. Therefore, the present disclosure limits a lower limit of the silicon (Si) content to 0.15% to achieve this effect.
- a preferred lower limit of the silicon (Si) content may be 0.2%, and a more preferred lower limit of the silicon (Si) content may be 0.3%.
- the silicon (Si) is excessively added, weldability of the steel plate may be deteriorated and an oxide film may be severely formed on a surface of the steel plate. Therefore, the present disclosure limits an upper limit of the silicon (Si) content to 0.55%.
- a preferred upper limit of the silicon (Si) content may be 0.5%, and a more preferred upper limit of the silicon (Si) content may be 0.4%.
- Manganese (Mn) may be an effective element for securing strength, and the present disclosure limits a lower limit of the manganese (Mn) content to 0.9% to achieve this effect.
- a preferred lower limit of the manganese (Mn) content may be 1.0%, and a more preferred lower limit of the manganese (Mn) content may be 1.2%.
- Manganese (Mn) may be combined with sulfur (S) to form a non-metallic inclusion such as MnS. When manganese (Mn) is added excessively, elongation at room temperature and low-temperature toughness may be deteriorated. Therefore, the present disclosure limits an upper limit of the manganese (Mn) content to 1.75%.
- a preferred upper limit of the manganese (Mn) content may be 1.7%, and a more preferred upper limit of the manganese (Mn) content may be 1.6%.
- aluminum (Al) may be an element as a strong deoxidizer
- the present disclosure limits a lower limit of the aluminum (Al) content to 0.001% for a deoxidation effect in a steelmaking process.
- the present disclosure limits an upper limit of the aluminum (Al) content to 0.05%.
- the aluminum (Al) content is more preferably 0.01 to 0.04%.
- Phosphorus (P) may be an element that impairs low-temperature toughness. Therefore, P may be desirable to have its content managed to be as low as possible. Since Phosphorus (P) may be an element that may be inevitably contained in a steelmaking process, may take excessive cost to completely remove it, the present disclosure limits an upper limit of the phosphorus (P) content to 0.03%. A preferred upper limit of the phosphorus (P) content may be 0.02%, and a more preferred upper limit of the phosphorus (P) content may be 0.01%.
- S may be also an element that adversely affects low-temperature toughness, together with phosphorus (P). Therefore, S may be desirable to have its content managed to be as low as possible. Since sulfur (S) may be an element that may be inevitably contained in a steelmaking process, like phosphorus (P), and may take excessive cost to completely remove it, the present disclosure limits an upper limit of the sulfur (S) content to 0.03%. A preferred upper limit of the sulfur (S) content may be 0.02%, and a more preferred upper limit of the sulfur (S) content may be 0.01%.
- chromium (Cr) may be an element contributing to an increase in strength
- the present disclosure limits a lower limit of the chromium (Cr) content to 0.05% to achieve this effect.
- Chromium (Cr) may be an expensive element. When Cr is added excessively, it is not preferable from a viewpoint of economic efficiency. Therefore, the present disclosure limits an upper limit of the chromium (Cr) content to 0.3%. Therefore, the chromium (Cr) content of the present disclosure may be 0.05 to 0.3%, and is more preferably 0.05 to 0.2%.
- Nickel (Ni) may be an effective element for improving low-temperature toughness. Therefore, the present disclosure limits a lower limit of the nickel (Ni) content to 0.05% to achieve this effect. Nickel (Ni) may be an expensive element. When Ni is excessively added, an increase in production cost may occur. Therefore, the present disclosure limits an upper limit of the nickel (Ni) content to 0.6%. Therefore, the nickel (Ni) content of the present disclosure may be 0.05 to 0.6%, and is more preferably 0.2 to 0.6%.
- Copper (Cu) may be an effective element for increasing strength. Therefore, the present disclosure limits a lower limit of the copper (Cu) content to 0.005% to achieve this effect. Copper (Cu) may be an expensive element. When Cu is excessively added, an increase in production cost may occur. Therefore, the present disclosure limits an upper limit of the copper (Cu) content to 0.35%. Therefore, the copper (Cu) content of the present disclosure may be 0.005 to 0.35%, and is more preferably 0.01 to 0.3%.
- Molybdenum (Mo) may be an alloy element effective for improving strength, and may be an element that prevents crack generation caused by sulfide. Therefore, the present disclosure limits a lower limit of the molybdenum (Mo) content to 0.05% to achieve this effect. Molybdenum (Mo) may be also an expensive element. When Mo is excessively added, an increase in production cost may occur. Therefore, the present disclosure limits an upper limit of the molybdenum (Mo) content to 0.2%. Therefore, the molybdenum (Mo) content of the present disclosure is 0.05 to 0.2%, and is preferably 0.1 to 0.2%.
- Vanadium (V) may be an effective element for improving low-temperature toughness. Therefore, the present disclosure limits a lower limit of the vanadium (V) content to 0.005% to achieve this effect. Vanadium (V) may be also an expensive element. When V is excessively added, an increase in production cost may occur. Therefore, the present disclosure limits an upper limit of the vanadium (V) content to 0.07%. Therefore, the vanadium (V) content of the present disclosure is 0.005 to 0.07%, and is preferably 0.01 to 0.07%.
- Niobium (Nb) may be an element that may be dissolved in austenite to increase hardenability of the austenite.
- niobium (Nb) may be an element that is precipitated as carbonitride (Nb (C,N)) matching with a matrix, together with titanium (Ti), and may be a major element for obtaining a tensile strength of 600 MPa or more for which the present disclosure seeks. Therefore, the present disclosure limits a lower limit of the niobium (Nb) content to 0.005% to achieve this effect.
- Nb When niobium (Nb) is excessively added, coarse precipitates may occur in the process of continuous casting, and Nb may act as a starting point for hydrogen-induced cracking (HIC) . Therefore, the present disclosure limits an upper limit of the niobium (Nb) content to 0.04%. Therefore, the niobium (Nb) content of the present disclosure is 0.005 to 0.04%, and is preferably 0.01 to 0.03%
- Calcium (Ca) may be combined with sulfur (S) to form a CaS precipitate, and may thus be an effective element for suppressing formation of MnS. Therefore, the present disclosure limits a lower limit of the calcium (Ca) content to 0.0005% to achieve this effect.
- Ca may react with oxygen in steel to produce CaO, which may be a non-metallic inclusion. Therefore, the present disclosure limits an upper limit of the calcium (Ca) content to 0.005%. Therefore, the calcium (Ca) content of the present disclosure is 0.0005 to 0.005%, and is preferably 0.001 to 0.003%.
- An appropriate content of titanium (Ti) may be fluidly limited according to the content of nitrogen (N).
- an amount of TiN produced may be relatively small, which may be disadvantageous for fine-graining.
- titanium (Ti) is added in an excessive amount, TiN may become coarse during a heating operation to reduce an effect of inhibiting grain growth. Therefore, in consideration of the content (e.g., 0.002 to 0.006%) of nitrogen (N), the content of titanium (Ti) of the present disclosure is 0.005 to 0.025%, and is preferably 0.01 to 0.02%.
- Nitrogen (N) may be widely known as an element that plays a role in increasing toughness of a base material and impact toughness of a heat-affected zone (HAZ) by forming a TiN precipitate with titanium (Ti) to refine grains.
- nitrogen (N) may be an element that should be added to achieve the purpose of grain refinement. Therefore, the present disclosure limits a lower limit of the nitrogen (N) content to 0.002% to achieve this effect.
- the nitrogen (N) content limits an upper limit of the nitrogen (N) content to 0.006%. Therefore, the nitrogen (N) content of the present disclosure is 0.002 to 0.006%, and is preferably 0.002 to 0.004%.
- the content of boron (B) may be actively suppressed, but excessive cost may be consumed to completely remove boron (B), which may be inevitably introduced during a steelmaking process. Therefore, the present disclosure limits the boron (B) content to less than 0.0005%.
- a preferred boron (B) content is 0.0002% or less, and a more preferred boron (B) content is 0.0001% or less.
- a high strength steel plate according to an aspect of the present disclosure satisfies relationships of Cu + Ni + Cr + Mo: 1.5% or less, Cr + Mo: 0.4% or less, V + Nb: 0.1% or less, and Ca/S: 1.0 or higher.
- the relationships of Cu + Ni + Cr + Mo, Cr + Mo, and V + Nb may be values that are respectively limited in the basic specification (ASTMA20) regarding steel for a pressure vessel, and the content of Cu + Ni + Cr + Mo is limited to 1.5% or less, the content of Cr + Mo is limited to 0.4% or less, and the content of V + Nb is limited to 0.1% or less.
- a ratio of Ca/s is an essential composition ratio of spheroidizing an MnS inclusion to improve hydrogen-induced crack resistance. When the ratio of Ca/s is less than 1.0, it may be difficult to expect the effect, the ratio is limited to satisfy 1.0 or more.
- a high strength steel plate includes a combined structure of tempered martensite and tempered bainite as a microstructure.
- Microstructure combined structure of tempered martensite and tempered bainite
- a microstructure of the steel material may have a microstructure of tempered martensite and tempered bainite.
- the tempered martensite and the tempered bainite includes 30 to 60 area% and 40 to 70 area%, respectively, and a tensile strength of 600 MPa, a nil-ductility transition temperature of -50°C or lower, and a Charpy impact toughness of 300 J or more at -60°C are effectively secured.
- a preferred area fraction of tempered martensite is 40 to 60%
- a preferred area fraction of tempered bainite is 40 to 60%.
- the sum of area fractions of the tempered martensite and the tempered bainite may be 100%.
- a grain aspect ratio (a ratio of long axis/short axis) is controlled within a certain range, and the grain aspect ratio may be controlled by a rolling (a recrystallization control rolling) process.
- a rolling a recrystallization control rolling
- the grain aspect ratio is less than 1.1, a shape of the grain may be rounded, surface energy thereof may become small, and it may be difficult to expect refinement of the grain. Therefore, it may be difficult to secure sufficient impact toughness and strength.
- the grain aspect ratio exceeds 2.5, a rolling load for forming the grain becomes too high, and impact toughness may be lowered, which is not preferable. Therefore, the present disclosure limits the grain aspect ratio (the ratio of long axis/short axis) to have a range of 1.1 to 2.5.
- a high strength steel plate is manufactured by reheating a steel slab at 1050 to 1250°C, the steel slab including, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfying relationships of Cu + Ni + Cr + Mo: 1.5% or less, Cr + Mo: 0.4% or less, V + Nb: 0.1% or less, and Ca/S: 1.0 or higher, rolling the slab in a temperature range of T
- an alloy composition and a content of the slab of the present disclosure correspond to the alloy composition and the content of the high strength steel plate described above, a description of the alloy composition and the content of the slab of the present disclosure may be replaced with the description of the alloy composition and the content of the steel plate described above.
- a slab provided with the above-described alloy composition is reheated at a temperature range of 1050 to 1250°C. This is because, when a reheating temperature thereof is less than 1050°C, it may be difficult to sufficiently dissolve solute atoms, and when a reheating temperature thereof exceeds 1250°C, an austenite grain size may be excessively coarsened and properties of a steel plate may be deteriorated.
- Recrystallization Control Rolling Operation a temperature range of Tnr to (Tnr + 100°C), a cumulative reduction amount of 50 to 90% at a rolling reduction ratio of 10% or more per rolling pass
- the recrystallization control rolling operation refers to a rolling operation to be performed at a temperature equal to or higher than an unrecrystallized temperature .
- the unrecrystallized temperature Tnr is derived by the following Equation 1, which has been already known.
- Equation 1 a unit of each alloy element is weight%.
- Tnr ° C 887 ⁇ 464 ⁇ C + 890 ⁇ Ti + 363 ⁇ Al ⁇ 357 ⁇ Si + 6445 ⁇ Nb ⁇ 644 ⁇ N b 1 / 2 + 732 ⁇ V ⁇ 230 ⁇ V 1 / 2 .
- the rolling operation is performed in a temperature range of Tnr to Tnr + 100°C.
- a rolling reduction ratio of 10% or more may be applied per rolling pass, to finally perform the rolling operation in a cumulative reduction amount of 50 to 90%.
- a reduction amount is provided to control an average size (30 ⁇ m or less) of a microstructure required in the present disclosure and a grain aspect ratio (a long axis/short axis ratio) to 1.1 to 2.5. Therefore, when the cumulative reduction amount is less than 50%, it may be difficult to expect a refinement effect of the microstructure and a control effect of the grain aspect ratio.
- the cumulative reduction amount exceeds 90%, a rolling load may be excessively applied, which may cause a problem in process.
- the quenching operation may be an important process for obtaining a combined structure of tempered martensite and tempered bainite, and may be necessary to strictly control process conditions to form a microstructure capable of securing a tensile strength of 600 MPa or more, a -60°C Charpy impact toughness of 300J or more, and a nil-ductility transition temperature property of -50°C or lower.
- the austenizing operation may be performed for a time period of 1.6 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes) in a temperature range of 870 to 950°C.
- the austenizing operation may be a heat treatment for austenizing the structure before the quenching operation.
- a temperature range of the heat treatment is less than 870°C, it may be difficult to re-solidify the solute elements, and thus it may be difficult to secure strength.
- a temperature range of the heat treatment exceeds 950°C, growth of grains may occur and coarse grains may occur, to impair low-temperature toughness. Therefore, a temperature range of the austenizing operation of the present disclosure may be limited to a temperature range of 870 to 950°C.
- the austenizing operation may be performed for a time period of 1.6 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes).
- a time period of the austenizing operation is excessively short, an effect of sufficient austenizing may not be expected due to insufficient heating time, and it may be difficult to homogenize the structure.
- a time period of the austenizing operation is excessively long, production time may be prolonged and productivity may be deteriorated. Therefore, a time period of the austenizing operation of the present disclosure may be limited to 1.6 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes) .
- 10 to 30 minutes may be set as a maintenance time period to perform the austenizing operation.
- the steel plate after the austenizing operation, is quenched, preferably water-cooled, to be transformed to a combined structure of martensite and bainite.
- Conditions for the quenching operation in the present disclosure are not particularly limited, and any rapid quenching method including a water cooling operation may be applied to the quenching operation of the present disclosure.
- the steel plate may be cooled to a temperature range of 300°C or lower.
- Tempering Operation 2.4 ⁇ t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes) in a temperature range of 595 to 700°C
- a tempering operation of the quenched steel material to 300°C or lower is used to remove residual stress in a structure thereof. Therefore, tempered martensite and tempered bainite is formed.
- a temperature range of the tempering operation of the present disclosure is limited to 595 to 700°C. This is because, when a temperature range of the tempering operation is less than 595°C, carbides and the like may be not smoothly precipitated, and when a temperature range of the tempering operation exceeds 700°C, strength of the steel material may be lowered.
- the tempering operation of the present disclosure may be carried out for a time period of 2.4 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes) to obtain a sufficient tempering effect.
- t denotes a thickness (mm) of the steel plate
- 10 to 30 minutes may be set as a maintenance time period to perform the tempering operation.
- Test pieces were prepared by performing a reheating operation, a recrystallization control rolling operation, an austenizing operation, a quenching operation, and a tempering operation using respective slabs made of the compositions of Inventive Steel and Comparative Steel, as illustrated in Table 2 below. Properties such as strength, low-temperature toughness, and nil-ductility transition temperature were evaluated, and the results therefrom are illustrated in Table 3 below.
- the low-temperature impact toughness may be evaluated as a Charpy impact energy value obtained by performing a Charpy impact test on a specimen having a V notch at -60°C.
- the nil-ductility transition temperature may be a result value according to the drop-weight test transition temperature set by the ASTM E208-06 method.
- Table 2 Condition Steel Plate Thickness (mm) Slab Reheatin g Temp. (°C) Rolling Temp. (°C) Recrystallization Control Rolling Cumulative Reduction Amount (%) Grain Aspect Ratio* Austenizing Temp. (°C) Tempering Temp.
- Inventive Examples 1 to 7 have microstructures of 30 to 60% of tempered martensite and 40 to 70% of tempered bainite, and secure a tensile strength of 600 MPa or more, an impact toughness of 300 J or more at -60°C, and a nil-ductility transition temperature property of -50°C or lower.
- Comparative Example 1 it can be seen that, since a steel composition satisfies the defined steel composition of the present disclosure, but a cumulative reduction amount of a recrystallization control rolling operation does not satisfy the defined scope of the present disclosure, the area fractions of a microstructure defined by the present disclosure are not satisfied, and a nil-ductility transition temperature property at -50°C or lower is, thus, not secured.
- a microstructure has 80 area% or more of tempered martensite and 20 area% or less of tempered bainite, and tensile strength, impact toughness, and nil-ductility transition temperature properties are degraded.
- a steel plate according to an embodiment of the present disclosure may control a steel composition, a microstructure, and manufacturing operations under optimal conditions, to secure tensile strength of 600 MPa or more, Charpy impact toughness of 300 J or more at -60°C, and a nil-ductility transition temperature of -50°C or lower, a high strength steel plate having properties suitable for a nuclear reactor containment vessel may be provided.
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Description
- The present disclosure relates to a high strength steel plate and a manufacturing method therefor, and more particularly, to a high strength steel plate having excellent tensile strength and impact toughness, particularly suitable for a nuclear reactor containment container, and a manufacturing method therefor.
- Various materials are used for the structures and facilities of a nuclear power plant according to the type, usage, and safety properties thereof. In particular, a nuclear reactor containment vessel utilizes a steel material, and A516-70 steel produced by a normalizing process is mainly used as a thick steel plate material.
- However, such A516-70 steel has insufficient tensile strength (about 500 Mpa) to ensure the nuclear power plant's safety, and, thus, a range of use thereof may be extremely limited. That is, since the A516-70 steel has relatively low tensile strength, when used to manufacture a nuclear reactor containment vessel, there may be a risk of damage or explosion due to the failure to withstand the high pressure inside. Accordingly, there may be an urgent need to develop a material suitable for a nuclear reactor containment container while having tensile strength of a certain level or more.
- In order to improve the tensile strength, if a relatively large amount of expensive alloying elements is added to a steel material or a separate heat treatment is performed, tensile strength may be hardly improved, but an increase in costs due to the addition of the alloying elements may be inevitable, and there may be other incidental problems involved.
- Patent Document 1 discloses a high strength steel plate with improved tensile strength, which may be a high strength steel plate that may be used for a nuclear reactor containment vessel. However, the steel plate disclosed in Patent Document 1 has a level of tensile strength that may be used as a steel plate for a nuclear reactor containment vessel, but may not be suitable as a material for a nuclear reactor containment vessel due to deteriorations in low-temperature toughness and nil-ductility transition temperature properties.
- Patent document 2 discloses a high strength steel plate including, by weight: 0.03% to 0.20% C, 0.15% to 0.55% Si, 0.9% to 1.5% Mn, 0.001% to 0.05% Al, 0.030% or less P, 0.030% or less S, 0.30% or less Cr, 0.2% or less Mo, 0.6% or less Ni, 0.07% or less V, 0.04% or less Nb, 5 ppm to 50 ppm Ca, 0.005% to 0.025% Ti, 0.0020% to 0.0060% N, 0.0005% to 0.0020% B, the balance of F and unavoidable impurities. The steel plate may be formed of tempered martensite, and conditions for cooling and recrystallization controlled rolling are optimized so as to control an average grain size of a microstructure and an aspect ratio of structure grains.
- Patent Document 3 discloses a thick steel plate for a reactor storage container having a composition comprising, by mass, 0.05 to 0.15% C, 0.05 to 0.60% Si, 0.8 to 1.8% Mn, 0.020% or lower of P, 0.005% or lower of S, 0.005 to 0.080% Al and 0.0005 to 0.0050% N and further comprising one or more kinds selected from 0.50% or lower of Cu, 0.70% or lower of Ni, 0.50% or lower of Cr, 0.40% or lower of Mo, 0.07% or lower of V and 0.0003 to 0 . 0020% B, and in which plate thickness satisfies 100 mm or lower, the microstructure in the 1/4 position of the plate thickness is made of tempered lower bainite and tempered martensite, and Tin an NRL drop hammer test in the 1/4 position of the plate thickness is -55°C or lower.
- (Patent Document 1)
Korea Patent Publication No. 10-2010-0076745 (published on July 6, 2010 - (Patent Document 2)
WO 2010/074473 A2 (published on 1 July 2010 ) - (Patent Document 3)
JP 2015124435 A (published on 6 July 2015 - According to an aspect of the present disclosure, a high strength steel plate having excellent tensile strength, low-temperature toughness, and nil-ductility transition temperature properties, particularly suitable for a nuclear reactor containment container of a nuclear power plant, and a manufacturing method therefor, may be provided.
- According to an aspect of the invention, a high strength steel plate includes, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfies relationships of Cu + Ni + Cr + Mo: 1.5% or less, Cr + Mo: 0.4% or less, V + Nb: 0.1% or less, and Ca/S: 1.0 or higher, and includes a microstructure of 30 to 60 area% of tempered martensite and 40 to 70 area% of tempered bainite, wherein the sum of the tempered martensite and the tempered bainite is 100 area%, wherein a grain aspect ratio as defined herein of the microstructure is 1.1 to 2.5,
wherein Charpy impact toughness of the steel plate is 300J or more at -60°C, and wherein the low-temperature impact toughness is evaluated as a Charpy impact energy value obtained by performing a Charpy impact test on a specimen having a V notch at -60°C. - The tempered martensite may be included in 40 to 60 area% in the microstructure, and the tempered bainite may be included in 40 to 60 area% in the microstructure.
- A nil-ductility transition temperature of the steel plate may be -50°C or lower, wherein the nil-ductility transition temperature is a result value according to the drop-weight test transition temperature set by the ASTM E208-06 method.
- Tensile strength of the steel plate is 600 MPa or more.
- According to an aspect of the invention, a method of manufacturing a high strength steel plate includes: reheating a steel slab at 1050 to 1250°C, the steel slab comprising, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfying relationships of Cu + Ni + Cr + Mo: 1.5% or less, Cr + Mo: 0.4% or less, V + Nb: 0.1% or less, and Ca/S: 1.0 or higher, rolling the slab in a temperature range of Tnr to Tnr + 100°C, wherein Tnr is determined in accordance with Equation 1 hereof, to provide a steel plate, austenizing the steel plate in a temperature range of 870 to 950°C, quenching the austenized steel plate to a temperature range of 300°C or lower, and tempering the quenched steel plate in a temperature range of 595 to 700°C, wherein a cumulative reduction amount of the rolling is 50 to 90%, and wherein a grain aspect ratio as defined herein of a microstructure of the steel plate by the rolling is controlled to have a range of 1.1 to 2.5,
- The austenizing may be performed for a time period of 1.6 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes).
- The tempering may be performed for a time period of 2.4 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes).
- According to an aspect of the present disclosure, a high strength steel plate securing a tensile strength of 600 MPa or more, a Charpy impact toughness of 300 J or more at -60°C, and a nil-ductility transition temperature of -50°C or lower, to be particularly suitable for a nuclear reactor containment container of a nuclear power plant, and a manufacturing method therefor, is provided.
- The present disclosure relates to a high strength steel plate and a manufacturing method therefor, and, hereinafter, preferred embodiments of the present disclosure will be described. Embodiments of the present disclosure may be modified in various forms, and the scope of the present disclosure should not be construed as being limited to embodiments to be described below. These embodiments may be provided to those skilled in the art to further detail the present disclosure.
- Hereinafter, the steel composition of the present disclosure will be described in more detail. Hereinafter, unless otherwise indicated, % representing the content of each element is based on weight.
- A high strength steel plate according to an embodiment of the present disclosure comprises, by weight: 0.05 to 0.2% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities.
- Carbon (C): 0.05 to 0.2%
- Since carbon (C) may be an effective element for securing strength, the present disclosure limits a lower limit of the carbon (C) content to 0.05% to prevent a decrease in strength on a matrix phase. When carbon (C) is excessively added, toughness and weldability may be deteriorated, making it unsuitable for use for a nuclear reactor containment container, and the present disclosure limits an upper limit of the carbon (C) content to 0.2%. Therefore, the carbon (C) content of the present disclosure is 0.05 to 0.2%, and a preferable carbon (C) content may be 0.08 to 0.15%.
- Silicon (Si) may be an element added for a deoxidation effect, a solid solution strengthening effect, and an impact transition temperature increasing effect. Therefore, the present disclosure limits a lower limit of the silicon (Si) content to 0.15% to achieve this effect. A preferred lower limit of the silicon (Si) content may be 0.2%, and a more preferred lower limit of the silicon (Si) content may be 0.3%. When the silicon (Si) is excessively added, weldability of the steel plate may be deteriorated and an oxide film may be severely formed on a surface of the steel plate. Therefore, the present disclosure limits an upper limit of the silicon (Si) content to 0.55%. A preferred upper limit of the silicon (Si) content may be 0.5%, and a more preferred upper limit of the silicon (Si) content may be 0.4%.
- Manganese (Mn) may be an effective element for securing strength, and the present disclosure limits a lower limit of the manganese (Mn) content to 0.9% to achieve this effect. A preferred lower limit of the manganese (Mn) content may be 1.0%, and a more preferred lower limit of the manganese (Mn) content may be 1.2%. Manganese (Mn) may be combined with sulfur (S) to form a non-metallic inclusion such as MnS. When manganese (Mn) is added excessively, elongation at room temperature and low-temperature toughness may be deteriorated. Therefore, the present disclosure limits an upper limit of the manganese (Mn) content to 1.75%. A preferred upper limit of the manganese (Mn) content may be 1.7%, and a more preferred upper limit of the manganese (Mn) content may be 1.6%.
- Since aluminum (Al) may be an element as a strong deoxidizer, the present disclosure limits a lower limit of the aluminum (Al) content to 0.001% for a deoxidation effect in a steelmaking process. When aluminum (Al) is added excessively, the deoxidation effect may be saturated, but manufacturing costs may be increased. The present disclosure limits an upper limit of the aluminum (Al) content to 0.05%. The aluminum (Al) content is more preferably 0.01 to 0.04%.
- Phosphorus (P) may be an element that impairs low-temperature toughness. Therefore, P may be desirable to have its content managed to be as low as possible. Since Phosphorus (P) may be an element that may be inevitably contained in a steelmaking process, may take excessive cost to completely remove it, the present disclosure limits an upper limit of the phosphorus (P) content to 0.03%. A preferred upper limit of the phosphorus (P) content may be 0.02%, and a more preferred upper limit of the phosphorus (P) content may be 0.01%.
- Sulfur (S) may be also an element that adversely affects low-temperature toughness, together with phosphorus (P). Therefore, S may be desirable to have its content managed to be as low as possible. Since sulfur (S) may be an element that may be inevitably contained in a steelmaking process, like phosphorus (P), and may take excessive cost to completely remove it, the present disclosure limits an upper limit of the sulfur (S) content to 0.03%. A preferred upper limit of the sulfur (S) content may be 0.02%, and a more preferred upper limit of the sulfur (S) content may be 0.01%.
- Since chromium (Cr) may be an element contributing to an increase in strength, the present disclosure limits a lower limit of the chromium (Cr) content to 0.05% to achieve this effect. Chromium (Cr) may be an expensive element. When Cr is added excessively, it is not preferable from a viewpoint of economic efficiency. Therefore, the present disclosure limits an upper limit of the chromium (Cr) content to 0.3%. Therefore, the chromium (Cr) content of the present disclosure may be 0.05 to 0.3%, and is more preferably 0.05 to 0.2%.
- Nickel (Ni): 0.05 to 0.6%
- Nickel (Ni) may be an effective element for improving low-temperature toughness. Therefore, the present disclosure limits a lower limit of the nickel (Ni) content to 0.05% to achieve this effect. Nickel (Ni) may be an expensive element. When Ni is excessively added, an increase in production cost may occur. Therefore, the present disclosure limits an upper limit of the nickel (Ni) content to 0.6%. Therefore, the nickel (Ni) content of the present disclosure may be 0.05 to 0.6%, and is more preferably 0.2 to 0.6%.
- Copper (Cu) may be an effective element for increasing strength. Therefore, the present disclosure limits a lower limit of the copper (Cu) content to 0.005% to achieve this effect. Copper (Cu) may be an expensive element. When Cu is excessively added, an increase in production cost may occur. Therefore, the present disclosure limits an upper limit of the copper (Cu) content to 0.35%. Therefore, the copper (Cu) content of the present disclosure may be 0.005 to 0.35%, and is more preferably 0.01 to 0.3%.
- Molybdenum (Mo) may be an alloy element effective for improving strength, and may be an element that prevents crack generation caused by sulfide. Therefore, the present disclosure limits a lower limit of the molybdenum (Mo) content to 0.05% to achieve this effect. Molybdenum (Mo) may be also an expensive element. When Mo is excessively added, an increase in production cost may occur. Therefore, the present disclosure limits an upper limit of the molybdenum (Mo) content to 0.2%. Therefore, the molybdenum (Mo) content of the present disclosure is 0.05 to 0.2%, and is preferably 0.1 to 0.2%.
- Vanadium (V) may be an effective element for improving low-temperature toughness. Therefore, the present disclosure limits a lower limit of the vanadium (V) content to 0.005% to achieve this effect. Vanadium (V) may be also an expensive element. When V is excessively added, an increase in production cost may occur. Therefore, the present disclosure limits an upper limit of the vanadium (V) content to 0.07%. Therefore, the vanadium (V) content of the present disclosure is 0.005 to 0.07%, and is preferably 0.01 to 0.07%.
- Niobium (Nb) may be an element that may be dissolved in austenite to increase hardenability of the austenite. In addition, niobium (Nb) may be an element that is precipitated as carbonitride (Nb (C,N)) matching with a matrix, together with titanium (Ti), and may be a major element for obtaining a tensile strength of 600 MPa or more for which the present disclosure seeks. Therefore, the present disclosure limits a lower limit of the niobium (Nb) content to 0.005% to achieve this effect. When niobium (Nb) is excessively added, coarse precipitates may occur in the process of continuous casting, and Nb may act as a starting point for hydrogen-induced cracking (HIC) . Therefore, the present disclosure limits an upper limit of the niobium (Nb) content to 0.04%. Therefore, the niobium (Nb) content of the present disclosure is 0.005 to 0.04%, and is preferably 0.01 to 0.03%.
- Calcium (Ca) may be combined with sulfur (S) to form a CaS precipitate, and may thus be an effective element for suppressing formation of MnS. Therefore, the present disclosure limits a lower limit of the calcium (Ca) content to 0.0005% to achieve this effect. When calcium (Ca) is excessively added, Ca may react with oxygen in steel to produce CaO, which may be a non-metallic inclusion. Therefore, the present disclosure limits an upper limit of the calcium (Ca) content to 0.005%. Therefore, the calcium (Ca) content of the present disclosure is 0.0005 to 0.005%, and is preferably 0.001 to 0.003%.
- An appropriate content of titanium (Ti) may be fluidly limited according to the content of nitrogen (N). When the content of titanium (Ti) is relatively small, compared to the content of nitrogen (N), an amount of TiN produced may be relatively small, which may be disadvantageous for fine-graining. When titanium (Ti) is added in an excessive amount, TiN may become coarse during a heating operation to reduce an effect of inhibiting grain growth. Therefore, in consideration of the content (e.g., 0.002 to 0.006%) of nitrogen (N), the content of titanium (Ti) of the present disclosure is 0.005 to 0.025%, and is preferably 0.01 to 0.02%.
- Nitrogen (N) may be widely known as an element that plays a role in increasing toughness of a base material and impact toughness of a heat-affected zone (HAZ) by forming a TiN precipitate with titanium (Ti) to refine grains. In this regard, according to the present disclosure, nitrogen (N) may be an element that should be added to achieve the purpose of grain refinement. Therefore, the present disclosure limits a lower limit of the nitrogen (N) content to 0.002% to achieve this effect. When the nitrogen (N) content is excessively added, an amount of TiN may be excessively increased and low-temperature toughness may be reduced. Therefore, the present disclosure limits an upper limit of the nitrogen (N) content to 0.006%. Therefore, the nitrogen (N) content of the present disclosure is 0.002 to 0.006%, and is preferably 0.002 to 0.004%.
- In the present disclosure, the content of boron (B) may be actively suppressed, but excessive cost may be consumed to completely remove boron (B), which may be inevitably introduced during a steelmaking process. Therefore, the present disclosure limits the boron (B) content to less than 0.0005%. A preferred boron (B) content is 0.0002% or less, and a more preferred boron (B) content is 0.0001% or less.
- A high strength steel plate according to an aspect of the present disclosure satisfies relationships of Cu + Ni + Cr + Mo: 1.5% or less, Cr + Mo: 0.4% or less, V + Nb: 0.1% or less, and Ca/S: 1.0 or higher.
- Hereinafter, the relationships of the present disclosure will be described in more detail.
- Cu + Ni + Cr + Mo: 1.5% or less
- Cr + Mo: 0.4% or less
- V + Nb: 0.1% or less
- Ca/S: 1.0 or higher
- The relationships of Cu + Ni + Cr + Mo, Cr + Mo, and V + Nb may be values that are respectively limited in the basic specification (ASTMA20) regarding steel for a pressure vessel, and the content of Cu + Ni + Cr + Mo is limited to 1.5% or less, the content of Cr + Mo is limited to 0.4% or less, and the content of V + Nb is limited to 0.1% or less. In addition, a ratio of Ca/s is an essential composition ratio of spheroidizing an MnS inclusion to improve hydrogen-induced crack resistance. When the ratio of Ca/s is less than 1.0, it may be difficult to expect the effect, the ratio is limited to satisfy 1.0 or more.
- Hereinafter, the microstructure of the present disclosure will be described in more detail.
- A high strength steel plate according to an aspect of the present disclosure includes a combined structure of tempered martensite and tempered bainite as a microstructure.
- Microstructure: combined structure of tempered martensite and tempered bainite
- When quenching and tempering a steel material provided with the above-described alloy composition, a microstructure of the steel material may have a microstructure of tempered martensite and tempered bainite. In the present disclosure, the tempered martensite and the tempered bainite includes 30 to 60 area% and 40 to 70 area%, respectively, and a tensile strength of 600 MPa, a nil-ductility transition temperature of -50°C or lower, and a Charpy impact toughness of 300 J or more at -60°C are effectively secured. A preferred area fraction of tempered martensite is 40 to 60%, and a preferred area fraction of tempered bainite is 40 to 60%. In addition, the sum of area fractions of the tempered martensite and the tempered bainite may be 100%.
- Grain Aspect Ratio: 1.1 ≤ Long axis/Short axis ≤ 2.5
- In the present disclosure, in order to secure high impact toughness and strength, a grain aspect ratio (a ratio of long axis/short axis) is controlled within a certain range, and the grain aspect ratio may be controlled by a rolling (a recrystallization control rolling) process. When the grain aspect ratio is less than 1.1, a shape of the grain may be rounded, surface energy thereof may become small, and it may be difficult to expect refinement of the grain. Therefore, it may be difficult to secure sufficient impact toughness and strength. In addition, when the grain aspect ratio exceeds 2.5, a rolling load for forming the grain becomes too high, and impact toughness may be lowered, which is not preferable. Therefore, the present disclosure limits the grain aspect ratio (the ratio of long axis/short axis) to have a range of 1.1 to 2.5.
- Hereinafter, a manufacturing method of the present disclosure will be described in more detail.
- A high strength steel plate according to an aspect of the present disclosure is manufactured by reheating a steel slab at 1050 to 1250°C, the steel slab including, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfying relationships of Cu + Ni + Cr + Mo: 1.5% or less, Cr + Mo: 0.4% or less, V + Nb: 0.1% or less, and Ca/S: 1.0 or higher, rolling the slab in a temperature range of Tnr to Tnr + 100°C to provide a steel plate, austenizing the steel plate in a temperature range of 870 to 950°C, quenching the austenized steel plate to a temperature range of 300°C or lower, and tempering the quenched steel plate in a temperature range of 595 to 700°C.
- Since an alloy composition and a content of the slab of the present disclosure correspond to the alloy composition and the content of the high strength steel plate described above, a description of the alloy composition and the content of the slab of the present disclosure may be replaced with the description of the alloy composition and the content of the steel plate described above.
- Slab Reheating Operation: 1050 to 1250°C
- In the present disclosure, a slab provided with the above-described alloy composition is reheated at a temperature range of 1050 to 1250°C. This is because, when a reheating temperature thereof is less than 1050°C, it may be difficult to sufficiently dissolve solute atoms, and when a reheating temperature thereof exceeds 1250°C, an austenite grain size may be excessively coarsened and properties of a steel plate may be deteriorated.
- Recrystallization Control Rolling Operation: a temperature range of Tnr to (Tnr + 100°C), a cumulative reduction amount of 50 to 90% at a rolling reduction ratio of 10% or more per rolling pass
- The recrystallization control rolling operation refers to a rolling operation to be performed at a temperature equal to or higher than an unrecrystallized temperature . In this case, the unrecrystallized temperature Tnr is derived by the following Equation 1, which has been already known. In the following Equation 1, a unit of each alloy element is weight%.
- In order to improve strength, it may be necessary to refine an average particle diameter of prior austenite to 30 +µm or less in the recrystallization control rolling operation. When the average particle diameter of the prior austenite exceeds 30 µm, strength and toughness of a product may not be sufficiently exhibited. Therefore, a safety level high enough for a nuclear reactor containment vessel may not be guaranteed. To this end, in the present disclosure, the rolling operation is performed in a temperature range of Tnr to Tnr + 100°C.
- In this case, a rolling reduction ratio of 10% or more may be applied per rolling pass, to finally perform the rolling operation in a cumulative reduction amount of 50 to 90%. Such a reduction amount is provided to control an average size (30 µm or less) of a microstructure required in the present disclosure and a grain aspect ratio (a long axis/short axis ratio) to 1.1 to 2.5. Therefore, when the cumulative reduction amount is less than 50%, it may be difficult to expect a refinement effect of the microstructure and a control effect of the grain aspect ratio. When the cumulative reduction amount exceeds 90%, a rolling load may be excessively applied, which may cause a problem in process.
- Heat Treatment and Quenching Operation: quenching after austenizing the steel plate for a time period of 1.6 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes) in a temperature range of 870 to 950°C
- The quenching operation may be an important process for obtaining a combined structure of tempered martensite and tempered bainite, and may be necessary to strictly control process conditions to form a microstructure capable of securing a tensile strength of 600 MPa or more, a -60°C Charpy impact toughness of 300J or more, and a nil-ductility transition temperature property of -50°C or lower.
- In the present disclosure, the austenizing operation may be performed for a time period of 1.6 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes) in a temperature range of 870 to 950°C. The austenizing operation may be a heat treatment for austenizing the structure before the quenching operation. When a temperature range of the heat treatment is less than 870°C, it may be difficult to re-solidify the solute elements, and thus it may be difficult to secure strength. When a temperature range of the heat treatment exceeds 950°C, growth of grains may occur and coarse grains may occur, to impair low-temperature toughness. Therefore, a temperature range of the austenizing operation of the present disclosure may be limited to a temperature range of 870 to 950°C.
- In addition, in the present disclosure, the austenizing operation may be performed for a time period of 1.6 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes). When a time period of the austenizing operation is excessively short, an effect of sufficient austenizing may not be expected due to insufficient heating time, and it may be difficult to homogenize the structure. When a time period of the austenizing operation is excessively long, production time may be prolonged and productivity may be deteriorated. Therefore, a time period of the austenizing operation of the present disclosure may be limited to 1.6 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes) . For reference, in the steel plate manufacturing process, when 1.6 * t is set as a heating time period, and a target temperature is reached, 10 to 30 minutes may be set as a maintenance time period to perform the austenizing operation.
- The steel plate, after the austenizing operation, is quenched, preferably water-cooled, to be transformed to a combined structure of martensite and bainite. Conditions for the quenching operation in the present disclosure are not particularly limited, and any rapid quenching method including a water cooling operation may be applied to the quenching operation of the present disclosure. In order to obtain a microstructure desired by the present disclosure, after the austenizing operation is finished, the steel plate may be cooled to a temperature range of 300°C or lower.
- Tempering Operation: 2.4 × t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes) in a temperature range of 595 to 700°C
- In the present disclosure, in order to secure excellent tensile strength, nil-ductility transition temperature, and low-temperature toughness properties, a tempering operation of the quenched steel material to 300°C or lower is used to remove residual stress in a structure thereof. Therefore, tempered martensite and tempered bainite is formed.
- A temperature range of the tempering operation of the present disclosure is limited to 595 to 700°C. This is because, when a temperature range of the tempering operation is less than 595°C, carbides and the like may be not smoothly precipitated, and when a temperature range of the tempering operation exceeds 700°C, strength of the steel material may be lowered.
- In addition, the tempering operation of the present disclosure may be carried out for a time period of 2.4 * t (where, t denotes a thickness (mm) of the steel plate) + (10 to 30 minutes) to obtain a sufficient tempering effect. For reference, in the steel plate manufacturing process, when 2.4 * t is set as a heating time period, and a target temperature is reached, 10 to 30 minutes may be set as a maintenance time period to perform the tempering operation.
- Hereinafter, the present disclosure will be described in more detail through examples. However, it may be necessary to note that the embodiments described below are only intended to further illustrate the present disclosure and are not intended to limit the scope of the present disclosure.
- A slab provided with the alloy composition of Table 1 below was prepared.
[Table 1] Compositi on (wt%) IS a IS b IS c CS d CS e CS f C 0.10 0.09 0.12 0.06 0.07 0.09 Mn 1.51 1.58 0.92 1.30 1.35 0.78 Al 0.02 0.03 0.032 0.035 0.030 0.032 Si 0.35 0.36 0.36 0.35 0.34 0.36 P 0.009 0.010 0.008 0.008 0.010 0.010 S 0.0010 0.0008 0.0011 0.0013 0.0014 0.0012 Cu 0.03 0.04 0.03 0.05 - - Ni 0.50 0.55 0.53 0.05 0.15 0.10 Cr 0.05 0.05 0.06 0.03 0.05 0.04 Mo 0.15 0.18 0.17 0.15 0.10 0.16 V 0.030 0.025 0.030 0.003 0.005 0.030 Nb 0.012 0.014 0.013 0.013 0.012 0.015 B - - - 0.0015 0.0012 0.0007 Ti 0.012 0.010 0.013 0.013 0.012 0.013 N 0.0028 0.0035 0.0034 0.0028 0.0035 0.0032 Ca 0.0020 0.0019 0.0021 0.0018 0.0021 0.0020 IS: Inventive Steel, CS: Comparative Steel - Test pieces were prepared by performing a reheating operation, a recrystallization control rolling operation, an austenizing operation, a quenching operation, and a tempering operation using respective slabs made of the compositions of Inventive Steel and Comparative Steel, as illustrated in Table 2 below. Properties such as strength, low-temperature toughness, and nil-ductility transition temperature were evaluated, and the results therefrom are illustrated in Table 3 below. In Table 3 below, the low-temperature impact toughness may be evaluated as a Charpy impact energy value obtained by performing a Charpy impact test on a specimen having a V notch at -60°C. In addition, the nil-ductility transition temperature may be a result value according to the drop-weight test transition temperature set by the ASTM E208-06 method.
[Table 2] Condition Steel Plate Thickness (mm) Slab Reheatin g Temp. (°C) Rolling Temp. (°C) Recrystallization Control Rolling Cumulative Reduction Amount (%) Grain Aspect Ratio* Austenizing Temp. (°C) Tempering Temp. (°C) IS a a-1 45 1200 780 60 1.75 900 680 a-2 80 1180 780 55 1.95 920 660 a-3 100 1100 790 50 1.25 910 650 a-4 50 1100 790 45 1.01 910 660 IS b b-1 45 1150 780 70 2.15 910 680 b-2 80 1100 780 60 2.00 920 660 b-3 100 1100 790 55 1.65 900 650 IS c C 50 1150 780 75 1.98 900 660 CS d d-1 45 1200 780 20 1.02 920** 680 d-2 100 1150 790 30 1.05 900** 650 CS e E 100 1100 780 40 1.06 900** 650 CS f f 80 1150 790 55 1.03 900 650 IS: Inventive Steel, CS: Comparative Steel
* Grain aspect ratio: Long grain/short grain
** Quenching temperatures of Comparative Steel are normalizing temperatures[Table 3] Condit ion Tempered Martensite Structural Fraction (%) Tempered Bainite Structural Fraction (%) YS (MPa) TS (MPa) -60°C Impact Toughne ss (J)*** NDT Transition Temp. (°C)**** IS a a-1 56 44 634 649 334 -80 IE 1 a-2 51 49 641 641 324 -70 IE 2 a-3 48 52 628 634 313 -65 IE 3 a-4 62 38 580 701 58 -40 CE 1 IS b b-1 58 42 642 660 324 -85 IE 4 b-2 50 50 648 652 318 -70 IE 5 b-3 45 55 634 635 334 -70 IE 6 IS c C 55 45 542 650 320 -80 IE 7 CS d d-1 85 15 370 639 180 -40 CE 2 d-2 80 20 365 630 172 -45 CE 3 CS e E 82 18 358 630 193 -40 CE 4 CS f F 85 15 443 650 140 -30 CE 5 IE: Inventive Example, CE: Comparative Example, IS: Inventive Steel, CS: Comparative Steel
*** Impact toughness: impact toughness in a T direction (having a V-notch in a direction, perpendicular to a rolling direction)
**** NDT transition temperature: transition temperature of the drop-weight test conducted by the ASTM208-06 method. - As in the results of Tables 2 and 3, it can be seen that Inventive Examples 1 to 7 have microstructures of 30 to 60% of tempered martensite and 40 to 70% of tempered bainite, and secure a tensile strength of 600 MPa or more, an impact toughness of 300 J or more at -60°C, and a nil-ductility transition temperature property of -50°C or lower.
- In a case of Comparative Example 1, it can be seen that, since a steel composition satisfies the defined steel composition of the present disclosure, but a cumulative reduction amount of a recrystallization control rolling operation does not satisfy the defined scope of the present disclosure, the area fractions of a microstructure defined by the present disclosure are not satisfied, and a nil-ductility transition temperature property at -50°C or lower is, thus, not secured.
- In addition, in cases of Comparative Examples 2 to 5, it can be seen that, since steel compositions do not satisfy the defined steel composition of the present disclosure, a microstructure has 80 area% or more of tempered martensite and 20 area% or less of tempered bainite, and tensile strength, impact toughness, and nil-ductility transition temperature properties are degraded.
- Therefore, since a steel plate according to an embodiment of the present disclosure may control a steel composition, a microstructure, and manufacturing operations under optimal conditions, to secure tensile strength of 600 MPa or more, Charpy impact toughness of 300 J or more at -60°C, and a nil-ductility transition temperature of -50°C or lower, a high strength steel plate having properties suitable for a nuclear reactor containment vessel may be provided.
- While example embodiments have been illustrated and described above, it will be apparent to those skilled in the art that modifications and variations could be made without departing from the scope of the present disclosure as defined by the appended claims.
Claims (6)
- A high strength steel plate comprising, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfying relationships of Cu + Ni + Cr + Mo: 1.5% or less, Cr + Mo: 0.4% or less, V + Nb: 0.1% or less, and Ca/S: 1.0 or higher, and comprising a microstructure of 30 to 60 area% of tempered martensite and 40 to 70 area% of tempered bainite, wherein the sum of the tempered martensite and the tempered bainite is 100 area%, wherein a grain aspect ratio as defined herein of the microstructure is 1.1 to 2.5,
wherein Charpy impact toughness of the steel plate is 300J or more at -60°C, and wherein the low-temperature impact toughness is evaluated as a Charpy impact energy value obtained by performing a Charpy impact test on a specimen having a V notch at -60°C , and wherein the tensile strength of the steel plate is 600 MPa or more. - The high strength steel plate according to claim 1, wherein the tempered martensite comprises 40 to 60 area% in the microstructure, and the tempered bainite comprises 40 to 60 area% in the microstructure.
- The high strength steel plate according to any one of claims 1 to 3, wherein a nil-ductility transition temperature of the steel plate is -50°C or lower and wherein the nil-ductility transition temperature is a result value according to the drop-weight test transition temperature set by the ASTM E208-06 method.
- A method of manufacturing a high strength steel plate, comprising:reheating a steel slab at 1050 to 1250°C, the steel slab comprising, by weight: 0.05 to 0.20% of C, 0.15 to 0.55% of Si, 0.9 to 1.75% of Mn, 0.001 to 0.05% of Al, 0.03% or less of P, 0.03% or less of S, 0.05 to 0.3% of Cr, 0.05 to 0.6% of Ni, 0.005 to 0.35% of Cu, 0.05 to 0.2% of Mo, 0.005 to 0.07% of V, 0.005 to 0.04% of Nb, 0.0005 to 0.005% of Ca, 0.005 to 0.025% of Ti, 0.002 to 0.006% of N, less than 0.0005% of B, and a balance of Fe, with inevitable impurities, satisfying relationships of Cu + Ni + Cr + Mo: 1.5% or less, Cr + Mo: 0.4% or less, V + Nb: 0.1% or less, and Ca/S: 1.0 or higher,rolling the slab in a temperature range of Tnr to Tnr + 100°C, wherein Tnr is determined in accordance with Equation 1 hereof and a unit of each alloy element is weight%, to provide a steel plate,austenizing the steel plate in a temperature range of 870 to 950°C,quenching the austenized steel plate to a temperature range of 300°C or lower, and tempering the quenched steel plate in a temperature range of 595 to 700°C, wherein a cumulative reduction amount of the rolling is 50 to 90%, and wherein a grain aspect ratio as defined herein of a microstructure of the steel plate by the rolling is controlled to have a range of 1.1 to 2.5,
- The method according to claim 4, wherein the austenizing is performed for a time period of 1.6 * t +(10 to 30 minutes) wherein t denotes a thickness in mm of the steel plate.
- The method according to claim 4, wherein the tempering is performed for a time period of 2.4 * t + (10 to 30 minutes) , wherein t denotes a thickness in mm of the steel plate.
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KR100833069B1 (en) * | 2006-12-13 | 2008-05-27 | 주식회사 포스코 | Steel plate for pressure vessel with ts 500mpa grade and excellent hic resistance and haz toughness and manufacturing method thereof |
KR101091306B1 (en) | 2008-12-26 | 2011-12-07 | 주식회사 포스코 | High Strength Steel Plate for Containment Vessel of Atomic Plant and Manufacturing Method Thereof |
CN101962741B (en) * | 2009-07-24 | 2012-08-08 | 宝山钢铁股份有限公司 | Quenched and tempered steel sheet and manufacturing method thereof |
KR101271990B1 (en) * | 2009-12-01 | 2013-06-05 | 주식회사 포스코 | High strength steel sheet and method for manufacturing the same |
CN103320701B (en) * | 2012-03-23 | 2016-08-03 | 宝山钢铁股份有限公司 | A kind of ferrite-bainite AHSS plate and manufacture method thereof |
JP5605527B2 (en) * | 2012-09-13 | 2014-10-15 | Jfeスチール株式会社 | Hot-rolled steel sheet and manufacturing method thereof |
WO2014162680A1 (en) * | 2013-04-04 | 2014-10-09 | Jfeスチール株式会社 | Hot-rolled steel sheet and method for manufacturing same |
JP5928405B2 (en) * | 2013-05-09 | 2016-06-01 | Jfeスチール株式会社 | Tempered steel sheet excellent in resistance to hydrogen-induced cracking and method for producing the same |
JP6132017B2 (en) * | 2013-05-14 | 2017-05-24 | 新日鐵住金株式会社 | Hot-rolled steel sheet and manufacturing method thereof |
JP6253974B2 (en) * | 2013-12-27 | 2017-12-27 | Jfeスチール株式会社 | Thick steel plate for reactor containment vessel with excellent brittle crack propagation stopping characteristics |
KR20150101735A (en) * | 2014-02-27 | 2015-09-04 | 현대제철 주식회사 | Steel sheet and method of manufacturing the same |
KR101657823B1 (en) * | 2014-12-24 | 2016-09-20 | 주식회사 포스코 | Steel having excellent low temperature toughness and hydrogen induced cracking resistance and manufacturing method thereof |
CN107406948B (en) * | 2015-03-26 | 2019-03-08 | 杰富意钢铁株式会社 | The manufacturing method and structural tube of the effective thick steel sheet of structure, the effective thick steel sheet of structure |
WO2019058422A1 (en) * | 2017-09-19 | 2019-03-28 | 新日鐵住金株式会社 | Steel tube and steel sheet |
-
2017
- 2017-12-24 KR KR1020170178924A patent/KR102031450B1/en active IP Right Grant
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2018
- 2018-11-28 US US16/957,021 patent/US20200347478A1/en active Pending
- 2018-11-28 WO PCT/KR2018/014855 patent/WO2019124793A1/en unknown
- 2018-11-28 EP EP18891912.0A patent/EP3730655B1/en active Active
- 2018-11-28 CN CN201880082338.2A patent/CN111566249B/en active Active
- 2018-11-28 JP JP2020535011A patent/JP7096337B2/en active Active
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WO2019124793A1 (en) | 2019-06-27 |
EP3730655A4 (en) | 2020-10-28 |
EP3730655A1 (en) | 2020-10-28 |
KR102031450B1 (en) | 2019-10-11 |
US20200347478A1 (en) | 2020-11-05 |
CN111566249A (en) | 2020-08-21 |
JP2021508774A (en) | 2021-03-11 |
JP7096337B2 (en) | 2022-07-05 |
CN111566249B (en) | 2022-05-13 |
KR20190077177A (en) | 2019-07-03 |
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