EP3392367A1 - High-strength steel material having excellent low-temperature strain aging impact properties and method for manufacturing same - Google Patents
High-strength steel material having excellent low-temperature strain aging impact properties and method for manufacturing same Download PDFInfo
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- EP3392367A1 EP3392367A1 EP16876051.0A EP16876051A EP3392367A1 EP 3392367 A1 EP3392367 A1 EP 3392367A1 EP 16876051 A EP16876051 A EP 16876051A EP 3392367 A1 EP3392367 A1 EP 3392367A1
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 98
- 239000010959 steel Substances 0.000 title claims abstract description 98
- 239000000463 material Substances 0.000 title claims abstract description 59
- 230000032683 aging Effects 0.000 title claims abstract description 32
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 23
- 238000000034 method Methods 0.000 title claims abstract description 16
- 239000010955 niobium Substances 0.000 claims abstract description 32
- 239000010936 titanium Substances 0.000 claims abstract description 24
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 23
- 239000011572 manganese Substances 0.000 claims abstract description 19
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 18
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 17
- 239000011575 calcium Substances 0.000 claims abstract description 16
- 239000010949 copper Substances 0.000 claims abstract description 16
- 239000011651 chromium Substances 0.000 claims abstract description 15
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 11
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 11
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 11
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 10
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 9
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 8
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 8
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 8
- 239000011733 molybdenum Substances 0.000 claims abstract description 8
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 7
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims abstract description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims abstract description 7
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 7
- 239000012535 impurity Substances 0.000 claims abstract description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 7
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 7
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 7
- 239000010703 silicon Substances 0.000 claims abstract description 7
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims abstract description 7
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims abstract description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 6
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 6
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims abstract description 6
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 6
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 6
- 229910052802 copper Inorganic materials 0.000 claims abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 6
- 239000011574 phosphorus Substances 0.000 claims abstract description 6
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 6
- 239000011593 sulfur Substances 0.000 claims abstract description 6
- 239000002131 composite material Substances 0.000 claims abstract description 5
- 238000005096 rolling process Methods 0.000 claims description 22
- 238000010438 heat treatment Methods 0.000 claims description 18
- 238000001816 cooling Methods 0.000 claims description 17
- 238000003303 reheating Methods 0.000 claims description 12
- 239000013078 crystal Substances 0.000 claims description 10
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 230000000694 effects Effects 0.000 description 21
- 230000000052 comparative effect Effects 0.000 description 8
- 239000000203 mixture Substances 0.000 description 8
- 239000007787 solid Substances 0.000 description 7
- 230000007928 solubilization Effects 0.000 description 7
- 238000005063 solubilization Methods 0.000 description 7
- 230000003247 decreasing effect Effects 0.000 description 6
- 239000002244 precipitate Substances 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 230000000704 physical effect Effects 0.000 description 5
- 230000007704 transition Effects 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- 230000000977 initiatory effect Effects 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 238000007670 refining Methods 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 238000003466 welding Methods 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 230000002542 deteriorative effect Effects 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 229910001567 cementite Inorganic materials 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000005065 mining Methods 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 241000446313 Lamella Species 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052593 corundum Inorganic materials 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000006477 desulfuration reaction Methods 0.000 description 1
- 230000023556 desulfurization Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000000605 extraction Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 229910001845 yogo sapphire Inorganic materials 0.000 description 1
Images
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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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
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- 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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- 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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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
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- 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
- C21D2211/005—Ferrite
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- 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
- C21D2211/009—Pearlite
Definitions
- the present disclosure relates to a steel material used as a material for pressure vessels, offshore structures and the like, and more particularly, to a high-strength steel material having excellent low-temperature strain aging impact properties, and a method for manufacturing the same.
- the steel material is required to significantly avoid a decrease in toughness due to strain aging by cold deformation.
- the mechanism of decreased toughness due to strain aging is as follows: The toughness of a steel material measured by a Charpy impact test is explained by a correlation between yield strength and fracture strength at the test temperature; and when the yield strength of a steel material at the test temperature is higher than the fracture strength, the steel material undergoes brittle fracture without ductile fracture, so that an impact energy value is lowered, but when the yield strength is lower than the fracture strength, the steel material is deformed to be ductile, thereby absorbing impact energy during work hardening, and being changed to undergo brittle fracture when the yield strength reaches fracture strength.
- the yield strength of the steel material is increased as deformation continues, and thus, the difference from the fracture strength becomes smaller, accompanied by decreased impact toughness.
- an element e.g., titanium (Ti), vanadium (V), etc.
- An aspect of the present disclosure is to provide a steel material which may not only secure high strength and high toughness, but may also significantly avoid a strength decrease due to cold deformation, thereby being appropriately applied as a material of pressure vessels, offshore structures and the like, and a method for manufacturing the same.
- a high-strength steel material having excellent low-temperature strain aging impact properties includes 0.04-0.14 wt% of carbon (C), 0.05-0.60 wt% of silicon (Si), 0.6-1.8 wt% of manganese (Mn), 0.005-0.06 wt% of soluble aluminum (sol.
- MA martensite-austenite
- a method for manufacturing a high-strength steel material having low-temperature strain aging impact properties includes reheating a steel slab satisfying the above-described component composition to a temperature within a range of 1080-1250°C; controlled-rolling the reheated slab to a rolling finish temperature of 780°C or more, thereby manufacturing a hot-rolled steel plate; cooling the hot-rolled steel plate by air cooling or water cooling; and after the cooling, subjecting the hot-rolled steel plate to normalizing heat treatment in a temperature range of 850-960°C.
- a heat-treated steel material having excellent low-temperature stain aging impact properties, simultaneously with high strength may be provided, and the steel material may be appropriately applied as a material for pressure vessels, offshore structures and the like, following a trend of being larger and more complicated.
- FIG. 1 is a graph representing lower yield strength and tensile strength in a tensile curve of a steel material according to an aspect of the present disclosure.
- the present inventors conducted an intensive study on the development of a steel material which may prevent a toughness decrease of the steel material by strain aging, while having high strength and high toughness, and as a result, confirmed that a steel material having a microstructure advantageous for securing the above-described physical properties from optimization of a steel component composition and manufacturing conditions may be provided, thereby completing the present disclosure.
- the steel material of the present disclosure may effectively prevent a toughness decrease by strain aging by optimizing the contents of the elements having an influence on MA phase formation in the steel component composition to significantly decrease the MA phase (martensite-austenite composite phase).
- the high-strength steel material having excellent low-temperature strain aging impact properties includes 0.04-0.14 wt% of carbon (C), 0.05-0.60 wt% of silicon (Si), 0.6-1.8 wt% of manganese (Mn), 0.005-0.06 wt% of soluble aluminum (sol.
- the content of each component refers to wt%.
- Carbon (C) an element advantageous for securing strength of a steel is bonded to pearlite or niobium (Nb), nitrogen (N) and the like to exist as carbonitrides, and thus, is a main element for securing tensile strength. It is not preferable that the content of this C is less than 0.04%, since the tensile strength on a matrix may be lowered, and when the content is more than 0.14%, pearlite may be excessively produced, so that low-temperature strain aging impact properties may be deteriorated.
- the content of C be limited to 0.04-0.14%.
- Silicon (Si) an element added for a deoxidation and desulfurization effect of a steel, and also for solid solution strengthening is add preferably at 0.05% or more for securing yield strength and tensile strength.
- the content of silicon is more than 0.60%, since weldability and low-temperature impact properties are lowered, and a steel surface is easily oxidized so that an oxide film may be severely formed.
- the content of Si is limited to 0.05-0.60%.
- Mn manganese
- MnS manganese
- the content of Mn is limited to 0.6-1.8%.
- Soluble aluminum (sol. Al) is used as a strong deoxidizing agent in a steel manufacturing process together with Si, and it is preferable to add at least of 0.005% of sol. Al in deoxidation alone or in combination.
- the content is more than 0.06%, the above-described effect is saturated, and the fraction of Al 2 O 3 in the oxidative inclusion produced as a resultant product of deoxidation is increased more than necessary, and the size is larger.
- the content of Sol. Al is limited to 0.005-0.06%.
- Niobium (Nb) has a large effect of being solid-solubilized in austenite when reheating a slab, thereby increasing hardenability of austenite, and being precipitated as fine carbonitrides (Nb,Ti) (C,N) upon hot rolling, thereby suppressing recrystallization during rolling or cooling to allow a final microstructure to be finely formed.
- the content is more than 0.05%, since it is easy to form excessive MA, or a coarse precipitate in the center in the thickness direction, thereby deteriorating low-temperature toughness in the center of the steel.
- the content of Nb is limited to 0.005-0.05%, more advantageously 0.02% or more, still more advantageously 0.022% or more.
- V 0.01% or less (exclusive of 0%)
- V Vanadium
- V is almost all solid-solubilized again when heating a slab, and thus, there is little effect of strength increase by precipitation or solid solubilization after rolling, normalizing heat treatment.
- V is an expensive element, and causes cost increase when adding it in a large amount, and thus, considering this, it is preferable to add 0.01% or less of V.
- Titanium (Ti) is present as a hexagonal precipitate mainly in the form of TiN at high temperature, or forms carbonitride (Nb,Ti) (C,N) precipitates with Nb and the like to suppress crystal grain growth in the welding heat-affected zone.
- Nb,Ti carbonitride
- C,N carbonitride precipitates with Nb and the like to suppress crystal grain growth in the welding heat-affected zone.
- it is preferable to add 0.001% or more of Ti when the content is excessive and more than 0.015%, coarse TiN is formed in the center of the steel in the thickness direction, which serves as a fracture crack initiation point, thereby greatly reducing strain aging impact properties.
- the content of Ti is limited to 0.001-0.015%.
- Copper (Cu) has an effect of greatly improve strength by solid solubilization and precipitation, and not greatly affecting strain aging impact properties, however, when excessively added, causes cracks on a steel surface, and is an expensive element, and thus, considering this, it is preferable to limit the content to 0.01-0.4%.
- Nickel (Ni) has little strength increase effect, however, is effective in improving low-temperature strain aging impact properties, and in particular, when adding Cu, has an effect of suppressing a surface crack by selective oxidation which occurs upon reheating a slab. For this, it is preferable to add 0.01% or more of Ni, however, considering the economic efficiency due to a high price, it is preferable to limit the content to 0.6% or less.
- Chromium (Cr) has a small effect of increasing yield strength and tensile strength by solid solubilization, however, slows down a cementite decomposition rate during heat treatment after welding or tempering, thereby preventing drop in strength .
- Molybdenum has an effect of delaying transformation in the course of cooling after heat treatment, resulting in a large increase in strength, and also, being effective in preventing drop in strength during heat treatment after welding or tempering like Cr, and preventing toughness decrease by grain boundary segregation of impurities such as P.
- it is preferable to add 0.001% or more of molybdenum however, it is also economically disadvantageous to excessively add molybdenum, an expensive element, and thus, it is preferable to limit the content to 0.3% or less.
- the content of Ca is limited to 0.0002-0.0040%.
- Nitrogen (N) has an effect of being bonded to added Nb, Ti, Al, etc. to form a precipitate, thereby refining the crystal grains of the steel to improve the strength and toughness of a base metal, however, when the content is excessive, precipitates are formed, and remaining N exists in an atom state to cause aging after cold deformation. Thus, nitrogen is known as a representative element to decrease low-temperature toughness therefrom. In addition, when manufacturing a slab by continuous casting, surface cracks are promoted by embrittlement at high temperature.
- the content of N is limited to 0.001-0.006%.
- Phosphorus (P) has an effect of increasing strength when added, however, in the heat-treated steel of the present disclosure, is an element which significantly impairs low-temperature toughness by grain boundary segregation, as compared with the effect of increasing strength, and thus, it is preferable to keep the content of P as low as possible. However, since a significant cost is required to excessively remove P in a steel manufacturing process, it is preferable to limit the content to the range not affecting the physical properties, i.e., 0.02% or less.
- S Sulfur
- MnS Sulfur
- the remaining component of the present disclosure is iron (Fe).
- Fe iron
- unintended impurities may be inevitably incorporated from raw materials or the surrounding environment, they may not be excluded. Since these impurities are known to any person skilled in the common steel manufacturing process, the entire contents thereof are not particularly mentioned in the present specification.
- the high-strength steel material of the present disclosure satisfying the alloy component composition as described above includes a mixed structure of ferrite, pearlite, bainite and a MA (martensite-austenite) composite phase.
- ferrite is the most important since it allows the ductile deformation of the steel material, and it is preferable to include this ferrite as a main phase, while finely controlling the average size to 15 ⁇ m or less.
- a grain boundary may be increased to suppress crack propagation, basic toughness of a steel material may be improved, and also strength increase by an effect of lowering a work hardening rate during cold deformation may be significantly reduced, thereby improving strain aging impact properties simultaneously.
- Hard phases including the pearlite, bainite, MA and the like other than the ferrite is advantageous for securing high strength by increasing the tensile strength of a steel material, however, serves as the fracture initiation point or propagation path due to high hardness, thereby deteriorating the strain aging impact properties. Therefore, it is preferable to control the fraction, and it is also preferable to limit the sum of fractions of the hard phases to 18% or less (exclusive of 0%).
- the fraction of the MA phase may be limited preferably to 3.5% or less (exclusive of 0%), and more preferably to 1.0-3.5%.
- the high-strength steel material of the present disclosure having the microstructure as described above includes carbonitrides produced by Nb, Ti, Al, etc., among the added elements, and the carbonitrides plays an important role in inhibiting crystal grain growth in the course of rolling, cooling and heat treatment to allow the grains to be fine.
- a steel slab satisfying the above-described alloy component alloy is manufactured, and then in order to obtain a steel material satisfying a microstructure, carbide conditions and the like aimed in the present disclosure, hot rolling (controlled rolling), cooling and normalizing heat treatment are performed.
- the manufactured steel slab Prior to this, it is preferable to subject the manufactured steel slab to a reheating process.
- the reheating temperature is controlled to 1080-1250°C, and when the reheating temperature is less than 1080°C, re-solid solubilization of carbides produced in the slab during continuous casting is difficult. Therefore, it is preferable to perform reheating to at least a temperature at which 50% or more of added Nb may be solid-solubilized again.
- the temperature is more than 1250°C, the size of austenite crystal grains is unduly large, so that the mechanical physical properties such as strength and toughness of the finally manufactured steel material are greatly deteriorated.
- the reheating temperature is limited to 1080-1250°C.
- the hot-rolled steel plate by finish rolling of the reheated steel slab as described above.
- the finish rolling process is preferably controlled rolling, and it is preferable that the rolling end temperature is controlled to 780°C or more.
- the rolling end temperature is about 820-1000°C, however, when this is lowered to less than 780°C, the quenching property is lowered in the region in which Mn and the like are not segregated during rolling, thereby producing ferrite during rolling, and as the ferrite is produced as such, solid-solubilized C and the like are segregated into remaining austenite region and concentrated. Accordingly, the region in which C and the like are concentrated during cooling after rolling is transformed into bainite, martensite or a MA phase, thereby producing a strong layered structure formed of ferrite and a hardened structure.
- the hardened structure of the layer in which C and the like are concentrated has high hardness and also a greatly increased fraction of the MA phase. As such, since low-temperature toughness is decreased by an increase of hardened structure and arrangement of a layered structure, it is preferable to control the rolled end temperature to 780°C or more.
- the hot-rolled steel plate obtained by controlled rolling according to the above is cooled by air cooling or water cooling, and then is subject to normalizing heat treatment in a constant temperature range, thereby manufacturing a steel material having the desired physical properties.
- the normalizing heat treatment is performed by maintaining in a temperature range of 850-960°C for a certain period of time, and then cooling in the air.
- the normalizing heat treatment temperature is less than 850°C, the re-solid solubilization of cementite and a MA phase in pearlite and bainite is difficult to decrease the solid-solubilized C, so that it is difficult to secure strength, and also, a finally remaining hardened phase remains coarse, thereby significantly impairing strain aging impact properties.
- the temperature is more than 960°C, crystal grain growth occurs to deteriorate the strain aging impact properties.
- the high-strength steel material obtained according to the above has excellent strength and toughness, and also, may effectively prevent toughness decrease by strain aging upon cold deformation.
- a yield ratio (YS (lower yield strength)/TS (tensile strength)) after heat treatment of 0.65-0.80 may be secured.
- the steel slabs having the component composition shown in the following Table 1 were subjected to reheating, hot rolling and normalizing heat treatment under the conditions shown in the following Table 2, thereby manufacturing hot-rolled steel plates having a final thickness of 6 mm or more.
- the microstructure fraction, size and carbonitride fraction of each of the manufactured hot-rolled steel plates were measured.
- a Charpy impact transition temperature was measured in the state of being aged at 250°C for 1 hour after 5% stretching of a cold deformation amount, which may represent strength (tensile strength and lower yield strength) and strain aging impact properties of each hot-rolled steel plate, and represented in the following Table 3.
- the steel plate section was polished with a mirror surface, and etched with Nital or Lepera as desired, thereby measuring an image for a certain area of a specimen at 100-500X magnification with an optical or scanning electron microscope, and then the fraction of each image was measured from the measured images using an image analyzer. In order to obtain a statistically significant value, the measurement was repeated for the same specimen but at the changed position, and the average value was calculated.
- the fraction of the fine carbonitrides having an average size of 300 mm or less was measured by an extraction residue method.
- tensile property values lower yield strength, tensile strength and a yield ratio (lower yield strength/tensile strength) were measured, respectively from a nominal strain-nominal stress curve obtained by a common tensile test, and a strain aging impact property value was measured by adding 0%, 5% and 8% in advance as a tensile strain, aging a stretched specimen at 250°C for 1 hour, and then performing a Charpy V-notch impact test.
- 'F fraction' refers to a ferrite fraction
- 'F size' refers to an average size of ferrite crystal grains
- the represented hardened phase fraction (%) includes the carbonitride fraction (%).
- the hot-rolled steel plate satisfying all of the component composition and manufacturing conditions of the present disclosure has high strength, and also secures excellent low-temperature toughness even after cold deformation, thereby being appropriately used in pressure vessels, offshore structures and the like, following a trend of being larger and more complicated.
- Comparative Example 5 in which the content of Ti is excessive, Ti which was excessively added as compared with added N was produced as a coarse TiN precipitate, and when impacted after 5% cold deformation, served as an initiation point of cracks, resulting in a higher impact transition temperature.
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Abstract
Description
- The present disclosure relates to a steel material used as a material for pressure vessels, offshore structures and the like, and more particularly, to a high-strength steel material having excellent low-temperature strain aging impact properties, and a method for manufacturing the same.
- Recently, mining areas have moved to deep-sea areas or areas of extreme cold due to the exhaustion of energy resources, and thus, mining and storage facilities are becoming larger and more complicated. Steel materials used therein are required to have excellent low-temperature toughness for securing high strength and facility stability for reducing weight.
- Meanwhile, since cold deformation often occurs in the course of manufacturing a steel material having strength and toughness as described above to form a steel pipe or other complicated structures, the steel material is required to significantly avoid a decrease in toughness due to strain aging by cold deformation.
- The mechanism of decreased toughness due to strain aging is as follows: The toughness of a steel material measured by a Charpy impact test is explained by a correlation between yield strength and fracture strength at the test temperature; and when the yield strength of a steel material at the test temperature is higher than the fracture strength, the steel material undergoes brittle fracture without ductile fracture, so that an impact energy value is lowered, but when the yield strength is lower than the fracture strength, the steel material is deformed to be ductile, thereby absorbing impact energy during work hardening, and being changed to undergo brittle fracture when the yield strength reaches fracture strength. That is, as the difference between the yield strength and the fracture strength is larger, the amount of the steel material deformed to be ductile is increased, so that the impact energy to be absorbed is increased. Therefore, when subjecting the steel material to cold deformation for manufacturing to form a steel pipe or other complicated structure, the yield strength of the steel material is increased as deformation continues, and thus, the difference from the fracture strength becomes smaller, accompanied by decreased impact toughness.
- Thus, in order to prevent decreased toughness by cold deformation, conventionally, a method of significantly decreasing the amount of carbon (C) or nitrogen (N) employed in the steel material, or adding an element (e.g., titanium (Ti), vanadium (V), etc.) to precipitate those elements at a minimum amount or more, for suppressing strength increase by an aging phenomenon after deformation, a method of performing SR (stress relief) heat treatment after cold deformation to decrease dislocation and the like produced in the steel material, thereby lowering the yield strength increased by work hardening, a method of adding an element (e.g., nickel (Ni), etc.) to lower stacking fault energy to facilitate the movement of dislocations, for increasing ductility of the steel material at low temperature, and the like have been suggested, and applied.
- However, as structures and the like are continuously becoming larger and more complicated, the cold deformation amount required for the steel material is increased, and also the temperature of a use environment is lowered to the level of arctic sea temperature. Thus, it is difficult to effectively prevent toughness decrease by strain aging of the steel material, with conventional methods.
- (Non-patent document 1) Effect of Ti addition on strain aging of low-carbon steel wire rod (Ikuo Ochiai, Hiroshi Ohba, Iron and Steel, Volume 75 (1989), issue 4, p. 642-) (Non-patent document 2) The effect of processing variables on the mechanical properties and strain ageing of high-strength low-alloy V and V-N steels (V. K. Heikkinen and J. D. Boyd, CANADIAN METALLURGICAL QUARTERLY Volume 15 Number 3 (1976), p. 219-)
- An aspect of the present disclosure is to provide a steel material which may not only secure high strength and high toughness, but may also significantly avoid a strength decrease due to cold deformation, thereby being appropriately applied as a material of pressure vessels, offshore structures and the like, and a method for manufacturing the same.
- According to an aspect of the present disclosure, a high-strength steel material having excellent low-temperature strain aging impact properties includes 0.04-0.14 wt% of carbon (C), 0.05-0.60 wt% of silicon (Si), 0.6-1.8 wt% of manganese (Mn), 0.005-0.06 wt% of soluble aluminum (sol. Al), 0.005-0.05 wt% of niobium (Nb), 0.01 wt% or less (exclusive of 0 wt%) of vanadium (V), 0.001-0.015 wt% of titanium (Ti), 0.01-0.4 wt% of copper (Cu), 0.01-0.6 wt% of nickel (Ni), 0.01-0.2 wt% of chromium (Cr), 0.001-0.3 wt% of molybdenum (Mo), 0.0002-0.0040 wt% of calcium (Ca), 0.001-0.006 wt% of nitrogen (N), 0.02 wt% or less (exclusive of 0 wt%) of phosphorus (P), and 0.003 wt% or less (exclusive of 0 wt%) of sulfur (S), with a balance of Fe and other inevitable impurities, and
- includes a mixed structure of ferrite, pearlite, bainite and a martensite-austenite (MA) composite phase as a microstructure, wherein a fraction of the MA phase is 3.5% or less (exclusive of 0%).
- According to another aspect of the present disclosure, a method for manufacturing a high-strength steel material having low-temperature strain aging impact properties includes reheating a steel slab satisfying the above-described component composition to a temperature within a range of 1080-1250°C; controlled-rolling the reheated slab to a rolling finish temperature of 780°C or more, thereby manufacturing a hot-rolled steel plate; cooling the hot-rolled steel plate by air cooling or water cooling; and after the cooling, subjecting the hot-rolled steel plate to normalizing heat treatment in a temperature range of 850-960°C.
- As set forth above, according to an exemplary embodiment in the present disclosure, a heat-treated steel material having excellent low-temperature stain aging impact properties, simultaneously with high strength may be provided, and the steel material may be appropriately applied as a material for pressure vessels, offshore structures and the like, following a trend of being larger and more complicated.
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FIG. 1 is a graph representing lower yield strength and tensile strength in a tensile curve of a steel material according to an aspect of the present disclosure. - As the cold deformation amount for the steel material used as a material for pressure vessels, offshore structures and the like is continuously increased, the present inventors conducted an intensive study on the development of a steel material which may prevent a toughness decrease of the steel material by strain aging, while having high strength and high toughness, and as a result, confirmed that a steel material having a microstructure advantageous for securing the above-described physical properties from optimization of a steel component composition and manufacturing conditions may be provided, thereby completing the present disclosure.
- In particular, the steel material of the present disclosure may effectively prevent a toughness decrease by strain aging by optimizing the contents of the elements having an influence on MA phase formation in the steel component composition to significantly decrease the MA phase (martensite-austenite composite phase).
- Hereinafter, the present disclosure will be described in detail.
- It is preferable that the high-strength steel material having excellent low-temperature strain aging impact properties according to an aspect of the present disclosure includes 0.04-0.14 wt% of carbon (C), 0.05-0.60 wt% of silicon (Si), 0.6-1.8 wt% of manganese (Mn), 0.005-0.06 wt% of soluble aluminum (sol. Al), 0.005-0.05 wt% of niobium (Nb), 0.01 wt% or less (exclusive of 0 wt%) of vanadium (V), 0.001-0.015 wt% of titanium (Ti), 0.01-0.4 wt% of copper (Cu), 0.01-0.6 wt% of nickel (Ni), 0.01-0.2 wt% of chromium (Cr), 0.001-0.3 wt% of molybdenum (Mo), 0.0002-0.0040 wt% of calcium (Ca), 0.001-0.006 wt% of nitrogen (N), 0.02 wt% or less (exclusive of 0 wt%) of phosphorus (P), and 0.003 wt% or less (exclusive of 0 wt%) of sulfur (S).
- Hereinafter, the reason why the alloy components of the high-strength steel material provided by the present disclosure are controlled as described above will be described in detail. Herein, unless otherwise stated, the content of each component refers to wt%.
- Carbon (C), an element advantageous for securing strength of a steel is bonded to pearlite or niobium (Nb), nitrogen (N) and the like to exist as carbonitrides, and thus, is a main element for securing tensile strength. It is not preferable that the content of this C is less than 0.04%, since the tensile strength on a matrix may be lowered, and when the content is more than 0.14%, pearlite may be excessively produced, so that low-temperature strain aging impact properties may be deteriorated.
- Therefore, it is preferable in the present disclosure that the content of C be limited to 0.04-0.14%.
- Silicon (Si), an element added for a deoxidation and desulfurization effect of a steel, and also for solid solution strengthening is add preferably at 0.05% or more for securing yield strength and tensile strength. However, it is not preferable that the content of silicon is more than 0.60%, since weldability and low-temperature impact properties are lowered, and a steel surface is easily oxidized so that an oxide film may be severely formed.
- Therefore, it is preferable in the present disclosure that the content of Si is limited to 0.05-0.60%.
- It is preferable that manganese (Mn) is added at 0.6% or more, since manganese has a large effect on strength increase by solid solution strengthening. However, when the content of Mn is excessive, segregation becomes severe in the center of a steel plate in the thickness direction, and at the same time formation of MnS, a nonmetallic inclusion, is encouraged, together with segregated S. The MnS inclusion produced in the center is stretched by rolling, and as a result, significantly deteriorates low-temperature toughness and lamella tear resistant properties, and thus, it is preferable to limit the content of Mn to 1.8% or less.
- Therefore, it is preferable in the present disclosure that the content of Mn is limited to 0.6-1.8%.
- Soluble aluminum (sol. Al) is used as a strong deoxidizing agent in a steel manufacturing process together with Si, and it is preferable to add at least of 0.005% of sol. Al in deoxidation alone or in combination. However, when the content is more than 0.06%, the above-described effect is saturated, and the fraction of Al2O3 in the oxidative inclusion produced as a resultant product of deoxidation is increased more than necessary, and the size is larger. Thus, it is not easy to be removed during refining, resulting in significant reduction in low-temperature toughness, and thus, is not preferable.
- Therefore, it is preferable in the present disclosure that the content of Sol. Al is limited to 0.005-0.06%.
- Niobium (Nb) has a large effect of being solid-solubilized in austenite when reheating a slab, thereby increasing hardenability of austenite, and being precipitated as fine carbonitrides (Nb,Ti) (C,N) upon hot rolling, thereby suppressing recrystallization during rolling or cooling to allow a final microstructure to be finely formed. In addition, as the added amount of Nb is increased, the formation of bainite or MA is promoted to increase strength, however, it is not preferable that the content is more than 0.05%, since it is easy to form excessive MA, or a coarse precipitate in the center in the thickness direction, thereby deteriorating low-temperature toughness in the center of the steel.
- Therefore, it is preferable in the present disclosure that the content of Nb is limited to 0.005-0.05%, more advantageously 0.02% or more, still more advantageously 0.022% or more.
- Vanadium (V) is almost all solid-solubilized again when heating a slab, and thus, there is little effect of strength increase by precipitation or solid solubilization after rolling, normalizing heat treatment. In addition, V is an expensive element, and causes cost increase when adding it in a large amount, and thus, considering this, it is preferable to add 0.01% or less of V.
- Titanium (Ti) is present as a hexagonal precipitate mainly in the form of TiN at high temperature, or forms carbonitride (Nb,Ti) (C,N) precipitates with Nb and the like to suppress crystal grain growth in the welding heat-affected zone. For this, it is preferable to add 0.001% or more of Ti, however, when the content is excessive and more than 0.015%, coarse TiN is formed in the center of the steel in the thickness direction, which serves as a fracture crack initiation point, thereby greatly reducing strain aging impact properties.
- Therefore, it is preferable in the present disclosure that the content of Ti is limited to 0.001-0.015%.
- Copper (Cu) has an effect of greatly improve strength by solid solubilization and precipitation, and not greatly affecting strain aging impact properties, however, when excessively added, causes cracks on a steel surface, and is an expensive element, and thus, considering this, it is preferable to limit the content to 0.01-0.4%.
- Nickel (Ni) has little strength increase effect, however, is effective in improving low-temperature strain aging impact properties, and in particular, when adding Cu, has an effect of suppressing a surface crack by selective oxidation which occurs upon reheating a slab. For this, it is preferable to add 0.01% or more of Ni, however, considering the economic efficiency due to a high price, it is preferable to limit the content to 0.6% or less.
- Chromium (Cr) has a small effect of increasing yield strength and tensile strength by solid solubilization, however, slows down a cementite decomposition rate during heat treatment after welding or tempering, thereby preventing drop in strength . For this, it is preferable to add 0.01% or more of Cr, however, it is not preferable that the content is more than 0.2%, since the manufacturing cost rises, and also low-temperature toughness of the welding heat-affected zone is deteriorated.
- Molybdenum (Mo) has an effect of delaying transformation in the course of cooling after heat treatment, resulting in a large increase in strength, and also, being effective in preventing drop in strength during heat treatment after welding or tempering like Cr, and preventing toughness decrease by grain boundary segregation of impurities such as P. For this, it is preferable to add 0.001% or more of molybdenum, however, it is also economically disadvantageous to excessively add molybdenum, an expensive element, and thus, it is preferable to limit the content to 0.3% or less.
- When calcium (Ca) is added after Al deoxidation, Ca is bonded to S which exists as MnS to inhibit production of MnS, simultaneously with formation of globular-shaped CaS, thereby having an effect of suppressing cracks in the center of the steel material. Therefore, in order to sufficiently transform S, added in the present disclosure, into CaS, it is preferable to add 0.0002% or more. However, when the content is more than 0.0040%, remaining Ca after forming CaS is bonded to 0 to produce a coarse oxidative inclusion, stretched and fractured in rolling to serve as a crack initiation point.
- Therefore, it is preferable in the present disclosure that the content of Ca is limited to 0.0002-0.0040%.
- Nitrogen (N) has an effect of being bonded to added Nb, Ti, Al, etc. to form a precipitate, thereby refining the crystal grains of the steel to improve the strength and toughness of a base metal, however, when the content is excessive, precipitates are formed, and remaining N exists in an atom state to cause aging after cold deformation. Thus, nitrogen is known as a representative element to decrease low-temperature toughness therefrom. In addition, when manufacturing a slab by continuous casting, surface cracks are promoted by embrittlement at high temperature.
- Therefore, considering this, it is preferable in the present disclosure that the content of N is limited to 0.001-0.006%.
- Phosphorus (P) has an effect of increasing strength when added, however, in the heat-treated steel of the present disclosure, is an element which significantly impairs low-temperature toughness by grain boundary segregation, as compared with the effect of increasing strength, and thus, it is preferable to keep the content of P as low as possible. However, since a significant cost is required to excessively remove P in a steel manufacturing process, it is preferable to limit the content to the range not affecting the physical properties, i.e., 0.02% or less.
- Sulfur (S) is a representative factor bonded to Mn to produce a MnS inclusion in the center of the steel plate in the thickness direction, thereby deteriorating low-temperature toughness. Therefore, it is preferable to keep the content of S as low as possible for securing the low-temperature strain aging impact properties, however, since a significant cost is required to excessively remove this S, it is preferable to limit the content to the range not affecting the physical properties, i.e., 0.003% or less.
- The remaining component of the present disclosure is iron (Fe). However, since in the common steel manufacturing process, unintended impurities may be inevitably incorporated from raw materials or the surrounding environment, they may not be excluded. Since these impurities are known to any person skilled in the common steel manufacturing process, the entire contents thereof are not particularly mentioned in the present specification.
- It is preferable that the high-strength steel material of the present disclosure satisfying the alloy component composition as described above includes a mixed structure of ferrite, pearlite, bainite and a MA (martensite-austenite) composite phase.
- In the structure, ferrite is the most important since it allows the ductile deformation of the steel material, and it is preferable to include this ferrite as a main phase, while finely controlling the average size to 15 µm or less. As such, by refining ferrite crystal grains, a grain boundary may be increased to suppress crack propagation, basic toughness of a steel material may be improved, and also strength increase by an effect of lowering a work hardening rate during cold deformation may be significantly reduced, thereby improving strain aging impact properties simultaneously.
- Hard phases including the pearlite, bainite, MA and the like other than the ferrite is advantageous for securing high strength by increasing the tensile strength of a steel material, however, serves as the fracture initiation point or propagation path due to high hardness, thereby deteriorating the strain aging impact properties. Therefore, it is preferable to control the fraction, and it is also preferable to limit the sum of fractions of the hard phases to 18% or less (exclusive of 0%).
- In particular, since the MA phase has the highest strength, and is transformed from martensite having strong brittleness by deformation, it is an element which deteriorates the low-temperature toughness most significantly. Therefore, the fraction of the MA phase may be limited preferably to 3.5% or less (exclusive of 0%), and more preferably to 1.0-3.5%.
- Meanwhile, the high-strength steel material of the present disclosure having the microstructure as described above includes carbonitrides produced by Nb, Ti, Al, etc., among the added elements, and the carbonitrides plays an important role in inhibiting crystal grain growth in the course of rolling, cooling and heat treatment to allow the grains to be fine. In order to significantly increase the effect, it is preferable to include 0.01% or more, preferably 0.01-0.06% of the carbonitrides having an average size of 300 nm or less by weight ratio.
- Hereinafter, a method for manufacturing a high-strength steel material having excellent low-temperature strain aging impact properties, another aspect of the present disclosure will be described in detail.
- It is preferable that first, a steel slab satisfying the above-described alloy component alloy is manufactured, and then in order to obtain a steel material satisfying a microstructure, carbide conditions and the like aimed in the present disclosure, hot rolling (controlled rolling), cooling and normalizing heat treatment are performed.
- Prior to this, it is preferable to subject the manufactured steel slab to a reheating process.
- Herein, it is preferable that the reheating temperature is controlled to 1080-1250°C, and when the reheating temperature is less than 1080°C, re-solid solubilization of carbides produced in the slab during continuous casting is difficult. Therefore, it is preferable to perform reheating to at least a temperature at which 50% or more of added Nb may be solid-solubilized again. However, when the temperature is more than 1250°C, the size of austenite crystal grains is unduly large, so that the mechanical physical properties such as strength and toughness of the finally manufactured steel material are greatly deteriorated.
- Therefore, it is preferable in the present disclosure that the reheating temperature is limited to 1080-1250°C.
- It is preferable to manufacture the hot-rolled steel plate by finish rolling of the reheated steel slab as described above. Herein, the finish rolling process is preferably controlled rolling, and it is preferable that the rolling end temperature is controlled to 780°C or more.
- When rolling is performed by a common rolling process, the rolling end temperature is about 820-1000°C, however, when this is lowered to less than 780°C, the quenching property is lowered in the region in which Mn and the like are not segregated during rolling, thereby producing ferrite during rolling, and as the ferrite is produced as such, solid-solubilized C and the like are segregated into remaining austenite region and concentrated. Accordingly, the region in which C and the like are concentrated during cooling after rolling is transformed into bainite, martensite or a MA phase, thereby producing a strong layered structure formed of ferrite and a hardened structure. The hardened structure of the layer in which C and the like are concentrated has high hardness and also a greatly increased fraction of the MA phase. As such, since low-temperature toughness is decreased by an increase of hardened structure and arrangement of a layered structure, it is preferable to control the rolled end temperature to 780°C or more.
- The hot-rolled steel plate obtained by controlled rolling according to the above is cooled by air cooling or water cooling, and then is subject to normalizing heat treatment in a constant temperature range, thereby manufacturing a steel material having the desired physical properties.
- It is preferable that the normalizing heat treatment is performed by maintaining in a temperature range of 850-960°C for a certain period of time, and then cooling in the air. When the normalizing heat treatment temperature is less than 850°C, the re-solid solubilization of cementite and a MA phase in pearlite and bainite is difficult to decrease the solid-solubilized C, so that it is difficult to secure strength, and also, a finally remaining hardened phase remains coarse, thereby significantly impairing strain aging impact properties. However, when the temperature is more than 960°C, crystal grain growth occurs to deteriorate the strain aging impact properties.
- When the normalizing heat treatment is performed within the temperature range, it is preferable to maintain it for {(1.3×t)+(10-60)} minutes (wherein 't' denotes a steel material thickness (mm)), and when the maintaining time is shorter than that, the uniformity of the structure is difficult, and when the time is longer than that, productivity is deteriorated.
- The high-strength steel material obtained according to the above has excellent strength and toughness, and also, may effectively prevent toughness decrease by strain aging upon cold deformation. In particular, a yield ratio (YS (lower yield strength)/TS (tensile strength)) after heat treatment of 0.65-0.80 may be secured.
- Hereinafter, the present disclosure will be specifically described through the following Examples. However, it should be noted that the following Examples are only for describing the present disclosure in detail by illustration, and not intended to limit the right scope of the present disclosure. The reason is that the right scope of the present disclosure is determined by the matters described in the claims and reasonably inferred therefrom.
- The steel slabs having the component composition shown in the following Table 1 were subjected to reheating, hot rolling and normalizing heat treatment under the conditions shown in the following Table 2, thereby manufacturing hot-rolled steel plates having a final thickness of 6 mm or more.
- The microstructure fraction, size and carbonitride fraction of each of the manufactured hot-rolled steel plates were measured. In addition, a Charpy impact transition temperature was measured in the state of being aged at 250°C for 1 hour after 5% stretching of a cold deformation amount, which may represent strength (tensile strength and lower yield strength) and strain aging impact properties of each hot-rolled steel plate, and represented in the following Table 3.
- For the microstructure of each hot-rolled steel plate, the steel plate section was polished with a mirror surface, and etched with Nital or Lepera as desired, thereby measuring an image for a certain area of a specimen at 100-500X magnification with an optical or scanning electron microscope, and then the fraction of each image was measured from the measured images using an image analyzer. In order to obtain a statistically significant value, the measurement was repeated for the same specimen but at the changed position, and the average value was calculated.
- The fraction of the fine carbonitrides having an average size of 300 mm or less was measured by an extraction residue method.
- As tensile property values, lower yield strength, tensile strength and a yield ratio (lower yield strength/tensile strength) were measured, respectively from a nominal strain-nominal stress curve obtained by a common tensile test, and a strain aging impact property value was measured by adding 0%, 5% and 8% in advance as a tensile strain, aging a stretched specimen at 250°C for 1 hour, and then performing a Charpy V-notch impact test.
- (In the above Table 3, 'F fraction' refers to a ferrite fraction, and 'F size' refers to an average size of ferrite crystal grains.
- In addition, the represented hardened phase fraction (%) includes the carbonitride fraction (%).)
- As shown in the above Tables 1 to 3, the hot-rolled steel plate satisfying all of the component composition and manufacturing conditions of the present disclosure has high strength, and also secures excellent low-temperature toughness even after cold deformation, thereby being appropriately used in pressure vessels, offshore structures and the like, following a trend of being larger and more complicated.
- However, though the steel component composition satisfies the present disclosure, in Comparative Example 1 in which the roll end temperature upon hot rolling after reheating was unduly low, a strong layered structure formed of ferrite and hardened structure was produced, and thus, low-temperature toughness was decreased, and the impact transition temperature after 5% cold deformation was shown to be higher, -34°C.
- In addition, in Comparative Example 2 in which reheating temperature was unduly low, added Nb was not sufficiently solid-solubilized again, so that a strengthen effect by phase transformation control or precipitation by Nb was significantly small, and thus, low yield strength was less than 350 MPa, and tensile strength was less than 500 MPa.
- Meanwhile, in Comparative Examples 3 to 7 in which the manufacturing conditions satisfied the present disclosure, but the steel component composition did not satisfy the present disclosure, low strength or deteriorated low-temperature toughness were confirmed.
- Among them, in Comparative Example 3 in which the content of C was not sufficient, the ferrite crystal grains were produced coarse when rolling and heat treating, so that sufficient strength was not secured.
- In Comparative Example 4 in which the content of C was excessive, a hardened phase fraction was more than 18%, and the fraction of MA phase was greatly increased, thereby lowering the yield ratio, resulting in a high impact transition temperature after 5% cold deformation.
- In Comparative Example 5 in which the content of Ti is excessive, Ti which was excessively added as compared with added N was produced as a coarse TiN precipitate, and when impacted after 5% cold deformation, served as an initiation point of cracks, resulting in a higher impact transition temperature.
- In Comparative Example 6 in which the content of Nb was insufficient, due to phase transformation delay by Nb re-solid solubilization, a strengthening effect by crystal grain refining and precipitation producing was not exhibited to deteriorate strength.
- In Comparative Example 7 in which the content of Cu was excessive, this Cu raises the solid solubilization of C in austenite when cooling after normalizing heat treatment, thereby increasing a MA phase fraction after final transformation, thereby lowering the yield ratio, and raising the impact transition temperature after 5% cold deformation.
Claims (10)
- A high-strength steel material having excellent low-temperature strain aging impact properties, the steel material comprising: 0.04-0.14 wt% of carbon (C), 0.05-0.60 wt% of silicon (Si), 0.6-1.8 wt% of manganese (Mn), 0.005-0.06 wt% of soluble aluminum (sol. Al), 0.005-0.05 wt% of niobium (Nb), 0.01 wt% or less (exclusive of 0 wt%) of vanadium (V), 0.001-0.015 wt% of titanium (Ti), 0.01-0.4 wt% of copper (Cu), 0.01-0.6 wt% of nickel (Ni), 0.01-0.2 wt% of chromium (Cr), 0.001-0.3 wt% of molybdenum (Mo), 0.0002-0.0040 wt% of calcium (Ca), 0.001-0.006 wt% of nitrogen (N), 0.02 wt% or less (exclusive of 0 wt%) of phosphorus (P), and 0.003 wt% or less (exclusive of 0 wt%) of sulfur (S), with a balance of Fe and other inevitable impurities, and
comprising a mixed structure of ferrite, pearlite, bainite and a martensite-austenite (MA) composite phase as a microstructure, wherein a fraction of the MA phase is 3.5% or less (exclusive of 0%). - The high-strength steel material of claim 1, wherein the niobium (Nb) is comprised in an amount of 0.02-0.05%.
- The high-strength steel material of claim 1, wherein a sum of fractions of remaining phases, other than ferrite, is 18% or less (exclusive of 0%).
- The high-strength steel material of claim 1, wherein an average of ferrite crystal grain size is 15 µm or less.
- The high-strength steel material of claim 1, comprising carbonitrides having an average size of 300 nm or less at 0.01% or more by weight ratio.
- The high-strength steel material of claim 1, wherein a yield ratio (YS (low yield strength) /TS (tensile strength)) is 0.65-0.80.
- A method for manufacturing a high-strength steel material having excellent low-temperature strain aging impact properties, the method comprising: reheating a steel slab including 0.04-0.14 wt% of carbon (C), 0.05-0.60 wt% of silicon (Si), 0.6-1.8 wt% of manganese (Mn), 0.005-0.06 wt% of soluble aluminum (sol. Al), 0.005-0.05 wt% of niobium (Nb), 0.01 wt% or less (exclusive of 0 wt%) of vanadium (V), 0.001-0.015 wt% of titanium (Ti), 0.01-0.4 wt% of copper (Cu), 0.01-0.6 wt% of nickel (Ni), 0.01-0.2 wt% of chromium (Cr), 0.001-0.3 wt% of molybdenum (Mo), 0.0002-0.0040 wt% of calcium (Ca), 0.001-0.006 wt% of nitrogen (N), 0.02 wt% or less (exclusive of 0 wt%) of phosphorus (P), and 0.003 wt% or less (exclusive of 0 wt%) of sulfur (S), with a balance of Fe and other inevitable impurities in a temperature range of 1080-1250°C;
controlled rolling the reheated slab so that a rolling end temperature is 780°C or more, thereby being manufactured to form a hot-rolled steel plate;
cooling the hot-rolled steel plate by air cooling or water cooling; and
after the cooling, subjecting the hot-rolled steel plate to normalizing heat treatment in a temperature range of 850-960°C. - The method of claim 7, wherein the steel slab includes 0.02-0.05% of niobium (Nb).
- The method of claim 7, wherein the normalizing heat treatment is performed for {(1.3×t)+(10-60)} minutes (wherein 't' refers to a steel material thickness (mm)).
- The method of claim 7, wherein the reheated slab is formed of 50% or more of Nb being solid-solubilized again.
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PCT/KR2016/014734 WO2017105109A1 (en) | 2015-12-15 | 2016-12-15 | High-strength steel material having excellent low-temperature strain aging impact properties and method for manufacturing same |
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JP7024063B2 (en) * | 2017-08-23 | 2022-02-22 | 宝山鋼鉄股▲分▼有限公司 | Steel for low temperature pressure vessels and its manufacturing method |
KR102020434B1 (en) * | 2017-12-01 | 2019-09-10 | 주식회사 포스코 | Steel material having exellent hydrogen induced crack resistance and low temperature impact toughness and method of manufacturing the same |
KR102218423B1 (en) * | 2019-08-23 | 2021-02-19 | 주식회사 포스코 | Thin steel plate having excellent low-temperature toughness and ctod properties, and method for manufacturing thereof |
WO2021256590A1 (en) * | 2020-06-19 | 2021-12-23 | 현대제철 주식회사 | Rebar and manufacturing method therefor |
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JP5516784B2 (en) * | 2012-03-29 | 2014-06-11 | Jfeスチール株式会社 | Low yield ratio high strength steel sheet, method for producing the same, and high strength welded steel pipe using the same |
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JP6616002B2 (en) | 2019-12-04 |
CN108368593B (en) | 2020-10-02 |
US20240110267A1 (en) | 2024-04-04 |
KR101758483B1 (en) | 2017-07-17 |
US20180363111A1 (en) | 2018-12-20 |
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JP2019504187A (en) | 2019-02-14 |
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