WO2017111345A1 - 저항복비형 고강도 강재 및 그 제조방법 - Google Patents
저항복비형 고강도 강재 및 그 제조방법 Download PDFInfo
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- WO2017111345A1 WO2017111345A1 PCT/KR2016/014135 KR2016014135W WO2017111345A1 WO 2017111345 A1 WO2017111345 A1 WO 2017111345A1 KR 2016014135 W KR2016014135 W KR 2016014135W WO 2017111345 A1 WO2017111345 A1 WO 2017111345A1
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 79
- 239000010959 steel Substances 0.000 title claims abstract description 79
- 238000004519 manufacturing process Methods 0.000 title claims description 24
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 24
- 239000010955 niobium Substances 0.000 claims abstract description 19
- 239000011572 manganese Substances 0.000 claims abstract description 18
- 239000010936 titanium Substances 0.000 claims abstract description 18
- 239000011651 chromium Substances 0.000 claims abstract description 17
- 239000011575 calcium Substances 0.000 claims abstract description 16
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims abstract description 14
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 8
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims abstract description 7
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 claims abstract description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 7
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 7
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims abstract description 7
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims abstract description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims abstract description 7
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims abstract description 7
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims abstract description 7
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052796 boron Inorganic materials 0.000 claims abstract description 7
- 229910052791 calcium Inorganic materials 0.000 claims abstract description 7
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 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
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 7
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 7
- 239000011574 phosphorus Substances 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
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 7
- 239000011593 sulfur Substances 0.000 claims abstract description 7
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 7
- 238000005096 rolling process Methods 0.000 claims description 24
- 238000001816 cooling Methods 0.000 claims description 21
- 229910001563 bainite Inorganic materials 0.000 claims description 20
- 229910000859 α-Fe Inorganic materials 0.000 claims description 18
- 238000000034 method Methods 0.000 claims description 15
- 239000010949 copper Substances 0.000 claims description 11
- 239000013078 crystal Substances 0.000 claims description 8
- 238000005098 hot rolling Methods 0.000 claims description 6
- 238000010438 heat treatment Methods 0.000 claims description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 4
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 4
- 229910052802 copper Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 239000011733 molybdenum Substances 0.000 claims description 4
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 4
- 230000000052 comparative effect Effects 0.000 description 26
- 230000000694 effects Effects 0.000 description 13
- 229910001566 austenite Inorganic materials 0.000 description 7
- 229910000734 martensite Inorganic materials 0.000 description 7
- 239000000203 mixture Substances 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 238000010276 construction Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 239000002245 particle Substances 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 3
- 229910000746 Structural steel Inorganic materials 0.000 description 2
- 239000010953 base metal Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000005553 drilling Methods 0.000 description 2
- 238000003303 reheating Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- TVEXGJYMHHTVKP-UHFFFAOYSA-N 6-oxabicyclo[3.2.1]oct-3-en-7-one Chemical compound C1C2C(=O)OC1C=CC2 TVEXGJYMHHTVKP-UHFFFAOYSA-N 0.000 description 1
- 229910001035 Soft ferrite Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000009172 bursting Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000009977 dual effect Effects 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 230000006355 external stress Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 230000000977 initiatory effect Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 230000008961 swelling Effects 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- RMLPZKRPSQVRAB-UHFFFAOYSA-N tris(3-methylphenyl) phosphate Chemical compound CC1=CC=CC(OP(=O)(OC=2C=C(C)C=CC=2)OC=2C=C(C)C=CC=2)=C1 RMLPZKRPSQVRAB-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
- C22C38/18—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
-
- 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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- 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
- 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
-
- 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
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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
-
- 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
-
- 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
-
- 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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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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
- C21D2211/005—Ferrite
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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 invention relates to a resistive high strength type steel and a method of manufacturing the same. More specifically, the present invention relates to a high yield strength steel having a low yield ratio and high tensile strength, which can be preferably used as construction steel, and a method of manufacturing the same.
- yield strength / tensile strength which is the ratio of tensile strength and yield strength
- yield point the point of plastic deformation
- the yield ratio of steel is mainly composed of a soft phase such as ferrite as the metal structure of the steel, and a hard phase such as bainite or marensite. It is known that the hard phase can be lowered by implementing a properly dispersed tissue.
- Patent Document 1 discloses proper quenching and tempering in the dual phase region of ferrite and austenite. A method of reducing the yield ratio is disclosed. However, in the above method, since the number of heat treatment processes is added in addition to the rolling manufacturing process, there is a problem that the productivity is reduced and the manufacturing cost is increased.
- Patent Document 1 Japanese Patent Application Laid-Open No. 55-97425
- One aspect of the present invention is to provide a resistive high-strength type high strength steel and a method of manufacturing the same. More specifically, the present invention provides a high-resistance-type high-strength steel and a method for manufacturing the same, which can secure ultra-high strength and low-cost ratio without lowering productivity and increasing manufacturing cost.
- One aspect of the present invention is carbon (C): 0.02 to 0.11% by weight, silicon (Si): 0.1 to 0.5% by weight, manganese (Mn): 1.5 to 2.5% by weight, aluminum (Al): 0.01 to 0.06% by weight, Nickel (Ni): 0.1-0.6% by weight, titanium (Ti): 0.01-0.03% by weight, niobium (Nb): 0.005-0.08% by weight, chromium (Cr): 0.1-0.5% by weight, phosphorus (P): 0.01 % By weight (excluding 0% by weight), sulfur (S): 0.01% by weight or less (excluding 0% by weight), boron (B): 5 to 30 ppm by weight, nitrogen (N): 20 to 70 ppm by weight, Calcium (Ca): 50 ppm or less (except 0 ppm), Tin (Sn): 5-50 ppm or less (except 0 ppm), resistive ratio including remaining iron (Fe) and other unavoidable im
- another aspect of the present invention is carbon (C): 0.02 to 0.11% by weight, silicon (Si): 0.1 to 0.5% by weight, manganese (Mn): 1.5 to 2.5% by weight, aluminum (Al): 0.01 to 0.06 Weight%, nickel (Ni): 0.1-0.6 weight%, titanium (Ti): 0.01-0.03 weight%, niobium (Nb): 0.005-0.08 weight%, chromium (Cr): 0.1-0.5 weight%, phosphorus (P ): 0.01% by weight or less (excluding 0% by weight), sulfur (S): 0.01% by weight or less (excluding 0% by weight), boron (B): 5-30% by weight, nitrogen (N): 20-70 Weight ppm, calcium (Ca): 50 ppm or less (except 0 ppm), tin (Sn): 5-50 ppm or less (except 0 ppm), remaining iron (Fe) and other unavoidable impurities Heating the
- Resistance ratio-type high strength steel is carbon (C): 0.02 ⁇ 0.11% by weight, silicon (Si): 0.1 ⁇ 0.5% by weight, manganese (Mn): 1.5 ⁇ 2.5% by weight, aluminum (Al) : 0.01 to 0.06 weight%, nickel (Ni): 0.1 to 0.6 weight%, titanium (Ti): 0.01 to 0.03 weight%, niobium (Nb): 0.005 to 0.08 weight%, chromium (Cr): 0.1 to 0.5 weight% , Phosphorus (P): 0.01% by weight or less (excluding 0% by weight), sulfur (S): 0.01% by weight or less (excluding 0% by weight), boron (B): 5-30% by weight, nitrogen (N) : 20 to 70 ppm by weight, calcium (Ca): 50 ppm or less (except 0 ppm), tin (Sn): 5 to 50 ppm or less (except 0 ppm),
- C is an important element that forms bainite or martensite and determines the size and fraction of bainite or martensite formed.
- C content is more than 0.11% by weight, low-temperature toughness is lowered, while if the C content is less than 0.02% by weight, it prevents the formation of bainite or martensite, leading to a decrease in strength. Therefore, it is preferable that C content is 0.02-0.11 weight%.
- the upper limit of the C content is more preferably 0.08% by weight for better weldability.
- Si is used as a deoxidizer and is an element to improve strength and toughness.
- Si content is more than 0.5% by weight, not only the low-temperature toughness and weldability deteriorate, but also a thick scale is formed on the surface of the plate, which may cause gas cutability and other surface cracks.
- Si content is less than 0.1% by weight, the deoxidation effect may be insufficient. Therefore, Si content is 0.1 to 0.5 weight%. More preferably, it may be 0.15 to 0.35% by weight.
- Mn is a useful element that improves strength by solid solution strengthening, so it needs to be added at least 1.5% by weight.
- the Mn content is more than 2.5% by weight, the toughness of the weld portion may be greatly reduced due to excessive increase in hardenability. Therefore, the content of Mn is preferably 1.5 to 2.5% by weight.
- Al is an element which can deoxidize molten steel at low cost and stabilizes ferrite.
- the Al content is less than 0.01% by weight, the above effects are insufficient.
- the Al content is more than 0.06% by weight, nozzle clogging may occur during continuous casting. Therefore, it is preferable that Al content is 0.01 to 0.06 weight%.
- Ni is an element which can improve the strength and toughness of a base material simultaneously. In order to fully show the effect mentioned above in this invention, it is preferable to add 0.1 weight% or more. However, since Ni is an expensive element, the addition of an amount exceeding 0.6% by weight may lower the economic efficiency and lower the weldability. Therefore, it is preferable that Ni content is 0.1 to 0.6%.
- Ti suppresses the growth of crystal grains upon reheating and greatly improves low temperature toughness
- Ti is preferably added at least 0.01% by weight.
- the Ti content is more than 0.03% by weight, problems such as clogging of the playing nozzle and reduction of low temperature toughness due to the center portion determination may occur. Therefore, it is preferable that Ti content is 0.01 to 0.03 weight%.
- Nb is an important element in the production of TMCP steel and precipitates in the form of NbC or NbCN to greatly improve the strength of the base metal and the welded portion.
- Nb dissolved in reheating at a high temperature suppresses recrystallization of austenite and transformation of ferrite or bainite, thereby exhibiting an effect of miniaturizing the tissue.
- the present invention not only forms bainite at a low cooling rate when the slab is cooled after rough rolling, but also increases the stability of austenite during cooling after the final rolling, thereby promoting martensite formation even at a low rate of cooling. Also
- Nb content is 0.005 weight% or more. However, if the Nb content is more than 0.08% by weight, brittle cracks may appear at the edges of the steel. Therefore, it is preferable that Nb content is 0.005 to 0.08 weight%.
- Cr is an element added to secure strength and also serves to increase hardenability. In order to fully acquire the above-mentioned effect, it is necessary to add 0.1% or more. However, when the Cr content is more than 0.5%, the hardness of the welded portion may be excessively increased and the toughness may be inhibited. Therefore, it is preferable that Cr content is 0.1 to 0.5%.
- Phosphorus (P) 0.01 wt% or less
- P is an element that is advantageous in improving strength and corrosion resistance, it is advantageous to keep it as low as possible because it can greatly impair impact toughness, and the upper limit thereof is preferably 0.01% by weight.
- S is an element that forms MnS or the like and greatly impairs the impact toughness, it is advantageous to keep S as low as possible, and the upper limit thereof is preferably 0.01% by weight.
- B is a very inexpensive addition element, exhibits strong hardening ability, and is a beneficial element that greatly contributes to the formation of bainite even at low speed cooling in the cooling after rough rolling.
- B content is more than 30 ppm by weight, Fe 23 (CB) 6 may be formed, thereby lowering the curing ability and significantly lowering the low temperature toughness. Therefore, it is preferable that B content is 5-30 weight ppm.
- the lower limit of the N content is preferably 20 wtppm.
- Ca is mainly used as an element to suppress non-metallic inclusions of MnS and to improve low temperature toughness.
- the excessive addition of Ca reacts with the oxygen contained in the steel to produce CaO, a non-metallic inclusion, so the upper limit is preferably 60 ppm by weight.
- Tin (Sn) 5 to 50 ppm by weight
- Sn is an element useful for securing corrosion resistance.
- Sn content is more than 50 ppm by weight, it may cause a problem that a large amount of defects in the form of swelling or bursting like a blister is generated on the surface of the steel rather than a contribution to improving the corrosion resistance.
- Sn can increase the strength of the steel, but the elongation and low temperature impact toughness is reduced, so the upper limit is preferably 50 ppm by weight.
- the remaining component of the present invention is iron (Fe).
- impurities which are not intended from the raw material or the surrounding environment may be inevitably mixed, and thus cannot be excluded. Since these impurities are known to those skilled in the art, all of them are not specifically mentioned in the present specification.
- Cu is an element that can increase the strength while minimizing the decrease in toughness of the base metal. In order to fully acquire the effect mentioned above, it is preferable to add 0.1 weight% or more. However, when the Cu content is more than 0.5% by weight can greatly inhibit the product surface quality. Therefore, it is preferable that Cu content is 0.1 to 0.5 weight%.
- Mo is required to add more than 0.15% by weight since it has the effect of greatly improving the hardenability even with a small amount of addition. However, when it is added in excess of 0.3% by weight, the hardness of the weld is excessively increased and the toughness is increased. May inhibit. Therefore, it is preferable that Mo content is 0.15 to 0.3 weight%.
- V has a lower solubility temperature than other microalloys and is effective in preventing the drop in strength due to precipitation in the weld heat affected zone. In order to fully acquire the effect mentioned above, it is preferable to add 0.005 weight% or more. However, when the V content is more than 0.3% by weight, the toughness may be lowered rather. Therefore, it is preferable that V content is 0.005 to 0.3 weight%.
- microstructure of the steel of the present invention may include bainitic ferrite and granular bainite as a main phase, and may include M-A (phase martensite) as a secondary phase.
- bainitic ferrite contains many high hard grain boundaries in the mouth while maintaining the initial austenite grain boundaries, it is useful for improving the strength and impact toughness due to the grain refinement effect.
- Granular bainite maintains initial austenite grains like bainitic ferrite, but secondary phases such as M-A exist in the mouth or grain boundaries. Although there is no high angle grain boundary in the mouth, it is somewhat disadvantageous in impact toughness, but the strength is somewhat increased by the presence of a large amount of low angle grain boundary such as intra-particle dislocation.
- bainitic ferrite and granular bainite as a column, resistance ratio and high strength can be secured.
- the area fraction of the bainitic ferrite is 80 to 95%
- the granular bainite is 5 to 20%
- the M-A may be 3% or less (including 0%).
- the area fraction of the bainitic ferrite is less than 80%, it is difficult to secure high tensile strength, and if it is more than 95%, the yield ratio is increased.
- Secondary phases such as M-A are preferably microstructures useful for implementing a resistive ratio, and have an area fraction of 3% or less.
- the yield ratio may be reduced when the area fraction of M-A is more than 3%, but it may adversely act to secure a high tensile strength because it may act as a crack initiation point for external stress.
- the steel according to the invention PImax. (111) / PImax. (100) may be 1.0 or more and 1.8 or less.
- the PImax. (111) is the pole intensity (PImax.) Of the (111) crystal plane obtained from a method such as X-ray diffraction or electron backscattering diffraction, and the PImax. (100) is the pole of the (100) crystal plane. Strength.
- the pole strength of the crystal plane is determined by the final microstructure of the steel according to one aspect of the invention.
- the bainitic ferrite and granular bainite are the main phases, the higher the bainitic ferrite fraction is, the larger the value of PImax. (111) is. Will become large.
- the final microstructure of the steel according to an aspect of the present invention is that the bainitic ferrite has a higher area fraction than granular bainite, and when the PImax. . If PImax. (111) / PImax. (100) exceeds 1.8, the resistance ratio is not satisfied, so the upper limit is preferably 1.8 or less. More preferable PImax. (111) / PImax. (100) is 1.6 or less.
- PImax. (111) / PImax. (100) is less than 1.0, the fraction of granular bainite is increased to more than 20%, making it difficult to secure high strength. Therefore, it is preferable that the lower limit of PImax. (111) / PImax. (100) is 1.0 or more, and a more preferable lower limit is 1.2 or more.
- the steel according to the present invention has a yield ratio of 0.85 or less, can secure a tensile strength of 800MPa or more, it can be preferably used as a steel for construction.
- the thickness of the steel according to the present invention may be 60mm or less.
- the plate thickness can be reduced to 60 mm or less, thereby facilitating machining and welding operations such as cutting and drilling. Therefore, it is preferable that the thickness of steel materials is 60 mm or less. More preferably, it is 40 mm or less, More preferably, it is 30 mm or less.
- the lower limit does not need to be particularly limited, but may be 15 mm or more in order to use the steel as a construction structural steel.
- Another aspect of the present invention provides a method for producing a resistive high strength steel sheet comprising the steps of heating the slab having the above-described alloy composition to 1050 ⁇ 1250 °C; Roughly rolling the heated slab at 950 ⁇ 1150 ° C. to obtain a bar; Hot rolling the bar to a finish rolling temperature of 700 to 950 ° C. to obtain a hot rolled steel sheet; And cooling the hot rolled steel sheet to a cooling end temperature of Bs temperature or less at a cooling rate of 25 to 50 ° C./s. It includes.
- the slab having the alloy composition described above is heated to 1050-1250 ° C.
- the heated slab is rough-rolled at 950-1050 ° C. to obtain a bar.
- the rough rolling temperature is less than 950 ° C, there is a fear that the particles become coarse as the austenite is deformed without recrystallization. If the rough rolling temperature is higher than 1050 ° C, recrystallization occurs and the particles grow and austenite also grows. The particles may be coarse.
- the bar is hot rolled to a finish rolling temperature of 700 to 950 ° C. to obtain a hot rolled steel sheet.
- finish rolling temperature is less than 700 °C low temperature of the plate material may cause a load in the rolling mill may not be able to roll to the final thickness, if it exceeds 950 °C there is a risk of recrystallization during rolling.
- the rolling reduction rate of the hot rolling may be 50 to 80%.
- finish rolling reduction rate is less than 50%, the load acting on the material during rolling increases, which may cause an accident of equipment, and if it exceeds 80%, the number of rolling passes increases to secure the final thickness up to the end temperature of rolling. There is a risk of not doing it.
- the hot rolled steel sheet is cooled to a cooling end temperature below the Bs temperature at a cooling rate of 25 ⁇ 50 °C / s.
- a slab satisfying the component system shown in Table 1 was heated to 1160 ° C., roughly rolled at 1000 ° C., and then hot rolled and cooled to meet the manufacturing conditions shown in Table 2 to obtain a steel. Yield strength, tensile strength, yield ratio and microstructure of the steel were measured and shown in Table 3 below.
- Yield strength and tensile strength were measured using a universal tensile tester.
- microstructures were observed by optical microscope after chemically corroding steels and polishing them.
- the pole strength and the texture strength were measured by X-ray diffractometer and electron back scattering diffractometer.
- each element content unit is weight percent.
- BF bainitic ferrite
- GB granular bainite
- MA phase martensite
- AF acicular ferrite
- B bainite
- the unit is area%.
- Inventive Examples 1 to 9 satisfying the alloy composition and the manufacturing conditions of the present invention can be seen that can secure a resistivity ratio of 0.85 or less and a tensile strength of 800MPa or more.
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Abstract
Description
강종 | C | Si | Mn | P | S | Al | Cr | Ni | Ti | Nb | B | N | Ca | Sn |
발명강A | 0.045 | 0.17 | 2.12 | 0.007 | 0.002 | 0.029 | 0.32 | 0.40 | 0.018 | 0.04 | 0.0016 | 0.0037 | 0.0010 | 0.0008 |
발명강B | 0.052 | 0.15 | 2.48 | 0.008 | 0.001 | 0.026 | 0.30 | 0.15 | 0.016 | 0.04 | 0.0015 | 0.0035 | 0.0007 | 0.0042 |
발명강C | 0.065 | 0.16 | 1.75 | 0.011 | 0.001 | 0.030 | 0.29 | 0.29 | 0.019 | 0.04 | 0.0014 | 0.0029 | 0.0012 | 0.0021 |
발명강D | 0.054 | 0.25 | 2.29 | 0.007 | 0.002 | 0.030 | 0.31 | 0.50 | 0.011 | 0.03 | 0.0013 | 0.0042 | 0.0005 | 0.0034 |
비교강E | 0.045 | 0.11 | 1.91 | 0.005 | 0.003 | 0.006 | 0.04 | 1.52 | 0.008 | 0.01 | 0.0001 | 0.0040 | 0.0011 | 0.0004 |
비교강F | 0.049 | 0.15 | 2.85 | 0.009 | 0.002 | 0.029 | 0.28 | 0.41 | 0.018 | 0.03 | 0.0015 | 0.0040 | 0.0014 | 0.0003 |
강종 | 구분 | 열간마무리압연 | 냉각 | Bs 온도(℃) | ||
온도(℃) | 압하율(%) | 냉각속도(℃/s) | 종료온도(℃) | |||
발명강A | 발명예1 | 844 | 75 | 46.6 | 523 | 589 |
발명예2 | 860 | 70 | 41.1 | 537 | ||
발명예3 | 892 | 60 | 40.6 | 492 | ||
발명강B | 발명예4 | 873 | 70 | 41.2 | 536 | 565 |
발명예5 | 890 | 60 | 37.7 | 506 | ||
발명예6 | 901 | 60 | 26.2 | 441 | ||
발명강C | 발명예7 | 899 | 60 | 25.8 | 451 | 623 |
발명예8 | 890 | 60 | 26.3 | 447 | ||
발명예9 | 859 | 70 | 41.4 | 528 | ||
발명강D | 비교예1 | 852 | 75 | 51.4 | 534 | 568 |
비교예2 | 863 | 75 | 57.7 | 507 | ||
비교예3 | 904 | 45 | 6.4 | 182 | ||
비교강E | 비교예4 | 870 | 72 | 34.1 | 350 | 574 |
비교예5 | 871 | 66 | 24.1 | 356 | ||
비교예6 | 869 | 52 | 20.2 | 357 | ||
비교강F | 비교예7 | 864 | 78 | 48.5 | 505 | 526 |
비교예8 | 877 | 65 | 31.4 | 502 | ||
비교예9 | 835 | 55 | 20.4 | 496 |
강종 | 구분 | 중심부 미세조직 | 항복강도(MPa) | 인장강도(MPa) | 항복비 | PImax.(111)/PImax.(100) | ||
BF | GB | M.A | ||||||
발명강A | 발명예1 | 86 | 12 | 2 | 677 | 843 | 0.80 | 1.14 |
발명예2 | 89 | 10 | 1 | 703 | 872 | 0.81 | 1.25 | |
발명예3 | 91 | 8 | 1 | 717 | 909 | 0.79 | 1.50 | |
발명강B | 발명예4 | 87 | 10 | 3 | 697 | 866 | 0.80 | 1.16 |
발명예5 | 92 | 6 | 2 | 736 | 898 | 0.82 | 1.64 | |
발명예6 | 88 | 11 | 1 | 707 | 871 | 0.81 | 1.27 | |
발명강C | 발명예7 | 92 | 7 | 1 | 761 | 919 | 0.83 | 1.52 |
발명예8 | 93 | 7 | 0 | 786 | 926 | 0.85 | 1.71 | |
발명예9 | 83 | 15 | 2 | 686 | 860 | 0.80 | 1.10 | |
발명강D | 비교예1 | 97 | 3 | 0 | 797 | 931 | 0.86 | 1.98 |
비교예2 | 98 | 2 | 0 | 893 | 981 | 0.91 | 1.96 | |
비교예3 | 71 | 24 | 5 | 613 | 780 | 0.79 | 0.87 | |
비교강E | 비교예4 | AF: 72, B: 28 | 562 | 694 | 0.81 | 1.08 | ||
비교예5 | AF: 79, B: 21 | 530 | 643 | 0.82 | 1.05 | |||
비교예6 | AF: 74, B: 26 | 504 | 612 | 0.82 | 1.07 | |||
비교강F | 비교예7 | BF: 97, GB: 3, MA: 0 | 876 | 984 | 0.89 | 1.97 | ||
비교예8 | BF: 72, GB: 24, MA: 4 | 725 | 841 | 0.86 | 0.85 | |||
비교예9 | BF: 66, GB: 31, MA: 3 | 660 | 776 | 0.85 | 0.82 |
Claims (10)
- 탄소(C): 0.02~0.11중량%, 실리콘(Si): 0.1~0.5중량%, 망간(Mn): 1.5~2.5중량%, 알루미늄(Al): 0.01~0.06중량%, 니켈(Ni): 0.1~0.6중량%, 티타늄(Ti): 0.01~0.03중량%, 니오븀(Nb): 0.005~0.08중량%, 크롬(Cr): 0.1~0.5중량%, 인(P): 0.01중량% 이하, 황(S): 0.01중량% 이하, 보론(B): 5~30중량ppm, 질소(N): 20~70중량ppm, 칼슘(Ca): 50중량ppm 이하(0은 제외), 주석(Sn): 5~50중량ppm 이하, 나머지 철(Fe) 및 기타 불가피한 불순물을 포함하는 저항복비형 고강도 강재.
- 제1항에 있어서,상기 강재는 구리(Cu): 0.1~0.5중량%, 몰리브덴(Mo): 0.15~0.3중량% 및 바나듐(V): 0.005~0.3중량% 중 1 이상을 추가로 포함하는 것을 특징으로 하는 저항복비형 고강도 강재.
- 제1항에 있어서,상기 강재의 미세조직은 베이니틱 페라이트와 그래뉼러 베이나이트를 주상으로 포함하고, M-A를 이차상으로 포함하는 것을 특징으로 하는 저항복비형 고강도 강재.
- 제3항에 있어서,면적분율로 상기 베이니틱 페라이트는 80~95%이고, 상기 그래뉼러 베이나이트는 5~20%이며, 상기 M-A는 3% 이하(0% 포함)인 것을 특징으로 하는 저항복비형 고강도 강재.
- 제1항에 있어서,상기 강재의 (100) 및 (111) 결정면의 극점 강도 (pole intensity, PImax.) 비인 PImax.(111)/PImax.(100)는 1.0 이상 1.8 이하인 것을 특징으로 하는 저항복비형 고강도 강재.(단, 상기 PImax.(111)은 (111) 결정면의 극점 강도이며, 상기 PImax.(100)은 (100) 결정면의 극점 강도이다.)
- 제1항에 있어서,상기 강재는 항복비가 0.85 이하이고, 인장강도가 800MPa 이상인 것을 특징으로 하는 저항복비형 고강도 강재.
- 제1항에 있어서,상기 강재의 두께는 60mm 이하인 것을 특징으로 하는 저항복비형 고강도 강재.
- 탄소(C): 0.02~0.11중량%, 실리콘(Si): 0.1~0.5중량%, 망간(Mn): 1.5~2.5중량%, 알루미늄(Al): 0.01~0.06중량%, 니켈(Ni): 0.1~0.6중량%, 티타늄(Ti): 0.01~0.03중량%, 니오븀(Nb): 0.005~0.08중량%, 크롬(Cr): 0.1~0.5중량%, 인(P): 0.01중량% 이하, 황(S): 0.01중량% 이하, 보론(B): 5~30중량ppm, 질소(N): 20~70중량ppm, 칼슘(Ca): 50중량ppm 이하(0은 제외), 주석(Sn): 5~50중량ppm 이하, 나머지 철(Fe) 및 기타 불가피한 불순물을 포함하는 슬라브를 1050~1250℃로 가열하는 단계;상기 가열된 슬라브를 950~1050℃에서 조압연하여 바(Bar)를 얻는 단계;상기 바(Bar)를 마무리압연온도 700~950 ℃로 열간압연하여 열연강판을 얻는 단계; 및상기 열연강판을 25~50℃/s의 냉각속도로 Bs 온도 이하의 냉각종료온도까지 냉각하는 단계; 를 포함하는 저항복비형 고강도 강재의 제조방법.
- 제8항에 있어서,상기 슬라브는 구리(Cu): 0.1~0.5중량%, 몰리브덴(Mo): 0.15~0.3중량% 및 바나듐(V): 0.005~0.3중량% 중 1 이상을 추가로 포함하는 것을 특징으로 하는 저항복비형 고강도 강재의 제조방법.
- 제8항에 있어서,상기 열간압연은 압하율은 50~80%로 행하는 것을 특징으로 하는 저항복비형 고강도 강재의 제조방법.
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- 2016-12-02 WO PCT/KR2016/014135 patent/WO2017111345A1/ko active Application Filing
- 2016-12-02 US US16/063,985 patent/US20180371590A1/en not_active Abandoned
- 2016-12-02 JP JP2018532049A patent/JP6845855B2/ja active Active
- 2016-12-02 CN CN201680075889.7A patent/CN108474090B/zh active Active
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JP2020509156A (ja) * | 2016-12-21 | 2020-03-26 | ポスコPosco | 低降伏比型超高強度鋼材及びその製造方法 |
Also Published As
Publication number | Publication date |
---|---|
KR102348539B1 (ko) | 2022-01-07 |
EP3395997A4 (en) | 2018-11-07 |
CN108474090B (zh) | 2021-02-12 |
JP6845855B2 (ja) | 2021-03-24 |
KR20170076912A (ko) | 2017-07-05 |
EP3395997B1 (en) | 2020-09-02 |
EP3395997A1 (en) | 2018-10-31 |
CN108474090A (zh) | 2018-08-31 |
JP2019504199A (ja) | 2019-02-14 |
US20180371590A1 (en) | 2018-12-27 |
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