US20210388458A1 - High strength steel plate for structure with good seawater corrosion resistant property and method of manufacturing same - Google Patents
High strength steel plate for structure with good seawater corrosion resistant property and method of manufacturing same Download PDFInfo
- Publication number
- US20210388458A1 US20210388458A1 US17/291,823 US201917291823A US2021388458A1 US 20210388458 A1 US20210388458 A1 US 20210388458A1 US 201917291823 A US201917291823 A US 201917291823A US 2021388458 A1 US2021388458 A1 US 2021388458A1
- Authority
- US
- United States
- Prior art keywords
- less
- steel
- steel plate
- strength
- content
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 120
- 239000010959 steel Substances 0.000 title claims abstract description 120
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 18
- 238000005260 corrosion Methods 0.000 title description 52
- 230000007797 corrosion Effects 0.000 title description 48
- 239000013535 sea water Substances 0.000 title description 16
- 239000012535 impurity Substances 0.000 claims abstract description 12
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 12
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 10
- 229910001562 pearlite Inorganic materials 0.000 claims abstract description 8
- 229910001568 polygonal ferrite Inorganic materials 0.000 claims abstract description 7
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 62
- 239000010949 copper Substances 0.000 claims description 47
- 239000011651 chromium Substances 0.000 claims description 39
- 239000011572 manganese Substances 0.000 claims description 37
- 238000001816 cooling Methods 0.000 claims description 33
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 26
- 229910052799 carbon Inorganic materials 0.000 claims description 26
- 229910052802 copper Inorganic materials 0.000 claims description 26
- 239000010955 niobium Substances 0.000 claims description 26
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 24
- 239000010936 titanium Substances 0.000 claims description 24
- 229910052759 nickel Inorganic materials 0.000 claims description 23
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 21
- 229910052748 manganese Inorganic materials 0.000 claims description 20
- 229910052804 chromium Inorganic materials 0.000 claims description 19
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 18
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 16
- 229910052710 silicon Inorganic materials 0.000 claims description 16
- 239000010703 silicon Substances 0.000 claims description 16
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 14
- 238000005096 rolling process Methods 0.000 claims description 14
- 229910052717 sulfur Inorganic materials 0.000 claims description 14
- 239000011593 sulfur Substances 0.000 claims description 14
- 229910052782 aluminium Inorganic materials 0.000 claims description 13
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 13
- 238000000034 method Methods 0.000 claims description 12
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 11
- 229910052758 niobium Inorganic materials 0.000 claims description 11
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 11
- 229910052719 titanium Inorganic materials 0.000 claims description 11
- 238000003303 reheating Methods 0.000 claims description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 7
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 7
- 230000000977 initiatory effect Effects 0.000 claims description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims description 7
- 239000011574 phosphorus Substances 0.000 claims description 7
- 238000005098 hot rolling Methods 0.000 claims description 4
- 230000000694 effects Effects 0.000 description 12
- 239000000463 material Substances 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 10
- 239000000203 mixture Substances 0.000 description 10
- 238000005266 casting Methods 0.000 description 8
- 238000005336 cracking Methods 0.000 description 7
- BHEPBYXIRTUNPN-UHFFFAOYSA-N hydridophosphorus(.) (triplet) Chemical compound [PH] BHEPBYXIRTUNPN-UHFFFAOYSA-N 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 4
- 230000007547 defect Effects 0.000 description 4
- 239000000243 solution Substances 0.000 description 4
- 238000009749 continuous casting Methods 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 239000011800 void material Substances 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000002378 acidificating effect Effects 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- VKYKSIONXSXAKP-UHFFFAOYSA-N hexamethylenetetramine Chemical compound C1N(C2)CN3CN1CN2C3 VKYKSIONXSXAKP-UHFFFAOYSA-N 0.000 description 2
- 150000002500 ions Chemical class 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000011780 sodium chloride Substances 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- PIGFYZPCRLYGLF-UHFFFAOYSA-N Aluminum nitride Chemical compound [Al]#N PIGFYZPCRLYGLF-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000000460 chlorine Substances 0.000 description 1
- 229910052801 chlorine Inorganic materials 0.000 description 1
- -1 chlorine ions Chemical class 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000003111 delayed effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000003487 electrochemical reaction Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 235000010299 hexamethylene tetramine Nutrition 0.000 description 1
- 239000004312 hexamethylene tetramine Substances 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 229960004011 methenamine Drugs 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 0.000 description 1
- 239000002244 precipitate 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
- 238000011160 research Methods 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- CADICXFYUNYKGD-UHFFFAOYSA-N sulfanylidenemanganese Chemical compound [Mn]=S CADICXFYUNYKGD-UHFFFAOYSA-N 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
- 239000010937 tungsten Substances 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- 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
- C22C38/02—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
- C22C38/48—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
-
- 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
-
- 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
-
- 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
- C21D2211/009—Pearlite
Definitions
- the present disclosure relates to a steel fora structure having excellent corrosion resistance in an environment in which corrosion is accelerated by seawater, such as a steel plate for building structures on the coast, a ballast tank in a ship and related appurtenant equipment, or the like, and a method of manufacturing the steel.
- Chromium and copper may play different roles depending on corrosive environments, and may exhibit an excellent anti-corrosion effect even in an environment, in which corrosion is accelerated by seawater, when added in an appropriate ratio.
- chromium does not have a significant effect in an acidic environment, and copper causes casting cracking to occur in a casting process, so that relatively expensive nickel should be added in a certain level or more.
- chromium has an effect of improving corrosion resistance, and the minimum amount of nickel added to prevent casting defects of copper-added steel may be reduced due to the recent development in continuous casting technology. Accordingly, the amount of expensive nickel added may be reduced, so that the cost of a product may be reduced.
- Patent Document 1 discloses that a composition system and manufacturing conditions are controlled to control a microstructure of a steel sheet, but it is difficult to secure strength when the content of a low-temperature structure is low (less than 20%).
- the content of nickel (Ni) is specified as being 0.05% or less, so that many casting defects may occur during casting.
- Patent Document 2 0.1% or more of Al is added to form coarse oxide inclusions in a steelmaking process, and inclusions are crushed and elongated during a rolling process to form elongated inclusions. Accordingly, void formation is promoted to reduce localized corrosion resistance.
- An aspect of the present disclosure is to provide a steel plate, having excellent corrosion resistance to a seawater environment, in which corrosion characteristics and a microstructure of a surface of the steel plate are controlled through optimization of a composition system and manufacturing conditions to improve strength characteristics of the steel plate and to significantly reduce a corrosion rate.
- a high-strength steel (or steel plate) for structure comprising, by weight, carbon (C): 0.03% or more to less than 0.1%, silicon (Si): 0.1% or more to less than 0.8%, manganese (Mn): 0.3% or more to less than 1.5%, chromium (Cr): 0.5% or more to less than 1.5%, copper (Cu): 0.1% or more to less than 0.5%, aluminum (Al): 0.01% or more to less than 0.08%, titanium (Ti): 0.01% or more to 0.1% or less, nickel (Ni): 0.05% or more to less than 0.1%, niobium (Nb): 0.002% or more to less than 0.07%, phosphorus (P): 0.03% or less, sulfur (S): 0.02% or less, and a balance of iron (Fe) and unavoidable impurities.
- C carbon
- Si silicon
- Mn manganese
- Cr chromium
- Cu copper
- Al aluminum
- the high-strength steel has a microstructure comprising, by area fraction, 20% or more of bainite, less than 80% of polygonal ferrite and acicular ferrite in total, and less than 10% of pearlite and MA as the other phases.
- the carbon (C) may be contained in an amount of 0.03% or more to less than 0.09%.
- the silicon (Si) may be contained in an amount of 0.2% or more to less than 0.8%.
- the copper (Cu) may be contained in an amount of 0.1% or more to less than 0.45%.
- the high-strength steel (or steel plate) for a structure may have yield strength of 500 MPa and tensile strength of 600 MPa.
- a method of manufacturing a high-strength steel (or steel plate) for a structure includes: reheating a slab to a temperature of 1000° C. or more to 1200° C. or less, the slab comprising, by weight, carbon (C): 0.03% or more to less than 0.1%, silicon (Si): 0.1% or more to less than 0.8%, manganese (Mn): 0.3% or more to less than 1.5%, chromium (Cr): 0.5% or more to less than 1.5%, copper (Cu): 0.1% or more to less than 0.5%, aluminum (Al): 0.01% or more to less than 0.08%, titanium (Ti): 0.01% or more to 0.1% or less, nickel (Ni): 0.05% or more to less than 0.1%, niobium (Nb): 0.002% or more to less than 0.07%, phosphorus (P): 0.03% or less, sulfur (S): 0.02% or less, and a balance of
- cooling a rolled steel plate from a cooling initiation temperature of 750° C. or more to a cooling finish temperature of 400° C. to 700° C. at a cooling rate of 10° C./sec or more.
- a steel (or steel plate) for a structure in which corrosion resistance of the steel itself is improved in seawater atmosphere, having excellent strength characteristics of yield strength of 500 MPa or more and tensile strength of 600 MPa or more may be provided.
- FIG. 1 is an image of Inventive Steel 4 observed with a microscope, in which (a) is an image obtained by observing a surface, (b) is an image obtained by observing a 1 ⁇ 4t portion in a thickness direction, and (c) is an image obtained by observing a 1 ⁇ 2t portion in the thickness direction.
- Example embodiments of the present disclosure may be modified in various forms, and the scope of the present disclosure should not be construed as being limited to the embodiments described below. These embodiments are provided to complete the present disclosure and to allow those skilled in the art to understand the scope of the disclosure.
- the present inventors have conducted deep research into a method of improving corrosion resistance of a steel (or steel plate) for a structure itself. As a result, the inventors have found that when the contents of chromium and copper are appropriately controlled and manufacturing conditions such as a reheating temperature, a finish rolling temperature, a cooling end temperature, and the like, are optimized to control a microstructure, excellent seawater-resistant characteristics and strength characteristic may be secured. Based on this knowledge, the inventors have invented the present invention.
- the high-strength steel (or steel plate) for a structure includes, by weight, carbon (C): 0.03% or more to less than 0.1%, silicon (Si): 0.1% or more to less than 0.8%, manganese (Mn): 0.3% or more to less than 1.5%, chromium (Cr): 0.5% or more to less than 1.5%, copper (Cu): 0.1% or more to less than 0.5%, aluminum (Al): 0.01% or more to less than 0.08%, titanium (Ti): 0.01% or more to 0.1% or less, nickel (Ni): 0.05% or more to less than 0.1%, niobium (Nb): 0.002% or more to less than 0.07%, phosphorus (P): 0.03% or less, sulfur (S): 0.02% or less, and a balance of iron (Fe) and unavoidable impurities
- Carbon (C) is an element added to improve strength.
- a content of carbon (C) is increased, hardenability may be increased to improve strength.
- general corrosion resistance is reduced.
- precipitation of carbide or the like is promoted, localized corrosion resistance is also affected.
- the content of carbon (C) should be decreased to improve the general corrosion resistance and the localized corrosion resistance.
- the content of carbon (C) is less than 0.03%, it is difficult to secure sufficient strength as a material for a steel (or steel plate) for a structure.
- the content of carbon (C) is 0.1% or more, weldability is deteriorated to be inappropriate for the steel (or steel plate) for a structure.
- the content of carbon (C) may be limited to 0.03% or more to less than 0.1%. From the viewpoint of corrosion resistance, the content of carbon (C) may be less than 0.09%. In some cases, the content of carbon (C) may be less than 0.08% to further prevent casting cracking and to reduce carbon equivalent.
- a lower limit of the content of carbon (C) may be, in detail, 0.035%.
- An upper limit of the content of carbon (C) may be, in detail, 0.06%. The upper limit of the content of carbon (C) may be, in further detail, 0.054%.
- Silicon (Si) needs to be present in amount of 0.1% or more to serve as a deoxidizer and to serve to increase strength of steel.
- silicon (Si) contributes to improvement in general corrosion resistance, it is advantageous to increase the content of silicon (Si).
- the content of silicon (Si) may be limited to, in detail, 0.1% or more to less than 0.8%.
- silicon (Si) is added in an amount of 0.2% or more to improve corrosion resistance.
- a lower limit of the content of silicon (Si) may be, in detail, 0.2%, and, in further detail, 0.27%.
- An upper limit of the content of silicon (Si) may be, in detail, 0.5% and, in further detail, 0.44%.
- Manganese (Mn) is an element effect in increasing the strength through solid-solution strengthening without reducing toughness.
- MN manganese
- an electrochemical reaction rate of a steel surface may be increased during a corrosion reaction to reduce corrosion resistance.
- manganese (Mn) is added in an amount of less than 0.3%, it may be difficult to secure durability of a steel plate for a structure. Meanwhile, when the content of manganese (Mn) is increased, hardenability may be increased to improve strength.
- manganese (Mn) when manganese (Mn) is added in an amount of 1.5% or more, a segregation zone may b significantly developed in a central portion of thickness during slab casting in a steelmaking process, weldability may be reduced, and corrosion resistance of a surface of a steel plate may be reduced. Therefore, the content of manganese (Mn) may be limited to, in detail, 0.3% or more to less than 1.5%.
- a lower limit of the content of manganese (Mn) may be, in detail, 0.4% and, in further detail, 0.5%.
- An upper limit of the content of manganese (Mn) may be, in detail, 1.4% and, in further detail, 0.9%.
- Chromium (Cr) is an element increasing the corrosion resistance by forming a chrome-containing oxide layer on a surface of the steel in a corrosive environment. Chromium (Cr) should be contained in an amount of 0.5 or more to exhibit a corrosion resistance effect depending on addition of chromium (Cr). However, when chromium (Cr) is contained in an amount of 1.5% or more, toughness and weldability are adversely affected. Therefore, the content of chromium (Cr) may be set to, in detail, be 0.5% or more to less than 1.5%. A lower limit of the content of chrome (Cr) may be, in detail, 0.6% and, in yet further detail, 1.2%.
- An upper limit of content of chrome (Cr) may be, in detail, 1.4%. That is, in the steel (or steel plate) for a structure according to an example embodiment, the content of chrome (Cr) may be, in detail, 1.2% or more to 1.4% or less (that is, 1.2% to 1.4%).
- copper (Cu) When copper (Cu) is contained in an amount of 0.05 wt % or more together with nickel (Ni), exudation of iron (Fe) is delayed, which is effective in improving general corrosion resistance and localized corrosion resistance.
- the content of copper (Cu) when the content of copper (Cu) is 0.5% or more, copper (Cu) in a liquid state melts into a grain boundary during production of a slab. Thus, cracking occurs during hot working (“hot shortness”). Therefore, the content of copper (Cu) may be limited to, in detail, 0.1% or more to less than 0.5%. In particular, a lower limit of the content of copper (Cu) may be, in detail, 0.2% and, in yet further detail, 0.28%.
- a frequency of occurrence of the surface cracking may vary depending on the content of each element, but the content of copper (Cu) may be set to be, in detail, less than 0.45% and, in yet further detail, 0.43% or less to significantly reduce possibility that surface cracking occurs, irrespective of the content of each element.
- Aluminum (Al) is an element added for deoxidation, and reacts with nitrogen (N) in the steel in such a manner that an aluminum nitride (AlN) is formed and austenite grains are refined to improve toughness.
- the content of aluminum (Al) in a dissolved state may be, in detail, 0.01% or more for sufficient deoxidation.
- a lower limit of the content of aluminum (Al) may be, in detail, 0.02% and, in further detail, 0.022%.
- the content of aluminum (Al) may be limited to, in detail, less than 0.08%.
- An upper limit of aluminum (Al) may be, in detail, 0.05% and, in further detail, 0.034%.
- Titanium (Ti) is bonded to carbon (C) in steel to form TiC when added in an amount of 0.01% or more, serving to improve strength due to a precipitation strengthening effect. Meanwhile, when the content of Ti is added in an amount of 0.1% or more, a strength improvement effect is not large, as compared with the increase in the content thereof. Accordingly, the content of titanium (Ti) may be limited to 0.01% or more to less than 0.1%. A lower limit of the content of titanium (Ti) may be, in detail, 0.015%. In addition, an upper limit of the content of titanium (Ti) may be, in further detail, 0.05%, and, in yet further detail, 0.028%.
- nickel (Ni) when nickel (Ni) is contained in an amount of 0.05% or more, it is effective in improving general corrosion resistance and localized corrosion resistance. Meanwhile, a lower limit of the content of Nickel (Ni) may be, in detail, 0.07%.
- nickel (Ni) when nickel (Ni) is added together with copper (Cu), nickel (Ni) reacts with copper (Cu) in such a manner that formation of a copper (Cu) phase is suppressed to prevent hot shortness from occurring. In most Cu-added steels, nickel (Ni) is generally added at one or more times of the content of copper (Cu).
- an element related to carbon equivalent such as carbon (C) or manganese (Mn)
- C carbon
- Mn manganese
- Cu copper
- an upper limit of the content of nickel (Ni) may be limited to, in detail, 0.1% in consideration of a relative addition effect.
- the upper limit of the content of nickel (Ni) may be, in further detail, 0.09%.
- Niobium (Nb) is an element bonded to carbon in steel to form NbC such as titanium (Ti), serving to strengthen precipitation.
- NbC such as titanium (Ti)
- Ti titanium
- the content of Nb may be limited to, in detail, 0.002% or more to less than 0.07%.
- a lower limit of the content of niobium (Nb) may be, in further detail, 0.01% and, in yet further detail, 0.017%.
- an upper limit of the content of niobium (Nb) may be, in further detail, 0.05% and, in yet further detail, 0.044%.
- Phosphorus (P) is present as an impurity element in steel.
- the phosphorous (P) is added in an amount greater than 0.03%, weldability is significantly reduced and toughness is deteriorated. Therefore, the content of phosphorous (P) is limited to, in detail, 0.03% or less.
- An upper limit of the content of phosphorous (P) may be, in detail, 0.02% and, in further detail, 0.018%. Since phosphorous (P) is an impurity, it is advantageous as the content of phosphorous (P) is reduced. Therefore, a lower limit of the content of phosphorous (P) is not separately limited.
- Sulfur (S) is present as an impurity in steel.
- the content of sulfur (S) is greater than 0.02%, ductility, impact toughness, and weldability of steel are deteriorated. Accordingly, the content of sulfur (S) may be limited to, in detail, 0.02% or less.
- Sulfur (S) is apt to react with manganese (Mn) to form an elongated inclusion such as manganese sulfide (MnS). And voids, formed on both ends of the elongated inclusion, may be an initiation point of localized corrosion. Therefore, an upper limit of the content of sulfur (S) may be limited to, in further detail, 0.01% and, in yet further detail, 0.008% or less.
- sulfur (S) is an impurity, it is advantageous as the content of sulfur (S) is reduced. Therefore, a lower limit of the content of sulfur (S) is not separately limited.
- a balance may be iron (Fe).
- Fe iron
- unintended impurities may be inevitably incorporated from raw materials or surrounding environments, so that they may not be excluded. Since these impurities are commonly known to those skilled in the art, and all contents thereof are not specifically mentioned in this specification.
- the high-strength steel (or steel plate) for a structure may have a microstructure including, by area fraction, 20% or more of bainite, less than 80% of polygonal ferrite and acicular ferrite in total, and less than 10% of pearlite and martensite-austenite (MA) as the other phases.
- a microstructure including, by area fraction, 20% or more of bainite, less than 80% of polygonal ferrite and acicular ferrite in total, and less than 10% of pearlite and martensite-austenite (MA) as the other phases.
- an area fraction of bainite may be, in detail, 20% or more, in further detail, 30% or more, and, in yet further detail, 51% or more.
- an area fraction of bainite may be 78% or less.
- an area fraction of bainite may be 68% or more to 71% or less.
- an area fraction of polygonal ferrite and acicular ferrite in total may be less than 80% and, in further detail, 45% or less.
- an area fraction of polygonal ferrite and acicular ferrite in total may be 10% or more and, in further detail, 19% or more.
- an area fraction of polygonal ferrite and acicular ferrite in total may be 25% or more to 30% or less and, in further detail, 27% or more to 30% or less.
- an area fraction of pearlite and martensite-austenite (MA) as the other phases may be less than 10%, in detail, 5% or less, in further detail, 4% or less, and, in yet further detail, 2% or less.
- thick steel plate strength of at least 500 MPa, in detail, 600 MPa or more should be secured to be used as a material of a high-strength steel plate for strength.
- a microstructure mainly included 20% or more of bainite and other phases of polygonal and/or acicular ferrite.
- pearlite and MA other phases, are contained in an amount of 10% or more, low-temperature toughness and corrosion resistance may be insufficient in an environment in which the steel (or steel plate) for a structure according to the present disclosure is used. Therefore, an upper limit of the area fraction of pearlite and MA may be less than 10%.
- the high-strength steel (or steel plate) for a structure according to an example embodiment may satisfy the above-mentioned composition system and microstructure to have yield strength of 500 MPa or more and tensile strength of 600 MPa or more.
- a method of manufacturing a high-strength steel (or steel plate) for a structure may include a slab reheating process, a hot rolling process, and a cooling process. Detailed conditions of each of the processes are as follows.
- a slab having the above-mentioned composition system is prepared, and then heated within a temperature range of 1000° C. to 1200° C.
- the reheating temperature may be set to 1000° C. or more to solid-solubilize carbonitride formed during casting.
- the reheating temperature may be set to, in further detail, 1050° C. or more to fully solid-solubilize the carbonitride.
- austenite may be formed to be coarse. Therefore, the reheating temperature may be, in detail, 1200° C. or less.
- a hot rolling process including rough rolling and finish rolling, may be performed on the reheated slab.
- the finish rolling may be completed, in detail, at 750° C. or more of finish rolling temperature.
- the finish rolling temperature is less than 750° C., it may cause a problem of producing a large amount of ferrite by air-cooling.
- the finish rolling temperature is more than 950 C, strength and toughness may be reduced due to structure coarseness. Therefore, the finish rolling temperature may be limited to, in detail, 750° C. to 950° C.
- the hot-rolled steel material is cooled through water cooling.
- a core technology is to secure high strength of even a thick steel plate through sufficient cooling, and it is necessary to perform a cooling process to a temperature of 700° C. or less at a cooling rate of 10° C. or more.
- the cooling process may be started at a cooling initiation temperature of 750° C. or more.
- micro-cracking may occur in a central portion due to a quenching process to cause deviation of material properties in a surface and a central portion of a product and a deviation of material properties in front/end portions of the product.
- the cooling process may be finished at temperature of, in detail, 400° C. or more.
- a steel plate rolled may be cooled, in detail, from the cooling initiation temperature of 750° C. or more to the cooling finish temperature of 400° C. to 700° C. at a cooling rate of 10° C./sec or more.
- a range of the cooling finish temperature may be, in further detail, 500° C. to 650° C. and, in yet further detail, 522° C. to 614° C.
- An upper limit of the cooling rate is mainly related to equipment capacity. When the cooling rate is 10° C./sec or more, a meaningful change in strength does not occur even with an increase in the cooling rate. Therefore, the upper limit of the cooling rate is not separately limited. On the other hand, a lower limit of the cooling rate may be, in detail, 20° C./sec, in further detail, 25° C./sec, and, in yet further detail, 30° C./sec.
- a slab was produced by preparing molten steel having a composition system listed in Table 1 below and then performing a continuous casting process. The produced slab was reheated, hot-rolled, and cooled under manufacturing conditions of Table 2 below to manufacture a steel plate.
- a microstructure of the manufactured steel plate was observed with optical and electron microscopes to measure an area fraction of each phase, and yield strength and tensile strength were measured through a tensile test and are listed in Table 3.
- a specimen was immersed in a 3.5% NaCl solution, simulating seawater. The specimen was inserted into an ultrasonic cleaner together with a 50% HCl+0.1% hexamethylene tetramine solution to be cleaned, and weight loss was measured and then divided by a surface area of an initial specimen to calculate a corrosion rate.
- a relative corrosion rate was evaluated based on the corrosion rate of Comparative Steel 1 as 100, and the results are listed in Table 3.
- Inventive Steels 1 to 4 had a microstructure having a low-temperature structure including 20% or more of bainite based on ferrite, and thus, had high strength of yield strength of 500 MPa or more and tensile strength of 600 MPa or more, so that they had a sufficient material of a steel (or steel plate) for a structure.
- Inventive Steels 1 to 4 satisfied the composition range specified in the present disclosure to exhibit a lower corrosion rate than Comparative Steel 1, and thus, may have sufficient lifespan in a seawater-resistant atmosphere.
- Comparative Steels 1 to 3 a composition range of Cr, Cu, Ni or Mn was outside the range of the present disclosure. For this reason, although Comparative Steels 1 to 3 were manufactured using a manufacturing method satisfying manufacturing conditions of the present disclosure, they exhibited a high corrosion rate of 100 or more. As a result, Comparative Steels 1 to 3 did not have sufficient lifespan in a sea-resistant atmosphere.
- a steel plate for a structure according to an example embodiment contained 1.2% or more to 1.4% or less of Cr to have most excellent lifespan characteristics in a seawater-resistant atmosphere.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
- The present disclosure relates to a steel fora structure having excellent corrosion resistance in an environment in which corrosion is accelerated by seawater, such as a steel plate for building structures on the coast, a ballast tank in a ship and related appurtenant equipment, or the like, and a method of manufacturing the steel.
- In general, corrosion of a metal is promoted when there are many inorganic substances in the form of ions dissolving easily in water, such as salt. In particular, in the case of ions having a property of promoting corrosion, such as chlorine ions (Cl−), significantly rapid corrosion may occur. Therefore, a metal containing an average of 3.5% NaCl corrodes in a seawater environment at a significantly high rate, so that corrosion is problematic under various conditions such as a structure adjacent to seawater and a ship sailing in a seawater environment, and the like.
- Accordingly, a corrosion inhibition technology using various types of anti-corrosion treatment has been proposed. However, since a term of such an anti-corrosion treatment is only 20 to 30 years, maintenance costs may be continuously incurred unless corrosion resistance of a material itself is secured. That is, in order to increase durability of a structure to a long period of 50 years or more and reduce various anti-corrosion costs during a management period of the structure, it is necessary to strengthen the corrosion resistance of the material itself.
- Among elements improving seawater resistance of a steel material, chromium (Cr) and copper (Cu) are most effective elements. Chromium and copper may play different roles depending on corrosive environments, and may exhibit an excellent anti-corrosion effect even in an environment, in which corrosion is accelerated by seawater, when added in an appropriate ratio. However, chromium does not have a significant effect in an acidic environment, and copper causes casting cracking to occur in a casting process, so that relatively expensive nickel should be added in a certain level or more. However, in most environments other than a strongly acidic environment, chromium has an effect of improving corrosion resistance, and the minimum amount of nickel added to prevent casting defects of copper-added steel may be reduced due to the recent development in continuous casting technology. Accordingly, the amount of expensive nickel added may be reduced, so that the cost of a product may be reduced.
- As the related art concerning a steel material having excellent resistance to seawater,
Patent Documents 1, 2, and 3 have been proposed.Patent Document 1 discloses that a composition system and manufacturing conditions are controlled to control a microstructure of a steel sheet, but it is difficult to secure strength when the content of a low-temperature structure is low (less than 20%). In addition, the content of nickel (Ni) is specified as being 0.05% or less, so that many casting defects may occur during casting. In the case of Patent Document 2, 0.1% or more of Al is added to form coarse oxide inclusions in a steelmaking process, and inclusions are crushed and elongated during a rolling process to form elongated inclusions. Accordingly, void formation is promoted to reduce localized corrosion resistance. In addition, when tungsten (W) is added as in the case of Patent Document 3, there are a risk of continuous casting defects and a risk of galvanic corrosion caused by formation of coarse precipitates. In addition, there is a risk that a structure is coarsened by air cooling to decrease strength. - Therefore, it may be difficult to internally secure corrosion resistance to seawater and strength in steel plates for structure according to
Patent Documents 1 to 3. - (Patent Document 1) Korean Patent Publication No. 10-2011-0076148
- (Patent Document 2) Korean Patent Publication No. 10-2011-0065949
- (Patent Document 3) Korean Patent Publication No. 10-2004-0054272
- An aspect of the present disclosure is to provide a steel plate, having excellent corrosion resistance to a seawater environment, in which corrosion characteristics and a microstructure of a surface of the steel plate are controlled through optimization of a composition system and manufacturing conditions to improve strength characteristics of the steel plate and to significantly reduce a corrosion rate.
- On the other hand, the feature of the present disclosure is not limited to the above description. It will be understood by those skilled in the art that there would be no difficulty in understanding additional features of the present disclosure.
- According to an aspect of the present disclosure, a high-strength steel (or steel plate) for structure comprising, by weight, carbon (C): 0.03% or more to less than 0.1%, silicon (Si): 0.1% or more to less than 0.8%, manganese (Mn): 0.3% or more to less than 1.5%, chromium (Cr): 0.5% or more to less than 1.5%, copper (Cu): 0.1% or more to less than 0.5%, aluminum (Al): 0.01% or more to less than 0.08%, titanium (Ti): 0.01% or more to 0.1% or less, nickel (Ni): 0.05% or more to less than 0.1%, niobium (Nb): 0.002% or more to less than 0.07%, phosphorus (P): 0.03% or less, sulfur (S): 0.02% or less, and a balance of iron (Fe) and unavoidable impurities. The high-strength steel has a microstructure comprising, by area fraction, 20% or more of bainite, less than 80% of polygonal ferrite and acicular ferrite in total, and less than 10% of pearlite and MA as the other phases.
- In the high-strength steel (or steel plate) for a structure, the carbon (C) may be contained in an amount of 0.03% or more to less than 0.09%.
- In the high-strength steel (or steel plate) for a structure, the silicon (Si) may be contained in an amount of 0.2% or more to less than 0.8%.
- In the high-strength steel (or steel plate) for a structure, the copper (Cu) may be contained in an amount of 0.1% or more to less than 0.45%.
- The high-strength steel (or steel plate) for a structure may have yield strength of 500 MPa and tensile strength of 600 MPa.
- According to an aspect of the present disclosure, a method of manufacturing a high-strength steel (or steel plate) for a structure includes: reheating a slab to a temperature of 1000° C. or more to 1200° C. or less, the slab comprising, by weight, carbon (C): 0.03% or more to less than 0.1%, silicon (Si): 0.1% or more to less than 0.8%, manganese (Mn): 0.3% or more to less than 1.5%, chromium (Cr): 0.5% or more to less than 1.5%, copper (Cu): 0.1% or more to less than 0.5%, aluminum (Al): 0.01% or more to less than 0.08%, titanium (Ti): 0.01% or more to 0.1% or less, nickel (Ni): 0.05% or more to less than 0.1%, niobium (Nb): 0.002% or more to less than 0.07%, phosphorus (P): 0.03% or less, sulfur (S): 0.02% or less, and a balance of iron (Fe) and unavoidable impurities; hot rolling the reheated slab within a finish rolling temperature of 750° C. or more to 950° C. or less; and cooling a rolled steel plate from a cooling initiation temperature of 750° C. or more to a cooling finish temperature of 400° C. to 700° C. at a cooling rate of 10° C./sec or more.
- The technical solutions to the above-mentioned problems do not fully enumerate all features of the present disclosure. Various features of the present disclosure and the resulting advantages and effects will be understood in more detail with reference to the following detailed examples.
- As set forth above, according to an example embodiment, a steel (or steel plate) for a structure, in which corrosion resistance of the steel itself is improved in seawater atmosphere, having excellent strength characteristics of yield strength of 500 MPa or more and tensile strength of 600 MPa or more may be provided.
- The various and beneficial advantages and effects of the present disclosure are not limited to the above description, and can be more easily understood in the course of describing a specific embodiment of the present disclosure.
-
FIG. 1 is an image of Inventive Steel 4 observed with a microscope, in which (a) is an image obtained by observing a surface, (b) is an image obtained by observing a ¼t portion in a thickness direction, and (c) is an image obtained by observing a ½t portion in the thickness direction. - Hereinafter, example embodiments of the present disclosure will be described below. Example embodiments of the present disclosure may be modified in various forms, and the scope of the present disclosure should not be construed as being limited to the embodiments described below. These embodiments are provided to complete the present disclosure and to allow those skilled in the art to understand the scope of the disclosure.
- The present inventors have conducted deep research into a method of improving corrosion resistance of a steel (or steel plate) for a structure itself. As a result, the inventors have found that when the contents of chromium and copper are appropriately controlled and manufacturing conditions such as a reheating temperature, a finish rolling temperature, a cooling end temperature, and the like, are optimized to control a microstructure, excellent seawater-resistant characteristics and strength characteristic may be secured. Based on this knowledge, the inventors have invented the present invention.
- Hereinafter, a high-strength steel (or steel plate) for a structure according to an example embodiment will be described in detail.
- High-Strength Steel (or Steel Plate) for Structure
- First, a composition system of a high-strength steel (or steel plate) fora structure according to an example embodiment will be described. The high-strength steel (or steel plate) for a structure includes, by weight, carbon (C): 0.03% or more to less than 0.1%, silicon (Si): 0.1% or more to less than 0.8%, manganese (Mn): 0.3% or more to less than 1.5%, chromium (Cr): 0.5% or more to less than 1.5%, copper (Cu): 0.1% or more to less than 0.5%, aluminum (Al): 0.01% or more to less than 0.08%, titanium (Ti): 0.01% or more to 0.1% or less, nickel (Ni): 0.05% or more to less than 0.1%, niobium (Nb): 0.002% or more to less than 0.07%, phosphorus (P): 0.03% or less, sulfur (S): 0.02% or less, and a balance of iron (Fe) and unavoidable impurities. Hereinafter, the unit of each alloy element is weight percentage (wt %).
- Carbon (C): 0.03% or More to Less than 0.1%
- Carbon (C) is an element added to improve strength. When a content of carbon (C) is increased, hardenability may be increased to improve strength. However, as the amount of added carbon is increased, general corrosion resistance is reduced. In addition, since precipitation of carbide or the like is promoted, localized corrosion resistance is also affected. The content of carbon (C) should be decreased to improve the general corrosion resistance and the localized corrosion resistance. However, when the content of carbon (C) is less than 0.03%, it is difficult to secure sufficient strength as a material for a steel (or steel plate) for a structure. When the content of carbon (C) is 0.1% or more, weldability is deteriorated to be inappropriate for the steel (or steel plate) for a structure. Therefore, the content of carbon (C) may be limited to 0.03% or more to less than 0.1%. From the viewpoint of corrosion resistance, the content of carbon (C) may be less than 0.09%. In some cases, the content of carbon (C) may be less than 0.08% to further prevent casting cracking and to reduce carbon equivalent. A lower limit of the content of carbon (C) may be, in detail, 0.035%. An upper limit of the content of carbon (C) may be, in detail, 0.06%. The upper limit of the content of carbon (C) may be, in further detail, 0.054%.
- Silicon (Si): 0.1% or More to Less than 0.8%
- Silicon (Si) needs to be present in amount of 0.1% or more to serve as a deoxidizer and to serve to increase strength of steel. In addition, since silicon (Si) contributes to improvement in general corrosion resistance, it is advantageous to increase the content of silicon (Si). However, when the content of silicon (Si) is 0.8% or more, toughness and weldability may be deteriorated and it may be difficult to detach a scale during rolling, so that the scale may causes surface defects. Therefore, the content of silicon (Si) may be limited to, in detail, 0.1% or more to less than 0.8%. In some cases, silicon (Si) is added in an amount of 0.2% or more to improve corrosion resistance. A lower limit of the content of silicon (Si) may be, in detail, 0.2%, and, in further detail, 0.27%. An upper limit of the content of silicon (Si) may be, in detail, 0.5% and, in further detail, 0.44%.
- Manganese (Mn): 0.3% or More to Less than 1.5%
- Manganese (Mn) is an element effect in increasing the strength through solid-solution strengthening without reducing toughness. However, when an excessive amount of manganese (MN) is added, an electrochemical reaction rate of a steel surface may be increased during a corrosion reaction to reduce corrosion resistance. When manganese (Mn) is added in an amount of less than 0.3%, it may be difficult to secure durability of a steel plate for a structure. Meanwhile, when the content of manganese (Mn) is increased, hardenability may be increased to improve strength. However, when manganese (Mn) is added in an amount of 1.5% or more, a segregation zone may b significantly developed in a central portion of thickness during slab casting in a steelmaking process, weldability may be reduced, and corrosion resistance of a surface of a steel plate may be reduced. Therefore, the content of manganese (Mn) may be limited to, in detail, 0.3% or more to less than 1.5%. On the other hand, a lower limit of the content of manganese (Mn) may be, in detail, 0.4% and, in further detail, 0.5%. An upper limit of the content of manganese (Mn) may be, in detail, 1.4% and, in further detail, 0.9%.
- Chromium (Cr): 0.5% or More to Less than 1.5%
- Chromium (Cr) is an element increasing the corrosion resistance by forming a chrome-containing oxide layer on a surface of the steel in a corrosive environment. Chromium (Cr) should be contained in an amount of 0.5 or more to exhibit a corrosion resistance effect depending on addition of chromium (Cr). However, when chromium (Cr) is contained in an amount of 1.5% or more, toughness and weldability are adversely affected. Therefore, the content of chromium (Cr) may be set to, in detail, be 0.5% or more to less than 1.5%. A lower limit of the content of chrome (Cr) may be, in detail, 0.6% and, in yet further detail, 1.2%. An upper limit of content of chrome (Cr) may be, in detail, 1.4%. That is, in the steel (or steel plate) for a structure according to an example embodiment, the content of chrome (Cr) may be, in detail, 1.2% or more to 1.4% or less (that is, 1.2% to 1.4%).
- Copper (Cu): 0.1% or More to Less than 0.5%
- When copper (Cu) is contained in an amount of 0.05 wt % or more together with nickel (Ni), exudation of iron (Fe) is delayed, which is effective in improving general corrosion resistance and localized corrosion resistance. However, when the content of copper (Cu) is 0.5% or more, copper (Cu) in a liquid state melts into a grain boundary during production of a slab. Thus, cracking occurs during hot working (“hot shortness”). Therefore, the content of copper (Cu) may be limited to, in detail, 0.1% or more to less than 0.5%. In particular, a lower limit of the content of copper (Cu) may be, in detail, 0.2% and, in yet further detail, 0.28%.
- Since surface cracking, occurring during production of the slab, interact with the contents of carbon (C), nickel (Ni), and manganese (Mn), a frequency of occurrence of the surface cracking may vary depending on the content of each element, but the content of copper (Cu) may be set to be, in detail, less than 0.45% and, in yet further detail, 0.43% or less to significantly reduce possibility that surface cracking occurs, irrespective of the content of each element.
- Aluminum (AL): 0.01% or More to Less than 0.08%
- Aluminum (Al) is an element added for deoxidation, and reacts with nitrogen (N) in the steel in such a manner that an aluminum nitride (AlN) is formed and austenite grains are refined to improve toughness. The content of aluminum (Al) in a dissolved state may be, in detail, 0.01% or more for sufficient deoxidation. A lower limit of the content of aluminum (Al) may be, in detail, 0.02% and, in further detail, 0.022%. When the aluminum (Al) is excessively included in an amount of 0.08% or more, a stretched inclusion, crushed and elongated during rolling, may be formed according to aluminum oxide-based characteristics. Since the formation of such an elongated inclusion promotes formation of a void around the inclusion and such a void may serve as an initiation point of localized corrosion, and the elongated inclusion serves to reduce the localized corrosion resistance. Therefore, the content of aluminum (Al) may be limited to, in detail, less than 0.08%. An upper limit of aluminum (Al) may be, in detail, 0.05% and, in further detail, 0.034%.
- Titanium (Ti): 0.01% or More to Less than 0.1%
- Titanium (Ti) is bonded to carbon (C) in steel to form TiC when added in an amount of 0.01% or more, serving to improve strength due to a precipitation strengthening effect. Meanwhile, when the content of Ti is added in an amount of 0.1% or more, a strength improvement effect is not large, as compared with the increase in the content thereof. Accordingly, the content of titanium (Ti) may be limited to 0.01% or more to less than 0.1%. A lower limit of the content of titanium (Ti) may be, in detail, 0.015%. In addition, an upper limit of the content of titanium (Ti) may be, in further detail, 0.05%, and, in yet further detail, 0.028%.
- Nickel (Ni): 0.05% or More to Less than 0.1%
- Similarly to the case of copper (Cu), when nickel (Ni) is contained in an amount of 0.05% or more, it is effective in improving general corrosion resistance and localized corrosion resistance. Meanwhile, a lower limit of the content of Nickel (Ni) may be, in detail, 0.07%. In addition, when nickel (Ni) is added together with copper (Cu), nickel (Ni) reacts with copper (Cu) in such a manner that formation of a copper (Cu) phase is suppressed to prevent hot shortness from occurring. In most Cu-added steels, nickel (Ni) is generally added at one or more times of the content of copper (Cu). However, as in the present disclosure, when the content of an element related to carbon equivalent, such as carbon (C) or manganese (Mn), is low and the content of chromium (Cr) is high, shortness may be sufficiently prevented even nickel (Ni) is added in less than half of the content of copper (Cu). In addition, since nickel (Ni) is an expensive element, an upper limit of the content of nickel (Ni) may be limited to, in detail, 0.1% in consideration of a relative addition effect. In addition, the upper limit of the content of nickel (Ni) may be, in further detail, 0.09%.
- Niobium (Nb): 0.002% or More to Less than 0.07%
- Niobium (Nb) is an element bonded to carbon in steel to form NbC such as titanium (Ti), serving to strengthen precipitation. When niobium (Nb) is added in an amount of 0.002% or more, Nb may effectively improve strength. However, when Nb is added in an amount of 0.07% or more, a strength improvement effect is not significantly large as compared with an increase in the content of niobium (Nb). Therefore, the content of Nb may be limited to, in detail, 0.002% or more to less than 0.07%. A lower limit of the content of niobium (Nb) may be, in further detail, 0.01% and, in yet further detail, 0.017%. In addition, an upper limit of the content of niobium (Nb) may be, in further detail, 0.05% and, in yet further detail, 0.044%.
- Phosphorus (P): 0.03% or Less
- Phosphorus (P) is present as an impurity element in steel. When the phosphorous (P) is added in an amount greater than 0.03%, weldability is significantly reduced and toughness is deteriorated. Therefore, the content of phosphorous (P) is limited to, in detail, 0.03% or less. An upper limit of the content of phosphorous (P) may be, in detail, 0.02% and, in further detail, 0.018%. Since phosphorous (P) is an impurity, it is advantageous as the content of phosphorous (P) is reduced. Therefore, a lower limit of the content of phosphorous (P) is not separately limited.
- Sulfur (S): 0.02% or Less
- Sulfur (S) is present as an impurity in steel. When the content of sulfur (S) is greater than 0.02%, ductility, impact toughness, and weldability of steel are deteriorated. Accordingly, the content of sulfur (S) may be limited to, in detail, 0.02% or less. Sulfur (S) is apt to react with manganese (Mn) to form an elongated inclusion such as manganese sulfide (MnS). And voids, formed on both ends of the elongated inclusion, may be an initiation point of localized corrosion. Therefore, an upper limit of the content of sulfur (S) may be limited to, in further detail, 0.01% and, in yet further detail, 0.008% or less. Since sulfur (S) is an impurity, it is advantageous as the content of sulfur (S) is reduced. Therefore, a lower limit of the content of sulfur (S) is not separately limited. In addition to the above-described alloy elements, a balance may be iron (Fe). However, in a common manufacturing process, unintended impurities may be inevitably incorporated from raw materials or surrounding environments, so that they may not be excluded. Since these impurities are commonly known to those skilled in the art, and all contents thereof are not specifically mentioned in this specification.
- The high-strength steel (or steel plate) for a structure according to an example embodiment may have a microstructure including, by area fraction, 20% or more of bainite, less than 80% of polygonal ferrite and acicular ferrite in total, and less than 10% of pearlite and martensite-austenite (MA) as the other phases.
- In the microstructure of the high-strength steel (or steel plate) for a structure according to an example embodiment, an area fraction of bainite may be, in detail, 20% or more, in further detail, 30% or more, and, in yet further detail, 51% or more.
- In the microstructure of the high-strength steel (or steel plate) for a structure according to an example embodiment, an area fraction of bainite may be 78% or less.
- In the microstructure of the high-strength steel (or steel plate) for a structure according to an example embodiment, an area fraction of bainite may be 68% or more to 71% or less.
- In the microstructure of the high-strength steel (or steel plate) for a structure according to an example embodiment, an area fraction of polygonal ferrite and acicular ferrite in total may be less than 80% and, in further detail, 45% or less.
- In the microstructure of the high-strength steel (or steel plate) for a structure according to an example embodiment, an area fraction of polygonal ferrite and acicular ferrite in total may be 10% or more and, in further detail, 19% or more.
- In the microstructure of the high-strength steel (or steel plate) for a structure according to an example embodiment, an area fraction of polygonal ferrite and acicular ferrite in total may be 25% or more to 30% or less and, in further detail, 27% or more to 30% or less.
- In the microstructure of the high-strength steel (or steel plate) for a structure according to an example embodiment, an area fraction of pearlite and martensite-austenite (MA) as the other phases may be less than 10%, in detail, 5% or less, in further detail, 4% or less, and, in yet further detail, 2% or less.
- In generally, thick steel plate strength of at least 500 MPa, in detail, 600 MPa or more should be secured to be used as a material of a high-strength steel plate for strength. To this end, a microstructure mainly included 20% or more of bainite and other phases of polygonal and/or acicular ferrite. When pearlite and MA, other phases, are contained in an amount of 10% or more, low-temperature toughness and corrosion resistance may be insufficient in an environment in which the steel (or steel plate) for a structure according to the present disclosure is used. Therefore, an upper limit of the area fraction of pearlite and MA may be less than 10%.
- The high-strength steel (or steel plate) for a structure according to an example embodiment may satisfy the above-mentioned composition system and microstructure to have yield strength of 500 MPa or more and tensile strength of 600 MPa or more.
- Hereinafter, a method of manufacturing a high-strength steel (or steel plate) for a structure according to an example embodiment of the present disclosure will be described.
- Method of Manufacturing High-Strength Steel (or Steel Plate) for Structure
- A method of manufacturing a high-strength steel (or steel plate) for a structure may include a slab reheating process, a hot rolling process, and a cooling process. Detailed conditions of each of the processes are as follows.
- Reheating of Slab
- A slab having the above-mentioned composition system is prepared, and then heated within a temperature range of 1000° C. to 1200° C. The reheating temperature may be set to 1000° C. or more to solid-solubilize carbonitride formed during casting. The reheating temperature may be set to, in further detail, 1050° C. or more to fully solid-solubilize the carbonitride. On the other hand, when the slab is reheated at significantly high temperature, austenite may be formed to be coarse. Therefore, the reheating temperature may be, in detail, 1200° C. or less.
- Hot Rolling
- A hot rolling process, including rough rolling and finish rolling, may be performed on the reheated slab. In this case, the finish rolling may be completed, in detail, at 750° C. or more of finish rolling temperature. When the finish rolling temperature is less than 750° C., it may cause a problem of producing a large amount of ferrite by air-cooling. On the other hand, when the finish rolling temperature is more than 950 C, strength and toughness may be reduced due to structure coarseness. Therefore, the finish rolling temperature may be limited to, in detail, 750° C. to 950° C.
- Cooling
- The hot-rolled steel material is cooled through water cooling. In the present disclosure, a core technology is to secure high strength of even a thick steel plate through sufficient cooling, and it is necessary to perform a cooling process to a temperature of 700° C. or less at a cooling rate of 10° C. or more. In addition, the cooling process may be started at a cooling initiation temperature of 750° C. or more. However, when the hot-rolled steel material is cooled to a temperature of less than 400° C., micro-cracking may occur in a central portion due to a quenching process to cause deviation of material properties in a surface and a central portion of a product and a deviation of material properties in front/end portions of the product. Therefore, the cooling process may be finished at temperature of, in detail, 400° C. or more. For example, in the cooling process, a steel plate rolled may be cooled, in detail, from the cooling initiation temperature of 750° C. or more to the cooling finish temperature of 400° C. to 700° C. at a cooling rate of 10° C./sec or more. In particular, a range of the cooling finish temperature may be, in further detail, 500° C. to 650° C. and, in yet further detail, 522° C. to 614° C.
- An upper limit of the cooling rate is mainly related to equipment capacity. When the cooling rate is 10° C./sec or more, a meaningful change in strength does not occur even with an increase in the cooling rate. Therefore, the upper limit of the cooling rate is not separately limited. On the other hand, a lower limit of the cooling rate may be, in detail, 20° C./sec, in further detail, 25° C./sec, and, in yet further detail, 30° C./sec.
- Hereinafter, embodiments of the present disclosure will be described more specifically through examples. However, the examples are for clearly explaining the embodiments of the present disclosure and are not intended to limit the scope of the present disclosure.
- A slab was produced by preparing molten steel having a composition system listed in Table 1 below and then performing a continuous casting process. The produced slab was reheated, hot-rolled, and cooled under manufacturing conditions of Table 2 below to manufacture a steel plate.
- A microstructure of the manufactured steel plate was observed with optical and electron microscopes to measure an area fraction of each phase, and yield strength and tensile strength were measured through a tensile test and are listed in Table 3. In addition, as an evaluation of seawater-resistant characteristics, a specimen was immersed in a 3.5% NaCl solution, simulating seawater. The specimen was inserted into an ultrasonic cleaner together with a 50% HCl+0.1% hexamethylene tetramine solution to be cleaned, and weight loss was measured and then divided by a surface area of an initial specimen to calculate a corrosion rate. In addition, to compare corrosion rates of comparative steels and inventive steels, a relative corrosion rate was evaluated based on the corrosion rate of
Comparative Steel 1 as 100, and the results are listed in Table 3. -
TABLE 1 C Si Mn P S Sol.Al Cu Ni Cr Nb Ti IS1 0.041 0.27 0.8 0.008 0.005 0.022 0.43 0.08 1.2 0.044 0.015 IS2 0.035 0.44 0.9 0.018 0.007 0.024 0.28 0.09 1.4 0.032 0.018 IS3 0.054 0.27 0.7 0.012 0.006 0.034 0.32 0.09 0.6 0.041 0.022 IS4 0.052 0.32 0.5 0.011 0.008 0.028 0.29 0.07 1.0 0.017 0.028 CS1 0.068 0.51 1.8 0.008 0.007 0.029 0.12 0.06 0.4 0.009 0.019 CS2 0.092 0.27 2.1 0.009 0.005 0.042 0.04 0.08 0.2 0.026 0.024 CS3 0.049 0.51 2.2 0.018 0.007 0.024 0.07 0.12 0.7 0.047 0.021 IS: Inventive Steel CS: Comparative Steel -
TABLE 2 Finishing Cooling Cooling Reheating Rolling Initiation Finish Cooling Temperature Temperature Temperature Temperature Rate (° C.) (° C.) (° C.) (° C.) (° C./sec) IS1 1142 870 774 542 36 IS2 1129 901 784 614 42 IS3 1161 840 754 601 39 IS4 1112 904 787 522 44 CS1 1119 875 769 565 15 CS2 1124 891 771 579 23 CS3 1151 880 773 612 14 IS: Inventive Steel CS: Comparative Steel -
TABLE 3 area fraction of a microstructure (%) polygonal the other ferrite + phases Yield Tensile Relative acicular (pearlite, Strength Strength Corrosion bainite ferrite MA) (MPa) (MPa) Rate IS1 71 27 2 564 636 66 IS2 68 30 2 512 608 64 IS3 51 45 4 574 678 71 IS4 78 19 3 551 643 77 CS1 64 34 2 574 671 100 CS2 57 39 4 564 659 137 CS3 63 33 4 592 702 143 IS: Inventive Steel CS: Comparative Steel - As can be seen from Table 1, all of
Inventive Steels 1 to 4 satisfied the composition range specified in the present disclosure. Meanwhile, inComparative Steels 1 to 3, a composition range of Cr, Cu, Ni or Mn was outside the range of the present disclosure. - As a result,
Inventive Steels 1 to 4 had a microstructure having a low-temperature structure including 20% or more of bainite based on ferrite, and thus, had high strength of yield strength of 500 MPa or more and tensile strength of 600 MPa or more, so that they had a sufficient material of a steel (or steel plate) for a structure. In addition, it was confirmed thatInventive Steels 1 to 4 satisfied the composition range specified in the present disclosure to exhibit a lower corrosion rate thanComparative Steel 1, and thus, may have sufficient lifespan in a seawater-resistant atmosphere. - Meanwhile, in
Comparative Steels 1 to 3, a composition range of Cr, Cu, Ni or Mn was outside the range of the present disclosure. For this reason, althoughComparative Steels 1 to 3 were manufactured using a manufacturing method satisfying manufacturing conditions of the present disclosure, they exhibited a high corrosion rate of 100 or more. As a result,Comparative Steels 1 to 3 did not have sufficient lifespan in a sea-resistant atmosphere. - It was confirmed that
Inventive Steels 1 and 2, containing 1.2% or more to 1.4% or less of Cr, exhibited a lower corrosion rate than Inventive Steels 3 and 4, not containing 1.2% or more to 1.4% or less of Cr. - From the above, it was confirmed that a steel plate for a structure according to an example embodiment contained 1.2% or more to 1.4% or less of Cr to have most excellent lifespan characteristics in a seawater-resistant atmosphere.
- While this disclosure includes specific examples, it will be apparent after gaining an understanding of the disclosure of this application that various changes in forms and details may be made in these examples without departing from the spirit and scope of the claims and their equivalents. The examples described herein are to be considered in a descriptive sense only, and not for purposes of limitation. Descriptions of features or aspects in each example are to be considered as being applicable to similar features or aspects in other examples. Suitable results may be achieved if the described techniques are performed in a different order, and/or if components in a described system, architecture, device, or circuit are combined in a different manner, and/or replaced or supplemented by other components or their equivalents. Therefore, the scope of the disclosure is defined not by the detailed description, but by the claims and their equivalents, and all variations within the scope of the claims and their equivalents are to be construed as being included in the disclosure.
Claims (6)
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1020180136846A KR102142774B1 (en) | 2018-11-08 | 2018-11-08 | High strength steel plate for structure with a good seawater corrosion resistive property and method of manufacturing thereof |
KR10-2018-0136846 | 2018-11-08 | ||
PCT/KR2019/015124 WO2020096398A1 (en) | 2018-11-08 | 2019-11-08 | High strength steel plate for structure with good seawater corrosion resistant property and method of manufacturing same |
Publications (1)
Publication Number | Publication Date |
---|---|
US20210388458A1 true US20210388458A1 (en) | 2021-12-16 |
Family
ID=70612140
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US17/291,823 Pending US20210388458A1 (en) | 2018-11-08 | 2019-11-08 | High strength steel plate for structure with good seawater corrosion resistant property and method of manufacturing same |
Country Status (6)
Country | Link |
---|---|
US (1) | US20210388458A1 (en) |
EP (1) | EP3878996A4 (en) |
JP (1) | JP7332692B2 (en) |
KR (1) | KR102142774B1 (en) |
CN (1) | CN112969809B (en) |
WO (1) | WO2020096398A1 (en) |
Family Cites Families (25)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06316723A (en) * | 1993-03-12 | 1994-11-15 | Kobe Steel Ltd | Production of weather resistant refractory steel material for building construction, excellent in gas cutting property and weldability |
JPH07216500A (en) * | 1994-01-28 | 1995-08-15 | Sumitomo Metal Ind Ltd | High strength steel material excellent in corrosion resistance and its production |
KR100371960B1 (en) * | 2000-09-29 | 2003-02-14 | 주식회사 포스코 | High atmosphere corrosion resting and workability hot rolled strip having tensile strength of 60 kg/㎟ and method for manufacturing it |
KR20040054272A (en) | 2002-12-18 | 2004-06-25 | 주식회사 포스코 | Method of manufacturing piping steel of a ship with a good seawater resistive property |
US8038809B2 (en) * | 2005-03-28 | 2011-10-18 | Kobe Steel, Ltd. | High strength hot rolled steel sheet excellent in bore expanding workability and method for production thereof |
KR100815709B1 (en) * | 2006-12-12 | 2008-03-20 | 주식회사 포스코 | Formable high strength cold-rolled steel sheet with excellent weather resistance and method manufacturing the same |
KR101018159B1 (en) * | 2008-05-15 | 2011-02-28 | 주식회사 포스코 | High-strength steel sheet with excellent low temperature toughness and manufacturing method thereof |
ES2402548T3 (en) * | 2007-12-04 | 2013-05-06 | Posco | Steel sheet with high strength and excellent low temperature hardness and method of manufacturing it |
KR100951296B1 (en) * | 2007-12-04 | 2010-04-02 | 주식회사 포스코 | Steel plate for linepipe having high strength and excellent low temperature toughness and manufacturing method of the same |
KR101125886B1 (en) * | 2008-11-29 | 2012-03-21 | 주식회사 포스코 | High strength ship-building steel with excellent general corrosion and pitting corrosion resistance at low ph chloride solution and excellent haz toughness and manufacturing method for the same |
CN102119236B (en) * | 2009-10-28 | 2013-07-10 | 新日铁住金株式会社 | Steel plate for line pipes with excellent strength and ductility and process for production of same |
KR101289124B1 (en) | 2009-12-10 | 2013-07-23 | 주식회사 포스코 | Ship-building steel with excellent corrosion resistance at sea water |
KR101289154B1 (en) | 2009-12-29 | 2013-07-23 | 주식회사 포스코 | Hot rolled steel sheet having excellent corrosion resistance and impcat toughness and manufacturing method thereof |
JP5573265B2 (en) | 2010-03-19 | 2014-08-20 | Jfeスチール株式会社 | High strength thick steel plate excellent in ductility with a tensile strength of 590 MPa or more and method for producing the same |
US10000829B2 (en) | 2013-04-15 | 2018-06-19 | Nippon Steel & Sumitomo Metal Corporation | Hot-rolled steel sheet |
KR101536471B1 (en) * | 2013-12-24 | 2015-07-13 | 주식회사 포스코 | Ultra-high strength steel sheet for welding structure with superior haz toughness for high heat input welding and method for manufacturing the same |
KR20150112517A (en) * | 2014-03-28 | 2015-10-07 | 현대제철 주식회사 | Steel sheet for line pipe and method of manufacturing the same |
CN106480374B (en) * | 2015-08-31 | 2018-04-24 | 鞍钢股份有限公司 | A kind of cold-resistant pipeline high tenacity low yield strength ratio hot-rolled thick plank and its production method |
CN105441799B (en) * | 2015-11-25 | 2017-05-24 | 武汉钢铁(集团)公司 | High-toughness and low-yield-ratio quenched and tempered steel plate used in low-temperature environment and manufacturing method of high-toughness and low-yield-ratio quenched and tempered steel plate |
JP6766642B2 (en) | 2016-02-25 | 2020-10-14 | 日本製鉄株式会社 | Steel sheet with excellent brittle crack propagation stop characteristics and its manufacturing method |
JP6911575B2 (en) | 2016-06-30 | 2021-07-28 | 日本製鉄株式会社 | Steel sheet with excellent brittle crack propagation stop characteristics and its manufacturing method |
KR101889182B1 (en) * | 2016-12-20 | 2018-08-16 | 주식회사 포스코 | Steel plate for welded steel pipe having excellent elogation of the longitudinal direction and toughness at low-temperature, method for manufacturing thereof and welded steel pipe using same |
KR101899689B1 (en) | 2016-12-23 | 2018-09-17 | 주식회사 포스코 | Steel plate for welded steel pipe having excellent elogation of the longitudinal direction, method for manufacturing thereof and welded steel pipe using same |
CN108728733A (en) * | 2017-04-24 | 2018-11-02 | 鞍钢股份有限公司 | Convey natural gas from coal X70 Pipeline Steel Plates and its manufacturing method |
CN108467993B (en) * | 2018-06-11 | 2020-02-18 | 鞍钢股份有限公司 | Ultra-wide high-toughness hot-rolled thick plate for low-temperature pipeline and production method thereof |
-
2018
- 2018-11-08 KR KR1020180136846A patent/KR102142774B1/en active IP Right Grant
-
2019
- 2019-11-08 CN CN201980073445.3A patent/CN112969809B/en active Active
- 2019-11-08 JP JP2021524195A patent/JP7332692B2/en active Active
- 2019-11-08 US US17/291,823 patent/US20210388458A1/en active Pending
- 2019-11-08 EP EP19883204.0A patent/EP3878996A4/en active Pending
- 2019-11-08 WO PCT/KR2019/015124 patent/WO2020096398A1/en unknown
Also Published As
Publication number | Publication date |
---|---|
EP3878996A1 (en) | 2021-09-15 |
JP2022506661A (en) | 2022-01-17 |
CN112969809B (en) | 2023-12-15 |
WO2020096398A1 (en) | 2020-05-14 |
KR20200053342A (en) | 2020-05-18 |
JP7332692B2 (en) | 2023-08-23 |
EP3878996A4 (en) | 2022-01-05 |
CN112969809A (en) | 2021-06-15 |
KR102142774B1 (en) | 2020-08-07 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US20200087764A1 (en) | High-strength steel sheet | |
KR101989726B1 (en) | High-strength steel sheet and production method therefor | |
JP5195413B2 (en) | High-strength hot-rolled steel sheet excellent in bending workability and toughness anisotropy and method for producing the same | |
KR100371960B1 (en) | High atmosphere corrosion resting and workability hot rolled strip having tensile strength of 60 kg/㎟ and method for manufacturing it | |
US20160199892A1 (en) | High-strength hot-rolled plated steel sheet and method for manufacturing the same | |
JP2017002332A (en) | High strength steel sheet excellent in processability and manufacturing method therefor | |
US20210388458A1 (en) | High strength steel plate for structure with good seawater corrosion resistant property and method of manufacturing same | |
KR20160025185A (en) | High strength plated hot-rolled steel sheet and method of manufacturing the same | |
CN111349850B (en) | High-corrosion-resistance weather-resistant steel and manufacturing method thereof | |
CN114761598B (en) | Steel sheet for structure having excellent seawater corrosion resistance and method for producing same | |
CN114008232B (en) | High-strength structural steel having excellent corrosion resistance and method for producing same | |
KR101185222B1 (en) | Api hot-rolled steel sheet with high strength and method for manufacturing the api hot-rolled steel sheet | |
KR101185232B1 (en) | Api hot-rolled steel with high strength and high toughness and method for manufacturing the api hot-rolled steel | |
CN113227426B (en) | Structural steel with excellent brittle fracture resistance and method for manufacturing the same | |
KR101467030B1 (en) | Method for manufacturing high strength steel plate | |
KR101546147B1 (en) | High strength steel plate and method for manufacturing the same | |
KR101505278B1 (en) | Steel for cargo oil tank and method of manufacturing the same | |
KR101443443B1 (en) | High strength steel plate and method for manufacturing the same | |
JP2023554299A (en) | High strength steel plate with excellent ductility and its manufacturing method | |
KR20140119898A (en) | Hot-rolled steel and method of manufacturing the same | |
KR20120044121A (en) | High strength api hot-rolled steel sheet with low yield ratio and method for manufacturing the api hot-rolled steel sheet | |
KR20110108787A (en) | High strength hot rolled steel sheet with excellent balance between strength and ductility and method of manufacturing the steel sheet | |
KR20120044126A (en) | Hot-rolled steel sheet for line pipe with excellent spiral weldability and method for manufacturing the hot-rolled steel sheet |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
AS | Assignment |
Owner name: POSCO, KOREA, REPUBLIC OF Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:PARK, JIN-HO;YI, JU-YEON;YU, SENG-HO;AND OTHERS;SIGNING DATES FROM 20210413 TO 20210420;REEL/FRAME:057112/0983 |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: DOCKETED NEW CASE - READY FOR EXAMINATION |
|
AS | Assignment |
Owner name: POSCO HOLDINGS INC., KOREA, REPUBLIC OF Free format text: CHANGE OF NAME;ASSIGNOR:POSCO;REEL/FRAME:061561/0730 Effective date: 20220302 |
|
AS | Assignment |
Owner name: POSCO CO., LTD, KOREA, REPUBLIC OF Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNOR:POSCO HOLDINGS INC.;REEL/FRAME:061777/0937 Effective date: 20221019 |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: NON FINAL ACTION MAILED |
|
STPP | Information on status: patent application and granting procedure in general |
Free format text: NON FINAL ACTION MAILED |