EP3246426B1 - Method for manufacturing a thick high-toughness high-strength steel sheet - Google Patents
Method for manufacturing a thick high-toughness high-strength steel sheet Download PDFInfo
- Publication number
- EP3246426B1 EP3246426B1 EP16737217.6A EP16737217A EP3246426B1 EP 3246426 B1 EP3246426 B1 EP 3246426B1 EP 16737217 A EP16737217 A EP 16737217A EP 3246426 B1 EP3246426 B1 EP 3246426B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- less
- steel
- temperature
- toughness
- thickness
- 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.)
- Active
Links
- 229910000831 Steel Inorganic materials 0.000 title claims description 158
- 239000010959 steel Substances 0.000 title claims description 158
- 238000000034 method Methods 0.000 title claims description 20
- 238000004519 manufacturing process Methods 0.000 title claims description 19
- 238000003303 reheating Methods 0.000 claims description 51
- 239000010953 base metal Substances 0.000 claims description 33
- 238000001816 cooling Methods 0.000 claims description 31
- 230000009467 reduction Effects 0.000 claims description 26
- 238000005096 rolling process Methods 0.000 claims description 25
- 238000010438 heat treatment Methods 0.000 claims description 23
- 230000001186 cumulative effect Effects 0.000 claims description 15
- 238000009864 tensile test Methods 0.000 claims description 12
- 229910045601 alloy Inorganic materials 0.000 claims description 10
- 239000000956 alloy Substances 0.000 claims description 10
- 238000005242 forging Methods 0.000 claims description 10
- 238000005496 tempering Methods 0.000 claims description 10
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 9
- 238000005098 hot rolling Methods 0.000 claims description 8
- 229910052748 manganese Inorganic materials 0.000 claims description 7
- 229910052804 chromium Inorganic materials 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims description 6
- 229910052759 nickel Inorganic materials 0.000 claims description 6
- 229910052720 vanadium Inorganic materials 0.000 claims description 6
- 229910052796 boron Inorganic materials 0.000 claims description 5
- 229910052791 calcium Inorganic materials 0.000 claims description 5
- 229910052758 niobium Inorganic materials 0.000 claims description 5
- 229910052719 titanium Inorganic materials 0.000 claims description 5
- 229910052727 yttrium Inorganic materials 0.000 claims description 5
- 229910052726 zirconium Inorganic materials 0.000 claims description 5
- 229910052715 tantalum Inorganic materials 0.000 claims 4
- 238000010791 quenching Methods 0.000 description 56
- 230000000171 quenching effect Effects 0.000 description 56
- 230000000694 effects Effects 0.000 description 14
- 238000003466 welding Methods 0.000 description 13
- 238000007711 solidification Methods 0.000 description 12
- 230000008023 solidification Effects 0.000 description 12
- 230000015572 biosynthetic process Effects 0.000 description 10
- 239000000463 material Substances 0.000 description 8
- 239000000203 mixture Substances 0.000 description 8
- 229910001566 austenite Inorganic materials 0.000 description 7
- 238000012360 testing method Methods 0.000 description 7
- 238000005275 alloying Methods 0.000 description 6
- 238000004364 calculation method Methods 0.000 description 6
- 238000005266 casting Methods 0.000 description 6
- 229910000734 martensite Inorganic materials 0.000 description 5
- 229910052799 carbon Inorganic materials 0.000 description 4
- 238000010276 construction Methods 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 3
- 229910001563 bainite Inorganic materials 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000003247 decreasing effect Effects 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 238000009863 impact test Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000007787 solid Substances 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000005265 energy consumption Methods 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- 238000009659 non-destructive testing Methods 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 230000008439 repair process Effects 0.000 description 2
- 238000004088 simulation Methods 0.000 description 2
- 238000012546 transfer Methods 0.000 description 2
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- ZPUCINDJVBIVPJ-LJISPDSOSA-N cocaine Chemical compound O([C@H]1C[C@@H]2CC[C@@H](N2C)[C@H]1C(=O)OC)C(=O)C1=CC=CC=C1 ZPUCINDJVBIVPJ-LJISPDSOSA-N 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- NRNCYVBFPDDJNE-UHFFFAOYSA-N pemoline Chemical compound O1C(N)=NC(=O)C1C1=CC=CC=C1 NRNCYVBFPDDJNE-UHFFFAOYSA-N 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000005855 radiation Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/38—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling sheets of limited length, e.g. folded sheets, superimposed sheets, pack 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing 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
- C22C38/42—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
-
- 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
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
- B21B1/024—Forging or pressing
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
- B21B1/026—Rolling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/02—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling heavy work, e.g. ingots, slabs, blooms, or billets, in which the cross-sectional form is unimportant ; Rolling combined with forging or pressing
- B21B2001/028—Slabs
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- 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
- C21D2211/008—Martensite
-
- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
-
- 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
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
-
- 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
Definitions
- the present invention relates to a method for manufacturing a thick-walled high-toughness high-strength steel plate for use in steel structures in construction, bridges, shipbuilding, offshore structures, construction and industrial machinery, tanks, penstocks, and the like.
- the surface of the steel plate has high toughness
- the inner part of the steel plate has high strength and toughness.
- the steel plate has a thickness of 100 mm or more and a yield strength of 620 MPa or more.
- steel for use in construction, bridges, shipbuilding, offshore structures, construction and industrial machinery, tanks, penstocks, and other fields is welded to have a desired shape.
- the strength and thickness of steel to be used have also been greatly increased.
- the cooling rate is higher on the surface of a steel plate than in the half-thickness portion.
- a martensite structure having low toughness is formed on the surface of the steel plate.
- a high-strength steel plate having a thickness of 100 mm or more rarely has both high surface toughness and high strength and toughness of the inner part thereof.
- Non Patent Literature 1 describes a material having a thickness of 210 mm
- Non Patent Literature 2 describes a material having a thickness of 180 mm.
- CN 102605280 A describes a method for manufacturing an ultra-thick high-strength high low-temperature toughness steel plate for ocean platforms, wherein the steel plate comprises, in weight percentage, 0.10-0.24% of C, 0.05-0.35% of Si, 0.60-1.15% of Mn, not more than 0.015% of P, not more than 0.005% of S, 0.01-0.030% of Ti, 1.45-1.75% of Cr, 0.15-0.44% of Mo, 0.80-2.50% of Ni, 0.010-0.070% of Nb, 0.020-0.080% of V, 0.02-0.06% of Alt, 0.001-0.004% of Ca, not more than 0.006% of N, 0.0007-0.0030% of B, the balance being Fe and unavoidable impurities and whereing the steel plate has a system of C, Ni-Cr-Mo alloyed and Nb-V-Ti microalloyed, and has a yield strength not smaller than 690MPa, a tensile strength not smaller than 770MPa
- the present invention has been made to solve such problems and aims to provide a method for manufacturing a thick-walled high-toughness high-strength steel plate that has high surface toughness and high strength and toughness of the inner part thereof.
- the present inventors have extensively studied the microstructure control factors that satisfy high toughness of the surface of a thick-walled steel plate having a yield strength of 620 MPa or more and a thickness of 100 mm or more and also satisfy high strength and toughness of the half-thickness portion of the thick-walled steel plate, and have found the following.
- the present invention provides a method for manufacturing a thick-walled high-toughness high-strength steel plate having a thickness of 100 mm or more and having a yield strength of 620 MPa or more and high toughness.
- the thick-walled high-toughness high-strength steel plate can be used to manufacture steel structures having high safety.
- a thick-walled high-toughness high-strength steel plate manufactured according to the present invention has a composition containing, on a mass percent basis, C: 0.08% to 0.20%, Si: 0.40% or less (including 0%), Mn: 0.5% to 5.0%, P: 0.010% or less (including 0%), S: 0.0050% or less (including 0%), Cr: 3.0% or less (including 0%), Ni: 0.1% to 5.0%, Al: 0.010% to 0.080%, N: 0.0070% or less (including 0%), and O: 0.0025% or less (including 0%).
- the symbol "%" in the component content refers to "% by mass”.
- C is an element useful for achieving the strength necessary for structural steel at low cost. This effect requires a C content of 0.08% or more. In a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding, however, a C content of more than 0.20% significantly deteriorates toughness of the base metal and weld. Thus, the C content has an upper limit of 0.20%. The C content preferably ranges from 0.08% to 0.14%.
- Si is added for deoxidation.
- a steel plate according to the present invention does not necessarily contain Si.
- a Si content of more than 0.40% significantly deteriorates toughness of the base metal and heat-affected zone.
- the Si content is 0.40% or less, preferably 0.05% to 0.3%, more preferably 0.1% to 0.3%.
- Mn is added to ensure high strength of the base metal. This effect is insufficient at a Mn content of less than 0.5%.
- a Mn content of more than 5.0% promotes center segregation, results in a larger casting defect of the slab, and deteriorates mechanical properties of the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding.
- the Mn content has an upper limit of 5.0%.
- the Mn content preferably ranges from 0.6% to 2%, more preferably 0.6% to 1.6%.
- a P content of more than 0.010% significantly deteriorates toughness of the base metal and heat-affected zone.
- the P content is preferably minimized (may be zero) and is limited to 0.010% or less.
- a S content of more than 0.0050% significantly deteriorates toughness of the base metal and heat-affected zone.
- the S content is preferably minimized (may be zero) and is 0.0050% or less.
- the Cr is an element effective in strengthening the base metal. However, an excessively high Cr content deteriorates weldability. Thus, the Cr content is 3.0% or less, preferably 0.1% to 2%, more preferably 0.7% to 1.7%. The Cr content may be 0%.
- Ni is an element useful for improving the strength of steel and the toughness of the heat-affected zone. This effect requires a Ni content of 0.1% or more. However, a Ni content of more than 5.0% significantly deteriorates economic efficiency. Thus, the Ni content has an upper limit of 5.0%.
- the Ni content preferably ranges from 0.4% to 4%, more preferably 0.8% to 3.8%.
- Al is added for sufficient deoxidation of molten steel.
- An Al content of less than 0.010% is insufficient for the effect.
- an Al content of more than 0.080% deteriorates toughness of the base metal due to an increased dissolved Al content in the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding.
- the Al content is 0.080% or less, preferably 0.030% to 0.080%, more preferably 0.030% to 0.070%.
- N together with Ti, forms a nitride and thereby performs refinement of the structure and improves the toughness of the base metal and heat-affected zone in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding.
- the toughness can be improved by a constituent other than N.
- a steel plate according to the present invention does not necessarily contain N.
- the N content is preferably 0.0015% or more.
- a N content of more than 0.0070% deteriorates toughness of the base metal due to an increased dissolved N content in the base metal and deteriorates toughness of the heat-affected zone due to the formation of coarse carbonitride.
- the N content is 0.0070% or less, preferably 0.006% or less, more preferably 0.005% or less.
- O content of more than 0.0025% significantly deteriorates toughness due to the formation of a hard oxide in steel.
- the O content is preferably minimized (may be zero) and is 0.0025% or less.
- a thick-walled high-toughness high-strength steel plate manufactured according to the present invention can contain at least one of Cu, Mo, V, Nb, and Ti in order to further improve strength and/or toughness.
- Cu can improve the strength of steel without reducing toughness.
- a Cu content of more than 0.50% may cause a crack on the surface of a steel plate during hot working.
- the Cu content, if any, is 0.50% or less.
- Mo contributes to high strength of the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding.
- a Mo content of more than 1.50% results in increased hardness and deteriorates toughness due to the precipitation of alloy carbide.
- the Mo content if any, has an upper limit of 1.50%.
- the Mo content preferably ranges from 0.2% to 0.8%.
- V 0.400% or less
- V contributes to improved strength and toughness of the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding.
- V precipitates as VN and is effective in decreasing the amount of dissolved N.
- a V content of more than 0.400% deteriorates toughness due to the precipitation of hard VC.
- the V content, if any, is preferably 0.400% or less, more preferably 0.01% to 0.1%.
- Nb is effective in improving the strength of the base metal.
- a Nb content of more than 0.100% deteriorates toughness of the base metal.
- the Nb content has an upper limit of 0.100%.
- the Nb content is preferably 0.025% or less.
- Ti forms TiN during heating and effectively suppresses the coarsening of austenite.
- Ti improves the toughness of the base metal and heat-affected zone.
- a Ti content of more than 0.020% results in coarsening of Ti nitride and deteriorates toughness of the base metal.
- the Ti content if any, ranges from 0.005% to 0.020%, preferably 0.008% to 0.015%.
- a thick-walled high-toughness high-strength steel plate manufactured according to the present invention can further contain at least one of Mg, Ta, Zr, Y, B, Ca, and REM to improve the material quality.
- Mg forms a stable oxide at high temperatures, effectively suppresses the coarsening of prior ⁇ grains in the heat-affected zone, and is effective in improving the toughness of the weld.
- These effects require a Mg content of 0.0001% or more.
- a Mg content of more than 0.0050% results in an increased number of inclusions and deteriorates toughness.
- the Mg content, if any, is preferably 0.0050% or less, more preferably 0.0001% to 0.015%.
- Ta 0.01% to 0.20%
- Ta content 0.01% or more is effective.
- a Ta content of more than 0.20% deteriorates toughness due to formation of precipitates.
- the Ta content if any, ranges from 0.01% to 0.20%.
- Zr is an element effective in improving strength.
- a Zr content of 0.005% or more is effective in producing this effect.
- a Zr content of more than 0.1% deteriorates toughness due to the formation of a coarse precipitate.
- the Zr content, if any, ranges from 0.005% to 0.1%.
- Y forms a stable oxide at high temperatures, effectively suppresses the coarsening of prior ⁇ grains in the heat-affected zone, and is effective in improving the toughness of the weld.
- An Y content of 0.001% or more is effective in producing these effects.
- an Y content of more than 0.01% results in an increased number of inclusions and deteriorates toughness.
- the Y content, if any, ranges from 0.001% to 0.01%.
- B segregates at austenite grain boundaries, suppresses ferrite transformation from the grain boundaries, and improves hardenability.
- a B content of more than 0.0030% deteriorates hardenability and toughness due to the precipitation of B as a carbonitride.
- the B content is 0.0030% or less.
- the B content, if any, preferably ranges from 0.0003% to 0.0030%, more preferably 0.0005% to 0.002%.
- Ca is an element useful for the morphology control of a sulfide inclusion. This effect requires a Ca content of 0.0005% or more. However, a Ca content of more than 0.0050% deteriorates cleanliness and toughness. Thus, the Ca content, if any, is preferably 0.0050% or less, more preferably 0.0005% to 0.0025%.
- REM forms an oxide and a sulfide in steel and is effective in improving the material quality. This effect requires a REM content of 0.0005% or more. However, the effect levels off at a REM content of 0.0100% or more. Thus, the REM content, if any, is 0.0100% or less, preferably 0.0005% to 0.005%.
- the present invention provides a steel plate having desirable characteristics even when the steel plate is manufactured from steel casted under conditions where the cooling rate of a slab surface during solidification is 1°C/s or less.
- microsegregation needs to be reduced to achieve high toughness (vE-40 ⁇ 70 J) of the surface of a thick-walled high-toughness high-strength steel plate having a thickness of 100 mm or more, particularly manufactured from steel casted under conditions where the cooling rate of a slab surface during solidification is 1°C/s or less.
- C L 0.2 ⁇ ⁇ 0.1 ⁇ 0.2 ⁇ Si ⁇ 0.03 ⁇ 1.1 ⁇ Mn ⁇ 0.12 ⁇ 0.2 ⁇ Cu ⁇ 0.11 ⁇ 3 ⁇ Ni + 0.025 ⁇ 1.2 ⁇ Cr + 0.1 ⁇ 0.5 ⁇ Mo + 0.2 ⁇ 0.04 ⁇ V ⁇ 0.05 ⁇ 0.06 ⁇ Al
- the element symbols denote the respective alloy component contents (% by mass), and in the absence of an element, the element symbol is denoted by 0.
- the C content needs to be specified depending on each component other than C, such as Si or Mn.
- the effects of an alloying element on the C solid solubility limit (C L ) of the ⁇ phase were calculated using thermodynamic calculation software "Thermo-Calc". The result was used to determine the factor.
- the factor "-0.1" for "Si” means that 1% Si decreases the C solid solubility limit of the ⁇ phase by 0.1%, and the C content of the base metal needs to be decreased to achieve the required percentage of the ⁇ phase.
- the calculation of C L was based on the component of C: 0.12%, Si: 0.2%, Mn: 1.1%, Cu: 0.2%, Cr: 1.2%, Ni: 3%, Mo: 0.5%, V: 0.04% and Al: 0.06%, and the factors for the calculation of C L were determined by calculating a variation from the dissolved C content caused by a variation in each alloying element content.
- the percentage (C L - C)/C L x 100 of C to be added relative to the C solid solubility limit in the ⁇ phase thus calculated is 30% or more, the percentage of the ⁇ phase at the beginning of the formation of the ⁇ phase can be 30% or more.
- the reduction of area in the thickness direction at half the thickness of the plate is 40% or more when measured by a method described in the example.
- the temperature "°C” refers to the temperature in the half-thickness portion except for the quenching temperature in the case of quenching without leaving to cool after rolling.
- the quenching temperature in the case of quenching without leaving to cool after rolling is the surface temperature of the steel plate. This is because the temperature distribution of the steel plate in the thickness direction increases during rolling, and a decrease in the surface temperature of the steel plate needs to be considered.
- the temperature of the half-thickness portion is determined, for example, by simulation calculation from the thickness, surface temperature, and cooling conditions. For example, the temperature of the half-thickness portion is determined by calculating the temperature distribution in the thickness direction using finite difference methods.
- a molten steel having the composition described above is produced by a conventional method, such as with a converter, an electric furnace, or a vacuum melting furnace, and is formed into a piece of steel, such as a slab or billet, by a conventional casting method, such as a continuous casting process or an ingot casting process.
- the cooling rate during solidification is determined by direct measurement with a thermocouple or by simulation calculation, such as heat-transfer calculation.
- steel manufactured under conditions where the cooling rate of a surface during solidification is 1°C/s or less can preferably be used.
- the thickness of the material may be reduced by slabbing.
- a cast bloom or steel bloom having the composition described above is heated to a temperature in the range of 1200°C to 1350°C.
- a reheating temperature of less than 1200°C results in not only an insufficient rolling reduction due to an increased load to achieve a predetermined cumulative rolling reduction in hot working but also low production efficiency due to additional heating as required during working.
- the reheating temperature is 1200°C or more.
- a large amount of additive alloying element as steel having a carbon equivalent of 0.65% or more according to the present invention results in a casting defect such as a center porosity or porous shrinkage cavity, having a much increased size in steel. In order to make them harmless by pressure bonding, the cumulative rolling reduction needs to be 25% or more.
- a reheating temperature of more than 1350°C results in excessive energy consumption, increased likelihood of occurrence of surface flaws due to scales during heating, and increased repair load after hot forging.
- the upper limit is 1350°C.
- a cast bloom or steel bloom having the composition described above is heated to a temperature in the range of 1200°C to 1350°C.
- a reheating temperature of less than 1200°C results in not only an insufficient rolling reduction due to an increased load to achieve a predetermined cumulative rolling reduction in hot working but also low production efficiency due to additional heating as required during working.
- the reheating temperature is 1200°C or more.
- the cumulative rolling reduction is 30% or more, preferably 40% or more in terms of good reduction of area (RA).
- a reheating temperature of more than 1350°C results in excessive energy consumption, increased likelihood of surface flaws due to scales during heating, and increased repair load after hot forging.
- the upper limit is 1350°C.
- the heating temperature preferably ranges from 1000°C to 1200°C.
- the Ac3 transformation temperature is calculated using the following formula (4).
- Ac 3 937.2 ⁇ 476.5 C + 56 Si ⁇ 19.7 Mn ⁇ 16.3 Cu ⁇ 26.6 Ni ⁇ 4.9 Cr + 38.1 Mo + 124.8 V + 136.3 Ti + 198.4 Al + 3315 B
- the element symbols in the formula (4) denote the respective alloy component contents (% by mass).
- a steel plate is left to cool (for example, air cooling) after hot rolling or is rapidly cooled from the Ar3 temperature or more to 350°C or less without leaving to cool after hot rolling.
- the steel plate is reheated to the Ac3 temperature to 1050°C and is rapidly cooled from the Ac3 temperature or more to 350°C or less.
- the reason for the reheating temperature of 1050°C or less is that reheating at a high temperature of more than 1050°C results in coarsening of austenite grains and significantly deteriorates toughness of the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding.
- the reheating temperature is the Ac3 temperature or more in order that the steel plate may entirely have an austenite structure.
- the quenching temperature is the Ac3 temperature or more because the desirable characteristics are not obtained at a temperature below the Ac3 temperature due to the formation of a nonuniform structure composed of ferrite and austenite.
- the quenching temperature is the Ar3 temperature or more for quenching from the austenite single phase region.
- the rapid cooling stop temperature is a lower temperature selected from 350°C or less and the Ar3 temperature or less in order to ensure that the steel plate entirely has a transformed structure.
- the stop temperature should be the Ar3 temperature or less and 350°C or less.
- the Ar3 transformation temperature is calculated using the following formula (5).
- Ar 3 910 ⁇ 310 C ⁇ 80 Mn ⁇ 20 Cu ⁇ 15 Cr ⁇ 55 Ni ⁇ 80 Mo
- the element symbols in the formula (5) denote the respective alloy component contents (% by mass).
- the rapid cooling method is industrially water cooling. It is desirable that the cooling rate be as high as possible.
- the cooling method is not necessarily water cooling and may be gas cooling, for example.
- quenching is sometimes repeated to strengthen steel. Although quenching may be repeated also in the present invention, final quenching requires rapid cooling to 350°C or less after heating to the Ac3 temperature to 1050°C and requires subsequent tempering at 450°C to 700°C.
- Steel plate samples No. 1 to No. 38 were manufactured by melting and casting steel No. 1 to No. 30 listed in Table 1 under the conditions listed in Table 2, performing hot forging (except for the samples No. 5, No. 6, and No. 41) or slabbing (the samples No. 5, No. 6, and No. 41), hot-rolling the steel to form a steel plate having a thickness listed in Table 2, and subjecting the steel plate to water quenching and tempering.
- the steel plate samples No. 1 to No. 38 were subjected to the following tests. In reheating and quenching in this example, the reheating temperature corresponds to the quenching temperature.
- the percentage of the ⁇ phase is calculated using the formula (2) from C L calculated using the formula (3) with each base metal component and the C content of the base metal.
- the cooling rate during solidification in the manufacture of steel is determined by heat-transfer calculation from the mold surface temperature data measured with a radiation thermometer.
- a round bar tensile test piece ( ⁇ 12.5 mm, GL 50 mm) was taken from the half-thickness portion of each steel plate in the direction perpendicular to the rolling direction and was measured in terms of yield strength (YS) and tensile strength (TS).
- Three 2-mm V-notched Charpy impact test specimens were taken from each surface and half-thickness portion of the steel plates.
- the rolling direction was the longitudinal direction.
- the absorbed energies of the test specimens were measured at a test temperature of -40°C in a Charpy impact test and were averaged (the average value for the test specimens taken from the half-thickness portion and the average value for the test specimens taken from the surface).
- a round bar tensile test piece ( ⁇ 10 mm) was taken from a region including the half-thickness portion of each steel plate in the thickness direction and was measured in terms of reduction of area (RA).
- the reduction of area is the percentage of the difference between the minimum cross-sectional area after the test specimen was broken and the original cross-sectional area relative to the original cross-sectional area.
- Table 2 shows the test results.
- the results showed that the steel plates of the examples having a steel composition according to the present invention (samples No. 1 to No. 21 and No. 41) had YS of 620 MPa or more, TS of 720 MPa or more, and toughness (vE-40) of 70 J or more at -40°C in the surface and half-thickness portion of the base metal, showing high strength and toughness of the base metal.
- a comparison between Nos. 5 and 6 and No. 41 showed that reduction of area (RA) was also satisfactory under particular slabbing conditions.
- the base metal had at least one of YS of less than 620 MPa, TS of less than 720 MPa, and toughness (vE-40) of less than 70 J, thus deteriorating characteristics.
- Thickness of material Cooling rate during solidification °C/s Hot forging or slabbing Hot rolling Thickness of product (mm)
- Type of heat treatment Final heat treatment conditions Mechanical properties of base metal (1/2t) Toughness of base metal (surface) Heating (°C) Cumulative rolling reduction (%) Heating (°C) Cumulative rolling reduction (%) Quenching temperature (°C) Cooling stop (°C) Tempering (°C) YS (MPa) TS (MPa) vE-40 (J) Tensile RA in thickness direction RA (%) vE-40 (J) 1 1 1000 0.32 1270 80 1130 43 100 Direct quenching 850 150 630 695 786 108 73 98 2 2 500 0.64 1230 65 1130 43 100 Reheating quenching 930 100 650 698 795 167 63 105 3 3 300 0.90 1200 30 1130 50 100 Reheating quenching 930 100 630 725 793 102 70 116 4 4 1000 0.33 1270 70 1160 43 150 Re
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)
Description
- The present invention relates to a method for manufacturing a thick-walled high-toughness high-strength steel plate for use in steel structures in construction, bridges, shipbuilding, offshore structures, construction and industrial machinery, tanks, penstocks, and the like. In particular, the surface of the steel plate has high toughness, and the inner part of the steel plate has high strength and toughness. The steel plate has a thickness of 100 mm or more and a yield strength of 620 MPa or more.
- In general, steel for use in construction, bridges, shipbuilding, offshore structures, construction and industrial machinery, tanks, penstocks, and other fields is welded to have a desired shape. In recent years, with significantly increasing in size of steel structures, the strength and thickness of steel to be used have also been greatly increased.
- Despite trying to manufacture a thick-walled high-strength steel plate having a thickness of 100 mm or more and having high strength and toughness in a half-thickness portion (the central portion in the thickness direction), a structure having relatively low strength, such as ferrite, tends to be formed in the half-thickness portion due to a decreased cooling rate. Thus, the addition of large amounts of alloying elements is required to reduce the formation of such a structure.
- In particular, in order to achieve high strength and toughness of a half-thickness portion of a thick-walled material (a thick-walled steel plate having a thickness of 100 mm or more), it is important to form bainite or a mixed structure of bainite and martensite in the half-thickness portion during quenching. This requires the addition of large amounts of alloying elements, such as Mn, Ni, Cr, and/or Mo.
- The cooling rate is higher on the surface of a steel plate than in the half-thickness portion. Thus, a martensite structure having low toughness is formed on the surface of the steel plate. Thus, a high-strength steel plate having a thickness of 100 mm or more rarely has both high surface toughness and high strength and toughness of the inner part thereof.
- A steel plate related to the present invention is described in the following two pieces of non-patent literature, for example. Non Patent Literature 1 describes a material having a thickness of 210 mm, and Non Patent Literature 2 describes a material having a thickness of 180 mm.
-
CN 102605280 A describes a method for manufacturing an ultra-thick high-strength high low-temperature toughness steel plate for ocean platforms, wherein the steel plate comprises, in weight percentage, 0.10-0.24% of C, 0.05-0.35% of Si, 0.60-1.15% of Mn, not more than 0.015% of P, not more than 0.005% of S, 0.01-0.030% of Ti, 1.45-1.75% of Cr, 0.15-0.44% of Mo, 0.80-2.50% of Ni, 0.010-0.070% of Nb, 0.020-0.080% of V, 0.02-0.06% of Alt, 0.001-0.004% of Ca, not more than 0.006% of N, 0.0007-0.0030% of B, the balance being Fe and unavoidable impurities and whereing the steel plate has a system of C, Ni-Cr-Mo alloyed and Nb-V-Ti microalloyed, and has a yield strength not smaller than 690MPa, a tensile strength not smaller than 770MPa, -40°C Charpy V-notch impact energy not smaller than 69J, NDT (non-destructive testing) not larger than -35°C, Z not smaller than 35%, and largest thickness of more than 200mm. -
- NPL 1: Nippon Steel Technical Report, 348 (1993), 10-16
- NPL 2: Nippon Kokan Technical Report, 107 (1985), 21-30
- These pieces of non-patent literature describe high strength and toughness of the half-thickness portion. However, these pieces of non-patent literature do not describe the toughness (Charpy impact characteristics) of the surface of a steel plate. In general, thick-walled materials are manufactured by a quenching and tempering process. The formation of a martensite structure on the surface of a steel plate, on which the cooling rate is higher than in the half-thickness portion, deteriorates the toughness (Charpy impact characteristics) of the surface of the steel plate. However, these pieces of non-patent literature do not describe the manufacture of a steel plate consistently having a tough surface.
- The present invention has been made to solve such problems and aims to provide a method for manufacturing a thick-walled high-toughness high-strength steel plate that has high surface toughness and high strength and toughness of the inner part thereof.
- In order to solve the problems, the present inventors have extensively studied the microstructure control factors that satisfy high toughness of the surface of a thick-walled steel plate having a yield strength of 620 MPa or more and a thickness of 100 mm or more and also satisfy high strength and toughness of the half-thickness portion of the thick-walled steel plate, and have found the following.
- 1. When the cooling rate during the solidification of a raw material steel exceeds 1°C/s, microsegregation competes with the solidification reaction. This reduces microsegregation. In the manufacture of a large piece of steel, the cooling rate during the solidification of the steel decreases to 1°C/s or less, and consequently microsegregation becomes noticeable. Even in such a case, in order to achieve high toughness of the surface of a steel plate, on which a martensite structure is formed during quenching, it is important to reduce the P content and microsegregation during solidification. When primary crystals during solidification form a δ phase, and the percentage of the δ phase at the beginning of the formation of a γ phase is 30% or more, this results in reduced microsegregation and improved toughness. The percentage % described above refers to % by volume.
- 2. In order to achieve high strength and toughness of the half-thickness portion, in which the cooling rate is much lower than on the surface of a steel plate during cooling after hot working, it is important to appropriately select the steel composition (components) so as to form a martensite and/or bainite microstructure even at a low cooling rate. To this end, the alloy components should be appropriately selected, and in particular the carbon equivalent (Ceq) should be 0.65% or more. In addition to the appropriate component design, it is also important to form the desired structure by hot working and heat treatment.
- 3. Refinement of prior γ grain size is effective in improving toughness. Refinement of prior γ grain size before heat treatment, that is, refinement of prior γ grain size just after hot working is important for refinement of prior γ grain size after heat treatment. Thus, it is important to select appropriate hot working conditions and rolling conditions.
- As a result of further investigation of these findings, a method for manufacturing a thick-walled high-toughness high-strength steel plate according to the present invention is defined in claims 1 through 4.
- The present invention provides a method for manufacturing a thick-walled high-toughness high-strength steel plate having a thickness of 100 mm or more and having a yield strength of 620 MPa or more and high toughness. The thick-walled high-toughness high-strength steel plate can be used to manufacture steel structures having high safety.
- Embodiments of the present invention will be described below. The present invention is not limited to these embodiments.
- A thick-walled high-toughness high-strength steel plate manufactured according to the present invention has a composition containing, on a mass percent basis, C: 0.08% to 0.20%, Si: 0.40% or less (including 0%), Mn: 0.5% to 5.0%, P: 0.010% or less (including 0%), S: 0.0050% or less (including 0%), Cr: 3.0% or less (including 0%), Ni: 0.1% to 5.0%, Al: 0.010% to 0.080%, N: 0.0070% or less (including 0%), and O: 0.0025% or less (including 0%). Each of the components will be described below. The symbol "%" in the component content refers to "% by mass".
- C is an element useful for achieving the strength necessary for structural steel at low cost. This effect requires a C content of 0.08% or more. In a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding, however, a C content of more than 0.20% significantly deteriorates toughness of the base metal and weld. Thus, the C content has an upper limit of 0.20%. The C content preferably ranges from 0.08% to 0.14%.
- Si is added for deoxidation. When another element is added for deoxidation, however, a steel plate according to the present invention does not necessarily contain Si. In a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding, a Si content of more than 0.40% significantly deteriorates toughness of the base metal and heat-affected zone. Thus, the Si content is 0.40% or less, preferably 0.05% to 0.3%, more preferably 0.1% to 0.3%.
- Mn is added to ensure high strength of the base metal. This effect is insufficient at a Mn content of less than 0.5%. A Mn content of more than 5.0% promotes center segregation, results in a larger casting defect of the slab, and deteriorates mechanical properties of the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding. Thus, the Mn content has an upper limit of 5.0%. The Mn content preferably ranges from 0.6% to 2%, more preferably 0.6% to 1.6%.
- In a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding, a P content of more than 0.010% significantly deteriorates toughness of the base metal and heat-affected zone. Thus, the P content is preferably minimized (may be zero) and is limited to 0.010% or less.
- In a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding, a S content of more than 0.0050% significantly deteriorates toughness of the base metal and heat-affected zone. Thus, the S content is preferably minimized (may be zero) and is 0.0050% or less.
- Cr is an element effective in strengthening the base metal. However, an excessively high Cr content deteriorates weldability. Thus, the Cr content is 3.0% or less, preferably 0.1% to 2%, more preferably 0.7% to 1.7%. The Cr content may be 0%.
- Ni is an element useful for improving the strength of steel and the toughness of the heat-affected zone. This effect requires a Ni content of 0.1% or more. However, a Ni content of more than 5.0% significantly deteriorates economic efficiency. Thus, the Ni content has an upper limit of 5.0%. The Ni content preferably ranges from 0.4% to 4%, more preferably 0.8% to 3.8%.
- Al is added for sufficient deoxidation of molten steel. An Al content of less than 0.010% is insufficient for the effect. On the other hand, an Al content of more than 0.080% deteriorates toughness of the base metal due to an increased dissolved Al content in the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding. Thus, the Al content is 0.080% or less, preferably 0.030% to 0.080%, more preferably 0.030% to 0.070%.
- N, together with Ti, forms a nitride and thereby performs refinement of the structure and improves the toughness of the base metal and heat-affected zone in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding. The toughness can be improved by a constituent other than N. Thus, a steel plate according to the present invention does not necessarily contain N. When trying to produce this effect with N, the N content is preferably 0.0015% or more. In a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding, however, a N content of more than 0.0070% deteriorates toughness of the base metal due to an increased dissolved N content in the base metal and deteriorates toughness of the heat-affected zone due to the formation of coarse carbonitride. Thus, the N content is 0.0070% or less, preferably 0.006% or less, more preferably 0.005% or less.
- An O content of more than 0.0025% significantly deteriorates toughness due to the formation of a hard oxide in steel. Thus, the O content is preferably minimized (may be zero) and is 0.0025% or less.
- In addition to these elements, a thick-walled high-toughness high-strength steel plate manufactured according to the present invention can contain at least one of Cu, Mo, V, Nb, and Ti in order to further improve strength and/or toughness.
- Cu can improve the strength of steel without reducing toughness. A Cu content of more than 0.50% may cause a crack on the surface of a steel plate during hot working. Thus, the Cu content, if any, is 0.50% or less.
- Mo contributes to high strength of the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding. However, a Mo content of more than 1.50% results in increased hardness and deteriorates toughness due to the precipitation of alloy carbide. Thus, the Mo content, if any, has an upper limit of 1.50%. The Mo content preferably ranges from 0.2% to 0.8%.
- V contributes to improved strength and toughness of the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding. V precipitates as VN and is effective in decreasing the amount of dissolved N. However, a V content of more than 0.400% deteriorates toughness due to the precipitation of hard VC. Thus, the V content, if any, is preferably 0.400% or less, more preferably 0.01% to 0.1%.
- Nb is effective in improving the strength of the base metal. A Nb content of more than 0.100% deteriorates toughness of the base metal. Thus, the Nb content has an upper limit of 0.100%. The Nb content is preferably 0.025% or less.
- Ti forms TiN during heating and effectively suppresses the coarsening of austenite. In a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding, Ti improves the toughness of the base metal and heat-affected zone. However, a Ti content of more than 0.020% results in coarsening of Ti nitride and deteriorates toughness of the base metal. Thus, the Ti content, if any, ranges from 0.005% to 0.020%, preferably 0.008% to 0.015%.
- In addition to these components, a thick-walled high-toughness high-strength steel plate manufactured according to the present invention can further contain at least one of Mg, Ta, Zr, Y, B, Ca, and REM to improve the material quality.
- Mg forms a stable oxide at high temperatures, effectively suppresses the coarsening of prior γ grains in the heat-affected zone, and is effective in improving the toughness of the weld. These effects require a Mg content of 0.0001% or more. However, a Mg content of more than 0.0050% results in an increased number of inclusions and deteriorates toughness. Thus, the Mg content, if any, is preferably 0.0050% or less, more preferably 0.0001% to 0.015%.
- The addition of an adequate amount of Ta is effective in improving strength. More specifically, a Ta content of 0.01% or more is effective. However, a Ta content of more than 0.20% deteriorates toughness due to formation of precipitates. Thus, the Ta content, if any, ranges from 0.01% to 0.20%.
- Zr is an element effective in improving strength. A Zr content of 0.005% or more is effective in producing this effect. However, a Zr content of more than 0.1% deteriorates toughness due to the formation of a coarse precipitate. Thus, the Zr content, if any, ranges from 0.005% to 0.1%.
- Y forms a stable oxide at high temperatures, effectively suppresses the coarsening of prior γ grains in the heat-affected zone, and is effective in improving the toughness of the weld. An Y content of 0.001% or more is effective in producing these effects. However, an Y content of more than 0.01% results in an increased number of inclusions and deteriorates toughness. Thus, the Y content, if any, ranges from 0.001% to 0.01%.
- B segregates at austenite grain boundaries, suppresses ferrite transformation from the grain boundaries, and improves hardenability. However, a B content of more than 0.0030% deteriorates hardenability and toughness due to the precipitation of B as a carbonitride. Thus, the B content is 0.0030% or less. The B content, if any, preferably ranges from 0.0003% to 0.0030%, more preferably 0.0005% to 0.002%.
- Ca is an element useful for the morphology control of a sulfide inclusion. This effect requires a Ca content of 0.0005% or more. However, a Ca content of more than 0.0050% deteriorates cleanliness and toughness. Thus, the Ca content, if any, is preferably 0.0050% or less, more preferably 0.0005% to 0.0025%.
- Like Ca, REM forms an oxide and a sulfide in steel and is effective in improving the material quality. This effect requires a REM content of 0.0005% or more. However, the effect levels off at a REM content of 0.0100% or more. Thus, the REM content, if any, is 0.0100% or less, preferably 0.0005% to 0.005%.
- These optional elements in amounts below the lower limits do not reduce the advantages of the present invention. Thus, the optional elements in amounts below the lower limits are considered to be contained as incidental impurities.
- In the present invention, an appropriate alloy component needs to be added to ensure that a half-thickness portion of a thick-walled high-toughness high-strength steel plate having a thickness of 100 mm or more has a yield strength of 620 MPa or more and high toughness. More specifically, as represented by the following formula (1), alloying element contents need to be adjusted such that the carbon equivalent (CeqIIW) is 0.65% or more.
-
- As described later, the present invention provides a steel plate having desirable characteristics even when the steel plate is manufactured from steel casted under conditions where the cooling rate of a slab surface during solidification is 1°C/s or less. In the present invention, microsegregation needs to be reduced to achieve high toughness (vE-40 ≥ 70 J) of the surface of a thick-walled high-toughness high-strength steel plate having a thickness of 100 mm or more, particularly manufactured from steel casted under conditions where the cooling rate of a slab surface during solidification is 1°C/s or less. To this end, primary crystals during solidification need to form a δ phase, and the percentage ((CL - C)/CL x 100) of the δ phase at the beginning of the formation of a γ phase needs to be 30% or more.
- In the formula (3), the element symbols denote the respective alloy component contents (% by mass), and in the absence of an element, the element symbol is denoted by 0.
- In order to form a δ phase, the C content needs to be specified depending on each component other than C, such as Si or Mn. The effects of an alloying element on the C solid solubility limit (CL) of the δ phase were calculated using thermodynamic calculation software "Thermo-Calc". The result was used to determine the factor. For example, the factor "-0.1" for "Si" means that 1% Si decreases the C solid solubility limit of the δ phase by 0.1%, and the C content of the base metal needs to be decreased to achieve the required percentage of the δ phase. In the present invention, the calculation of CL was based on the component of C: 0.12%, Si: 0.2%, Mn: 1.1%, Cu: 0.2%, Cr: 1.2%, Ni: 3%, Mo: 0.5%, V: 0.04% and Al: 0.06%, and the factors for the calculation of CL were determined by calculating a variation from the dissolved C content caused by a variation in each alloying element content. When the percentage (CL - C)/CL x 100 of C to be added relative to the C solid solubility limit in the δ phase thus calculated is 30% or more, the percentage of the δ phase at the beginning of the formation of the γ phase can be 30% or more.
- In the present invention, in order to ensure the safety of steel during use, the reduction of area in the thickness direction at half the thickness of the plate is 40% or more when measured by a method described in the example.
- The manufacturing conditions in the present invention will be described below. In the description, the temperature "°C" refers to the temperature in the half-thickness portion except for the quenching temperature in the case of quenching without leaving to cool after rolling. The quenching temperature in the case of quenching without leaving to cool after rolling is the surface temperature of the steel plate. This is because the temperature distribution of the steel plate in the thickness direction increases during rolling, and a decrease in the surface temperature of the steel plate needs to be considered. The temperature of the half-thickness portion is determined, for example, by simulation calculation from the thickness, surface temperature, and cooling conditions. For example, the temperature of the half-thickness portion is determined by calculating the temperature distribution in the thickness direction using finite difference methods.
- A molten steel having the composition described above is produced by a conventional method, such as with a converter, an electric furnace, or a vacuum melting furnace, and is formed into a piece of steel, such as a slab or billet, by a conventional casting method, such as a continuous casting process or an ingot casting process. The cooling rate during solidification is determined by direct measurement with a thermocouple or by simulation calculation, such as heat-transfer calculation. As described above, in the present invention, steel manufactured under conditions where the cooling rate of a surface during solidification is 1°C/s or less can preferably be used.
- When the loads of a forging machine and a rolling mill and so on are restricted, the thickness of the material may be reduced by slabbing.
- A cast bloom or steel bloom having the composition described above is heated to a temperature in the range of 1200°C to 1350°C. A reheating temperature of less than 1200°C results in not only an insufficient rolling reduction due to an increased load to achieve a predetermined cumulative rolling reduction in hot working but also low production efficiency due to additional heating as required during working. Thus, the reheating temperature is 1200°C or more. A large amount of additive alloying element as steel having a carbon equivalent of 0.65% or more according to the present invention results in a casting defect such as a center porosity or porous shrinkage cavity, having a much increased size in steel. In order to make them harmless by pressure bonding, the cumulative rolling reduction needs to be 25% or more. On the other hand, a reheating temperature of more than 1350°C results in excessive energy consumption, increased likelihood of occurrence of surface flaws due to scales during heating, and increased repair load after hot forging. Thus, the upper limit is 1350°C.
- A cast bloom or steel bloom having the composition described above is heated to a temperature in the range of 1200°C to 1350°C. A reheating temperature of less than 1200°C results in not only an insufficient rolling reduction due to an increased load to achieve a predetermined cumulative rolling reduction in hot working but also low production efficiency due to additional heating as required during working. Thus, the reheating temperature is 1200°C or more. In order to make casting defects harmless by pressure bonding and to provide the advantages of the present invention, the cumulative rolling reduction is 30% or more, preferably 40% or more in terms of good reduction of area (RA). On the other hand, a reheating temperature of more than 1350°C results in excessive energy consumption, increased likelihood of surface flaws due to scales during heating, and increased repair load after hot forging. Thus, the upper limit is 1350°C.
- Steel after forging is heated to an Ac3 transformation temperature or more and 1200°C or less in order that the steel may have a uniform austenite structure alone. The heating temperature preferably ranges from 1000°C to 1200°C.
-
- The element symbols in the formula (4) denote the respective alloy component contents (% by mass).
- Steel is hot-rolled to form a plate having a desired thickness. In order to ensure desirable mechanical properties of a half-thickness portion of a thick-walled steel plate having a thickness of 100 mm or more, it is necessary to adjust the steel in the rolling step in order to sufficiently elicit an effect of adjusting and refining of the prior γ grain size. More specifically, rolling at a cumulative rolling reduction of 40% or more can adjust the grain size in the rolling step even in the half-thickness portion in which recrystallization rarely occurs in processing.
- In order to achieve high strength and toughness of a half-thickness portion, in the present invention, a steel plate is left to cool (for example, air cooling) after hot rolling or is rapidly cooled from the Ar3 temperature or more to 350°C or less without leaving to cool after hot rolling. When the steel plate is left to cool, the steel plate is reheated to the Ac3 temperature to 1050°C and is rapidly cooled from the Ac3 temperature or more to 350°C or less. The reason for the reheating temperature of 1050°C or less is that reheating at a high temperature of more than 1050°C results in coarsening of austenite grains and significantly deteriorates toughness of the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding. The reheating temperature is the Ac3 temperature or more in order that the steel plate may entirely have an austenite structure. The quenching temperature is the Ac3 temperature or more because the desirable characteristics are not obtained at a temperature below the Ac3 temperature due to the formation of a nonuniform structure composed of ferrite and austenite. In the case of rapid cooling without leaving to cool, the quenching temperature is the Ar3 temperature or more for quenching from the austenite single phase region. The rapid cooling stop temperature is a lower temperature selected from 350°C or less and the Ar3 temperature or less in order to ensure that the steel plate entirely has a transformed structure. The stop temperature should be the Ar3 temperature or less and 350°C or less.
-
- The element symbols in the formula (5) denote the respective alloy component contents (% by mass).
- In general, the rapid cooling method is industrially water cooling. It is desirable that the cooling rate be as high as possible. Thus, the cooling method is not necessarily water cooling and may be gas cooling, for example.
- The reason for tempering at a temperature in the range of 450°C to 700°C after rapid cooling is described below. Residual stress is not effectively relieved at less than 450°C. On the other hand, a temperature of more than 700°C results in precipitation of various carbides and coarsens the structure of the base metal and deteriorates strength and toughness of the base metal in a steel structure manufactured from a thick-walled high-toughness high-strength steel plate by welding.
- Industrially, quenching is sometimes repeated to strengthen steel. Although quenching may be repeated also in the present invention, final quenching requires rapid cooling to 350°C or less after heating to the Ac3 temperature to 1050°C and requires subsequent tempering at 450°C to 700°C.
- Steel plate samples No. 1 to No. 38 were manufactured by melting and casting steel No. 1 to No. 30 listed in Table 1 under the conditions listed in Table 2, performing hot forging (except for the samples No. 5, No. 6, and No. 41) or slabbing (the samples No. 5, No. 6, and No. 41), hot-rolling the steel to form a steel plate having a thickness listed in Table 2, and subjecting the steel plate to water quenching and tempering. The steel plate samples No. 1 to No. 38 were subjected to the following tests. In reheating and quenching in this example, the reheating temperature corresponds to the quenching temperature.
- The percentage of the δ phase is calculated using the formula (2) from CL calculated using the formula (3) with each base metal component and the C content of the base metal.
- The cooling rate during solidification in the manufacture of steel is determined by heat-transfer calculation from the mold surface temperature data measured with a radiation thermometer.
- A round bar tensile test piece (φ12.5 mm, GL 50 mm) was taken from the half-thickness portion of each steel plate in the direction perpendicular to the rolling direction and was measured in terms of yield strength (YS) and tensile strength (TS).
- Three 2-mm V-notched Charpy impact test specimens were taken from each surface and half-thickness portion of the steel plates. The rolling direction was the longitudinal direction. The absorbed energies of the test specimens were measured at a test temperature of -40°C in a Charpy impact test and were averaged (the average value for the test specimens taken from the half-thickness portion and the average value for the test specimens taken from the surface).
- A round bar tensile test piece (φ10 mm) was taken from a region including the half-thickness portion of each steel plate in the thickness direction and was measured in terms of reduction of area (RA). The reduction of area is the percentage of the difference between the minimum cross-sectional area after the test specimen was broken and the original cross-sectional area relative to the original cross-sectional area.
- Table 2 shows the test results. The results showed that the steel plates of the examples having a steel composition according to the present invention (samples No. 1 to No. 21 and No. 41) had YS of 620 MPa or more, TS of 720 MPa or more, and toughness (vE-40) of 70 J or more at -40°C in the surface and half-thickness portion of the base metal, showing high strength and toughness of the base metal. A comparison between Nos. 5 and 6 and No. 41 showed that reduction of area (RA) was also satisfactory under particular slabbing conditions.
- In contrast, in the steel plates according to comparative examples having a composition outside the scope of the present invention (samples No. 22 to No. 32), the base metal had at least one of YS of less than 620 MPa, TS of less than 720 MPa, and toughness (vE-40) of less than 70 J, thus deteriorating characteristics.
- As in samples No. 33 to No. 40, even if steel plates had a steel composition according to the present invention, steel plates manufactured under the conditions outside the scope of the present invention had at least one deterioration in YS, TS, and toughness (vE-40) .
[Table 2] Category Sample No. Steel ingot No. Thickness of material (mm) Cooling rate during solidification °C/s Hot forging or slabbing Hot rolling Thickness of product (mm) Type of heat treatment Final heat treatment conditions Mechanical properties of base metal (1/2t) Toughness of base metal (surface) Heating (°C) Cumulative rolling reduction (%) Heating (°C) Cumulative rolling reduction (%) Quenching temperature (°C) Cooling stop (°C) Tempering (°C) YS (MPa) TS (MPa) vE-40 (J) Tensile RA in thickness direction RA (%) vE-40 (J) 1 1 1000 0.32 1270 80 1130 43 100 Direct quenching 850 150 630 695 786 108 73 98 2 2 500 0.64 1230 65 1130 43 100 Reheating quenching 930 100 650 698 795 167 63 105 3 3 300 0.90 1200 30 1130 50 100 Reheating quenching 930 100 630 725 793 102 70 116 4 4 1000 0.33 1270 70 1160 43 150 Reheating quenching 900 100 630 785 856 205 65 221 5 4 1000 0.33 1320 55 1200 53 210 Reheating quenching 900 100 630 743 829 145 71 124 6 4 1000 0.33 1300 55 1180 67 150 Direct quenching 860 100 630 751 832 126 58 159 7 5 500 0.61 1270 45 1160 43 150 Reheating quenching 900 100 630 725 821 153 63 205 8 6 1000 0.32 1270 55 1130 60 180 Reheating quenching 880 100 630 705 816 238 61 211 9 7 1000 0.31 1270 55 1130 53 210 Reheating quenching 880 100 650 756 864 216 63 163 10 8 1000 0.31 1300 55 1130 53 210 Reheating quenching 880 100 650 741 836 193 60 121 Example 11 9 1000 0.30 1270 55 1130 53 210 Reheating quenching 880 100 650 759 857 186 62 101 12 10 1200 0.25 1270 55 1160 50 250 Reheating quenching 900 100 630 748 852 221 59 146 13 11 1000 0.29 1270 70 1160 43 150 Reheating quenching 880 100 630 728 839 169 71 101 14 12 1300 0.19 1270 60 1160 50 250 Reheating quenching 880 100 660 793 912 221 68 145 15 13 1200 0.32 1270 85 1130 43 100 Reheating quenching 930 100 650 665 756 103 73 126 16 14 1000 0.31 1270 55 1160 53 210 Reheating quenching 880 100 650 723 814 203 69 163 17 15 1000 0.32 1270 55 1160 53 210 Reheating quenching 1050 150 670 641 738 145 70 101 18 16 500 0.64 1230 65 1130 43 100 Reheating quenching 930 100 650 732 841 167 77 83 19 17 500 0.65 1230 65 1160 43 100 Reheating quenching 900 100 650 703 789 196 73 113 20 18 300 0.91 1200 40 1160 43 100 Direct quenching 880 150 650 752 846 138 65 106 21 19 1000 0.29 1350 50 1160 50 250 Reheating quenching 900 100 650 746 863 231 62 93 22 20 1000 0.29 1270 55 1160 53 210 Reheating quenching 880 100 640 716 815 196 61 43 23 21 300 0.92 1200 40 1160 43 100 Reheating quenching 930 100 650 589 695 22 69 121 24 22 1000 0.31 1270 70 1160 43 150 Reheating quenching 900 100 630 845 956 19 62 96 25 23 1000 0.29 1270 70 1160 43 150 Reheating quenching 930 100 630 547 663 21 68 124 26 24 1000 0.29 1270 55 1130 53 210 Reheating quenching 930 100 650 728 823 41 64 39 27 25 1200 0.24 1270 55 1160 50 250 Reheating quenchinq 880 100 630 802 915 23 51 96 28 26 1000 0.28 1270 70 1160 43 150 Reheating quenching 880 100 630 731 829 32 57 23 29 27 1000 0.31 1270 55 1130 53 210 Reheating quenching 900 100 650 741 854 35 63 31 30 28 000 0.29 1270 55 1130 53 210 Reheating quenching 900 100 650 796 921 43 61 89 Comparative example 31 29 1000 0.32 1270 55 1130 53 210 Reheating quenching 900 100 650 732 816 48 72 56 32 30 1000 0.31 1270 70 1160 43 150 Reheating quenching 900 100 630 698 784 61 70 52 33 3 300 0.91 1200 15 1130 60 100 Reheating quenching 930 100 630 716 804 43 23 115 34 3 300 0.89 1200 55 1130 20 100 Reheating quenching 930 100 630 722 816 45 35 96 35 3 300 0.90 1200 30 1130 50 100 Reheating quenching 1100 100 630 735 824 36 53 49 36 3 300 0.92 1200 30 1130 50 100 Reheating quenching 840 100 630 536 646 46 49 52 37 3 300 0.90 1200 30 1130 50 100 Direct quenchinq 623 100 630 596 683 52 51 61 38 3 300 0.91 1200 30 130 50 100 Reheating quenching 930 400 630 503 641 32 64 103 39 3 300 0.90 1200 30 1130 50 100 Reheating quenching 930 100 720 569 657 153 68 146 40 3 300 0.91 1200 30 1130 50 100 Reheating quenching 930 100 400 793 902 41 63 53 Comparative Example 41 5 500 0.61 1300 30 1180 40 210 Reheating quenching 900 100 600 683 766 105 29 192
Claims (4)
- A method for manufacturing a thick-walled high-toughness high-strength steel plate having a thickness of 100 mm or more, a yield strength of 620 MPa or more, and comprising, on a mass percent basis,C: 0.08% to 0.20%,Si: 0.40% or less,Mn: 0.5% to 5.0%,P: 0.010% or less,S: 0.0050% or less,Cr: 3.0% or less,Ni: 0.1% to 5.0%,Al: 0.010% to 0.080%,N: 0.0070% or less, andO: 0.0025% or less,following formulae (1) and (2) being satisfied, optionally at least one ofCu: 0.50% or less,Mo: 1.50% or less,V: 0.400% or less,Nb: 0.100% or less,Ti: 0.005% to 0.020%,Mg: 0.0001% to 0.0050%,Ta: 0.01% to 0.20%,Zr: 0.005% to 0.1%,Y: 0.001% to 0.01%,B: 0.0030% or less,Ca: 0.0005% to 0.0050%, andREM: 0.0005% to 0.0100%,a remainder being Fe and incidental impurities, and comprising a toughness (vE-40) of 70 J or more at -40°C in the surface portion of the base metal:
a reduction of area in a thickness direction at half the thickness of the plate, which is the percentage of the difference between the minimum cross-sectional area after a round bar tensile test specimen including the half-thickness portion of the steel plate in the thickness direction is broken in a tensile test and the original cross-sectional area relative to the original cross-sectional area, is 40% or more,
wherein the method comprises:heating steel to 1200°C to 1350°C,hot-forging the steel at a cumulative reduction of 25% or more,heating the steel to an Ac3 temperature or more and 1200°C or less,hot-rolling the steel at a cumulative rolling reduction of 40% or more,leaving the steel to cool,reheating the steel to the Ac3 temperature or more and 1050°C or less,rapidly cooling the steel from the Ac3 temperature or more to a lower temperature, which is both 350°C or less and an Ar3 temperature or less, andtempering the steel at a temperature in the range of 450°C to 700°C. - A method for manufacturing a thick-walled high-toughness high-strength steel plate having a thickness of 100 mm or more, a yield strength of 620 MPa or more, and comprising, on a mass percent basis,C: 0.08% to 0.20%,Si: 0.40% or less,Mn: 0.5% to 5.0%,P: 0.010% or less,S: 0.0050% or less,Cr: 3.0% or less,Ni: 0.1% to 5.0%,Al: 0.010% to 0.080%,N: 0.0070% or less, andO: 0.0025% or less,following formulae (1) and (2) being satisfied, optionally at least one ofCu: 0.50% or less,Mo: 1.50% or less,V: 0.400% or less,Nb: 0.100% or less,Ti: 0.005% to 0.020%,Mg: 0.0001% to 0.0050%,Ta: 0.01% to 0.20%,Zr: 0.005% to 0.1%,Y: 0.001% to 0.01%,B: 0.0030% or less,Ca: 0.0005% to 0.0050%, andREM: 0.0005% to 0.0100%,a remainder being Fe and incidental impurities, and comprising a toughness (vE-40) of 70 J or more at -40°C in the surface portion of the base metal:
a reduction of area in a thickness direction at half the thickness of the plate, which is the percentage of the difference between the minimum cross-sectional area after a round bar tensile test specimen including the half-thickness portion of the steel plate in the thickness direction is broken in a tensile test and the original cross-sectional area relative to the original cross-sectional area, is 40% or more,
wherein the method comprises:heating steel to 1200°C to 1350°C,hot-forging the steel at a cumulative reduction of 25% or more,heating the steel to an Ac3 temperature or more and 1200°C or less,hot-rolling the steel at a cumulative rolling reduction of 40% or more,rapidly cooling the steel from an Ar3 temperature or more to a lower temperature which is both 350°C or less and the Ar3 temperature or less, andtempering the steel at a temperature in the range of 450°C to 700°C. - A method for manufacturing a thick-walled high-toughness high-strength steel plate having a thickness of 100 mm or more, a yield strength of 620 MPa or more, and comprising, on a mass percent basis,C: 0.08% to 0.20%,Si: 0.40% or less,Mn: 0.5% to 5.0%,P: 0.010% or less,S: 0.0050% or less,Cr: 3.0% or less,Ni: 0.1% to 5.0%,Al: 0.010% to 0.080%,N: 0.0070% or less, andO: 0.0025% or less,following formulae (1) and (2) being satisfied, optionally at least one ofCu: 0.50% or less,Mo: 1.50% or less,V: 0.400% or less,Nb: 0.100% or less,Ti: 0.005% to 0.020%,Mg: 0.0001% to 0.0050%,Ta: 0.01% to 0.20%,Zr: 0.005% to 0.1%,Y: 0.001% to 0.01%,B: 0.0030% or less,Ca: 0.0005% to 0.0050%, andREM: 0.0005% to 0.0100%,a remainder being Fe and incidental impurities, and comprising a toughness (vE-40) of 70 J or more at -40°C in the surface portion of the base metal:
a reduction of area in a thickness direction at half the thickness of the plate, which is the percentage of the difference between the minimum cross-sectional area after a round bar tensile test specimen including the half-thickness portion of the steel plate in the thickness direction is broken in a tensile test and the original cross-sectional area relative to the original cross-sectional area, is 40% or more,
wherein the method comprises:heating steel to 1200°C to 1350°C,slabbing the steel at a cumulative rolling reduction of 40% or more,heating the steel to an Ac3 temperature or more and 1200°C or less,hot-rolling the steel at a cumulative rolling reduction of 40% or more, leaving the steel to cool,reheating the steel to the Ac3 temperature or more and 1050°C or less,rapidly cooling the steel from the Ac3 temperature or more to a lower temperature which is both 350°C or less and an Ar3 temperature or less, andtempering the steel at a temperature in the range of 450°C to 700°C. - A method for manufacturing a thick-walled high-toughness high-strength steel plate having a thickness of 100 mm or more, a yield strength of 620 MPa or more, and comprising, on a mass percent basis,C: 0.08% to 0.20%,Si: 0.40% or less,Mn: 0.5% to 5.0%,P: 0.010% or less,S: 0.0050% or less,Cr: 3.0% or less,Ni: 0.1% to 5.0%,Al: 0.010% to 0.080%,N: 0.0070% or less, andO: 0.0025% or less,following formulae (1) and (2) being satisfied, optionally at least one ofCu: 0.50% or less,Mo: 1.50% or less,V: 0.400% or less,Nb: 0.100% or less,Ti: 0.005% to 0.020%,Mg: 0.0001% to 0.0050%,Ta: 0.01% to 0.20%,Zr: 0.005% to 0.1%,Y: 0.001% to 0.01%,B: 0.0030% or less,Ca: 0.0005% to 0.0050%, andREM: 0.0005% to 0.0100%,a remainder being Fe and incidental impurities, and comprising a toughness (vE-40) of 70 J or more at -40°C in the surface portion of the base metal:
a reduction of area in a thickness direction at half the thickness of the plate, which is the percentage of the difference between the minimum cross-sectional area after a round bar tensile test specimen including the half-thickness portion of the steel plate in the thickness direction is broken in a tensile test and the original cross-sectional area relative to the original cross-sectional area, is 40% or more,
wherein the method comprises:heating steel to 1200°C to 1350°C,slabbing the steel at a cumulative rolling reduction of 40% or more,heating the steel to an Ac3 temperature or more and 1200°C or less,hot-rolling the steel at a cumulative rolling reduction of 40% or more,rapidly cooling the steel from an Ar3 temperature or more to a lower temperature, which is both 350°C or less and the Ar3 temperature or less, andtempering the steel at a temperature in the range of 450°C to 700°C.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2015006670 | 2015-01-16 | ||
PCT/JP2016/000197 WO2016114146A1 (en) | 2015-01-16 | 2016-01-15 | Thick high-toughness high-strength steel sheet and method for manufacturing same |
Publications (3)
Publication Number | Publication Date |
---|---|
EP3246426A1 EP3246426A1 (en) | 2017-11-22 |
EP3246426A4 EP3246426A4 (en) | 2018-01-10 |
EP3246426B1 true EP3246426B1 (en) | 2020-06-24 |
Family
ID=56405694
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP16737217.6A Active EP3246426B1 (en) | 2015-01-16 | 2016-01-15 | Method for manufacturing a thick high-toughness high-strength steel sheet |
Country Status (8)
Country | Link |
---|---|
US (1) | US20170369958A1 (en) |
EP (1) | EP3246426B1 (en) |
JP (1) | JP6048626B1 (en) |
KR (1) | KR101994784B1 (en) |
CN (1) | CN107208212B (en) |
CA (1) | CA2969200C (en) |
SG (1) | SG11201704242TA (en) |
WO (1) | WO2016114146A1 (en) |
Families Citing this family (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP6447253B2 (en) * | 2015-03-06 | 2019-01-09 | 新日鐵住金株式会社 | High strength steel for welding |
EP3680358A1 (en) * | 2017-09-08 | 2020-07-15 | JFE Steel Corporation | Steel sheet and method for producing same |
JP6984319B2 (en) * | 2017-10-31 | 2021-12-17 | 日本製鉄株式会社 | Nickel-containing steel sheet for low temperature with excellent toughness and its manufacturing method |
KR101999024B1 (en) * | 2017-12-26 | 2019-07-10 | 주식회사 포스코 | Steel plate having excellent HIC resistance and manufacturing method for the same |
CN110318008B (en) * | 2019-06-20 | 2022-01-14 | 江阴兴澄特种钢铁有限公司 | Large-thickness lamellar tearing resistant 960 MPa-grade high-strength steel plate and production method thereof |
CN110172646A (en) * | 2019-06-24 | 2019-08-27 | 南京钢铁股份有限公司 | A kind of storage tank for ship P690QL1 steel plate and manufacturing method |
KR102255821B1 (en) * | 2019-09-17 | 2021-05-25 | 주식회사 포스코 | Ultra-thick steel plate having high strength and excellent low-temperature impact toughness and method for manufacturing thereof |
KR102509355B1 (en) | 2020-12-21 | 2023-03-14 | 주식회사 포스코 | Extra heavy gauged steel plate for steam drum having excellent surface quality and lamellar tearing resistance, and manufacturing method for the same |
CN114032453B (en) * | 2021-10-14 | 2022-06-21 | 首钢集团有限公司 | Large-thickness 1000 MPa-grade non-quenched and tempered high-toughness structural steel and preparation method thereof |
KR20230094388A (en) | 2021-12-21 | 2023-06-28 | 주식회사 포스코 | Extra heavy steel materials for flange having excellent strength and low temperature impact toughness, and manufacturing method for the same |
KR20230094389A (en) | 2021-12-21 | 2023-06-28 | 주식회사 포스코 | Extra heavy steel materials for flange having excellent strength and low temperature impact toughness, and manufacturing method for the same |
CN114592156B (en) * | 2022-03-09 | 2023-08-18 | 广东一诺重工钢构有限公司 | High-strength steel beam and processing technology thereof |
KR20230171665A (en) | 2022-06-14 | 2023-12-21 | 주식회사 포스코 | Extra heavy steel materials for flange having excellent strength and low temperature impact toughness, and manufacturing method for the same |
Family Cites Families (20)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS52128821A (en) * | 1976-04-12 | 1977-10-28 | Nippon Steel Corp | Preparation of high tensile steel having superior low temperature toughness and yield point above 40 kg/pp2 |
JP2913426B2 (en) * | 1991-03-13 | 1999-06-28 | 新日本製鐵株式会社 | Manufacturing method of thick high strength steel sheet with excellent low temperature toughness |
JP3333619B2 (en) * | 1994-02-24 | 2002-10-15 | 川崎製鉄株式会社 | Manufacturing method of extra thick steel plate |
JP3499705B2 (en) * | 1997-03-26 | 2004-02-23 | 株式会社神戸製鋼所 | 950N / mm2 class tempered high-strength steel sheet having excellent homogeneity in thickness direction and low anisotropy of toughness, and method for producing the same |
JP2002210502A (en) * | 2001-01-19 | 2002-07-30 | Kawasaki Steel Corp | Manufacturing method for extremely thick steel |
JP2002256380A (en) * | 2001-03-06 | 2002-09-11 | Sumitomo Metal Ind Ltd | Thick high tensile strength steel plate having excellent brittle crack propagation arrest property and weld zone property and production method therefor |
JP4792778B2 (en) * | 2005-03-29 | 2011-10-12 | 住友金属工業株式会社 | Manufacturing method of thick-walled seamless steel pipe for line pipe |
JP5194878B2 (en) * | 2007-04-13 | 2013-05-08 | Jfeスチール株式会社 | High-strength hot-dip galvanized steel sheet excellent in workability and weldability and method for producing the same |
JP5365217B2 (en) * | 2008-01-31 | 2013-12-11 | Jfeスチール株式会社 | High strength steel plate and manufacturing method thereof |
CN101962741B (en) * | 2009-07-24 | 2012-08-08 | 宝山钢铁股份有限公司 | Quenched and tempered steel sheet and manufacturing method thereof |
JP2011153366A (en) * | 2010-01-28 | 2011-08-11 | Nippon Steel Corp | Method for manufacturing high-tensile-strength steel sheet to be laser-welded or laser/arc hybrid-welded having tensile strength of 1,100 mpa or more |
JP2011202214A (en) * | 2010-03-25 | 2011-10-13 | Jfe Steel Corp | Thick high tensile strength steel plate having excellent low temperature toughness in multilayer weld zone and method for producing the same |
JP5924058B2 (en) * | 2011-10-03 | 2016-05-25 | Jfeスチール株式会社 | High tensile strength steel sheet with excellent low temperature toughness of weld heat affected zone and method for producing the same |
CN102605280A (en) * | 2012-03-15 | 2012-07-25 | 宝山钢铁股份有限公司 | Ultra-thick high-strength high low-temperature toughness steel plates for ocean platforms and production method thereof |
JP5590271B1 (en) * | 2012-12-28 | 2014-09-17 | 新日鐵住金株式会社 | Steel sheet having a yield strength of 670-870 N / mm 2 and a tensile strength of 780-940 N / mm 2 |
CN105008570B (en) * | 2013-03-15 | 2017-12-19 | 杰富意钢铁株式会社 | Heavy wall high tenacity high-tensile steel and its manufacture method |
KR101732997B1 (en) * | 2013-03-26 | 2017-05-08 | 제이에프이 스틸 가부시키가이샤 | High strength thick steel plate for high heat input welding with excellent brittle crack arrestability and manufacturing method therefor |
KR101838424B1 (en) * | 2014-03-20 | 2018-03-13 | 제이에프이 스틸 가부시키가이샤 | High toughness and high tensile strength thick steel plate and production method therefor |
JP5871109B1 (en) * | 2014-04-24 | 2016-03-01 | Jfeスチール株式会社 | Thick steel plate and manufacturing method thereof |
CN107109561B (en) * | 2014-11-18 | 2018-12-21 | 杰富意钢铁株式会社 | The excellent heavy wall high tenacity high-tensile steel of property uniform in material and its manufacturing method |
-
2016
- 2016-01-15 JP JP2016532648A patent/JP6048626B1/en active Active
- 2016-01-15 EP EP16737217.6A patent/EP3246426B1/en active Active
- 2016-01-15 KR KR1020177019203A patent/KR101994784B1/en active IP Right Grant
- 2016-01-15 CN CN201680005979.9A patent/CN107208212B/en active Active
- 2016-01-15 CA CA2969200A patent/CA2969200C/en active Active
- 2016-01-15 US US15/543,364 patent/US20170369958A1/en not_active Abandoned
- 2016-01-15 SG SG11201704242TA patent/SG11201704242TA/en unknown
- 2016-01-15 WO PCT/JP2016/000197 patent/WO2016114146A1/en active Application Filing
Non-Patent Citations (1)
Title |
---|
None * |
Also Published As
Publication number | Publication date |
---|---|
US20170369958A1 (en) | 2017-12-28 |
JP6048626B1 (en) | 2016-12-21 |
WO2016114146A1 (en) | 2016-07-21 |
CN107208212A (en) | 2017-09-26 |
KR20170095307A (en) | 2017-08-22 |
SG11201704242TA (en) | 2017-06-29 |
EP3246426A4 (en) | 2018-01-10 |
KR101994784B1 (en) | 2019-07-01 |
CA2969200C (en) | 2020-06-02 |
JPWO2016114146A1 (en) | 2017-04-27 |
EP3246426A1 (en) | 2017-11-22 |
CA2969200A1 (en) | 2016-07-21 |
CN107208212B (en) | 2020-01-17 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP3246426B1 (en) | Method for manufacturing a thick high-toughness high-strength steel sheet | |
EP2942414B1 (en) | Thick, tough, high tensile strength steel plate and production method therefor | |
EP3135787B1 (en) | Steel plate and method of producing same | |
EP3239327B1 (en) | High-strength steel plate for pressure vessel having excellent toughness after post weld heat treatment and manufacturing method thereof | |
EP3222744B1 (en) | High toughness and high tensile strenght thick steel plate with excellent material homogeneity | |
EP3120941B1 (en) | High toughness and high tensile strength thick steel plate and production method therefor | |
EP2589676B1 (en) | Abrasion-resistant steel plate or sheet with excellent weld toughness and delayed fracture resistance | |
EP2481826B1 (en) | High-strength and high-toughness cast steel material and method for producing the same | |
EP2792761B1 (en) | High-strength extra-thick steel h-beam | |
EP3026138A1 (en) | High-strength steel material for oil well use, and oil well pipe | |
EP2400041B1 (en) | Steel material for welding and method for producing same | |
EP3722448B1 (en) | High-mn steel and method for manufacturing same | |
KR20200033901A (en) | High Mn steel and its manufacturing method | |
JP5630321B2 (en) | High-tensile steel plate with excellent toughness and manufacturing method thereof | |
EP3831973A1 (en) | High-mn steel and method for producing same | |
EP3178954A1 (en) | Cold-rolled steel sheet having excellent spot weldability, and manufacturing method therefor | |
JPWO2019050010A1 (en) | Steel sheet and manufacturing method thereof | |
JP6536459B2 (en) | Thick steel plate and method of manufacturing the same | |
JP6179609B2 (en) | Manufacturing method of thick high-strength steel sheet with excellent cold workability | |
RU2652281C1 (en) | Method of production of hot-rolled sheets from high-strength steel | |
EP4245876A1 (en) | High yield ratio and high strength steel sheet having excellent thermal stability, and manufacturing method therefor |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE |
|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE |
|
17P | Request for examination filed |
Effective date: 20170713 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
AX | Request for extension of the european patent |
Extension state: BA ME |
|
A4 | Supplementary search report drawn up and despatched |
Effective date: 20171208 |
|
DAV | Request for validation of the european patent (deleted) | ||
DAX | Request for extension of the european patent (deleted) | ||
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: EXAMINATION IS IN PROGRESS |
|
17Q | First examination report despatched |
Effective date: 20190206 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R079 Ref document number: 602016038711 Country of ref document: DE Free format text: PREVIOUS MAIN CLASS: C22C0038000000 Ipc: C21D0009460000 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: GRANT OF PATENT IS INTENDED |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C22C 38/00 20060101ALI20200203BHEP Ipc: C22C 38/16 20060101ALI20200203BHEP Ipc: C21D 9/46 20060101AFI20200203BHEP Ipc: C22C 38/46 20060101ALI20200203BHEP Ipc: B21B 3/02 20060101ALN20200203BHEP Ipc: C22C 38/12 20060101ALI20200203BHEP Ipc: C21D 8/02 20060101ALI20200203BHEP Ipc: C21D 9/00 20060101ALN20200203BHEP Ipc: C22C 38/02 20060101ALI20200203BHEP Ipc: C21D 7/13 20060101ALN20200203BHEP Ipc: B21B 1/02 20060101ALN20200203BHEP Ipc: C22C 38/48 20060101ALI20200203BHEP Ipc: C22C 38/50 20060101ALI20200203BHEP Ipc: C22C 38/58 20060101ALI20200203BHEP Ipc: C22C 38/42 20060101ALI20200203BHEP Ipc: B21B 3/00 20060101ALN20200203BHEP Ipc: C21D 6/00 20060101ALI20200203BHEP Ipc: C22C 38/08 20060101ALI20200203BHEP Ipc: C22C 38/44 20060101ALI20200203BHEP Ipc: C22C 38/54 20060101ALI20200203BHEP Ipc: C22C 38/04 20060101ALI20200203BHEP Ipc: C22C 38/06 20060101ALI20200203BHEP |
|
INTG | Intention to grant announced |
Effective date: 20200219 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE PATENT HAS BEEN GRANTED |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: REF Ref document number: 1283965 Country of ref document: AT Kind code of ref document: T Effective date: 20200715 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602016038711 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: TRGR |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200925 Ref country code: FI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: LT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 |
|
REG | Reference to a national code |
Ref country code: NO Ref legal event code: T2 Effective date: 20200624 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LV Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: HR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: RS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: BG Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200924 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20200624 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 1283965 Country of ref document: AT Kind code of ref document: T Effective date: 20200624 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: NL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: PT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201026 Ref country code: CZ Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: ES Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: EE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: AT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: IT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: RO Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: SM Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201024 Ref country code: SK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: PL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602016038711 Country of ref document: DE |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: DK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
26N | No opposition filed |
Effective date: 20210325 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 Ref country code: MC Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
GBPC | Gb: european patent ceased through non-payment of renewal fee |
Effective date: 20210115 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210115 |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20210131 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210131 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210131 Ref country code: GB Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210115 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210115 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20201024 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20210131 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: HU Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO Effective date: 20160115 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CY Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SE Payment date: 20231127 Year of fee payment: 9 Ref country code: FR Payment date: 20231212 Year of fee payment: 9 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20200624 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20231128 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NO Payment date: 20240108 Year of fee payment: 9 |