EP3088557A1 - Hot dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement - Google Patents
Hot dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement Download PDFInfo
- Publication number
- EP3088557A1 EP3088557A1 EP14875617.4A EP14875617A EP3088557A1 EP 3088557 A1 EP3088557 A1 EP 3088557A1 EP 14875617 A EP14875617 A EP 14875617A EP 3088557 A1 EP3088557 A1 EP 3088557A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel sheet
- alloy layer
- hot
- layer
- liquid metal
- 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.)
- Granted
Links
- 229910001338 liquidmetal Inorganic materials 0.000 title claims abstract description 23
- 238000005336 cracking Methods 0.000 title claims description 31
- 229910001335 Galvanized steel Inorganic materials 0.000 title claims description 30
- 239000008397 galvanized steel Substances 0.000 title claims description 30
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 92
- 239000010959 steel Substances 0.000 claims abstract description 92
- 229910001297 Zn alloy Inorganic materials 0.000 claims abstract description 40
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 11
- 229910045601 alloy Inorganic materials 0.000 claims description 38
- 239000000956 alloy Substances 0.000 claims description 38
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 26
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 23
- 238000005246 galvanizing Methods 0.000 claims description 18
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 claims description 17
- 229910052782 aluminium Inorganic materials 0.000 claims description 14
- 239000011572 manganese Substances 0.000 claims description 14
- 229910018137 Al-Zn Inorganic materials 0.000 claims description 10
- 229910018573 Al—Zn Inorganic materials 0.000 claims description 10
- 238000005275 alloying Methods 0.000 claims description 8
- 239000011651 chromium Substances 0.000 claims description 7
- 230000001629 suppression Effects 0.000 claims description 7
- 229910052748 manganese Inorganic materials 0.000 claims description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 239000010936 titanium Substances 0.000 claims description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 3
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 3
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims description 3
- 239000011574 phosphorus Substances 0.000 claims description 3
- 229910052710 silicon Inorganic materials 0.000 claims description 3
- 239000010703 silicon Substances 0.000 claims description 3
- 229910052717 sulfur Inorganic materials 0.000 claims description 3
- 239000011593 sulfur Substances 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 2
- 229910052757 nitrogen Inorganic materials 0.000 claims description 2
- 229910052719 titanium Inorganic materials 0.000 claims description 2
- 239000011248 coating agent Substances 0.000 claims 1
- 238000000576 coating method Methods 0.000 claims 1
- 239000011701 zinc Substances 0.000 abstract description 47
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 abstract description 32
- 229910052725 zinc Inorganic materials 0.000 abstract description 32
- 238000003466 welding Methods 0.000 abstract description 12
- 238000000465 moulding Methods 0.000 abstract description 2
- CPELXLSAUQHCOX-UHFFFAOYSA-M Bromide Chemical compound [Br-] CPELXLSAUQHCOX-UHFFFAOYSA-M 0.000 abstract 4
- 239000010410 layer Substances 0.000 description 103
- 238000007747 plating Methods 0.000 description 62
- 229910000937 TWIP steel Inorganic materials 0.000 description 16
- 230000000052 comparative effect Effects 0.000 description 14
- 239000011247 coating layer Substances 0.000 description 13
- 238000003780 insertion Methods 0.000 description 10
- 230000037431 insertion Effects 0.000 description 10
- 238000000926 separation method Methods 0.000 description 10
- 230000003247 decreasing effect Effects 0.000 description 8
- 238000001816 cooling Methods 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 7
- 239000007788 liquid Substances 0.000 description 7
- 238000000034 method Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- 239000007789 gas Substances 0.000 description 5
- 238000009792 diffusion process Methods 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 238000010583 slow cooling Methods 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000009713 electroplating Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 238000005554 pickling Methods 0.000 description 3
- 101100493710 Caenorhabditis elegans bath-40 gene Proteins 0.000 description 2
- 229910021328 Fe2Al5 Inorganic materials 0.000 description 2
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 2
- 238000004140 cleaning Methods 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 230000008646 thermal stress Effects 0.000 description 2
- QIVUCLWGARAQIO-OLIXTKCUSA-N (3s)-n-[(3s,5s,6r)-6-methyl-2-oxo-1-(2,2,2-trifluoroethyl)-5-(2,3,6-trifluorophenyl)piperidin-3-yl]-2-oxospiro[1h-pyrrolo[2,3-b]pyridine-3,6'-5,7-dihydrocyclopenta[b]pyridine]-3'-carboxamide Chemical compound C1([C@H]2[C@H](N(C(=O)[C@@H](NC(=O)C=3C=C4C[C@]5(CC4=NC=3)C3=CC=CN=C3NC5=O)C2)CC(F)(F)F)C)=C(F)C=CC(F)=C1F QIVUCLWGARAQIO-OLIXTKCUSA-N 0.000 description 1
- HFGHRUCCKVYFKL-UHFFFAOYSA-N 4-ethoxy-2-piperazin-1-yl-7-pyridin-4-yl-5h-pyrimido[5,4-b]indole Chemical compound C1=C2NC=3C(OCC)=NC(N4CCNCC4)=NC=3C2=CC=C1C1=CC=NC=C1 HFGHRUCCKVYFKL-UHFFFAOYSA-N 0.000 description 1
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000037396 body weight Effects 0.000 description 1
- 239000004566 building material Substances 0.000 description 1
- 150000001768 cations Chemical class 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000005238 degreasing Methods 0.000 description 1
- 230000032798 delamination Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000002452 interceptive effect Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- AYOOGWWGECJQPI-NSHDSACASA-N n-[(1s)-1-(5-fluoropyrimidin-2-yl)ethyl]-3-(3-propan-2-yloxy-1h-pyrazol-5-yl)imidazo[4,5-b]pyridin-5-amine Chemical compound N1C(OC(C)C)=CC(N2C3=NC(N[C@@H](C)C=4N=CC(F)=CN=4)=CC=C3N=C2)=N1 AYOOGWWGECJQPI-NSHDSACASA-N 0.000 description 1
- VOVZXURTCKPRDQ-CQSZACIVSA-N n-[4-[chloro(difluoro)methoxy]phenyl]-6-[(3r)-3-hydroxypyrrolidin-1-yl]-5-(1h-pyrazol-5-yl)pyridine-3-carboxamide Chemical compound C1[C@H](O)CCN1C1=NC=C(C(=O)NC=2C=CC(OC(F)(F)Cl)=CC=2)C=C1C1=CC=NN1 VOVZXURTCKPRDQ-CQSZACIVSA-N 0.000 description 1
- XULSCZPZVQIMFM-IPZQJPLYSA-N odevixibat Chemical compound C12=CC(SC)=C(OCC(=O)N[C@@H](C(=O)N[C@@H](CC)C(O)=O)C=3C=CC(O)=CC=3)C=C2S(=O)(=O)NC(CCCC)(CCCC)CN1C1=CC=CC=C1 XULSCZPZVQIMFM-IPZQJPLYSA-N 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 230000003252 repetitive effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- KMIOJWCYOHBUJS-HAKPAVFJSA-N vorolanib Chemical compound C1N(C(=O)N(C)C)CC[C@@H]1NC(=O)C1=C(C)NC(\C=C/2C3=CC(F)=CC=C3NC\2=O)=C1C KMIOJWCYOHBUJS-HAKPAVFJSA-N 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C18/00—Alloys based on zinc
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/50—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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0222—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating in a reactive atmosphere, e.g. oxidising or reducing atmosphere
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0224—Two or more thermal pretreatments
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/026—Deposition of sublayers, e.g. adhesion layers or pre-applied alloying elements or corrosion protection
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/02—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D only coatings only including layers of metallic material
Definitions
- the present disclosure relates to a hot-dip galvanized steel sheet having excellent resistance to cracking caused by liquid metal embrittlement.
- body components of a vehicle are required to be lightweight while having stability. To this end, it is required to ensure high strength, ductility, and corrosion resistance in a steel sheet used for a component for a vehicle.
- Patent Document 1 A representative technique therefor is disclosed in Patent Document 1.
- the technique relates to a Twinning-Induced Plasticity (TWIP) type ultra high strength steel sheet including 0.15 wt% to 0.30 wt% of carbon (C), 0.01 wt% to 0.03 wt% of silicon (Si), 15 wt% to 25 wt% of manganese (Mn), 1.2 wt% to 3. 0 wt% of aluminum (Al), 0. 020 wt% or less of phosphorus (P), 0.001 wt% to 0.002 wt% of sulfur (S), and iron (Fe) as a residual component thereof, and inevitable impurities, and a microstructure of steel is formed of a structure in an austenite phase. Ultra high tensile and high elongation are ensured, whereby the TWIP type ultra high strength steel sheet complies with vehicle body weight requirements.
- TWIP Twinning-Induced Plasticity
- a hot-dip steel sheet has excellent corrosion resistance, whereby such hot-dip steel sheets have been widely used in building materials, structures, household appliances, vehicle bodies, and the like.
- Types of hot-dip steel sheet which have been most recently widely used can be divided into either a hot-dip galvanized steel sheet (hereinafter referred to as 'GI steel sheet') or an alloyed hot-dip galvanized steel sheet (hereinafter referred to as 'GA steel sheet').
- a GI steel sheet is a steel sheet plated with molten zinc.
- the GI steel sheet can be easily plated, and has excellent corrosion resistance.
- the GI steel sheet has been widely used in vehicle bodies.
- a general GI steel sheet is a steel sheet in which a plating layer is formed as the GI steel sheet is submerged in a zinc plating bath to which 0.16 wt% to 0.25 wt% of Al has been added.
- the plating layer is composed mostly of zinc, but an alloying suppression layer capable of suppressing the alloying of iron and zinc is provided in a thickness of 1 ⁇ m or less at an interface between a base steel and a zinc plating layer.
- the alloying suppression layer is generally composed of Fe 2 Al 5-x Zn x .
- spot-welding is generally performed.
- an alloying suppression layer formed in the GI steel sheet is melted by welding heat, thereby generating liquid zinc. More particularly, when spot-welding, a temperature of a welded portion is increased to about 1500°C or more within about 1 second, whereby a base steel and a plating layer are melted and welded. At this time, in a welding heat affected zone (HAZ) region, a temperature of a plating layer is increased to 600°C to 800°C.
- HTZ welding heat affected zone
- Fe is diffused in the plating layer, whereby a portion of the plating layer is alloyed to form an Fe-Zn alloy layer, and the remainder thereof is liquid zinc.
- the liquid zinc may penetrate into a grain boundary of a surface of a base steel and enters the grain boundary thereof.
- a crack having a size of about 10 ⁇ m to 100 ⁇ m may occur, thereby causing a brittle fracture phenomenon. This is referred to as liquid metal embrittlement (hereinafter referred to as 'LME').
- the TWIP steel In the case of a TWIP steel in which an austenite fraction is greater or the like, the TWIP steel has a higher resistance value than that of other types of steel, whereby the TWIP steel will be in a state of high temperature. In addition, as a grain boundary is expanded by a high thermal expansion coefficient, a liquid metal embrittlement problem may occur severely. In addition, in the case of TWIP steel, the TWIP steel has a higher thermal expansion coefficient than that of other types of steel such as a ferritic steel sheet and the like, whereby thermal stress may be caused. As a result, without external tensile stress, the thermal stress is applied to a welded portion, whereby the possibility of the occurrence of liquid metal embrittlement may be very high.
- FIG. 1 is a view illustrating GI TWIP steel in which an LME crack is present in a welded portion.
- the LME crack causes fracturing of a steel sheet, whereby it may be difficult to use GI TWIP steel as a component for a vehicle and the like.
- Patent document 1 Korea Patent Laid-Open Publication No. 2007-0018416
- An aspect of the present disclosure is to provide a hot-dip galvanized steel sheet having excellent resistance to cracking caused by liquid metal embrittlement.
- a hot-dip galvanized steel sheet having excellent resistance to cracking caused by liquid metal embrittlement may include: a base steel sheet having a microstructure in which an austenite fraction is 90 area% or more; and a hot-dip galvanizing layer formed on the base steel sheet.
- the hot-dip galvanizing layer may include: an Fe-Zn alloy layer; and a Zn layer formed on the Fe-Zn alloy layer.
- the Fe-Zn alloy layer may have a thickness of [(3.4 ⁇ t)/6] ⁇ m or more, where t is a thickness of the hot-dip galvanizing layer.
- a hot-dip galvanized steel sheet in which plating layer delamination which may easily occur under vehicle welding and molding conditions according to the related art may be prevented, and the occurrence of cracking caused by liquid metal embrittlement may be suppressed.
- the inventors have conducted research into effectively suppressing the occurrence of cracking caused by liquid metal embrittlement (LME) when the above mentioned GI TIWP steel is manufactured.
- LME liquid metal embrittlement
- the present disclosure is proposed under the discovery that occurrence of cracking caused by LME may be prevented by suppressing the formation of a surface oxide used to suppress the diffusion of iron (Fe) and an Fe-Al or Fe-Al-Zn alloy layer, and by forming an Fe-Zn alloy layer having a sufficient thickness.
- FIG. 2A is a schematic view illustrating a cross section of existing GI TWIP steel
- FIG. 2B is a schematic view illustrating a cross section of a hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure.
- FIG. 2 schematically illustrates an exemplary embodiment in the present disclosure to illustrate the present disclosure, but does not limit the scope of the present disclosure.
- an alloying suppression layer Fe-Al or Fe-Al-Zn alloy layer 2 is formed on a base steel sheet 1, and a Zn layer 3 is formed on the alloying suppression layer 2.
- a surface oxide 4 such as MnO or the like exists between the base steel sheet 1 and the Zn layer 3.
- GI TWIP steel including a plating layer having such a structure when spot-welding, liquid zinc is generated due to the alloying suppression layer 2, thereby causing LME cracking.
- a hot-dip galvanized steel sheet includes a base steel sheet 10, and a hot-dip galvanizing layer 20 formed on the base steel sheet.
- the hot-dip galvanizing layer 20 has a structure in which an Fe-Zn alloy layer 21 and a Zn layer 22 are sequentially formed.
- the hot-dip galvanizing layer 20 according to an exemplary embodiment in the present disclosure formed on the base steel sheet 10 may preferably have a structure in which an Fe-Zn alloy layer 21 and a Zn layer 22 are sequentially formed.
- a hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure may preferably have a microstructure in which an austenite fraction is 90 area% or more.
- a base steel sheet used in a hot-dip galvanized steel sheet may include, by wt%, carbon (C): 0.10% to 0.30%, manganese (Mn): 10% to 30%, silicon (Si): 0.01% to 0.03%, titanium (Ti): 0.05% to 0.2%, manganese (Mn) : 10% to 30%, aluminum (Al) : 0.5% to 3.0%, nickel (Ni) : 0.001% to 10%, chromium (Cr) : 0.001% to 10%, nitrogen (N) : 0.001% to 0.05%, phosphorus (P): 0.020% or less, sulfur (S): 0.001% to 0.005%, and iron (Fe) as a residual component thereof, and inevitable impurities.
- the Fe-Zn alloy layer 21 is formed to have a sufficient thickness.
- the Fe-Zn alloy layer 21 allows the formation of liquid zinc to be decreased, thereby suppressing occurrence of cracking caused by LME.
- Zn preferentially reacts with Fe, the transformation of Zn into liquid zinc due to a heat effect caused by welding may be suppressed.
- the Fe-Zn alloy layer 21 is formed to a sufficient thickness in advance, thereby improving the above-described effect.
- a thickness of the Fe-Zn alloy layer be [(3.4 ⁇ t)/6] ⁇ m or more.
- a thickness of the Fe-Zn alloy layer is less than [(3.4 ⁇ t)/6] ⁇ m, an effect of suppressing occurrence of cracking caused by LME may not be sufficiently obtained.
- the above described t refers to a thickness of the hot-dip galvanizing layer. According to an exemplary embodiment in the present disclosure, as a thickness of the Fe-Zn alloy layer is increased, a preferable effect may be obtained.
- an upper limit of the Fe-Zn alloy layer thickness is not particularly limited.
- the Fe-Zn alloy layer 21 includes Fe of 3 wt% to 15 wt%.
- Fe contents inside the Fe-Zn alloy layer are less than 3 wt%, in an amount the same as that of an existing GI steel sheet, there may be a disadvantage that cracking caused by LME occurs.
- Fe contents inside the Fe-Zn alloy layer are more than 15 wt%, a problem of decreasing workability may occur.
- Zn may remain as a Zn layer on the Fe-Zn alloy layer 21 as Zn does not react to Fe.
- the Fe-Al or Fe-Al-Zn alloy layer 23 may cause cracking caused by LME by forming liquid zinc when welding.
- a thickness of the Fe-Al or Fe-Al-Zn alloy layer 23 is formed to be as thin as possible.
- component contents of the Fe-Al and Fe-Al-Zn alloy layer are not particularly limited.
- the Fe-Al alloy layer may be Fe 2 Al 5
- the Fe-Al-Zn alloy layer may be Fe 2 Al 5 Zn x .
- the alloy layer 23 includes 0.3 wt% or less of Al.
- Al contents contained in the alloy layer 23 exceed 0.3 wt%, diffusion of Fe is suppressed. Thus, it may be difficult to ensure an Fe-Zn alloy layer having a sufficient thickness.
- an Fe-Ni alloy layer 30 is further included directly below a surface of the base steel sheet. More particularly, the Fe-Ni alloy layer 30 may ensure excellent plating adhesion as MnO or the like exists as an internal oxide 40 by suppressing a surface oxide such as MnO or the like from being formed, as an oxidizing element such as Mn or the like is enriched on a surface of the Fe-Ni alloy layer 30, in the manner of TWIP steel. To ensure the above effect, the Fe-Ni alloy layer may be formed by a Ni coating layer having an adhesion amount of 300 mg/m 2 to 1000 mg/m 2 , and a thickness of the Fe-Ni alloy layer may be different according to manufacturing conditions.
- a thickness of the Fe-Ni alloy layer may have a range of 0.05 ⁇ m to 5 ⁇ m.
- the Fe-Ni alloy layer is formed to have a thickness less than 0.05 ⁇ m, zinc wettability is decreased, thereby being non-plated or decreasing plating adhesion.
- a thickness of the Fe-Ni alloy layer exceeds 5 ⁇ m, a problem that an amount of Fe diffused into a plating layer from a base steel sheet is reduced may occur, and manufacturing costs may be sharply increased.
- one or more type selected from a group consisting of an Fe-X alloy layer, an Fe-Al-X alloy layer, an Fe-Al-Zn-X alloy layer, and an Fe-Zn-X alloy layer may be additionally included between the base steel sheet and the hot-dip galvanizing layer.
- the alloy layer As the alloy layer is formed, plating adhesion and excellent resistance to occurrence of cracking caused by LME may be ensured.
- the above-described X for example, is a material which may have cations inside an electroplating solution, and the X may be one of Ni and Cr.
- the hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure provided as described above may ensure excellent resistance to cracking caused by LME, and may ensure an excellent level of plating adhesion, a physical property typically required in a hot-dip galvanized steel sheet.
- the hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure may be manufactured by various methods.
- the base steel sheet is heated to a temperature of 700°C to 900°C in a reducing atmosphere furnace charged with a H 2 -N 2 mixed gas, and the heated base steel sheet is cooled.
- the base steel sheet is submerged in a molten zinc plating bath at 440°C to 460°C including 0.13 wt% or less of Al.
- the hot-dip galvanized steel sheet may be manufactured by using the above-mentioned method.
- the hot-dip galvanized steel sheet proposed according to an exemplary embodiment in the present disclosure may be manufactured.
- a base steel sheet having a microstructure in which an austenite fraction is 90 area% or more is prepared.
- the base steel sheet as TWIP steel, has a high austenite fraction.
- the base steel sheet includes a large amount of Mn, Al, Ni, and the like such as an oxidizing element.
- a surface of the base steel sheet is required to be cleaned beforehand. For example, to remove foreign substances or an oxide film or the like from a surface thereof, it may be preferable to perform a pickling or cleaning process. When the pickling or cleaning process is not performed, a coating layer or a plating layer is not uniform, and a plating appearance or adhesion may be decreased.
- a Ni coating layer is formed on the prepared base steel sheet as described above. Formation of the Ni coating layer may be performed by electro-plating. Thus, a coating layer having a uniform thickness may be formed. On the other hand, the Ni coating layer preferably has an adhesion of 300 mg/m 2 to 1000 mg/m 2 . When an adhesion of the Ni coating layer is less than 300 mg/m 2 , an Fe-Ni alloy layer having a sufficient thickness is not formed. Thus, a surface enrichment amount of Mn is not sufficiently suppressed, and zinc wettability is also decreased, thereby causing a non-plating phenomenon or decreasing plating adhesion.
- an adhesion amount of the Ni coating layer exceeds 1000 mg/m 2 , an amount of Fe diffused into a plating layer from a base steel sheet is decreased by forming an Fe-Ni alloy layer in which Ni contents are high. Thus, an Fe-Zn alloy layer having a sufficient thickness may not be obtained, and manufacturing costs may be sharply increased.
- the base steel sheet having the Ni coating layer is heated to a temperature of 700°C to 900°C in a reducing atmosphere furnace charged with a H 2 -N 2 mixed gas.
- Ni in the Ni coating layer may penetrate into an interior of the base steel sheet, thereby forming an Fe-Ni alloy layer.
- the heating temperature is lower than 700°C, a steel sheet structure is not transformed into a structure formed in an austenite phase after cold-rolling the steel sheet structure.
- the heating temperature exceeds 900°C, chances that deformation and fractures will occur in a steel sheet are increased.
- the base steel sheet After heating, it may be preferable that the base steel sheet is maintained in the heating temperature range for 20 or more seconds. When the retention time is less than 20 seconds, an Fe-Ni alloy layer having a sufficient thickness is not formed. Thus, a surface enrichment amount of Mn is not sufficiently suppressed.
- the heated base steel sheet is cooled to a temperature between 400°C to 500°C at a cooling rate of 5°C/s or more.
- the cooling rate is less than 5°C/s, it may be difficult to obtain austenite of 90 area% or more.
- a plating bath insertion temperature of the cooled base steel sheet is controlled to have a range of (molten zinc plating bath-40°C) to (molten zinc plating bath+10°C) .
- the plating bath insertion temperature is lower than (molten zinc plating bath-40°C)
- Fe contained in a base steel sheet is less eluted, thereby suppressing formation of a structure in an Fe-Zn alloy phase.
- the plating bath insertion temperature exceeds (molten zinc plating bath+10°C), an Fe-Al or Fe-Al-Zn alloy layer is thickly formed, thereby interfering in diffusion of Fe.
- controlling a plating bath insertion temperature of the base steel sheet may be performed by cooling the base steel sheet when the cooling stop temperature is higher than the plating bath insertion temperature, maintaining the base steel sheet at temperature when the cooling stop temperature is the same as the plating bath insertion temperature, and heating the base steel sheet when the cooling stop temperature is lower than the plating bath insertion temperature.
- the base steel sheet controlled in a range of the plating bath insertion temperature is submerged into a molten zinc plating bath at 440°C to 460°C including 0.13 wt% or less of Al, whereby a plating solution is applied to a surface of the base steel sheet.
- contents of Al of the molten zinc plating bath exceed 0.13 wt%, diffusion of Fe is suppressed, whereby it may be difficult to obtain an Fe-Zn alloy layer having a sufficient thickness.
- a temperature of the molten zinc plating bath is lower than 440°C, it may be difficult to ensure fluidity of a plating solution, whereby plating may not be performed smoothly.
- a temperature of the molten zinc plating bath exceeds 460°C, a problem that a plating solution is volatilized or the like, may occur.
- the base steel sheet to which the plating solution is applied is slowly cooled at a slow cooling rate of 4°C/s to 20°C/s, thereby forming a hot-dip galvanizing layer.
- the slow cooling rate is lower than 4°C/s, unsolidified zinc may be smeared on equipment such as a roll, thereby causing secondary product defects.
- the slow cooling rate exceeds 20°C/s, there may be a disadvantage that the Fe-Zn alloy layer does not grow enough to have a sufficient thickness.
- an Fe-Ni alloy layer is formed directly below a surface of the base steel sheet, and Fe contained inside the base steel sheet is diffused to a plating layer simultaneously.
- a hot-dip galvanizing layer having a structure required according to an exemplary embodiment in the present disclosure may be formed on the base steel sheet.
- a Ni coating layer was formed on the base steel sheet through electro-plating and provided as an adhesion amount in table 1 (comparative examples 2 to 4 were not carried out) .
- the base steel sheet was heated under the conditions of table 1 in a reducing atmosphere furnace charged with a 5% H 2 -N 2 mixed gas, the base steel sheet was cooled to 400°C.
- the base steel sheet was submerged in a molten zinc plating bath at 460°C, and then a plating solution was applied to the base steel sheet.
- the hot-dip galvanized steel sheet was spot-welded at a welding current of 5.8 kA, a size of individual cracks caused by LME was measured, and results thereof were shown in table 1.
- the plating adhesion evaluation was conducted by checking whether a plating material was smeared on tape after bending a hot-dip galvanized steel sheet through 180°. When the plating material was smeared on the tape, it was shown as separation. When plating material was not smeared on the tape, it was shown as non-separation.
Abstract
Description
- The present disclosure relates to a hot-dip galvanized steel sheet having excellent resistance to cracking caused by liquid metal embrittlement.
- In general, body components of a vehicle are required to be lightweight while having stability. To this end, it is required to ensure high strength, ductility, and corrosion resistance in a steel sheet used for a component for a vehicle.
- A representative technique therefor is disclosed in
Patent Document 1. The technique relates to a Twinning-Induced Plasticity (TWIP) type ultra high strength steel sheet including 0.15 wt% to 0.30 wt% of carbon (C), 0.01 wt% to 0.03 wt% of silicon (Si), 15 wt% to 25 wt% of manganese (Mn), 1.2 wt% to 3. 0 wt% of aluminum (Al), 0. 020 wt% or less of phosphorus (P), 0.001 wt% to 0.002 wt% of sulfur (S), and iron (Fe) as a residual component thereof, and inevitable impurities, and a microstructure of steel is formed of a structure in an austenite phase. Ultra high tensile and high elongation are ensured, whereby the TWIP type ultra high strength steel sheet complies with vehicle body weight requirements. - On the other hand, a hot-dip steel sheet has excellent corrosion resistance, whereby such hot-dip steel sheets have been widely used in building materials, structures, household appliances, vehicle bodies, and the like. Types of hot-dip steel sheet which have been most recently widely used, can be divided into either a hot-dip galvanized steel sheet (hereinafter referred to as 'GI steel sheet') or an alloyed hot-dip galvanized steel sheet (hereinafter referred to as 'GA steel sheet').
- A GI steel sheet is a steel sheet plated with molten zinc. The GI steel sheet can be easily plated, and has excellent corrosion resistance. Thus, the GI steel sheet has been widely used in vehicle bodies. A general GI steel sheet is a steel sheet in which a plating layer is formed as the GI steel sheet is submerged in a zinc plating bath to which 0.16 wt% to 0.25 wt% of Al has been added. In the GI steel sheet, the plating layer is composed mostly of zinc, but an alloying suppression layer capable of suppressing the alloying of iron and zinc is provided in a thickness of 1 µm or less at an interface between a base steel and a zinc plating layer. Thus, adhesion between a base steel and a plating layer is excellent. The alloying suppression layer is generally composed of Fe2Al5-xZnx.
- On the other hand, to use the GI steel sheet as a component of a vehicle, spot-welding is generally performed. In this case, an alloying suppression layer formed in the GI steel sheet is melted by welding heat, thereby generating liquid zinc. More particularly, when spot-welding, a temperature of a welded portion is increased to about 1500°C or more within about 1 second, whereby a base steel and a plating layer are melted and welded. At this time, in a welding heat affected zone (HAZ) region, a temperature of a plating layer is increased to 600°C to 800°C. Thus, Fe is diffused in the plating layer, whereby a portion of the plating layer is alloyed to form an Fe-Zn alloy layer, and the remainder thereof is liquid zinc. The liquid zinc may penetrate into a grain boundary of a surface of a base steel and enters the grain boundary thereof. At this time, when tensile stress is applied to the HAZ, a crack having a size of about 10 µm to 100 µm may occur, thereby causing a brittle fracture phenomenon. This is referred to as liquid metal embrittlement (hereinafter referred to as 'LME'). In the case of a TWIP steel in which an austenite fraction is greater or the like, the TWIP steel has a higher resistance value than that of other types of steel, whereby the TWIP steel will be in a state of high temperature. In addition, as a grain boundary is expanded by a high thermal expansion coefficient, a liquid metal embrittlement problem may occur severely. In addition, in the case of TWIP steel, the TWIP steel has a higher thermal expansion coefficient than that of other types of steel such as a ferritic steel sheet and the like, whereby thermal stress may be caused. As a result, without external tensile stress, the thermal stress is applied to a welded portion, whereby the possibility of the occurrence of liquid metal embrittlement may be very high.
-
FIG. 1 is a view illustrating GI TWIP steel in which an LME crack is present in a welded portion. When an LME crack occurs as illustrated inFIG. 1 , the LME crack causes fracturing of a steel sheet, whereby it may be difficult to use GI TWIP steel as a component for a vehicle and the like. - Because of these technical problems, with respect to a GI TWIP steel plate in which an austenite phase fraction is great, the development of a technology for improving resistance to cracking caused by liquid metal embrittlement after welding is required.
- (Patent document 1) Korea Patent Laid-Open Publication No.
2007-0018416 - An aspect of the present disclosure is to provide a hot-dip galvanized steel sheet having excellent resistance to cracking caused by liquid metal embrittlement.
- According to an aspect of the present disclosure, a hot-dip galvanized steel sheet having excellent resistance to cracking caused by liquid metal embrittlement may include: a base steel sheet having a microstructure in which an austenite fraction is 90 area% or more; and a hot-dip galvanizing layer formed on the base steel sheet. The hot-dip galvanizing layer may include: an Fe-Zn alloy layer; and a Zn layer formed on the Fe-Zn alloy layer. The Fe-Zn alloy layer may have a thickness of [(3.4×t)/6]µm or more, where t is a thickness of the hot-dip galvanizing layer.
- According to an exemplary embodiment in the present disclosure, provided is a hot-dip galvanized steel sheet in which plating layer delamination which may easily occur under vehicle welding and molding conditions according to the related art may be prevented, and the occurrence of cracking caused by liquid metal embrittlement may be suppressed.
-
-
FIG. 1 is a view illustrating GI TWIP steel in which an LME crack occurs in a welded portion. -
FIG. 2A is a schematic view illustrating a cross section of existing GI TWIP steel, andFIG. 2B is a schematic view illustrating a cross section of a hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure. -
FIG. 3 is a view of a cross section of a welded portion of inventive example 1 according to an exemplary embodiment in the present disclosure. -
FIG. 4 is a view of a cross section of a welded portion of comparative example 1 outside of a range according to an exemplary embodiment in the present disclosure. - The inventors have conducted research into effectively suppressing the occurrence of cracking caused by liquid metal embrittlement (LME) when the above mentioned GI TIWP steel is manufactured. The present disclosure is proposed under the discovery that occurrence of cracking caused by LME may be prevented by suppressing the formation of a surface oxide used to suppress the diffusion of iron (Fe) and an Fe-Al or Fe-Al-Zn alloy layer, and by forming an Fe-Zn alloy layer having a sufficient thickness.
-
FIG. 2A is a schematic view illustrating a cross section of existing GI TWIP steel, andFIG. 2B is a schematic view illustrating a cross section of a hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure. Hereinafter, an exemplary embodiment in the present disclosure will be described with reference toFIG. 2. FIG. 2 schematically illustrates an exemplary embodiment in the present disclosure to illustrate the present disclosure, but does not limit the scope of the present disclosure. - As illustrated in
FIG. 2A , in existing general GI TWIP steel, an alloying suppression layer (Fe-Al or Fe-Al-Zn alloy layer) 2 is formed on abase steel sheet 1, and aZn layer 3 is formed on thealloying suppression layer 2. In addition, asurface oxide 4 such as MnO or the like exists between thebase steel sheet 1 and theZn layer 3. In a case of GI TWIP steel including a plating layer having such a structure, when spot-welding, liquid zinc is generated due to thealloying suppression layer 2, thereby causing LME cracking. - However, as illustrated in
FIG. 2B , a hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure includes abase steel sheet 10, and a hot-dip galvanizinglayer 20 formed on the base steel sheet. In this case, the hot-dip galvanizinglayer 20 has a structure in which an Fe-Zn alloy layer 21 and a Zn layer 22 are sequentially formed. Thus, plating adhesion and excellent resistance to the occurrence of cracking caused by LME may be ensured. - As described above, the hot-
dip galvanizing layer 20 according to an exemplary embodiment in the present disclosure formed on thebase steel sheet 10 may preferably have a structure in which an Fe-Zn alloy layer 21 and a Zn layer 22 are sequentially formed. - For a base steel sheet 100 applied to an exemplary embodiment in the present disclosure, TWIP steel in which a cracking problem caused by LME severely occurs as described above, is a target. Accordingly, a hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure may preferably have a microstructure in which an austenite fraction is 90 area% or more. In addition, in order to ensure the above-mentioned microstructure and to ensure excellent mechanical properties and the like, a base steel sheet used in a hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure may include, by wt%, carbon (C): 0.10% to 0.30%, manganese (Mn): 10% to 30%, silicon (Si): 0.01% to 0.03%, titanium (Ti): 0.05% to 0.2%, manganese (Mn) : 10% to 30%, aluminum (Al) : 0.5% to 3.0%, nickel (Ni) : 0.001% to 10%, chromium (Cr) : 0.001% to 10%, nitrogen (N) : 0.001% to 0.05%, phosphorus (P): 0.020% or less, sulfur (S): 0.001% to 0.005%, and iron (Fe) as a residual component thereof, and inevitable impurities.
- According to an exemplary embodiment in the present disclosure, the Fe-Zn alloy layer 21 is formed to have a sufficient thickness. The Fe-Zn alloy layer 21 allows the formation of liquid zinc to be decreased, thereby suppressing occurrence of cracking caused by LME. To suppress occurrence of cracking caused by LME, when welding, it is advantageous to allow Fe to be quickly diffused and then Fe to react with Zn, thereby forming an Fe-Zn alloy layer. Thus, as Zn preferentially reacts with Fe, the transformation of Zn into liquid zinc due to a heat effect caused by welding may be suppressed. Thus, according to an exemplary embodiment in the present disclosure, the Fe-Zn alloy layer 21 is formed to a sufficient thickness in advance, thereby improving the above-described effect. To this end, it may be preferable that a thickness of the Fe-Zn alloy layer be [(3.4×t)/6] µm or more. When a thickness of the Fe-Zn alloy layer is less than [(3.4×t)/6] µm, an effect of suppressing occurrence of cracking caused by LME may not be sufficiently obtained. On the other hand, the above described t refers to a thickness of the hot-dip galvanizing layer. According to an exemplary embodiment in the present disclosure, as a thickness of the Fe-Zn alloy layer is increased, a preferable effect may be obtained. Thus, an upper limit of the Fe-Zn alloy layer thickness is not particularly limited.
- Furthermore, it may be preferable that the Fe-Zn alloy layer 21 includes Fe of 3 wt% to 15 wt%. When Fe contents inside the Fe-Zn alloy layer are less than 3 wt%, in an amount the same as that of an existing GI steel sheet, there may be a disadvantage that cracking caused by LME occurs. When Fe contents inside the Fe-Zn alloy layer are more than 15 wt%, a problem of decreasing workability may occur.
- Zn may remain as a Zn layer on the Fe-Zn alloy layer 21 as Zn does not react to Fe.
- On the other hand, according to an exemplary embodiment in the present disclosure, it may be preferable to suppress the formation of an Fe-Al or Fe-Al-Zn alloy layer 23 formed in a lower part of the hot-
dip galvanizing layer 20, in other words, between abase steel sheet 10 and an Fe-Zn alloy layer 21 as possible. The Fe-Al or Fe-Al-Zn alloy layer 23 may cause cracking caused by LME by forming liquid zinc when welding. Thus, according to an exemplary embodiment in the present disclosure, a thickness of the Fe-Al or Fe-Al-Zn alloy layer 23 is formed to be as thin as possible. On the other hand, according to an exemplary embodiment in the present disclosure, component contents of the Fe-Al and Fe-Al-Zn alloy layer are not particularly limited. For example, the Fe-Al alloy layer may be Fe2Al5, and the Fe-Al-Zn alloy layer may be Fe2Al5Znx. - In addition, it may be preferable that the alloy layer 23 includes 0.3 wt% or less of Al. When Al contents contained in the alloy layer 23 exceed 0.3 wt%, diffusion of Fe is suppressed. Thus, it may be difficult to ensure an Fe-Zn alloy layer having a sufficient thickness.
- On the other hand, it may be preferable that an Fe-
Ni alloy layer 30 is further included directly below a surface of the base steel sheet. More particularly, the Fe-Ni alloy layer 30 may ensure excellent plating adhesion as MnO or the like exists as aninternal oxide 40 by suppressing a surface oxide such as MnO or the like from being formed, as an oxidizing element such as Mn or the like is enriched on a surface of the Fe-Ni alloy layer 30, in the manner of TWIP steel. To ensure the above effect, the Fe-Ni alloy layer may be formed by a Ni coating layer having an adhesion amount of 300 mg/m2 to 1000 mg/m2, and a thickness of the Fe-Ni alloy layer may be different according to manufacturing conditions. For example, a thickness of the Fe-Ni alloy layer may have a range of 0.05 µm to 5 µm. When the Fe-Ni alloy layer is formed to have a thickness less than 0.05 µm, zinc wettability is decreased, thereby being non-plated or decreasing plating adhesion. On the other hand, in the case that a thickness of the Fe-Ni alloy layer exceeds 5 µm, a problem that an amount of Fe diffused into a plating layer from a base steel sheet is reduced may occur, and manufacturing costs may be sharply increased. - In addition, one or more type selected from a group consisting of an Fe-X alloy layer, an Fe-Al-X alloy layer, an Fe-Al-Zn-X alloy layer, and an Fe-Zn-X alloy layer may be additionally included between the base steel sheet and the hot-dip galvanizing layer. As the alloy layer is formed, plating adhesion and excellent resistance to occurrence of cracking caused by LME may be ensured. The above-described X, for example, is a material which may have cations inside an electroplating solution, and the X may be one of Ni and Cr.
- The hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure provided as described above may ensure excellent resistance to cracking caused by LME, and may ensure an excellent level of plating adhesion, a physical property typically required in a hot-dip galvanized steel sheet.
- On the other hand, the hot-dip galvanized steel sheet according to an exemplary embodiment in the present disclosure may be manufactured by various methods. Preferably, after a Ni coating layer is formed on a base steel sheet, the base steel sheet is heated to a temperature of 700°C to 900°C in a reducing atmosphere furnace charged with a H2-N2 mixed gas, and the heated base steel sheet is cooled. Then, the base steel sheet is submerged in a molten zinc plating bath at 440°C to 460°C including 0.13 wt% or less of Al. Thus, the hot-dip galvanized steel sheet may be manufactured by using the above-mentioned method. As a person of ordinary skill in the art is able to easily control other conditions without separate and repetitive experimentation, the hot-dip galvanized steel sheet proposed according to an exemplary embodiment in the present disclosure may be manufactured.
- First, a base steel sheet having a microstructure in which an austenite fraction is 90 area% or more, is prepared. The base steel sheet as TWIP steel, has a high austenite fraction. To this end, the base steel sheet includes a large amount of Mn, Al, Ni, and the like such as an oxidizing element. Thus, a surface of the base steel sheet is required to be cleaned beforehand. For example, to remove foreign substances or an oxide film or the like from a surface thereof, it may be preferable to perform a pickling or cleaning process. When the pickling or cleaning process is not performed, a coating layer or a plating layer is not uniform, and a plating appearance or adhesion may be decreased.
- A Ni coating layer is formed on the prepared base steel sheet as described above. Formation of the Ni coating layer may be performed by electro-plating. Thus, a coating layer having a uniform thickness may be formed. On the other hand, the Ni coating layer preferably has an adhesion of 300 mg/m2 to 1000 mg/m2. When an adhesion of the Ni coating layer is less than 300 mg/m2, an Fe-Ni alloy layer having a sufficient thickness is not formed. Thus, a surface enrichment amount of Mn is not sufficiently suppressed, and zinc wettability is also decreased, thereby causing a non-plating phenomenon or decreasing plating adhesion. When an adhesion amount of the Ni coating layer exceeds 1000 mg/m2, an amount of Fe diffused into a plating layer from a base steel sheet is decreased by forming an Fe-Ni alloy layer in which Ni contents are high. Thus, an Fe-Zn alloy layer having a sufficient thickness may not be obtained, and manufacturing costs may be sharply increased.
- Hereafter, the base steel sheet having the Ni coating layer is heated to a temperature of 700°C to 900°C in a reducing atmosphere furnace charged with a H2-N2 mixed gas. Through the heating process, Ni in the Ni coating layer may penetrate into an interior of the base steel sheet, thereby forming an Fe-Ni alloy layer. When the heating temperature is lower than 700°C, a steel sheet structure is not transformed into a structure formed in an austenite phase after cold-rolling the steel sheet structure. When the heating temperature exceeds 900°C, chances that deformation and fractures will occur in a steel sheet are increased.
- On the other hand, as a fraction of the H2-N2 mixed gas used for forming a reducing atmosphere which is commonly used in the art, is used, such a fraction of the H2-N2 mixed gas is not particularly mentioned according to an exemplary embodiment in the present disclosure.
- After heating, it may be preferable that the base steel sheet is maintained in the heating temperature range for 20 or more seconds. When the retention time is less than 20 seconds, an Fe-Ni alloy layer having a sufficient thickness is not formed. Thus, a surface enrichment amount of Mn is not sufficiently suppressed.
- Next, the heated base steel sheet is cooled to a temperature between 400°C to 500°C at a cooling rate of 5°C/s or more. When the cooling rate is less than 5°C/s, it may be difficult to obtain austenite of 90 area% or more.
- After cooling, a plating bath insertion temperature of the cooled base steel sheet is controlled to have a range of (molten zinc plating bath-40°C) to (molten zinc plating bath+10°C) . When the plating bath insertion temperature is lower than (molten zinc plating bath-40°C), Fe contained in a base steel sheet is less eluted, thereby suppressing formation of a structure in an Fe-Zn alloy phase. When the plating bath insertion temperature exceeds (molten zinc plating bath+10°C), an Fe-Al or Fe-Al-Zn alloy layer is thickly formed, thereby interfering in diffusion of Fe. On the other hand, controlling a plating bath insertion temperature of the base steel sheet may be performed by cooling the base steel sheet when the cooling stop temperature is higher than the plating bath insertion temperature, maintaining the base steel sheet at temperature when the cooling stop temperature is the same as the plating bath insertion temperature, and heating the base steel sheet when the cooling stop temperature is lower than the plating bath insertion temperature.
- The base steel sheet controlled in a range of the plating bath insertion temperature is submerged into a molten zinc plating bath at 440°C to 460°C including 0.13 wt% or less of Al, whereby a plating solution is applied to a surface of the base steel sheet. When contents of Al of the molten zinc plating bath exceed 0.13 wt%, diffusion of Fe is suppressed, whereby it may be difficult to obtain an Fe-Zn alloy layer having a sufficient thickness. When a temperature of the molten zinc plating bath is lower than 440°C, it may be difficult to ensure fluidity of a plating solution, whereby plating may not be performed smoothly. When a temperature of the molten zinc plating bath exceeds 460°C, a problem that a plating solution is volatilized or the like, may occur.
- Hereafter, the base steel sheet to which the plating solution is applied, is slowly cooled at a slow cooling rate of 4°C/s to 20°C/s, thereby forming a hot-dip galvanizing layer. When the slow cooling rate is lower than 4°C/s, unsolidified zinc may be smeared on equipment such as a roll, thereby causing secondary product defects. When the slow cooling rate exceeds 20°C/s, there may be a disadvantage that the Fe-Zn alloy layer does not grow enough to have a sufficient thickness.
- Through a process as described above, an Fe-Ni alloy layer is formed directly below a surface of the base steel sheet, and Fe contained inside the base steel sheet is diffused to a plating layer simultaneously. Thus, a hot-dip galvanizing layer having a structure required according to an exemplary embodiment in the present disclosure may be formed on the base steel sheet.
- Hereinafter, the present disclosure will be described more in detail through an exemplary embodiment. However, the below exemplary embodiment is an example for describing the present disclosure more in detail, but does not limit the scope of the present disclosure.
- After a cold-rolled TWIP base steel sheet was cleaned by alkalic degreasing and pickling the cold-rolled TWIP base steel sheet, a Ni coating layer was formed on the base steel sheet through electro-plating and provided as an adhesion amount in table 1 (comparative examples 2 to 4 were not carried out) . Next, after the base steel sheet was heated under the conditions of table 1 in a reducing atmosphere furnace charged with a 5% H2-N2 mixed gas, the base steel sheet was cooled to 400°C. In addition, after a plating bath insertion temperature was controlled, the base steel sheet was submerged in a molten zinc plating bath at 460°C, and then a plating solution was applied to the base steel sheet. After a plating adhesion amount was controlled by air-knifing the base steel sheet to which the plating solution was applied, the base steel sheet was slowly cooled under the conditions of table 1, thereby forming an Fe-Ni alloy layer directly below a surface of the base steel sheet. In addition, a hot-dip galvanized steel sheet in which a hot-dip galvanizing layer was formed of an Fe-Al or Fe-Al-Zn alloy layer, an Fe-Zn alloy layer, and a Zn layer, was manufactured. After a thickness of the Fe-Zn alloy layer of the hot-dip galvanized steel sheet was measured, and plating adhesion was evaluated, results thereof were shown in table 1. In addition, after the hot-dip galvanized steel sheet was spot-welded at a welding current of 5.8 kA, a size of individual cracks caused by LME was measured, and results thereof were shown in table 1. On the other hand, the plating adhesion evaluation was conducted by checking whether a plating material was smeared on tape after bending a hot-dip galvanized steel sheet through 180°. When the plating material was smeared on the tape, it was shown as separation. When plating material was not smeared on the tape, it was shown as non-separation.
[Table 1] Classification Ni adhesion amount (mg/m2) Heating temperature (°C) Plating bath insertion temperature (°C) Plating bath Al contents (wt%) Plating adhesion amount (g/m2) Slow cooling rate (°C/s ) Fe-Zn alloy layer thickness (µm) Plating adhesion LME crack length (µm) comparative example1 300 760 480 0.2 60 10 0 non-sepa ration 24.5 comparative example2 - 760 420 0.12 60 10 1.6 separati on 37.0 comparative example3 - 760 460 0.12 60 10 1.8 separati on 25.5 comparative example4 - 760 500 0.12 60 10 0.8 separati on 40.0 comparative example5 300 760 420 0.12 60 10 2.3 non-sepa ration 6.3 comparative example6 300 760 460 0.12 60 10 2.3 non-sepa ration 7.3 comparative example7 300 760 500 0.12 60 10 2.0 non-sepa ration 23.0 comparative example8 500 760 420 0.12 60 10 2.9 non-sepa ration 6.3 comparative example9 500 760 460 0.12 60 10 3.7 non-sepa ration 2.8 inventive example1 780 760 450 0.12 60 10 4.8 non-sepa ration 0 inventive example2 500 760 460 0.12 45 10 3.8 non-sepa ration 0 - As shown in above table 1, in a case of inventive examples 1 and 2 having a hot-dip galvanizing layer satisfying a thickness of an Fe-Zn alloy layer proposed by an exemplary embodiment in the present disclosure, it may be seen that plating adhesion was excellent and cracking caused by LME did not occur at all.
- On the other hand, in a case of comparative example 1, contents of an Al plating bath were excessive, thereby not forming an Fe-Zn alloy layer. Thus, it may be seen that cracking caused by LME occurred in a level of 24.5 µm.
- In a case of comparative examples 2 to 4, as a Ni coating layer was not formed, it may be seen that all plating layers were separated. As an Fe-Zn alloy layer thickness proposed by an exemplary embodiment in the present disclosure was not satisfied, it may be seen that cracking caused by LME severely occurred.
- In a case of comparative examples 4 to 9, as an Fe-Zn alloy layer having a sufficient thickness proposed by an exemplary embodiment in the present disclosure was not formed, it may be seen that cracking caused by LME occurred.
Claims (9)
- A hot-dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement, comprising:a base steel sheet having a microstructure in which an austenite fraction is 90 area% or more; anda hot-dip galvanizing layer formed on the base steel sheet,wherein the hot-dip galvanizing layer includes an Fe-Zn alloy layer, and a Zn layer formed on the Fe-Zn alloy layer, and the Fe-Zn alloy layer has a thickness of [(3.4×t) /6] µm or more, where t is a thickness of the hot-dip galvanizing layer.
- The hot-dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement of claim 1, wherein the Fe-Zn alloy layer includes 3 wt% to 15 wt% of iron (Fe).
- The hot-dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement of claim 1, wherein the base steel sheet comprises, by wt%, carbon (C) : 0.10% to 0.30%, manganese (Mn) : 10% to 30%, silicon (Si) : 0.01% to 0.03%, titanium (Ti): 0.05% to 0.2%, manganese (Mn): 10% to 30%, aluminum (Al): 0.5% to 3.0%, nickel (Ni): 0.001% to 10%, chromium (Cr): 0.001% to 10%, nitrogen (N): 0.001% to 0.05%, phosphorus (P): 0.020% or less, sulfur (S): 0.001% to 0.005%, and iron (Fe) as a residual component thereof, and inevitable impurities.
- The hot-dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement of claim 1, wherein the hot-dip galvanizing layer further includes an Fe-Al or Fe-Al-Zn alloy layer below the Fe-Zn alloy layer.
- The hot-dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement of claim 4, wherein the alloying suppression layer includes 0.6 wt% or less of aluminum (Al).
- The hot-dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement of claim 1, further comprising an Fe-Ni alloy layer disposed directly below a surface of the base steel sheet.
- The hot-dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement of claim 1, wherein the Fe-Ni alloy layer is provided by coating Ni having an adhesion amount of 300 mg/m2 to 1000 mg/m2.
- The hot-dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement of claim 1, wherein the Fe-Ni alloy layer has a thickness of 0.05 µm to 5 µm.
- The hot-dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement of claim 1, further comprising one or more selected from a group consisting of an Fe-X alloy layer, an Fe-Al-X alloy layer, an Fe-Al-Zn-X alloy layer, and an Fe-Zn-X alloy layer, disposed between the base steel sheet and the hot-dip galvanizing layer, where X is one of nickel (Ni) and chromium (Cr).
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
KR1020130163336A KR101568543B1 (en) | 2013-12-25 | 2013-12-25 | Galvanized steel sheet having excellent resistance to crack by liquid metal embrittlement |
PCT/KR2014/012824 WO2015099455A1 (en) | 2013-12-25 | 2014-12-24 | Molten zinc plated steel sheet with excellent crack resistance due to liquid metal bromide |
Publications (3)
Publication Number | Publication Date |
---|---|
EP3088557A1 true EP3088557A1 (en) | 2016-11-02 |
EP3088557A4 EP3088557A4 (en) | 2017-03-22 |
EP3088557B1 EP3088557B1 (en) | 2018-07-11 |
Family
ID=53479219
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP14875617.4A Active EP3088557B1 (en) | 2013-12-25 | 2014-12-24 | Hot dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement |
Country Status (6)
Country | Link |
---|---|
US (1) | US20160319415A1 (en) |
EP (1) | EP3088557B1 (en) |
JP (1) | JP6317453B2 (en) |
KR (1) | KR101568543B1 (en) |
CN (1) | CN105849304A (en) |
WO (1) | WO2015099455A1 (en) |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2018115948A1 (en) * | 2016-12-21 | 2018-06-28 | Arcelormittal | A method for the manufacture of a coated steel sheet |
WO2018115947A1 (en) * | 2016-12-21 | 2018-06-28 | Arcelormittal | A method for the manufacture of a coated steel sheet |
WO2018115946A1 (en) * | 2016-12-21 | 2018-06-28 | Arcelormittal | A method for the manufacture of a coated steel sheet |
WO2018203126A1 (en) * | 2017-05-05 | 2018-11-08 | Arcelormittal | A method for the manufacturing of liquid metal embrittlement resistant galvannealed steel sheet |
WO2019082037A1 (en) * | 2017-10-24 | 2019-05-02 | Arcelormittal | A method for the manufacture of a coated steel sheet, two spot welded metal sheets and use thereof |
WO2019082035A1 (en) * | 2017-10-24 | 2019-05-02 | Arcelormittal | A method for the manufacture of a coated steel sheet |
WO2019082036A1 (en) * | 2017-10-24 | 2019-05-02 | Arcelormittal | A method for the manufacture of a coated steel sheet |
US11566310B2 (en) | 2017-11-17 | 2023-01-31 | Arcelormittal | Method for the manufacturing of liquid metal embrittlement resistant zinc coated steel sheet |
US11578378B2 (en) | 2017-10-24 | 2023-02-14 | Arcelormittal | Method for the manufacture of a galvannealed steel sheet |
Families Citing this family (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN108842122B (en) * | 2018-08-06 | 2021-06-15 | 首钢集团有限公司 | Hot-dip plated steel sheet and method for producing same |
KR102200155B1 (en) * | 2019-12-06 | 2021-01-07 | 주식회사 포스코 | Method for manufacturing of welded structure, and welded structure manufactured by thereof |
MX2022009801A (en) | 2020-02-13 | 2022-09-12 | Jfe Steel Corp | High-strength steel sheet and method for producing same. |
WO2022107580A1 (en) * | 2020-11-17 | 2022-05-27 | 日本製鉄株式会社 | Plated steel sheet for spot welding use, joining member, automotive member, and method for manufacturing joining member |
US11441039B2 (en) * | 2020-12-18 | 2022-09-13 | GM Global Technology Operations LLC | High temperature coatings to mitigate weld cracking in resistance welding |
WO2023080076A1 (en) * | 2021-11-02 | 2023-05-11 | Jfeスチール株式会社 | Resistance spot welded member, and resistance spot welding method for same |
CN114369782B (en) * | 2021-12-10 | 2023-06-13 | 首钢集团有限公司 | Hot dip galvanized steel sheet without microcrack and preparation method thereof |
WO2023132244A1 (en) * | 2022-01-06 | 2023-07-13 | 日本製鉄株式会社 | Welded joint |
Family Cites Families (13)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US2631319A (en) * | 1947-12-09 | 1953-03-17 | Gotsfeld Morris | Bath brush having oppositely extending detachable handle |
JPH0559513A (en) * | 1991-09-02 | 1993-03-09 | Sumitomo Metal Ind Ltd | Production of plated steel sheet with powdering resistance |
JP2004124187A (en) * | 2002-10-03 | 2004-04-22 | Sumitomo Metal Ind Ltd | High-strength hot dip galvanized steel sheet having excellent adhesion property and weldability |
JP4329639B2 (en) | 2004-07-23 | 2009-09-09 | 住友金属工業株式会社 | Steel plate for heat treatment with excellent liquid metal brittleness resistance |
WO2006082104A1 (en) * | 2005-02-02 | 2006-08-10 | Corus Staal Bv | Austenitic steel having high strength and formability, method of producing said steel and use thereof |
KR20070018416A (en) | 2005-08-10 | 2007-02-14 | 현대자동차주식회사 | TWinning Induced Plasticity type ultra-high strength steel sheets and process of manufacturing the same |
EP2402472B2 (en) * | 2010-07-02 | 2017-11-15 | ThyssenKrupp Steel Europe AG | High-tensile, cold formable steel and flat steel product composed of such steel |
KR20120004248A (en) * | 2010-07-06 | 2012-01-12 | 주식회사 영우디에스피 | Aging apparatus for organic light emitting display panel |
KR20120041544A (en) * | 2010-10-21 | 2012-05-02 | 주식회사 포스코 | Galvanized steel sheet having excellent coatability, coating adhesion and spot weldability and method for manufacturing the same |
KR101242859B1 (en) * | 2010-11-05 | 2013-03-12 | 주식회사 포스코 | Galvanized steel sheet containing high manganese with excellent galvanizing properties and coating adhesion and method for manufacturing the same |
JP5817479B2 (en) * | 2011-03-10 | 2015-11-18 | Jfeスチール株式会社 | Manufacturing method of hot press member |
KR101359183B1 (en) * | 2011-06-28 | 2014-02-06 | 주식회사 포스코 | Plated steel sheet for hot press forming having good anti-lme property |
KR20130026133A (en) * | 2011-09-05 | 2013-03-13 | 주식회사 포스코 | Hot dip galvanized steel sheet containing high manganese content having coatability excellent coatability and surface appearance and method for manufacturing the same |
-
2013
- 2013-12-25 KR KR1020130163336A patent/KR101568543B1/en active IP Right Grant
-
2014
- 2014-12-24 WO PCT/KR2014/012824 patent/WO2015099455A1/en active Application Filing
- 2014-12-24 US US15/108,263 patent/US20160319415A1/en not_active Abandoned
- 2014-12-24 EP EP14875617.4A patent/EP3088557B1/en active Active
- 2014-12-24 JP JP2016543078A patent/JP6317453B2/en active Active
- 2014-12-24 CN CN201480071104.XA patent/CN105849304A/en active Pending
Cited By (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
RU2742644C1 (en) * | 2016-12-21 | 2021-02-09 | Арселормиттал | Method for producing coated sheet steel |
WO2018115947A1 (en) * | 2016-12-21 | 2018-06-28 | Arcelormittal | A method for the manufacture of a coated steel sheet |
WO2018115946A1 (en) * | 2016-12-21 | 2018-06-28 | Arcelormittal | A method for the manufacture of a coated steel sheet |
WO2018115948A1 (en) * | 2016-12-21 | 2018-06-28 | Arcelormittal | A method for the manufacture of a coated steel sheet |
RU2759389C2 (en) * | 2016-12-21 | 2021-11-12 | Арселормиттал | Method for manufacturing coated sheet steel |
WO2018203126A1 (en) * | 2017-05-05 | 2018-11-08 | Arcelormittal | A method for the manufacturing of liquid metal embrittlement resistant galvannealed steel sheet |
WO2018203097A1 (en) * | 2017-05-05 | 2018-11-08 | Arcelormittal | A method for the manufacturing of liquid metal embrittlement resistant galvannealed steel sheet |
US11654653B2 (en) | 2017-05-05 | 2023-05-23 | Arcelormittal | Method for the manufacturing of liquid metal embrittlement resistant galvannealed steel sheet |
WO2019082035A1 (en) * | 2017-10-24 | 2019-05-02 | Arcelormittal | A method for the manufacture of a coated steel sheet |
WO2019082036A1 (en) * | 2017-10-24 | 2019-05-02 | Arcelormittal | A method for the manufacture of a coated steel sheet |
WO2019082037A1 (en) * | 2017-10-24 | 2019-05-02 | Arcelormittal | A method for the manufacture of a coated steel sheet, two spot welded metal sheets and use thereof |
US11466354B2 (en) | 2017-10-24 | 2022-10-11 | Arcelormittal | Method for the manufacture of a coated steel sheet |
US11578378B2 (en) | 2017-10-24 | 2023-02-14 | Arcelormittal | Method for the manufacture of a galvannealed steel sheet |
US11680331B2 (en) | 2017-10-24 | 2023-06-20 | Arcelormittal | Method for the manufacture of a coated steel sheet |
US11566310B2 (en) | 2017-11-17 | 2023-01-31 | Arcelormittal | Method for the manufacturing of liquid metal embrittlement resistant zinc coated steel sheet |
Also Published As
Publication number | Publication date |
---|---|
JP6317453B2 (en) | 2018-04-25 |
US20160319415A1 (en) | 2016-11-03 |
WO2015099455A8 (en) | 2015-08-20 |
KR101568543B1 (en) | 2015-11-11 |
WO2015099455A1 (en) | 2015-07-02 |
KR20150075291A (en) | 2015-07-03 |
EP3088557A4 (en) | 2017-03-22 |
EP3088557B1 (en) | 2018-07-11 |
CN105849304A (en) | 2016-08-10 |
JP2017510702A (en) | 2017-04-13 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP3088557B1 (en) | Hot dip galvanized steel sheet having excellent resistance to cracking due to liquid metal embrittlement | |
US10253386B2 (en) | Steel sheet for hot press-forming, method for manufacturing the same, and method for producing hot press-formed parts using the same | |
EP3719156B1 (en) | High-strength galvanized steel sheet and method for manufacturing same | |
EP2794950B1 (en) | Hot-dip galvanized steel sheet having excellent adhesiveness at ultra-low temperatures and method of manufacturing the same | |
EP2684985A1 (en) | Steel sheet for hot pressing, and process for producing hot-pressed member utilizing same | |
EP2728032A2 (en) | Plated steel sheet having plated layer with excellent stability for hot press molding | |
CN104870679B (en) | High manganese hot-dip galvanizing sheet steel and its manufacture method | |
KR101692129B1 (en) | Method for manufacturing high strength galvanized steel sheet and high strength galvanized steel sheet | |
KR101657866B1 (en) | High strength galvanized steel sheet and method for manufacturing the same | |
EP3382049B1 (en) | Method for manufacturing cold-rolled steel sheet for high-strength hot-dip galvanized steel sheet, method for manufacturing high-strength hot-dip galvanized steel sheet | |
WO2014136412A1 (en) | High-strength steel sheet, method for manufacturing same, high-strength molten-zinc-plated steel sheet, and method for manufacturing same | |
KR102065287B1 (en) | Austenitic hot-dip aluminum coated steel sheet with excellent plating property and weldability, and a manufacturing method thereof | |
EP3034646A1 (en) | Production method for high-strength hot-dip galvanized steel sheets and production method for high-strength alloyed hot-dip galvanized steel sheets | |
EP3900866A1 (en) | Spot welding member | |
KR101528010B1 (en) | High manganese hot dip galvanized steel sheet with superior weldability and method for manufacturing the same | |
US11408047B2 (en) | Alloyed hot-dip galvanized steel sheet and alloyed hot-dip galvanized steel sheet production method | |
JPWO2019097729A1 (en) | Al-plated welded pipe for quenching, Al-plated hollow member and method for producing the same | |
JP4940813B2 (en) | Method for producing hot-dip galvanized steel sheet having a value of TS × El of 21000 MPa ·% or more | |
KR101630960B1 (en) | Galvanized steel having good spot weldabity and workability, and method for manufacturing the same | |
EP4215294A1 (en) | Hot-pressed member, steel sheet for hot-pressing, and methods for producing same | |
KR101736640B1 (en) | Hot dip zinc alloy coated steel sheet having excellent coatability and spot weldability and method for manufacturing same | |
JP4975406B2 (en) | High-strength galvannealed steel sheet and method for producing the same | |
CN110088349B (en) | High manganese hot-dip aluminum-plated steel sheet having excellent sacrificial corrosion protection and plating properties, and method for producing same | |
KR20120041619A (en) | Galvanizing steel sheet having good galvanizabilty and adhesion and method for manufacturing the same | |
KR101978014B1 (en) | High-strength steel sheet, high-strength hot-dip zinc-coated steel sheet, and methods for producing said steel sheets |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
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 |
|
17P | Request for examination filed |
Effective date: 20160622 |
|
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: 20170222 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C22C 38/28 20060101ALI20170216BHEP Ipc: C22C 38/06 20060101ALI20170216BHEP Ipc: C22C 38/04 20060101ALI20170216BHEP Ipc: C22C 38/58 20060101ALI20170216BHEP Ipc: C23C 2/06 20060101AFI20170216BHEP Ipc: C23C 2/02 20060101ALI20170216BHEP Ipc: C22C 38/00 20060101ALI20170216BHEP Ipc: C23C 2/40 20060101ALI20170216BHEP Ipc: C22C 18/00 20060101ALI20170216BHEP Ipc: C23C 28/00 20060101ALI20170216BHEP Ipc: C22C 38/08 20060101ALI20170216BHEP Ipc: C22C 38/02 20060101ALI20170216BHEP Ipc: C22C 38/50 20060101ALI20170216BHEP |
|
DAX | Request for extension of the european patent (deleted) | ||
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
INTG | Intention to grant announced |
Effective date: 20180131 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
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: 1016959 Country of ref document: AT Kind code of ref document: T Effective date: 20180715 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602014028514 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: MP Effective date: 20180711 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 1016959 Country of ref document: AT Kind code of ref document: T Effective date: 20180711 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20180711 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20180711 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: 20180711 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: 20180711 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: 20180711 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: 20181111 Ref country code: NO 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: 20181011 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: 20181011 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: 20181012 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: 20180711 Ref country code: SE 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: 20180711 |
|
REG | Reference to a national code |
Ref country code: SK Ref legal event code: T3 Ref document number: E 28834 Country of ref document: SK |
|
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: 20180711 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: 20180711 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: 20180711 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602014028514 Country of ref document: DE |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20180711 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: 20180711 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: 20180711 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: 20180711 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: 20180711 |
|
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 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20180711 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: 20180711 |
|
26N | No opposition filed |
Effective date: 20190412 |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: PL |
|
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: 20181224 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: 20180711 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: 20180711 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: MM4A |
|
REG | Reference to a national code |
Ref country code: BE Ref legal event code: MM Effective date: 20181231 |
|
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: 20181224 |
|
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: 20181231 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20181231 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20181231 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MT Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20181224 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: TR 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: 20180711 |
|
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: 20180711 |
|
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: 20141224 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: 20180711 Ref country code: MK Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20180711 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R081 Ref document number: 602014028514 Country of ref document: DE Owner name: POSCO CO., LTD, POHANG-SI, KR Free format text: FORMER OWNER: POSCO, POHANG-SI, GYEONGSANGBUK-DO, KR Ref country code: DE Ref legal event code: R081 Ref document number: 602014028514 Country of ref document: DE Owner name: POSCO CO., LTD, POHANG- SI, KR Free format text: FORMER OWNER: POSCO, POHANG-SI, GYEONGSANGBUK-DO, KR Ref country code: DE Ref legal event code: R081 Ref document number: 602014028514 Country of ref document: DE Owner name: POSCO HOLDINGS INC., KR Free format text: FORMER OWNER: POSCO, POHANG-SI, GYEONGSANGBUK-DO, KR |
|
REG | Reference to a national code |
Ref country code: SK Ref legal event code: TC4A Ref document number: E 28834 Country of ref document: SK Owner name: POSCO HOLDINGS INC., SEOUL, KR Effective date: 20221013 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: 732E Free format text: REGISTERED BETWEEN 20221027 AND 20221102 |
|
REG | Reference to a national code |
Ref country code: SK Ref legal event code: PC4A Ref document number: E 28834 Country of ref document: SK Owner name: POSCO CO., LTD, GYEONGSANGBUK-DO, KR Free format text: FORMER OWNER: POSCO HOLDINGS INC., SEOUL, KR Effective date: 20221124 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R081 Ref document number: 602014028514 Country of ref document: DE Owner name: POSCO CO., LTD, POHANG-SI, KR Free format text: FORMER OWNER: POSCO HOLDINGS INC., SEOUL, KR Ref country code: DE Ref legal event code: R081 Ref document number: 602014028514 Country of ref document: DE Owner name: POSCO CO., LTD, POHANG- SI, KR Free format text: FORMER OWNER: POSCO HOLDINGS INC., SEOUL, KR |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20230105 Year of fee payment: 9 Ref country code: DE Payment date: 20230105 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SK Payment date: 20231227 Year of fee payment: 10 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20231226 Year of fee payment: 10 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20240105 Year of fee payment: 10 Ref country code: GB Payment date: 20240105 Year of fee payment: 10 |