EP4114994B1 - Hochfestes kaltgewalztes und verzinktes stahlblech und verfahren zu seiner herstellung - Google Patents
Hochfestes kaltgewalztes und verzinktes stahlblech und verfahren zu seiner herstellung Download PDFInfo
- Publication number
- EP4114994B1 EP4114994B1 EP21703775.3A EP21703775A EP4114994B1 EP 4114994 B1 EP4114994 B1 EP 4114994B1 EP 21703775 A EP21703775 A EP 21703775A EP 4114994 B1 EP4114994 B1 EP 4114994B1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel sheet
- temperature
- comprised
- cold rolled
- galvannealed
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
- 229910000831 Steel Inorganic materials 0.000 title claims description 86
- 239000010959 steel Substances 0.000 title claims description 86
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 229910000859 α-Fe Inorganic materials 0.000 claims description 22
- 229910001563 bainite Inorganic materials 0.000 claims description 19
- 229910000734 martensite Inorganic materials 0.000 claims description 19
- 229910001566 austenite Inorganic materials 0.000 claims description 17
- 238000002791 soaking Methods 0.000 claims description 17
- 238000000137 annealing Methods 0.000 claims description 14
- 238000000034 method Methods 0.000 claims description 11
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 10
- 238000001816 cooling Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 10
- 239000010960 cold rolled steel Substances 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 8
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 7
- 238000000576 coating method Methods 0.000 claims description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims description 7
- 239000010703 silicon Substances 0.000 claims description 7
- 239000011248 coating agent Substances 0.000 claims description 6
- 239000011701 zinc Substances 0.000 claims description 6
- 229910052796 boron Inorganic materials 0.000 claims description 5
- 229910052804 chromium Inorganic materials 0.000 claims description 5
- 238000005097 cold rolling Methods 0.000 claims description 5
- 229910052742 iron Inorganic materials 0.000 claims description 5
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 4
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 238000005098 hot rolling Methods 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 3
- 238000003723 Smelting Methods 0.000 claims description 2
- 238000007598 dipping method Methods 0.000 claims description 2
- 238000010438 heat treatment Methods 0.000 claims description 2
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- 229910052757 nitrogen Inorganic materials 0.000 claims description 2
- 229910052698 phosphorus Inorganic materials 0.000 claims description 2
- 238000005096 rolling process Methods 0.000 claims description 2
- 229910052717 sulfur Inorganic materials 0.000 claims description 2
- 229910052719 titanium Inorganic materials 0.000 claims description 2
- 238000005554 pickling Methods 0.000 claims 2
- 238000003303 reheating Methods 0.000 claims 2
- 238000005266 casting Methods 0.000 claims 1
- 239000000126 substance Substances 0.000 claims 1
- 238000005244 galvannealing Methods 0.000 description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 6
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 6
- 229910052799 carbon Inorganic materials 0.000 description 6
- 238000003618 dip coating Methods 0.000 description 6
- 239000011733 molybdenum Substances 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- 239000011651 chromium Substances 0.000 description 5
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- 239000004411 aluminium Substances 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 239000011572 manganese Substances 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 230000000717 retained effect Effects 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 238000010191 image analysis Methods 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910001335 Galvanized steel Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 239000012141 concentrate Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000007571 dilatometry Methods 0.000 description 1
- 239000008397 galvanized steel Substances 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- KFZAUHNPPZCSCR-UHFFFAOYSA-N iron zinc Chemical compound [Fe].[Zn] KFZAUHNPPZCSCR-UHFFFAOYSA-N 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 238000005088 metallography Methods 0.000 description 1
- 239000010955 niobium Substances 0.000 description 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- LIVNPJMFVYWSIS-UHFFFAOYSA-N silicon monoxide Chemical group [Si-]#[O+] LIVNPJMFVYWSIS-UHFFFAOYSA-N 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- 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
- 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
- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
- C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
- C23G1/08—Iron or steel
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to a high strength cold rolled and galvannealed steel sheet and to a method to obtain such steel sheet.
- These steels are usually coated with a metallic coating improving properties such corrosion resistance.
- the metallic coatings can be deposited by hot-dip galvanizing after the annealing of the steel sheets. To obtain an improved spot weldability, the hot dip coating can be followed by an alloying treatment to obtain a galvannealed steel sheet, so that the iron of the steel sheet diffuses towards the zinc coating in order to obtain a zinc-iron alloy on the steel sheet.
- the publication WO2019188190 relates to a high strength galvanized or galvannealed steel sheet, having a tensile strength higher than 1470MPa.
- the carbon content of the steel sheet is comprised between 0.200%wt and 0.280%wt, which may reduce the weldability of the steel sheet.
- the formation of ferrite and bainite, whose total amount of the sum of the two with pearlite is less than 2%, is avoided to ensure good level of tensile strength.
- the soaking step after cold rolling has to be performed at a temperature above Ac3.
- the publication WO2016199922 relates to a high strength galvannealed steel sheet with a tensile strength higher than 1470MPa.
- the high amount of carbon between 0.25% and 0.70% allow to obtain this high level of tensile strength. But the weldability of the steel sheet may be reduced.
- the steel sheet After the alloying step, the steel sheet must be cooled in a controlled manner, in order to obtain at the end of the cooling, more than 10% of retained austenite.
- the galvannealed steel sheet is subjected to a step of tempering to obtain tempered martensite, to promote bainite transformation and to cause carbon to concentrate into retained austenite, in order to obtain the desired final microstructure : between 10% and 60% of retained austenite, less than 5% of high temperature tempered martensite, less than 5% of low temperature tempered martensite, less than 10% of fresh martensite, less than 15% of ferrite, less than 10% of pearlite, the balance being bainite.
- US 2016/319385 A1 discloses a high-strength galvanized steel sheet excellent in terms of spot weldability, anti-crash property, and bending formability which can preferably be used as an automotive steel sheet.
- the purpose of the invention therefore is to solve the above-mentioned problem and to provide a galvannealed steel sheet having a tensile strength above or equal to1450MPa and easily processable on conventional process route.
- the yield strength YS is above or equal to 1050MPa.
- the object of the present invention is achieved by providing a steel sheet according to claim 1.
- the steel sheet can also comprise characteristics of anyone of claims 2 to 5.
- Another object is achieved by providing the method according to claim 6.
- the method can also comprise characteristics of anyone of claims 7 to 8.
- Ac3 designates the temperature above which microstructure is fully austenitic
- Ac1 designates the temperature above which austenite begins to form.
- composition of the steel according to the invention will now be described, the content being expressed in weight percent.
- the carbon content is comprised from 0.15% to 0.25% to ensure a satisfactory strength. If the carbon content is too high, the weldability of the steel sheet is insufficient. A carbon content level below 0.15% does not make it possible to achieve a sufficient tensile strength.
- the manganese content is comprised from 2.4% to 3.5% to ensure satisfactory strength and to limit bainitic transformation. Above 3.5% of addition, the risk of central segregation increases to the detriment of the ductility. An amount of at least 2.4% of manganese is mandatory in order to provide the strength and hardenability of the steel sheet as well as to stabilize austenite. Preferably, the manganese content is comprised from 2.5% to 3.2%.
- the silicon content is comprised from 0.30% to 0.90%.
- Silicon is an element participating in the hardening in solid solution. A silicon addition of at least 0.30% makes it possible to obtain sufficient hardening of the ferrite and bainite. Above 0.90%, silicon oxides form at the surface, which impairs the coatability of the steel. Moreover, silicon can impair the weldability.
- the silicon content is comprised from 0.30% to 0.70%. In an other preferred embodiment, the silicon content is comprised from 0.30% to 0.50%.
- the chromium content is comprised from 0.30% to 0.70%.
- Chromium is an element participating in the hardening in solid solution.
- a chromium content level below 0.30% does not make it possible to achieve a sufficient tensile strength.
- the chromium content has to be below or equal to 0.70% to obtain a satisfactory elongation at break and limit costs.
- the molybdenum content is comprised between 0.05% and 0.35%.
- a molybdenum addition of at least 0.05% improves the hardenability of the steel and limits bainitic transformation before and during the hot dip coating. Above 0.35%, the addition of molybdenum is costly and ineffective in view of the properties which are required.
- the molybdenum content is comprised between 0.05% and 0.20%.
- the aluminium content is comprised between 0.001% and 0.09% as it is a very effective element for deoxidizing the steel in the liquid phase during elaboration.
- the aluminium content is lower than 0.09% to avoid oxidation problems and ferrite formation during cooling after intercritical soaking.
- the aluminium amount is between 0.001% and 0.06%.
- Titanium is added in an amount between 0.01% and 0.06% to provide precipitation strengthening and to protect boron against the formation of BN.
- the boron content is comprised between 0.0010% and 0.0040%.
- molybdenum boron improves the hardenability of the steel.
- the boron content is lower than 0.0040% to avoid a risk of breaking the slab during continuous casting.
- Niobium is added between 0.01% and 0.05% to refine the austenite grains during hot-rolling and to provide precipitation strengthening.
- the remainder of the composition of the steel is iron and impurities resulting from the smelting.
- P, S and N at least are considered as residual elements which are unavoidable impurities.
- Their content is less than 0.010 % for S, less than 0.020 % for P and less than 0.008 % for N.
- the cold rolled steel sheet is heated to a soaking temperature T soak and maintained at said temperature for a holding time t soak , both chosen in order to obtain, at the end of this intercritical soaking, a steel sheet with a microstructure consisting of between 85% and 95% of austenite and between 5% and 15% of ferrite.
- a part of austenite is transformed in bainite after the cooling after the intercritical soaking, during the hot dip coating.
- the cold rolled and galvannealed steel sheet has a final microstructure consisting of, in surface fraction, between 80% and 90% of martensite, the balance being ferrite and bainite.
- This martensite comprises auto tempered martensite and fresh martensite.
- the sum of ferrite and bainite is between 10% and 20% in order to ensure that the galvannealing step is successful.
- the ferrite is above or equal to 5%. In an other preferred embodiment of the invention, the bainite is above or equal to 5%.
- the cold rolled and galvannealed steel sheet according to the invention has a tensile strength TS above or equal to 1450 MPa.
- the yield strength YS is above or equal to 1050 MPa.
- TS and YS are measured according to ISO standard ISO 6892-1.
- the steel sheet according to the invention can be produced by any appropriate manufacturing method and the man skilled in the art can define one. It is however preferred to use the method according to the invention comprising the following steps: A semi-product able to be further hot-rolled, is provided with the steel composition described above. The semi product is heated to a temperature comprised from 1150°C to 1300°C, so to make it possible to ease hot rolling, with a final hot rolling temperature FRT comprises from 850°C to 950°C.
- the hot-rolled steel is then cooled and coiled at a temperature Tcoil comprised from 250°C to 650°C.
- the sheet After the coiling, the sheet is pickled to remove oxidation.
- the steel sheet is annealed to an annealing temperature T A comprised from 500°C and 650°C and maintaining at said temperature T A for a holding time t A in order to improve the cold-rollability.
- the sheet After the annealing, the sheet can be pickled to remove oxidation.
- the steel sheet is then cold rolled with a reduction rate between 20% and 80%, to obtain a cold rolled steel sheet, having a thickness that can be, for example, between 0.7 mm and 3 mm, or even better in the range of 0.8 mm to 2 mm.
- the cold-rolling reduction ratio is comprised between 20% and 80%. Below 20%, the recrystallization during subsequent heat-treatment is not favored, which may impair the ductility of the cold-rolled and galvannealed steel sheet. Above 80%, the force required to deform during cold-rolling would be too high.
- the cold rolled steel sheet is then reheated to a soaking temperature T soak comprised from Ac1 and Ac3 and maintained at said temperature T soak for a holding time t soak comprised from 30s and 200s so to obtain, at the end of this intercritical soaking, a microstructure comprising between 85% and 95% of austenite and between 5% and 15% of ferrite.
- the cold rolled steel sheet is then cooled to a temperature comprised from 440°C to 480°C in order for the sheet to reach a temperature close to the coating bath, before to be coated by continuous dipping in a zinc bath at a temperature T Zn comprised from 450° C to 480° C.
- the hot dip coated steel sheet is then reheated to a galvannealed temperature T GA comprised from 510°C to 550°C, and maintained at said temperature T GA for a holding time t GA comprised from 10s to 30s.
- the steel sheet is then cooled to room temperature to obtain a cold rolled and galvannealed steel sheet.
- the annealing step of the hot rolled steel sheet is performed by batch in an inert atmosphere, at a heat-treating temperature T A comprised from 500°C to 650°C and maintaining at said T A temperature for a holding time t A comprised from 1800s to 36000s.
- the annealing step of the hot rolled steel sheet is performed by continuous annealing, at a heat-treating temperature T A comprised from 550°C to 650°C. and maintaining at said T A temperature for a holding time t A comprised from 30s to 100s.
- the cold rolled steel sheets are reheated to a soaking temperature T soak and maintained at said temperature during t soak , and coated by hot dip coating in a zinc bath at temperature T Zn of 460°C, followed by galvannealing, with a galvannealed temperature T GA comprised from 510°C to 550°C and maintained at said temperature during t GA of 20s.
- the steel sheets are quenched after the soaking to transform 100% of austenite in martensite, austenite being instable at room temperature. Martensite amount thus corresponds to the austenite amount at the end of the soaking. Martensite and ferrite amounts are then quantified through image analysis.
- the surface fractions are determined through the following method: a specimen is cut from the cold-rolled and galvannealed steel sheet, polished and etched with a reagent (Nital), to reveal the microstructure.
- the determination of the surface fraction of each constituent are performed with image analysis through optical microscope: Martensite has a darker contrast than ferrite and bainite. Bainite is quantified by measuring the difference of martensite fractions of the sample quenched after soaking and of the sample cooled after galvannealing.
- the bainite is identified thanks to the carbides inside this bainite.
- Table 5 Properties of the cold rolled and galvannealed steel sheets Trials TS (MPa) YS (MPa) Success of GA 1 1522 1095 Yes 2 1634 1055 Yes 3 1519 1163 No 4 1611 1096 No 5 1363 954 Yes Underline values: Insufficient TS or YS, or fail of the galvannealing step.
- the success of the galvannealing step is checked by measuring the amount of iron in the coating.
- the steel is galvannealed if the iron content in the coating is between 7% and 12%.
- the examples show that the steel sheet according to the invention, namely examples 1 and 2 are the only one to show all the targeted mechanical properties with success of the galvannealing, thanks to their specific composition and microstructures.
- the mechanical properties are ensured thanks to the martensite between 80% and 90%.
- the galvannealing step is ensured thanks to the presence of ferrite and bainite in a total comprised between 10% and 20%.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Metallurgy (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Coating With Molten Metal (AREA)
Claims (7)
- Kaltgewalztes und galvannealtes Stahlblech, das eine chemische Zusammensetzung aufweist, umfassend in Gewichtsprozent:C: 0,15 - 0,25 %Mn: 2,4 - 3,5 %Si: 0,30 - 0,90 %Cr: 0,30 - 0,70 %Mo: 0,05 - 0,35 %AI: 0,001 - 0,09 %Ti: 0,01 - 0,06 %B: 0,0010 - 0,0040 %Nb 0,01-0,05 %P ≤ 0,020 %S ≤ 0,010 %N ≤ 0,008 %wobei der Rest der Zusammensetzung aus Eisen und unvermeidlichen Verunreinigungen aus der Verhüttung besteht, das Stahlblech eine Mikrostruktur aufweist, das in Oberflächenfraktion aus Folgendem besteht:- von 80 % bis 90 % Martensit,- der Rest ist Ferrit und Bainit.
- Kaltgewalztes und galvannealtes Stahlblech nach Anspruch 1, wobei der Ferritgehalt über oder gleich 5 % ist.
- Kaltgewalztes und galvannealtes Stahlblech nach Anspruch 1, wobei der Bainitgehalt über oder gleich 5 % ist.
- Kaltgewalztes und galvannealtes Stahlblech nach einem der Ansprüche 1 bis 3, wobei der Silikongehalt zwischen 0,30 % und 0,70 % liegt.
- Verfahren zum Herstellen eines kaltgewalzten und galvannealten Stahlblechs, umfassend die folgenden aufeinanderfolgenden Schritte:- Gießen eines Stahls, um ein Halbzeug zu erhalten, wobei das Halbzeug eine Zusammensetzung gemäß Anspruch 1 aufweist,- Wiedererhitzen der Bramme auf eine Temperatur Treheat von 1150 °C bis 1300 °C,- Warmwalzen der wiedererhitzten Bramme mit einer abschließenden Walztemperatur, die zwischen 850 °C und 950 °C liegt, um ein warmgewalztes Stahlblech zu erhalten, dann- Abkühlen des Stahlblechs auf eine Wickeltemperatur Tcoil von 250 °C bis 650 °C, dann- Wickeln des Stahlblechs bei der Temperatur Tcoil, um ein gewickeltes Stahlblech zu erhalten, dann- Beizen des Stahlblechs,- Glühen des Stahlblechs auf eine Glühtemperatur TA von 500 °C bis 650 °C und Halten des Stahlblechs bei der Temperatur TA für eine Haltezeit tA,- optionales Beizen des Stahlblechs,- Kaltwalzen des warmgewalzten Stahlblechs mit einem Reduktionsgrad zwischen 20 % und 80 %, um ein kaltgewalztes Stahlblech zu erhalten,- Erhitzen des kaltgewalzten Stahlblechs auf eine Tränktemperatur Tsoak , die zwischen Ac1 und Ac3 liegt, und Halten des Stahlblechs bei der Temperatur Tsoak während einer Haltezeit tsoak , die zwischen 30 s und 200 s liegt, um zwischen 85 % und 95 % Austenit und zwischen 5 % und 15 % Ferrit zu erhalten,- Abkühlen des Stahlblechs auf eine Temperatur zwischen 440 °C und 480 °C,- Beschichten des Stahlblechs durch kontinuierliches Eintauchen in ein Zinkbad bei einer Temperatur TZn von 450 °C bis 480 °C,- Wiedererwärmen des Stahlblechs auf eine Galvannealungsttemperatur TGA von 510 °C bis 550 °C und Halten des Stahlblechs bei der Temperatur TGA für eine Haltezeit tGA von 10 s bis 30 s.- Abkühlen des wiedererhitzten Stahlblechs auf Raumtemperatur, um ein kaltgewalztes und galvannealtes Stahlblech zu erhalten.
- Verfahren zum Herstellen eines kaltgewalzten und galvannealten Stahlblechs nach Anspruch 5,wobei das Glühen des warmgewalztenStahlblechs chargenweise in einer inerten Atmosphäre bei einer Wärmebehandlungstemperatur TA von 500 °C bis 650 °C ausgeführt wird, wobei die Dauer tA bei der Glühtemperatur zwischen 1800 s und 36000 s liegt.
- Verfahren zum Herstellen eines kaltgewalzten und galvannealten Stahlblechs nach Anspruch 5, wobei das Glühen des warmgewalzten Stahlblechs durch kontinuierliches Glühen bei einer Wärmebehandlungstemperatur TA von 550 °C bis 650 °C erfolgt, wobei die Dauer tA bei der Glühtemperatur zwischen 30s und 100 s liegt.
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/IB2020/051750 WO2021176249A1 (en) | 2020-03-02 | 2020-03-02 | High strength cold rolled and galvannealed steel sheet and manufacturing process thereof |
PCT/IB2021/050994 WO2021176285A1 (en) | 2020-03-02 | 2021-02-08 | High strength cold rolled and galvannealed steel sheet and manufacturing process thereof |
Publications (2)
Publication Number | Publication Date |
---|---|
EP4114994A1 EP4114994A1 (de) | 2023-01-11 |
EP4114994B1 true EP4114994B1 (de) | 2024-03-27 |
Family
ID=69770986
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP21703775.3A Active EP4114994B1 (de) | 2020-03-02 | 2021-02-08 | Hochfestes kaltgewalztes und verzinktes stahlblech und verfahren zu seiner herstellung |
Country Status (13)
Country | Link |
---|---|
US (1) | US20230141248A1 (de) |
EP (1) | EP4114994B1 (de) |
JP (1) | JP7488351B2 (de) |
KR (1) | KR20220128659A (de) |
CN (1) | CN115066507B (de) |
BR (1) | BR112022014638A2 (de) |
CA (1) | CA3167692A1 (de) |
FI (1) | FI4114994T3 (de) |
MA (1) | MA58835B1 (de) |
MX (1) | MX2022010798A (de) |
PL (1) | PL4114994T3 (de) |
WO (2) | WO2021176249A1 (de) |
ZA (1) | ZA202207671B (de) |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CA3236022A1 (en) * | 2021-10-29 | 2023-05-04 | Arcelormittal | Cold rolled and heat treated steel sheet and a method of manufacturing thereof |
CN117004878A (zh) * | 2022-04-29 | 2023-11-07 | 宝山钢铁股份有限公司 | 一种抗拉强度在1450MPa以上的超高强度冷轧钢带及其制造方法 |
Family Cites Families (18)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR101660144B1 (ko) | 2012-01-13 | 2016-09-26 | 신닛테츠스미킨 카부시키카이샤 | 핫 스탬프 성형체 및 그 제조 방법 |
MX2016007954A (es) * | 2013-12-18 | 2016-09-09 | Jfe Steel Corp | Lamina de acero galvanizada de alta resistencia y metodo para la fabricacion de la misma. |
JP5862651B2 (ja) * | 2013-12-18 | 2016-02-16 | Jfeスチール株式会社 | 耐衝撃性および曲げ加工性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法 |
JP6234845B2 (ja) | 2014-03-06 | 2017-11-22 | 株式会社神戸製鋼所 | 焼付け硬化性と曲げ性に優れた高強度合金化溶融亜鉛めっき鋼板 |
MX2016016129A (es) * | 2014-06-06 | 2017-03-28 | Arcelormittal | Hoja de acero galvanizada multifasica de alta resistencia, metodo de produccion y uso. |
WO2016001704A1 (en) * | 2014-07-03 | 2016-01-07 | Arcelormittal | Method for manufacturing a high strength steel sheet and sheet obtained |
KR101913530B1 (ko) | 2014-12-22 | 2018-10-30 | 제이에프이 스틸 가부시키가이샤 | 고강도 용융 아연 도금 강판 및 그 제조 방법 |
JP6093411B2 (ja) * | 2015-01-09 | 2017-03-08 | 株式会社神戸製鋼所 | めっき性、加工性、および耐遅れ破壊特性に優れた高強度めっき鋼板、並びにその製造方法 |
WO2016177420A1 (de) * | 2015-05-06 | 2016-11-10 | Thyssenkrupp Steel Europe Ag | Stahlflachprodukt und verfahren zu seiner herstellung |
BR112017025389A2 (pt) | 2015-06-11 | 2018-08-07 | Nippon Steel & Sumitomo Metal Corporation | chapa de aço galvanizada e método para fabricar a mesma |
WO2017109541A1 (en) * | 2015-12-21 | 2017-06-29 | Arcelormittal | Method for producing a high strength coated steel sheet having improved ductility and formability, and obtained coated steel sheet |
WO2017125773A1 (en) * | 2016-01-18 | 2017-07-27 | Arcelormittal | High strength steel sheet having excellent formability and a method of manufacturing the same |
JP6852736B2 (ja) | 2016-07-15 | 2021-03-31 | 日本製鉄株式会社 | 溶融亜鉛めっき冷延鋼板 |
WO2018115935A1 (en) * | 2016-12-21 | 2018-06-28 | Arcelormittal | Tempered and coated steel sheet having excellent formability and a method of manufacturing the same |
US11427880B2 (en) | 2017-11-29 | 2022-08-30 | Jfe Steel Corporation | High-strength galvanized steel sheet and method for manufacturing same |
US11319622B2 (en) | 2018-03-26 | 2022-05-03 | Kobe Steel, Ltd. | High-strength steel sheet and high-strength galvanized steel sheet |
MX2020011439A (es) | 2018-05-01 | 2020-12-07 | Nippon Steel Corp | Lamina de acero enchapada con zinc y metodo de fabricacion de la misma. |
CN110643800A (zh) * | 2019-10-22 | 2020-01-03 | 马鞍山钢铁股份有限公司 | 一种1200MPa级热轧高强双相钢板及其制造方法 |
-
2020
- 2020-03-02 WO PCT/IB2020/051750 patent/WO2021176249A1/en active Application Filing
-
2021
- 2021-02-08 MX MX2022010798A patent/MX2022010798A/es unknown
- 2021-02-08 MA MA58835A patent/MA58835B1/fr unknown
- 2021-02-08 JP JP2022552553A patent/JP7488351B2/ja active Active
- 2021-02-08 CA CA3167692A patent/CA3167692A1/en active Pending
- 2021-02-08 WO PCT/IB2021/050994 patent/WO2021176285A1/en active Application Filing
- 2021-02-08 KR KR1020227028588A patent/KR20220128659A/ko not_active Application Discontinuation
- 2021-02-08 PL PL21703775.3T patent/PL4114994T3/pl unknown
- 2021-02-08 CN CN202180013081.7A patent/CN115066507B/zh active Active
- 2021-02-08 FI FIEP21703775.3T patent/FI4114994T3/fi active
- 2021-02-08 EP EP21703775.3A patent/EP4114994B1/de active Active
- 2021-02-08 BR BR112022014638A patent/BR112022014638A2/pt unknown
- 2021-02-08 US US17/907,836 patent/US20230141248A1/en active Pending
-
2022
- 2022-07-11 ZA ZA2022/07671A patent/ZA202207671B/en unknown
Also Published As
Publication number | Publication date |
---|---|
ZA202207671B (en) | 2023-04-26 |
WO2021176249A1 (en) | 2021-09-10 |
KR20220128659A (ko) | 2022-09-21 |
MX2022010798A (es) | 2022-09-27 |
WO2021176285A1 (en) | 2021-09-10 |
JP7488351B2 (ja) | 2024-05-21 |
CN115066507B (zh) | 2023-12-22 |
JP2023508240A (ja) | 2023-03-01 |
US20230141248A1 (en) | 2023-05-11 |
BR112022014638A2 (pt) | 2022-09-13 |
MA58835B1 (fr) | 2024-05-31 |
FI4114994T3 (fi) | 2024-04-26 |
PL4114994T3 (pl) | 2024-06-24 |
EP4114994A1 (de) | 2023-01-11 |
CA3167692A1 (en) | 2021-09-10 |
CN115066507A (zh) | 2022-09-16 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP3653738B1 (de) | Verfahren zur herstellung eines hochfesten beschichteten stahlblechs mit verbesserter duktilität und umformbarkeit sowie erhaltenes beschichtetes stahlblech | |
EP3152336B1 (de) | Kalt gewalztes und feuerbeschichtetes stahlblech und dessen herstellungsverfahren und verwendung | |
EP3899067B1 (de) | Kaltgewalztes und wärmebehandeltes stahlblech und verfahren zur herstellung davon | |
US10640855B2 (en) | High-strength air-hardening multiphase steel having excellent processing properties, and method for manufacturing a strip of said steel | |
US10626478B2 (en) | Ultra high-strength air-hardening multiphase steel having excellent processing properties, and method for manufacturing a strip of said steel | |
EP2444510A1 (de) | Hochfestes, feuerverzinktes stahlblech mit hervorragenden verarbeitungs- und materialermüdungseigenschaften und herstellungsverfahren dafür | |
US20180044759A1 (en) | High-strength air-hardening multi-phase steel comprising outstanding processing properties and method for the production of a steel strip from said steel | |
US20210147953A1 (en) | Method for producing a high-strength steel strip with improved properties for further processing, and a steel strip of this type | |
US10570476B2 (en) | High-strength steel sheet and production method therefor | |
RU2742998C1 (ru) | Сверхпрочная многофазная сталь и способ изготовления стальной полосы из этой многофазной стали | |
KR20190076258A (ko) | 충돌특성 및 성형성이 고강도 강판 및 이의 제조방법 | |
CN111684084A (zh) | 高强度热轧或冷轧并退火的钢及其生产方法 | |
EP4114994B1 (de) | Hochfestes kaltgewalztes und verzinktes stahlblech und verfahren zu seiner herstellung | |
US20220106662A1 (en) | High-strength hot-dip galvanized steel sheet and manufacturing method therefor | |
EP4234750A1 (de) | Ultrahochfestes stahlblech mit hervorragender duktilität und verfahren zur herstellung davon | |
KR101406444B1 (ko) | 연신율 및 굽힘가공성이 우수한 초고강도 냉연강판 및 이의 제조방법 | |
CN110073023B (zh) | 弯曲性和延伸凸缘性优异的高张力钢及其制造方法 | |
CN116601321A (zh) | 经涂覆的钢板和高强度压制硬化钢部件及其制造方法 | |
KR20140086273A (ko) | 가공성 및 도금밀착성이 우수한 고강도 합금화 용융 아연도금강판 및 그 제조방법 | |
KR101452052B1 (ko) | 도금밀착성이 우수한 고강도 합금화 용융아연도금강판 및 그 제조방법 | |
JP2003193189A (ja) | 深絞り性に優れた複合組織型高張力溶融亜鉛めっき鋼板およびその製造方法 | |
JP2022535255A (ja) | 冷間圧延及び被覆された鋼板並びにその製造方法 | |
JPH06145893A (ja) | 延性と耐遅れ破壊特性に優れた高強度溶融亜鉛めっき鋼板およびその製造方法 | |
RU2795257C1 (ru) | Высокопрочный холоднокатаный и отожжённый оцинкованный стальной лист и способ его изготовления | |
US11891676B2 (en) | Flat steel product having improved processing properties |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: UNKNOWN |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE |
|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE |
|
17P | Request for examination filed |
Effective date: 20221004 |
|
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 |
|
DAX | Request for extension of the european patent (deleted) | ||
RAV | Requested validation state of the european patent: fee paid |
Extension state: MA Effective date: 20221004 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: GRANT OF PATENT IS INTENDED |
|
INTG | Intention to grant announced |
Effective date: 20231017 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
P01 | Opt-out of the competence of the unified patent court (upc) registered |
Effective date: 20231223 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE PATENT HAS BEEN GRANTED |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602021010946 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: TRGR |
|
REG | Reference to a national code |
Ref country code: MA Ref legal event code: VAGR Ref document number: 58835 Country of ref document: MA Kind code of ref document: B1 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: FP |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20240327 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG9D |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GR Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20240628 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20240627 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: 20240327 |