EP2627790A1 - Procédé de formage à chaud d'un flan d'acier et pièce formée à chaud - Google Patents
Procédé de formage à chaud d'un flan d'acier et pièce formée à chaudInfo
- Publication number
- EP2627790A1 EP2627790A1 EP11772882.4A EP11772882A EP2627790A1 EP 2627790 A1 EP2627790 A1 EP 2627790A1 EP 11772882 A EP11772882 A EP 11772882A EP 2627790 A1 EP2627790 A1 EP 2627790A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- steel
- blank
- temperature
- article
- hot forming
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 105
- 239000010959 steel Substances 0.000 title claims abstract description 105
- 238000000034 method Methods 0.000 title claims abstract description 54
- 238000001816 cooling Methods 0.000 claims abstract description 62
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 35
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 34
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 24
- 230000000717 retained effect Effects 0.000 claims abstract description 22
- 238000010438 heat treatment Methods 0.000 claims description 22
- 239000000203 mixture Substances 0.000 claims description 20
- 230000008569 process Effects 0.000 claims description 15
- 238000002791 soaking Methods 0.000 claims description 12
- 229910052799 carbon Inorganic materials 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 6
- 230000000930 thermomechanical effect Effects 0.000 claims description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical group [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 3
- 238000000137 annealing Methods 0.000 claims description 2
- 150000003839 salts Chemical class 0.000 claims description 2
- 101100379081 Emericella variicolor andC gene Proteins 0.000 claims 1
- 239000011572 manganese Substances 0.000 description 16
- 230000009466 transformation Effects 0.000 description 16
- 230000015572 biosynthetic process Effects 0.000 description 9
- 230000000694 effects Effects 0.000 description 9
- 229910001563 bainite Inorganic materials 0.000 description 8
- 238000004519 manufacturing process Methods 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 7
- 239000000956 alloy Substances 0.000 description 7
- 238000005097 cold rolling Methods 0.000 description 7
- 229910001567 cementite Inorganic materials 0.000 description 6
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 6
- 238000005098 hot rolling Methods 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 229910001562 pearlite Inorganic materials 0.000 description 5
- 239000000047 product Substances 0.000 description 5
- 238000010422 painting Methods 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 238000005275 alloying Methods 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 229910001568 polygonal ferrite Inorganic materials 0.000 description 3
- 230000000087 stabilizing effect Effects 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 238000000354 decomposition reaction Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 238000012546 transfer Methods 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- 229910000712 Boron steel Inorganic materials 0.000 description 1
- 229910006639 Si—Mn Inorganic materials 0.000 description 1
- 239000004115 Sodium Silicate Substances 0.000 description 1
- 229910000794 TRIP steel Inorganic materials 0.000 description 1
- YHEXKHYQCQBLJR-UHFFFAOYSA-N [B].[Mn].[C] Chemical compound [B].[Mn].[C] YHEXKHYQCQBLJR-UHFFFAOYSA-N 0.000 description 1
- 230000001464 adherent effect Effects 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 238000005279 austempering Methods 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 239000011247 coating layer Substances 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000001419 dependent effect Effects 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000010193 dilatometric analysis Methods 0.000 description 1
- 239000001177 diphosphate Substances 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 238000004886 process control Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 238000000844 transformation Methods 0.000 description 1
- 230000001131 transforming effect Effects 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/62—Quenching devices
- C21D1/673—Quenching devices for die quenching
-
- 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
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
- C22C38/22—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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
Definitions
- the invention relates to a method of hot forming a steel blank into a hot formed article having very high mechanical properties, such as an automotive part, to an article thus hot formed and to a steel strip, sheet or blank for use in a thermomechanical treatment process, in particular for use in a hot forming method according to the invention!
- AHSS advanced high strength steels
- hot (press) forming (hot stamping or press hardening) has been developed.
- hot (press) forming By hot (press) forming, the strength of the steel article is improved through fast cooling after heating it to a temperature range where an austenitic phase exists and through the phase transformations of the austenite to harder phases such as bainite and martensite.
- the basics of the hot forming technique and steel compositions adapted to be used were for the first time described in GB1490535. Afterwards a lot of Carbon - Manganese - Boron based steels have been developed for use in hot press forming.
- a typical steel used for the hot press forming is based on a composition system of 22MnB5, i.e.
- Hot press forming of 22MnB5 steel can produce complex parts such as bumpers and pillars with ultrahigh strength, minimum springback, and reduced sheet thickness.
- the tensile strength of boron steels is up to 1600 MPa, which is far above that of the highest-strength conventional cold stamping steels.
- the ductility of total elongation A5 is less than 6%.
- the ductility and toughness should be further increased.
- Advanced high strength steels with TRIP (transformation induced plasticity) added multiphase microstructure are a solution. These steels are characterized by a ferritic-bainitic microstructure with retained austenite, which undergoes martensitic transformation during forming of products, additionally contributing to the strengthening of a ready part.
- US2008/0286603 A1 has disclosed a steel sheet that exhibits an ultra-high strength after hot press forming followed by rapid cooling, and an enhanced yield strength after painting.
- the steel sheet has a composition (expressed in % by weight) comprising 0.1 to 0.5 C, 0.01 to 1.0 Si, 0.5 to 4.0 Mn, 0.1 or less P, 0.03 or less S, 0.1 soluble Al, 0.01 to 0.1 N, 0.3 or less W, and the balance being Fe and other inevitable impurities.
- a hot-pressed part made of the steel sheet and a method for manufacturing the hot-pressed part are disclosed.
- the hot-pressed part achieves a high increment in yield strength after heat treatment for painting while ensuring an ultra-high tensile strength.
- the steel provided according to this US patent application has an ultimate tensile strength (UTS) of 1500 MPa with the total elongation being less than 8%.
- a high-strength cold-rolled steel sheet having an uniform elongation including (in wt.%): 0.10 - 0.28 C; 1.0 - 2.0 Si; and 1.0 - 3.0 Mn.
- the structure has the space factors: 30 - 65% of bainitic ferrite; 30 - 50% of polygonal ferrite; and 5 - 20% of residual austenite.
- the desired microstructures were obtained according to the following process.
- the steel sheet was heated for soaking up to a temperature which is equal to or higher than the A3 transformation point (A3), then cooled down temporarily to a temperature Tq expressed by the formula A3-250 (°C) ⁇ Tq ⁇ A3-20 (°C) at an average cooling rate of 1 - 10 °C/s, and then quenched from this temperature down into a bainitic transformation temperature range at an average cooling rate of 11 °C/s or faster.
- US2008/0308194 A1 has disclosed a process for manufacturing a part made of steel having a multiphase microstructure.
- the composition of steel comprises, in % by weight: C 0.01 - 0.50, Mn 0.5 - 3.0, Si 0.001 - 3.0, Al 0.005 - 3.0, Mo ⁇ 1.0, Cr ⁇ 1.5, P ⁇ 0.10, Ti ⁇ 0.20, V ⁇ 1.0 and optionally, one or more elements such as: Ni ⁇ 2.0, Cu ⁇ 2.0, S ⁇ 0.05 and Nb ⁇ 0.15, the balance of the composition being iron and inevitable impurities.
- the steel sheet is heated to reach a soaking temperature Ts above Ac1 but below Ac3 and is held at this soaking temperature Ts for a soaking time ts so that the steel has an austenite content equal to or greater than 25 % by area; the steel blank is transferred into a forming tool for hot forming; and the part obtained is cooled within the tool at a cooling rate V to obtain a multiphase microstructure comprising ferrite, martensite or bainite and retained austenite, and ferrite is homogeneous in each of the regions.
- JP2003193193 teaches steel sheet having a two phase microstructure comprising bainite/bainitic ferrite as a main phase and austenite as a second phase.
- the manufacturing process comprises an isothermal heat treatment at 200 - 450 °C for 1 - 3000 seconds.
- TBF TRIP-aided bainitic ferrite
- Another object of the present invention is to provide a multiphase microstructured steel resulting in simultaneously improved strength and ductility. Yet a further object is to provide a steel having an ultimate tensile strength higher than 1400 MPa, such as about 1500 Mpa. Still another object is to provide a steel having a total elongation higher than 8%, such as about 12%.
- the invention provides a method of hot forming a steel blank into an article, such as an automotive part, as defined in claim 1 , wherein the method comprises the following steps:
- the steel blank as a starting material for executing the method according to the invention can be obtained by standard casting processes, or indirectly from steel strip or sheet material.
- the preheating temperature may be about 1100 - 1250 °C.
- Traditional hot rolling passes and rolling conditions may be implemented to roll the steel ingot to a sheet product of about 3 to 5 mm in thickness.
- the finish rolling temperature is about 850 - 880 °C.
- the steel sheet is cooled at an average cooling rate of 5 - 50 °C/s to a coiling temperature between 550 and 700 °C. An excess of martensite or bainite is formed at a coiling temperature lower than 550 °C, resulting in an excessive increase in the strength of the hot-rolled steel sheet.
- the excessively increased strength acts as a load during subsequent cold rolling for the production of a cold-rolled steel sheet causing problems, such as a poor appearance.
- cold rolling the coiled hot-rolled sheet is pickled and cold-rolled.
- Cold rolling can also be carried out under standard conditions at a reduction of about 30 - 75%.
- the cold rolling reduction is preferably controlled to range from 40 to 70%.
- the sheet has a thickness of about 1 to 2 mm according to product requirements.
- the sheet may be decoiled and blanked to proper size suitable for hot forming according to the invention.
- a cold rolled sheet is a preferred starting product in the method according to the invention.
- the two-step cooling pattern and the interrupt cooling temperature are properly controlled.
- the heated steel blank used in step d) has an austenite structure.
- the method according to the invention also comprises the steps of
- These austenitizing steps of the method for obtaining an austenite structure are performed by heating steel sheets, strips of blanks e.g. in a furnace or in a hot forming facility itself, to a temperature T1 above Ac3, more preferably in the range of Ac3 + 20 °C to Ac3 + 60 °C.
- the heating rate is in the range of 10 - 25 °C/s.
- This heating step is followed by soaking at a temperature above Ac3, preferably in the range of Ac3 + 20 °C to Ac3 + 60 °C, for a short period of time, preferably 1 - 5 min (Ac3 being the temperature at which transformation of ferrite into austenite is completed in hypoeutectoid steel, upon heating).
- the austenitizing temperature (T1 ) and soaking time are selected to ensure complete dissolution of carbides. If applicable, then the steel blank thus soaked is transferred to the hot forming device such as a hot forming press. If applicable, the transferring time is controlled, usually to a short transfer time such as less than 10 seconds to prevent cooling of the blank below the starting temperature T2 of the next hot forming step.
- the starting temperature T2 for hot forming and simultaneous cooling should be above the Ar3 point (typically in the range of 780-830 °C) to prevent any ferrite phase transformation, e.g. during transferring.
- the steel blank is allowed to cool down further to room temperature at a further cooling rate V3 of 0.2 - 10 °C/s.
- the higher cooling rates above 5 °C/s within said range are advantageous for achieving a high total elongation (At).
- the range of 0.5 - 5 °C/s is preferred in view of high Ultimate Tensile Strength (UTS).
- UTS Ultimate Tensile Strength
- T3 is too high, generally above 550 °C, some pearlite structure may form during the following slow cooling step at cooling rate V3. If T3 is too low, below Ms point, bainitic structure may be obtained in an insufficient amount in the final microstructure. If V3 is too fast, too much martensite is obtained in the final microstructure, and it is impossible to ensure sufficient elongation. If V3 is too small, too less martensite is obtained in order to guarantee the high strength. Moreover, the combination of T3 and V3 is selected such that the article obtained comprises a multiphase microstructure comprising by volume fraction 55 - 90% of bainitic ferrite, 5 - 15% retained austenite and 5 - 30% martensite.
- a relatively high UTS is achieved if the multiphase microstructure comprises 55 - 85% bainitic ferrite, 5 - 15% retained austenite and 10 - 30% martensite. Generally the higher the interrupt temperature T3, the lower V3 has to be in order to get this multiphase microstructure.
- the steel, in particular TBF steel, in the article as manufactured is characterized by a multiphase structure comprising, more preferably consisting of, carbide free bainitic ferrite, carbon enriched retained austenite and a relatively small amount of martensite.
- the mother- phase structure comprises fine plates of essentially carbide free bainitic ferrite.
- the formation of such a microstructure is due to the fact that the precipitation of cementite during bainitic transformation is suppressed by alloying the steel with a sufficient amount of Si and/or Al, which have very low solubility in cementite and greatly retards growth of cementite from austenite. Carbon that is rejected from the bainitic ferrite enriches the residual austenite, thereby transforming to martensite during cooling after bainitic transformation or stabilizing it down to room temperature.
- the advantages of this type of microstructure are manifold.
- the bainitic ferrite in TBF steel is present in the form of plates with an ultra fine grain size, usually the length ranging up to about 15 micrometer at most and the thickness ranging up to 0.3 micrometer at most (typically -10 pm long and ⁇ 0.2 pm thick). Furthermore the strength and ductility are improved simultaneously.
- the high flow stresses are due to the small thickness of the bainitic laths and to the absence of proeutectoid polygonal ferrite contrary to existing TRIP (transformation induced plasticity) steels. It is assumed that the retained austenite offers an additional TRIP effect, and that it is useful for improving total elongation.
- the constituents of the various phases in the final microstructure preferably comprise, by volume fraction, bainitic ferrite: 55 - 90%, retained austenite: 5 - 15% and martensite: 5 - 30%.
- a preferred embodiment of the present invention relates to a method of hot forming a steel blank into an article, wherein the method comprises heating the steel blank to an austenitizing temperature T1 , advantageously in the range of Ac3 + 20 °C and Ac3 + 60 °C, and soaking the steel blank in the austenitizing temperature range, such that carbides are completely dissolved; introducing the heated and soaked blank in a hot forming device, such as a hot press, while preventing ferrite phase transformation; hot forming the steel blank to form a shaped article starting at a starting temperature T2 above Ar3 and cooling the article thus being hot formed to an interrupt temperature T3 in the bainitic transformation range at a cooling rate such that formation of proeutectoid ferrite and pearlite is avoided; and further cooling the article from the interrupt temperature T3 to ambient temperature at
- the steel comprises the following elements (in wt. %):C 0.15 - 0.45, Si 0.6 - 2.5, Mn 1.0 - 3.0, Mo 0 - 0.5, Cr 0 - 1.0, P 0.001 - 0.05, S ⁇ 0.03, Ca ⁇ 0.003, Ti 0.1 or less and V 0.1 or less and the balance Fe and other inevitable impurities.
- the steel may also contain Al less than 1.5%, partially replacing the same amount of Si, provided that the sum of Si and Al is in the range of 1.2 - 2.5%.
- the amounts of Mn and Cr satisfy Mn + Cr ⁇ 3%, while also preferably, the amounts of C and Mo satisfy C + 1/3Mo ⁇ 0.45% for better control of the multiphase microstructure.
- C is an element for securing high strength, and for securing retained austenite.
- C is added in an amount of 0.15% or more to form the desired multiphase microstructure to achieve ultra-high strength and ductility.
- C content exceeds 0.45%, it is difficult to obtain the multiphase microstructure through the method according to the invention comprising a contiguous cooling subprocess.
- C is preferably present in an amount of 0.2 - 0.4%, more preferably 0.2 - 0.35%.
- Mn is one of the main elements in the steel composition according to the invention.
- the functions of Mn include stabilizing the austenite and obtaining the desired multiphase microstructure. If Mn is less than 1.0%, the effects are not sufficiently marked. Whereas if the content exceeds 3%, a fully martensite structure is easily created. As a result, the steel is hardened and embrittled during press forming.
- Mn is an element that is useful in lowering the Ac3 temperature. A higher Mn content is advantageous in lowering the temperature necessary for hot press forming.
- the Mn content is limited to the range of 1.0 - 3.0%, preferably 1.5 - 2.5% and more preferably 1.6 - 2.5%, even more preferably 1.7 - 2.4%.
- Si is an element effective for reinforcing a solid solution, and is useful for suppressing production of carbide due to decomposition of retained austenite.
- carbides either transition carbide or cementite
- Si suppresses the precipitation of brittle cementite during bainite formation, and hence results in an improvement in formability and toughness.
- a minimum of 1.0% Si is needed to form carbide free bainite.
- Si is also known to deteriorate galvanizability due to the formation of oxides adherent to the steel substrate. Therefore, the upper limit of Si is controlled below 2.5%.
- the Si content is advantageously limited to the range of 1.2 - 2.5% and more preferably to the range of 1.4 - 2.0%.
- Al is also an element useful for suppressing production of carbide due to decomposition of, particularly, retained austenite. Partial replacement of Si by a same amount of Al has been shown to effectively retard cementite formation without a detrimental effect on hot-dip coatability in TBF steels. However, a high concentration of Al leads to higher possibility of polygonal ferrite to be generated, which is less effective than fine plate ferrite in view of strength. A full substitution of Si by an equivalent amount of Al leads to a marked deterioration of the strength-ductility balance. If added, the amount of Al is limited to 1.5% or smaller.
- P is an element useful for maintaining desired retained austenite, and its effect is exerted by an amount of P of 0.001 % or larger, more preferably 0.005% or larger, but P may deteriorate the workability of the steel when it is added in an excess amount. Accordingly, the P content is preferably limited to 0.05% or less.
- S is a harmful element which forms sulfide based inclusions such as MnS, which initiates crack formation, and deteriorates processibility. Therefore, it is desirable to reduce the amount of S as much as possible. Accordingly, S is controlled to 0.03% or smaller.
- Mo and Cr serve to improve the hardenability of the steel and facilitate the formation of bainite ferrite. At the same time, they are elements having similar effectiveness useful for stabilizing retained austenite. Therefore, Mo and Cr are very effective for process control. It is advantageous that each of them is contained at 0.05% or larger. However, when each of them is added excessively, the effect is saturated and a higher addition is not economical. Therefore, the amount of Mo is 0.5% or smaller, and the amount of Cr is 1 % or smaller.
- Ti and V have the effect of forming strengthening precipitates and refining microstructure.
- the amount of each of them is 0.1 % or smaller, preferably 0.05% or smaller.
- Ca is an element effective for controlling a form of sulfide in the steel, and improving processibility. It is recommended that Ca is contained at 0.0003% or more. However, when it is added excessively, the effect is saturated. Therefore, the preferred amount is 0.0003 - 0.003%.
- the heat treatment described above may be carried out by heating and cooling in a continuous annealing facility (CAL), hot press forming facility, salt bath or the like.
- CAL continuous annealing facility
- the first combined deformation/cooling step d) is performed in a hot forming facility.
- the second cooling step e) is performed in air or in stock outside the hot forming facility.
- the steel of the formed article has an ultimate tensile strength (UTS) of at least 1400 MPa, advantageously at least 1500 MPa, more preferably at least 1600 MPa, and most preferably at least 1700 MPa.
- UTS ultimate tensile strength
- the steel of the formed article has a total elongation of at least 8%, preferably at least 10%, more preferably at least 12%, and most preferably at least 14%.
- the heat treatment processes can be simply performed by applying the hot (press) forming in a standard hot forming facility with only modification of the simultaneous cooling process, including cooling interrupt temperature and velocities.
- the heat blank is inserted into the die sets of a hot press, in which the blank is shaped and cooled.
- the transfer time e.g. 5 to 10 s
- the cooling rate V2 of the steel part in the forming tool depends on the deformation and on the quality of the contact between the tool and the steel blank.
- the forming tools may be cooled for example by using circulation of a liquid to ensure that the cooling rate is high enough (>25 °C/s) during quenching in the press mould.
- the interrupt cooling temperature can be controlled by the time for separation of the pressing tools.
- the formed article is then removed from the mould and cooled to room temperature in air.
- the formed articles e.g. sheets, may also be stacked and then cooled to ambient temperature in air. After cooling down to room temperature, the parts will be built in the car body structure. Then the paintbake process is performed.
- the paintbake cycle does not affect the properties.
- the present invention provides a steel article, preferably formed according to the method of the present invention, wherein the steel has a microstructure comprising by volume fraction:
- the steel has an Ultimate Tensile Strength of at least 1400 MPa, advantageously at least 1500 MPa, preferably at least 1600 MPa, more preferably at least 1700 MPa and/or a total elongation of at least 8%, preferably at least 10%, more preferably at least 12%, most preferably at least 14%.
- the present invention provides a steel strip, sheet or strip for use in a thermomechanical treatment, in particular a hot forming method according to the invention described above, having a composition, in weight %:
- the balance being Fe and inevitable impurities
- compositions of the steel strip, sheet or blank according to the third aspect of the invention comprises, the alloying elements are present in, expressed in weight %,:
- Si 0.8 - 2.0, preferably 1.2 - 1.8 and/or
- Mn 1.5 - 2.5, preferably 1.7 -2.4 and/or
- the articles obtained from the strip, sheet or blank exhibit a high tensile strength by rapid cooling after heat treatment and achieve a high increment in yield strength after heat treatment, especially for painting. Based on these advantages, excellent impact properties of the steel article according to the present invention are attained. In addition, the steel article according to the present invention advantageously exhibits good adhesion to a coating layer. Furthermore, other advantages of the steel article according to the present invention are good surface appearance and superior corrosion resistance after painting.
- FIG. 1 A schematic representation of a practical embodiment of the method according to the invention is shown in Fig. 1 , showing a temperature vs. time plot.
- a steel blank is heated at a heating rate of 15 °C to the austenitizing temperature T1 in the range of Ac3 + 20 °C to Ac3 + 60 °C and soaked at that temperature during a soaking time t1.
- the thus heated and soaked blank is transferred from the furnace to the hot forming facility, during which cooling by air occurs to some extent. Care is taken that the temperature T2 is not decreased below Ar3 before hot press forming of the blank.
- After hot press forming the blank thus formed is cooled down to the interrupt temperature T3 at a rate of more than 25 °C. Then air cooling is carried out.
- the invention is further illustrated by the following examples.
- Steels having compositions A-F as specified in Table 1 were cast to ingots of about 25 kg (100x110x330 mm). The ingots were reheated and then roughly hot rolled to slabs having a thickness of 40 mm. Then finish hot rolling was applied with the following process parameters: preheating at 1200°C for 30 min; multipass rolling to thickness 4 mm (40-27-18-12-8-6-4 mm); and finishing rolling temperature 860 ⁇ 20 °C. Controlled cooling at a rate 30 °C/s to 600 °C in a runout-table was carried out in order to simulate the commercially used coiling process. After the coiling process the steel plates contain a microstructure consisting of ferrite and pearlite and have a tensile strength less than 700 MPa. The plate was then cold rolled from 4 to 1 mm sheet.
- the critical temperatures such as Ac3 and Ms were determined by applying standard dilatometric analysis to facilitate the determination of the temperatures in the process according to the invention.
- the resulting cold rolled sheets were subjected to a heat treatment by using a CASIM simulator. Specifically, the steel sheets were heated to 870 to 920°C at a rate of 15 °C/s, holding the sheets at this temperature for 2 min, then cooling at a rate of 50 °C/s to an interrupt temperature between 400 and 550 °C, thereafter, cooling at a rate of 0.2 to 10 °C/s to simulate different air cooling conditions.
- Tensile tests were conducted by applying JIS 5 tensile test specimen to measure tensile strength and elongation of the specimens with the required microstructures. The volume fraction of bainite and/or martensite in the microstructures was estimated by using metallographic characterisation in combination with dilatametric analysis. The volume fraction of the retained austenite was determined by using TEM. Other measurements are standard.
- the tensile test results and the invented alloys with the required the microstructure constituents are given in Table 2.
- the experimental results indicate that the microstructures and the properties are essentially independent from the austenitizing temperature T1 as long as the T1 is above Ac3, advantageously between Ac3 + 20 °C and Ac3 + 60 °C. It is also proven that the transferring temperature T2 and the cooling rate V2 do not significantly affect the microstructures and properties as well provided that T2 is higher than Ar3 and V2 is equal to or more than 25 °C/s and preferably less than 100 °C/s. However, the microstructures and the properties are strongly dependent on the interrupt temperature T3 and the cooling rate V3. The C content and alloying element contents have a large effect on the selection of T3 and V3.
- the conditions for the required multiphase microstructures of the alloys according to the invention can be obtained by careful adjustment of T3 and V3.
- the cooling rate V3 can be controlled in a lower range 0.25 to 2 °C/s; for alloys containing lower C or lower Mo, the cooling rate V3 can be controlled in a higher range 2 to 10° C/s.
- higher cooling rate will result in less bainitic ferrite, but relatively more martensite. Therefore higher strength will be obtained.
- Lower cooling rate will result in more bainitic ferrite, but relatively less martensite, then higher elongation will be achieved.
- the higher T3 temperature is, the relatively more bainitic ferrite will be in the final microstructure for a given cooling rate, resulting in high strength but lower elongation.
- HV5 Vickers hardness measured at load of 5 kgf
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP11772882.4A EP2627790B1 (fr) | 2010-10-12 | 2011-10-10 | Methode pour deformation a chaud d' une tole d'acier et tole d'acier |
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP10013537 | 2010-10-12 | ||
PCT/EP2011/005053 WO2012048841A1 (fr) | 2010-10-12 | 2011-10-10 | Procédé de formage à chaud d'un flan d'acier et pièce formée à chaud |
EP11772882.4A EP2627790B1 (fr) | 2010-10-12 | 2011-10-10 | Methode pour deformation a chaud d' une tole d'acier et tole d'acier |
Publications (2)
Publication Number | Publication Date |
---|---|
EP2627790A1 true EP2627790A1 (fr) | 2013-08-21 |
EP2627790B1 EP2627790B1 (fr) | 2014-10-08 |
Family
ID=43640446
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP11772882.4A Revoked EP2627790B1 (fr) | 2010-10-12 | 2011-10-10 | Methode pour deformation a chaud d' une tole d'acier et tole d'acier |
Country Status (5)
Country | Link |
---|---|
US (1) | US20130192726A1 (fr) |
EP (1) | EP2627790B1 (fr) |
JP (1) | JP2013545890A (fr) |
CN (1) | CN103154279B (fr) |
WO (1) | WO2012048841A1 (fr) |
Families Citing this family (37)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
HUE057362T2 (hu) | 2006-10-30 | 2022-05-28 | Arcelormittal | Bevonatolt acélszalagok, eljárások azok elõállítására, eljárások azok alkalmazására, azokból készített nyersdarabok, azokból készített sajtolt termékek, továbbá ilyen sajtolt terméket tartalmazó késztermékek |
CN103597107B (zh) * | 2011-06-10 | 2016-06-22 | 株式会社神户制钢所 | 热压成形品、其制造方法和热压成形用薄钢板 |
CN103597106B (zh) | 2011-06-10 | 2016-03-02 | 株式会社神户制钢所 | 热压成形品、其制造方法和热压成形用薄钢板 |
CN105734404B (zh) * | 2011-07-21 | 2018-01-02 | 株式会社神户制钢所 | 热压成形钢构件的制造方法 |
JP5802155B2 (ja) * | 2012-03-09 | 2015-10-28 | 株式会社神戸製鋼所 | プレス成形品の製造方法およびプレス成形品 |
BR112015000178B1 (pt) * | 2012-08-03 | 2020-03-17 | Tata Steel Ijmuiden Bv | Processo para produzir tira de aço laminado a quente e tira de aço laminado a quente |
JP5862591B2 (ja) | 2013-03-28 | 2016-02-16 | Jfeスチール株式会社 | 高強度鋼板およびその製造方法 |
DE102013009232A1 (de) * | 2013-05-28 | 2014-12-04 | Salzgitter Flachstahl Gmbh | Verfahren zur Herstellung eines Bauteils durch Warmumformen eines Vorproduktes aus Stahl |
DE102013010946B3 (de) * | 2013-06-28 | 2014-12-31 | Daimler Ag | Verfahren und Anlage zum Herstellen eines pressgehärteten Stahlblechbauteils |
EP3045550A4 (fr) * | 2013-09-10 | 2017-05-31 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Procédé pour fabriquer un article moulé à la presse, et article moulé à la presse |
EP3020845B1 (fr) * | 2013-09-18 | 2018-01-31 | Nippon Steel & Sumitomo Metal Corporation | Corps moulé par estampage à chaud et son procédé de production |
EP2851440A1 (fr) * | 2013-09-19 | 2015-03-25 | Tata Steel IJmuiden BV | Acier pour formage à chaud |
ES2955824T3 (es) * | 2013-10-21 | 2023-12-07 | Magna Int Inc | Método para recortar una pieza conformada en caliente |
JP6288287B2 (ja) * | 2014-10-03 | 2018-03-07 | 新日鐵住金株式会社 | ろう付継手の製造方法及びろう付継手 |
KR101931041B1 (ko) | 2014-10-24 | 2018-12-19 | 제이에프이 스틸 가부시키가이샤 | 고강도 핫 프레스 부재 및 그 제조 방법 |
EP3029162B1 (fr) * | 2014-12-01 | 2018-04-25 | Voestalpine Stahl GmbH | Procédé de traitement à chaud d'un produit en manganèse-acier |
CN104513927B (zh) * | 2014-12-19 | 2017-04-05 | 宝山钢铁股份有限公司 | 一种抗拉强度800MPa级高强度高韧性钢板及其制造方法 |
CN104561790B (zh) * | 2015-01-23 | 2017-11-28 | 宝钢特钢有限公司 | 一种1500MPa级高强度钢及其生产方法 |
EP3061837A1 (fr) * | 2015-02-27 | 2016-08-31 | Swiss Steel AG | Produit longitudinal bainitique nu et son procédé de fabrication |
EP3162558A1 (fr) * | 2015-10-30 | 2017-05-03 | Outokumpu Oyj | Composant constitué d'un matériau composite métallique et procédé pour la fabrication du composant par formage à chaud |
GB201521443D0 (en) * | 2015-12-04 | 2016-01-20 | Impression Technologies Ltd | Method for operating a press for metal sheet forming |
CN106048430B (zh) * | 2016-07-06 | 2017-11-03 | 马钢(集团)控股有限公司 | 一种高韧性轨道交通用贝氏体钢车轮及其制造方法 |
CN106191666B (zh) | 2016-07-06 | 2018-01-02 | 马钢(集团)控股有限公司 | 一种低成本精节生产的轨道交通用贝氏体钢车轮及其制造方法 |
CA3039083A1 (fr) * | 2016-10-17 | 2018-04-26 | Tata Steel Ijmuiden B.V. | Substrat en acier pour pieces peintes |
CN109983139A (zh) | 2016-11-25 | 2019-07-05 | 日本制铁株式会社 | 淬火成形品的制造方法、热压用钢材的制造方法及热压用钢材 |
KR102477323B1 (ko) * | 2016-11-29 | 2022-12-13 | 타타 스틸 이즈무이덴 베.뷔. | 열간 성형 물품 제조 방법 및 획득 물품 |
EP3327152B1 (fr) * | 2016-11-29 | 2023-10-11 | Tata Steel UK Limited | Procédé de formage à chaud d'une ébauche d'acier |
WO2018115933A1 (fr) | 2016-12-21 | 2018-06-28 | Arcelormittal | Tôle d'acier laminée à froid à haute résistance présentant une formabilité élevée et son procédé de fabrication |
CN106947907B (zh) * | 2017-03-03 | 2018-12-07 | 北京科技大学 | 一种石墨化易切削钢高速线材的制备方法 |
US20180372146A1 (en) * | 2017-06-26 | 2018-12-27 | GM Global Technology Operations LLC | Fine grain steel alloy and automotive components formed thereof |
KR101978054B1 (ko) * | 2017-09-27 | 2019-05-13 | 현대제철 주식회사 | 핫 스탬핑 부품의 제조방법 |
WO2019173681A1 (fr) * | 2018-03-08 | 2019-09-12 | Northwestern University | Bainite sans carbure et aciers austénitiques retenus, procédé de production et applications |
US20210189517A1 (en) * | 2018-05-22 | 2021-06-24 | Thyssenkrupp Steel Europe Ag | Sheet Metal Part Formed from a Steel Having a High Tensile Strength and Method for Manufacturing Said Sheet Metal Part |
CN111254351B (zh) * | 2020-01-21 | 2021-07-20 | 鞍钢股份有限公司 | 一种高性能热轧耐磨钢薄板及其生产方法 |
WO2021236619A1 (fr) * | 2020-05-18 | 2021-11-25 | Magna International Inc. | Procédé pour le traitement d'un acier à haute résistance avancé |
KR102345608B1 (ko) * | 2020-12-23 | 2021-12-30 | 현대제철 주식회사 | 핫 스탬핑 부품, 및 이의 제조 방법 |
KR102584563B1 (ko) * | 2021-10-29 | 2023-10-04 | 현대제철 주식회사 | 핫 스탬핑 부품 및 이의 제조 방법 |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SE435527B (sv) | 1973-11-06 | 1984-10-01 | Plannja Ab | Forfarande for framstellning av en detalj av herdat stal |
JP3854506B2 (ja) | 2001-12-27 | 2006-12-06 | 新日本製鐵株式会社 | 溶接性、穴拡げ性および延性に優れた高強度鋼板およびその製造方法 |
KR100764253B1 (ko) | 2005-01-28 | 2007-10-05 | 가부시키가이샤 고베 세이코쇼 | 내수소취화 특성이 우수한 고강도 스프링용 강 |
CN100510142C (zh) * | 2005-01-28 | 2009-07-08 | 株式会社神户制钢所 | 耐氢脆特性优良的高强度螺栓 |
JP4716359B2 (ja) | 2005-03-30 | 2011-07-06 | 株式会社神戸製鋼所 | 均一伸びに優れた高強度冷延鋼板およびその製造方法 |
EP1767659A1 (fr) | 2005-09-21 | 2007-03-28 | ARCELOR France | Procédé de fabrication d'une pièce en acier de microstructure multi-phasée |
SK288275B6 (sk) | 2005-12-01 | 2015-06-02 | Posco | Oceľová doska na tvarovanie lisovaním za horúca s tepelnou úpravou a rázovými vlastnosťami, za horúca lisovaný diel z nej vyrobený a spôsob ich výroby |
KR100990772B1 (ko) * | 2005-12-28 | 2010-10-29 | 가부시키가이샤 고베 세이코쇼 | 초고강도 박강판 |
EP1832667A1 (fr) * | 2006-03-07 | 2007-09-12 | ARCELOR France | Procédé de fabrication de tôles d'acier à très hautes caractéristiques de résistance, de ductilité et de tenacité, et tôles ainsi produites |
EP1990431A1 (fr) * | 2007-05-11 | 2008-11-12 | ArcelorMittal France | Procédé de fabrication de tôles d'acier laminées à froid et recuites à très haute résistance, et tôles ainsi produites |
-
2011
- 2011-10-10 US US13/819,281 patent/US20130192726A1/en not_active Abandoned
- 2011-10-10 CN CN201180048067.7A patent/CN103154279B/zh not_active Expired - Fee Related
- 2011-10-10 JP JP2013533121A patent/JP2013545890A/ja active Pending
- 2011-10-10 EP EP11772882.4A patent/EP2627790B1/fr not_active Revoked
- 2011-10-10 WO PCT/EP2011/005053 patent/WO2012048841A1/fr active Application Filing
Non-Patent Citations (1)
Title |
---|
See references of WO2012048841A1 * |
Also Published As
Publication number | Publication date |
---|---|
JP2013545890A (ja) | 2013-12-26 |
WO2012048841A1 (fr) | 2012-04-19 |
CN103154279A (zh) | 2013-06-12 |
CN103154279B (zh) | 2015-09-23 |
WO2012048841A8 (fr) | 2013-04-25 |
US20130192726A1 (en) | 2013-08-01 |
EP2627790B1 (fr) | 2014-10-08 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP2627790B1 (fr) | Methode pour deformation a chaud d' une tole d'acier et tole d'acier | |
US20220282348A1 (en) | Method for manufacturing a high strength steel product and steel product thereby obtained | |
EP3548641B1 (fr) | Procédé de fabrication d'un article formé à chaud et article ainsi obtenu | |
KR101892661B1 (ko) | 핫 스탬핑용 강판, 핫 스탬핑 방법 및 핫 스탬핑된 부품 | |
CA2725210C (fr) | Procede de production d'une piece moulee en acier a structure a predominance ferritique-bainitique | |
US20130295402A1 (en) | Steel Sheet for Formed Member Having Enhanced Ductility, Formed Member, and Method for Manufacturing the Formed Member | |
EP3556896B1 (fr) | Tôle d'acier laminée à froid à haute résistance présentant une excellente limite d'élasticité, une excellente ductilité et une excellente capacité d'expansion de trou, et tôle d'acier galvanisée par immersion à chaud | |
EP3395993B1 (fr) | Tôle d'acier haute résistance laminée à froid de type à haute limite d'élasticité et son procédé de fabrication | |
US10626478B2 (en) | Ultra high-strength air-hardening multiphase steel having excellent processing properties, and method for manufacturing a strip of said steel | |
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 | |
CN112585284A (zh) | 由钢形成的具有高抗拉强度的板材成型件及其制造方法 | |
CN113316650B (zh) | 高强度钢带材 | |
KR20170084209A (ko) | 탁월한 가공 특성을 갖는 고강도의 공기 경화 다상 강 및 상기 강의 스트립을 제조하기 위한 방법 | |
US20190185951A1 (en) | Method for producing a high-strength steel strip with improved properties for further processing, and a steel strip of this type | |
CN110621794B (zh) | 具有优异延展性和可拉伸翻边性的高强度钢片 | |
KR101917452B1 (ko) | 굽힘가공성과 구멍확장성이 우수한 냉연강판 및 그 제조방법 | |
KR101406444B1 (ko) | 연신율 및 굽힘가공성이 우수한 초고강도 냉연강판 및 이의 제조방법 | |
EP4114994B1 (fr) | Tôle d'acier laminée à froid à résistance élevée et recuite après galvanisation et son procédé de fabrication | |
WO2020128571A1 (fr) | Pièce durcie à la presse ayant une résistance élevée à la rupture différée et procédé de fabrication associé | |
CN111465710B (zh) | 高屈强比型高强度钢板及其制造方法 |
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: 20130513 |
|
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) | ||
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R079 Ref document number: 602011010493 Country of ref document: DE Free format text: PREVIOUS MAIN CLASS: C21D0009460000 Ipc: C21D0008000000 |
|
RIC1 | Information provided on ipc code assigned before grant |
Ipc: C21D 8/00 20060101AFI20140224BHEP Ipc: C22C 38/28 20060101ALI20140224BHEP Ipc: C21D 9/46 20060101ALI20140224BHEP Ipc: C21D 9/48 20060101ALI20140224BHEP Ipc: C22C 38/38 20060101ALI20140224BHEP Ipc: C22C 38/14 20060101ALI20140224BHEP Ipc: C21D 8/02 20060101ALI20140224BHEP Ipc: C22C 38/02 20060101ALI20140224BHEP Ipc: C22C 38/04 20060101ALI20140224BHEP Ipc: C21D 1/673 20060101ALI20140224BHEP Ipc: C22C 38/22 20060101ALI20140224BHEP Ipc: C22C 38/12 20060101ALI20140224BHEP |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
INTG | Intention to grant announced |
Effective date: 20140422 |
|
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 Ref country code: AT Ref legal event code: REF Ref document number: 690660 Country of ref document: AT Kind code of ref document: T Effective date: 20141015 |
|
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: 602011010493 Country of ref document: DE Effective date: 20141120 |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: VDEP Effective date: 20141008 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: MK05 Ref document number: 690660 Country of ref document: AT Kind code of ref document: T Effective date: 20141008 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: 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: 20141008 |
|
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: 20150209 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: 20141008 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: 20141008 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: 20141008 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: 20150208 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: 20150108 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20141008 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: 20141008 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: 20141008 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: 20141008 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: 20141008 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: 20141008 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: 20150109 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: 20141008 |
|
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: BE Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20141031 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R026 Ref document number: 602011010493 Country of ref document: DE |
|
PLBI | Opposition filed |
Free format text: ORIGINAL CODE: 0009260 |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: MM4A |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20141008 Ref country code: CH Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20141031 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: 20141008 Ref country code: LI Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20141031 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: 20141008 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: 20141008 Ref country code: SK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20141008 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: 20141008 |
|
26 | Opposition filed |
Opponent name: ARCELORMITTAL Effective date: 20150707 |
|
PLAX | Notice of opposition and request to file observation + time limit sent |
Free format text: ORIGINAL CODE: EPIDOSNOBS2 |
|
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: 20141008 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 5 |
|
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: 20141010 |
|
PLAF | Information modified related to communication of a notice of opposition and request to file observations + time limit |
Free format text: ORIGINAL CODE: EPIDOSCOBS2 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20141008 |
|
PLBB | Reply of patent proprietor to notice(s) of opposition received |
Free format text: ORIGINAL CODE: EPIDOSNOBS3 |
|
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: 20141008 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
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: 20141008 |
|
PLAB | Opposition data, opponent's data or that of the opponent's representative modified |
Free format text: ORIGINAL CODE: 0009299OPPO |
|
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: 20111010 Ref country code: LU Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES Effective date: 20141010 Ref country code: MT 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: 20141008 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: 20141008 |
|
R26 | Opposition filed (corrected) |
Opponent name: ARCELORMITTAL Effective date: 20150707 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 6 |
|
PLAB | Opposition data, opponent's data or that of the opponent's representative modified |
Free format text: ORIGINAL CODE: 0009299OPPO |
|
R26 | Opposition filed (corrected) |
Opponent name: ARCELORMITTAL Effective date: 20150707 |
|
APAH | Appeal reference modified |
Free format text: ORIGINAL CODE: EPIDOSCREFNO |
|
APBM | Appeal reference recorded |
Free format text: ORIGINAL CODE: EPIDOSNREFNO |
|
APBP | Date of receipt of notice of appeal recorded |
Free format text: ORIGINAL CODE: EPIDOSNNOA2O |
|
APBQ | Date of receipt of statement of grounds of appeal recorded |
Free format text: ORIGINAL CODE: EPIDOSNNOA3O |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 7 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20141008 |
|
APAH | Appeal reference modified |
Free format text: ORIGINAL CODE: EPIDOSCREFNO |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: PLFP Year of fee payment: 8 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20141008 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20191029 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20191025 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20191028 Year of fee payment: 9 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R064 Ref document number: 602011010493 Country of ref document: DE Ref country code: DE Ref legal event code: R103 Ref document number: 602011010493 Country of ref document: DE |
|
APBU | Appeal procedure closed |
Free format text: ORIGINAL CODE: EPIDOSNNOA9O |
|
RDAF | Communication despatched that patent is revoked |
Free format text: ORIGINAL CODE: EPIDOSNREV1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: PATENT REVOKED |
|
RDAG | Patent revoked |
Free format text: ORIGINAL CODE: 0009271 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: PATENT REVOKED |
|
REG | Reference to a national code |
Ref country code: FI Ref legal event code: MGE |
|
27W | Patent revoked |
Effective date: 20200701 |
|
GBPR | Gb: patent revoked under art. 102 of the ep convention designating the uk as contracting state |
Effective date: 20200701 |