EP2020451A1 - Verfahren zur Herstellung von Stahlblechen mit hoher Widerstandsfähigkeit und Duktilität und damit hergestellte Bleche - Google Patents
Verfahren zur Herstellung von Stahlblechen mit hoher Widerstandsfähigkeit und Duktilität und damit hergestellte Bleche Download PDFInfo
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- EP2020451A1 EP2020451A1 EP07290908A EP07290908A EP2020451A1 EP 2020451 A1 EP2020451 A1 EP 2020451A1 EP 07290908 A EP07290908 A EP 07290908A EP 07290908 A EP07290908 A EP 07290908A EP 2020451 A1 EP2020451 A1 EP 2020451A1
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
- C23C2/0224—Two or more thermal pretreatments
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
- C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
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- 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
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- 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
- C23C2/12—Aluminium or alloys based thereon
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- 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
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12736—Al-base component
- Y10T428/1275—Next to Group VIII or IB metal-base component
- Y10T428/12757—Fe
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
- Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
- Y10T428/00—Stock material or miscellaneous articles
- Y10T428/12—All metal or with adjacent metals
- Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
- Y10T428/12771—Transition metal-base component
- Y10T428/12785—Group IIB metal-base component
- Y10T428/12792—Zn-base component
- Y10T428/12799—Next to Fe-base component [e.g., galvanized]
Definitions
- the invention relates to the manufacture of hot rolled sheets of so-called "multiphase" steels, simultaneously having a very high strength and a deformation capacity for carrying out cold forming operations.
- the invention more specifically relates to predominantly bainitic microstructure steels having a strength greater than 800 MPa and an elongation rate greater than 10% rupture.
- the automotive industry is in particular a preferred field of application for these hot-rolled steel sheets.
- TRIP Transform Induced Plasticity
- the present invention aims to solve the problems mentioned above. It aims to provide a hot-rolled steel having a mechanical strength greater than 800 MPa together with an elongation rate greater than 10% rupture, both in long direction and in cross-direction relative to rolling.
- the invention also aims at providing a steel that is not very sensitive to damage during cutting by a mechanical method.
- the invention also aims to provide a method of manufacturing a steel in the uncoated, electrogalvanized or galvanized state. This therefore requires that the mechanical characteristics of this steel are insensitive to the thermal cycles associated with dipping zinc coating processes.
- composition of the steel preferably comprises the content being expressed by weight: 0.050% ⁇ C ⁇ 0.070%
- the composition comprises, the content being expressed by weight: 0.070% ⁇ C ⁇ 0.090%
- the composition comprises: 1.4% ⁇ Mn ⁇ 1.8%.
- the composition comprises: 0.020% ⁇ Al ⁇ 0.040%.
- the composition of the steel preferably comprises: 0.12% ⁇ V ⁇ 0.16%. In a preferred embodiment, the composition of the steel comprises 0.18% ⁇ Mo ⁇ 0.30%.
- the composition comprises: Nb ⁇ 0.005%
- the composition comprises: 0.20% ⁇ Cr ⁇ 0.45%
- the microstructure of the steel preferably comprises, as a surface fraction, at least 80% of higher bainite, the optional complement being constituted by lower bainite, martensite and residual austenite, the sum of the martensite and residual austenite contents being lower. at 5%.
- the invention also relates to a beam welded assembly with high energy density made from a steel sheet according to one of the above modes.
- the subject of the invention is also a process for manufacturing a hot-rolled steel sheet with a resistance greater than 800 MPa and an elongation at break of greater than 10%, according to which a steel of the above composition is supplied, a semi-finished product is poured at a temperature above 1150 ° C.
- the semi-finished product is hot rolled to a temperature T FL in a temperature range where the microstructure of the steel is entirely austenitic so as to obtain a sheet.
- This is then cooled to a cooling rate V R of 75 and 200 ° C./s, then the sheet is reeled at a temperature T bob of between 500 and 600 ° C.
- the end of rolling temperature T FL is between 870 and 930 ° C.
- the cooling rate V R is between 80 and 150 ° C / s.
- the sheet is pickled, then optionally skin-passed, and then coated with zinc or zinc alloy.
- the coating is made by dipping.
- the invention also relates to the use of a hot-rolled steel sheet according to one of the above modes, or manufactured by a method according to one of the above modes for the manufacture of parts of structure or reinforcement elements, in the automotive field.
- carbon plays an important role in the formation of the microstructure and in the mechanical properties.
- the carbon content is between 0.050 and 0.090% by weight: Below 0.050%, sufficient strength can not be obtained. Beyond 0.090%, the microstructure formed consists mainly of lower bainite, this structure being characterized by the presence of carbides precipitated within the slats of bainitic ferrite: the resistance thus obtained is high, but the elongation is then significantly reduced. it.
- the carbon content is between 0.050 and 0.070%.
- figure 1 illustrates the influence of carbon content on the long-term elongation of LASER beam splicing welds: A particularly high elongation at break of 17-23% is associated with a carbon content of 0.050 at 0.070%.
- the carbon content is greater than 0.070% and less than or equal to 0.090%: even if this range does not lead to such a high ductility, the elongation at break of the LASER welds is greater than 15%, and remains comparable to that of the base steel sheet.
- manganese increases the quenchability and avoids the formation of ferrite cooling after rolling.
- Manganese also helps to deoxidize steel during liquid phase processing.
- the addition of manganese also contributes to effective solid solution hardening and increased strength.
- the manganese is between 1.4 and 1.8%: thus forming a completely bainitic structure without risk of appearance of harmful band structure.
- aluminum is an effective element for the deoxidation of steel. This efficiency is obtained in a particularly economical and stable manner when the aluminum content is between 0.020 and 0.040%.
- silicon contributes to liquid phase deoxidation and hardening in solid solution.
- An addition of silicon above 0.3% causes the formation of strongly adherent oxides and the possible appearance of surface defects, due in particular to a lack of wettability in dip galvanizing operations.
- molybdenum retards bainitic transformation during cooling after rolling, contributes to hardening by solid solution and refines the size of bainitic slats.
- the molybdenum content is less than or equal to 0.40% to prevent excessive formation of quenching structures. This limited molybdenum content also makes it possible to lower the manufacturing cost.
- the molybdenum content is greater than or equal to 0.18% and less than or equal to 0.30%. In this way, the level is ideally adjusted to avoid the formation of ferrite or perlite in the steel sheet on the cooling table after hot rolling.
- Phosphorus is a known element to segregate at grain boundaries. Its content must be limited to 0.025% in order to maintain sufficient hot ductility.
- the composition may comprise chromium in an amount of less than or equal to 0.45%. Thanks to the other elements of the composition and to the process according to the invention, its presence is however not absolutely necessary, which has the advantage of avoiding expensive additions.
- the steel contains less than 0.005% Ti and less than 0.020% Nb.
- these elements fix too much nitrogen in the form of nitrides or carbonitrides. There is not enough nitrogen available to precipitate with vanadium. In addition, excessive precipitation of niobium would increase the hot hardness and would not easily allow the realization of thin-rolled hot-rolled sheets.
- the niobium content is less than 0.005%
- Vanadium is an important element according to the invention: the steel contains a vanadium content of between 0.12 and 0.22%. Compared to a vanadium-free steel, the increase in strength due to a hardening precipitation of carbonitrides can be up to 300 MPa. Below 0.12%, there is no significant effect on the mechanical tensile characteristics. Beyond 0.22% vanadium, under the conditions of manufacture according to the invention, a saturation of the effect on the mechanical characteristics is noted. A content of less than 0.22% thus makes it possible to obtain high mechanical characteristics in a very economical manner with respect to steels which contain higher levels of vanadium.
- microstructure refinement and structural hardening are particularly effective.
- the nitrogen content is greater than or equal to 0.003% in order to obtain a precipitation of vanadium carbonitrides in a sufficient quantity.
- the nitrogen content is less than or equal to 0.009% to avoid the presence of solid solution nitrogen or the formation of larger carbonitrides, which would reduce ductility.
- the rest of the composition consists of unavoidable impurities resulting from the preparation, such as for example Sb, Sn, As.
- microstructural percentages above are surface fractions that can be measured on polished and etched sections.
- the microstructure therefore has no primary or proeutectoid ferrite: it then has a great homogeneity since the property gap Mechanics between the matrix (upper bainite) and the other possible constituents (lower bainite and martensite) is weak. During a mechanical stress, the deformations are distributed homogeneously. Dislocation accumulation does not occur at the interfaces between the constituents and premature damage is avoided, contrary to what can be noted in structures with a significant amount of primary ferrite, a phase whose flow limit is very low. , or martensite with a very high level of resistance. In this way, the steel according to the invention has a particular aptitude for certain demanding deformation modes such as the expansion of holes, the mechanical stress of cut edges, the folding.
- the cast semifinished products are first brought to a temperature higher than 1150 ° C. to reach at any point a temperature favorable to the high deformations which the steel will undergo during rolling.
- the hot rolling step of these semi-finished products starting at more than 1150 ° C. can be done directly after casting so well. that an intermediate heating step is not necessary in this case.
- the semi-finished product is hot-rolled in a temperature range where the structure of the steel is totally austenitic up to an end-of-rolling temperature T FL .
- the temperature T FL is preferably between 870 and 930 ° C to obtain a grain size adapted to the bainitic transformation that follows.
- Cooling is then carried out at a speed V R of between 75 and 200 ° C / s: a minimum speed of 75 ° C / s prevents the formation of proeutectoid ferrite and perlite, while a speed V R of 200 ° C / s or less prevents formation excessive martensite.
- the speed V R is between 80 and 150 ° C / s:
- a minimum speed of 80 ° C / s leads to the formation of upper bainite with a very small slat size, associated with excellent mechanical properties.
- a speed of less than 150 ° C / s makes it possible to avoid, for the most part, the formation of martensite.
- the sheet can be used in the bare state or coated. Depending on the use envisaged, the sheet is scoured after rolling according to a method known per se, so as to obtain a surface state suitable for promoting the implementation of the subsequent coating.
- the sheet may be subjected to a slight cold deformation, usually less than 1% ("skin-pass").
- the sheet is then coated with zinc or aluminum. an alloy based on zinc, for example by electrogalvanizing or dip galvanizing.
- electrogalvanizing or dip galvanizing it has been demonstrated that the particular microstructure of the steel, composed mainly of higher bainite, is not very sensitive to the thermal conditions of the subsequent galvanizing treatment, so that the mechanical characteristics of the sheets coated with dipping have a high great stability even in case of untimely fluctuation of these conditions.
- the sheet in the galvanized state therefore has mechanical characteristics very similar to those in the naked state.
- the microstructure of steel I1 illustrated in figure 2 comprises more than 80% higher bainite, the remainder being lower bainite and MA compounds.
- the total content of martensite and residual austenite is less than 5%.
- the size of the old austenitic grains and bainitic batten bundles is about 10 microns.
- the limitation of the size of the batten packets and the strong disorientation between the adjacent packets results in a high resistance to the propagation of any microcracks. Due to the small difference in hardness between the various constituents of the microstructure, the steel is not very sensitive to damage during cutting by a mechanical process.
- Steel R1 with too high a carbon content and a too low vanadium content, has insufficient breaking elongation.
- Steel R2 has a carbon content and phosphorus too high, its winding temperature is also too low. As a result, its elongation at break is also significantly less than 10%.
- LASER autogenous welded joints were made under the following conditions: power: 4.5kW, welding speed: 2.5m / min.
- the lengthwise elongation of the LASER welds of I-1 steel is 17%, whereas it is 10 and 13% respectively for the R-1 and R-2 steels. These values lead, particularly for steel R1, to difficulties in stamping welded joints.
- Steel sheets I1 according to the invention were also galvanized under the following conditions: after heating at 680 ° C., the sheets were cooled to 455 ° C. and then quenched in a Zn bath at this temperature and finally cooled. at room temperature.
- the invention allows the manufacture of steels bainitic matrix steels without excessive addition of expensive elements. These combine high strength and high ductility.
- the steel sheets according to the invention are used profitably for the manufacture of structural parts or reinforcement elements in the automotive field and general industry.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
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- Crystallography & Structural Chemistry (AREA)
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- Heat Treatment Of Steel (AREA)
Priority Applications (23)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP07290908A EP2020451A1 (de) | 2007-07-19 | 2007-07-19 | Verfahren zur Herstellung von Stahlblechen mit hoher Widerstandsfähigkeit und Duktilität und damit hergestellte Bleche |
US12/669,188 US20100221573A1 (en) | 2007-07-19 | 2008-07-09 | Process for manufacturing steel sheet having high tensile strength and ductility characteristics, and sheet thus produced |
RU2010105699/02A RU2451764C2 (ru) | 2007-07-19 | 2008-07-09 | Способ изготовления стальных листов с высокими характеристиками прочности и пластичности и листы, изготовленные при помощи этого способа |
KR1020147007669A KR20140044407A (ko) | 2007-07-19 | 2008-07-09 | 높은 인장강도 및 연성을 갖는 강판의 제조 공정, 및 이렇게 제조된 판 |
JP2010516534A JP5298127B2 (ja) | 2007-07-19 | 2008-07-09 | 高抵抗特性および延性特性を有する鋼板を製造する方法およびこのようにして得られた鋼板 |
CN2008801040865A CN101784688B (zh) | 2007-07-19 | 2008-07-09 | 具有高拉伸强度和延展特性的钢片材的制造方法以及由此获得的片材 |
CA2694069A CA2694069C (fr) | 2007-07-19 | 2008-07-09 | Procede de fabrication de toles d'acier a hautes caracteristiques de resistance et de ductilite, et toles ainsi produites |
KR1020127034336A KR20130010030A (ko) | 2007-07-19 | 2008-07-09 | 높은 인장강도 및 연성을 갖는 강판의 제조 공정, 및 이렇게 제조된 판 |
BRPI0814514A BRPI0814514B1 (pt) | 2007-07-19 | 2008-07-09 | chapa ou peça de aço, conjunto soldado, processo para a produção de uma chapa de aço, processo para produção de uma peça e uso de uma chapa de aço |
PCT/FR2008/000993 WO2009034250A1 (fr) | 2007-07-19 | 2008-07-09 | Procede de fabrication de tôles d'acier a hautes caracteristiques de resistance et de ductilite, et tôles ainsi produites |
KR1020157029946A KR20150123957A (ko) | 2007-07-19 | 2008-07-09 | 높은 인장강도 및 연성을 갖는 강판의 제조 공정, 및 이렇게 제조된 판 |
KR1020187002754A KR101892423B1 (ko) | 2007-07-19 | 2008-07-09 | 높은 인장강도 및 연성을 갖는 강판의 제조 공정, 및 이렇게 제조된 판 |
AT08830766T ATE534756T1 (de) | 2007-07-19 | 2008-07-09 | Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche |
ES08830766T ES2375429T3 (es) | 2007-07-19 | 2008-07-09 | Procedimiento de fabricación de chapas de acero con elevadas caracter�?sticas de resistencia y de ductilidad, y chapas as�? producidas. |
UAA201001690A UA98798C2 (ru) | 2007-07-19 | 2008-07-09 | Горячекатанный стальной лист или ДЕТАЛЬ, СПОСОБ ИХ ИЗГОТОВЛЕНИя И ПРИМЕНЕНИЕ, Сварные соединения из стальных листов ИЛИ ДЕТАЛИ |
KR1020107003457A KR20100037147A (ko) | 2007-07-19 | 2008-07-09 | 높은 인장강도 및 연성을 갖는 강판의 제조 공정, 및 이렇게 제조된 판 |
EP08830766A EP2171112B1 (de) | 2007-07-19 | 2008-07-09 | Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche |
PL08830766T PL2171112T3 (pl) | 2007-07-19 | 2008-07-09 | Sposób wytwarzania blach stalowych o dobrych własnościach wytrzymałościowych i plastycznych oraz blachy tak wytworzone |
ARP080103095A AR067594A1 (es) | 2007-07-19 | 2008-07-18 | Lamina de acero laminada en caliente y procedimiento para la fabricacion de la lamina de acero. |
ZA201000290A ZA201000290B (en) | 2007-07-19 | 2010-01-15 | Process for manufacturing steel sheet having high tensile strength and ductility characteristics, and sheet thus produced |
MA32523A MA31525B1 (fr) | 2007-07-19 | 2010-01-18 | Procede de fabrication de toles d'acier à hautes caractéristiques de résistance et de ductilité, et toles ainsi produites |
US14/575,475 US10214792B2 (en) | 2007-07-19 | 2014-12-18 | Process for manufacturing steel sheet |
US15/879,944 US10428400B2 (en) | 2007-07-19 | 2018-01-25 | Steel sheet having high tensile strength and ductility |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP07290908A EP2020451A1 (de) | 2007-07-19 | 2007-07-19 | Verfahren zur Herstellung von Stahlblechen mit hoher Widerstandsfähigkeit und Duktilität und damit hergestellte Bleche |
Publications (1)
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EP2020451A1 true EP2020451A1 (de) | 2009-02-04 |
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Family Applications (2)
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EP07290908A Withdrawn EP2020451A1 (de) | 2007-07-19 | 2007-07-19 | Verfahren zur Herstellung von Stahlblechen mit hoher Widerstandsfähigkeit und Duktilität und damit hergestellte Bleche |
EP08830766A Active EP2171112B1 (de) | 2007-07-19 | 2008-07-09 | Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche |
Family Applications After (1)
Application Number | Title | Priority Date | Filing Date |
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EP08830766A Active EP2171112B1 (de) | 2007-07-19 | 2008-07-09 | Verfahren zur herstellung eines stahlblechs mit sehr hohen festigkeits- und biegbarkeitseigenschaften und in diesem verfahren hergestellte bleche |
Country Status (16)
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US (3) | US20100221573A1 (de) |
EP (2) | EP2020451A1 (de) |
JP (1) | JP5298127B2 (de) |
KR (5) | KR20150123957A (de) |
CN (1) | CN101784688B (de) |
AR (1) | AR067594A1 (de) |
AT (1) | ATE534756T1 (de) |
BR (1) | BRPI0814514B1 (de) |
CA (1) | CA2694069C (de) |
ES (1) | ES2375429T3 (de) |
MA (1) | MA31525B1 (de) |
PL (1) | PL2171112T3 (de) |
RU (1) | RU2451764C2 (de) |
UA (1) | UA98798C2 (de) |
WO (1) | WO2009034250A1 (de) |
ZA (1) | ZA201000290B (de) |
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CN101509102B (zh) * | 2009-03-27 | 2011-01-05 | 攀钢集团研究院有限公司 | 热轧低碳冲压用钢及其生产方法 |
WO2012127125A1 (fr) | 2011-03-24 | 2012-09-27 | Arcelormittal Investigatión Y Desarrollo Sl | Tôle d'acier laminée à chaud et procédé de fabrication associé |
WO2016005780A1 (fr) | 2014-07-11 | 2016-01-14 | Arcelormittal Investigación Y Desarrollo Sl | Tôle d'acier laminée à chaud et procédé de fabrication associé |
WO2017012958A1 (de) * | 2015-07-17 | 2017-01-26 | Salzgitter Flachstahl Gmbh | Verfahren zum herstellen eines warmbandes aus einem bainitischen mehrphasenstahl mit einer zn-mg-al-beschichtung und ein entsprechendes warmband |
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- 2008-07-09 RU RU2010105699/02A patent/RU2451764C2/ru active
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- 2008-07-09 JP JP2010516534A patent/JP5298127B2/ja active Active
- 2008-07-09 AT AT08830766T patent/ATE534756T1/de active
- 2008-07-09 KR KR1020147007669A patent/KR20140044407A/ko not_active Application Discontinuation
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- 2008-07-09 WO PCT/FR2008/000993 patent/WO2009034250A1/fr active Application Filing
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Cited By (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN101509102B (zh) * | 2009-03-27 | 2011-01-05 | 攀钢集团研究院有限公司 | 热轧低碳冲压用钢及其生产方法 |
WO2012127125A1 (fr) | 2011-03-24 | 2012-09-27 | Arcelormittal Investigatión Y Desarrollo Sl | Tôle d'acier laminée à chaud et procédé de fabrication associé |
WO2012127136A2 (fr) | 2011-03-24 | 2012-09-27 | Arcelormittal Investigación Y Desarrollo Sl | Tôle d'acier laminée à chaud et procédé de fabrication associé |
RU2551727C2 (ru) * | 2011-03-24 | 2015-05-27 | Арселормитталь Инвестигасьон И Десарролло Сл | Горячекатаный стальной лист и соответствующий способ изготовления |
US9540719B2 (en) | 2011-03-24 | 2017-01-10 | Arcelormittal Investigacion Y Desarrollo Sl | Hot-rolled steel sheet and associated production method |
WO2016005780A1 (fr) | 2014-07-11 | 2016-01-14 | Arcelormittal Investigación Y Desarrollo Sl | Tôle d'acier laminée à chaud et procédé de fabrication associé |
WO2016005811A1 (fr) | 2014-07-11 | 2016-01-14 | Arcelormittal | Tôle d'acier laminée à chaud et procédé de fabrication associé |
US10858716B2 (en) | 2014-07-11 | 2020-12-08 | Arcelormittal | Hot rolled steel sheet and associated manufacturing method |
US11447844B2 (en) | 2014-07-11 | 2022-09-20 | Arcelormittal | Manufacturing method for hot rolled steel sheet |
WO2017012958A1 (de) * | 2015-07-17 | 2017-01-26 | Salzgitter Flachstahl Gmbh | Verfahren zum herstellen eines warmbandes aus einem bainitischen mehrphasenstahl mit einer zn-mg-al-beschichtung und ein entsprechendes warmband |
EP3325684B1 (de) | 2015-07-17 | 2020-03-04 | Salzgitter Flachstahl GmbH | Verfahren zum herstellen eines warmbandes aus einem bainitischen mehrphasenstahl mit einer zn-mg-al-beschichtung und ein entsprechendes warmband |
US11512364B2 (en) | 2015-07-17 | 2022-11-29 | Salzgitter Flachstahl Gmbh | Method for producing a hot strip of a bainitic multi-phase steel having a Zn—Mg—Al coating, and a corresponding hot strip |
Also Published As
Publication number | Publication date |
---|---|
US20180148806A1 (en) | 2018-05-31 |
ATE534756T1 (de) | 2011-12-15 |
KR101892423B1 (ko) | 2018-08-27 |
WO2009034250A1 (fr) | 2009-03-19 |
US10214792B2 (en) | 2019-02-26 |
KR20180014843A (ko) | 2018-02-09 |
US20150203932A1 (en) | 2015-07-23 |
US10428400B2 (en) | 2019-10-01 |
PL2171112T3 (pl) | 2012-04-30 |
CN101784688B (zh) | 2011-11-23 |
UA98798C2 (ru) | 2012-06-25 |
EP2171112B1 (de) | 2011-11-23 |
RU2451764C2 (ru) | 2012-05-27 |
KR20130010030A (ko) | 2013-01-24 |
MA31525B1 (fr) | 2010-07-01 |
KR20140044407A (ko) | 2014-04-14 |
ZA201000290B (en) | 2010-10-27 |
CN101784688A (zh) | 2010-07-21 |
JP5298127B2 (ja) | 2013-09-25 |
US20100221573A1 (en) | 2010-09-02 |
KR20150123957A (ko) | 2015-11-04 |
EP2171112A1 (de) | 2010-04-07 |
CA2694069A1 (fr) | 2009-03-19 |
BRPI0814514B1 (pt) | 2019-09-03 |
ES2375429T3 (es) | 2012-02-29 |
BRPI0814514A2 (pt) | 2015-02-03 |
CA2694069C (fr) | 2013-05-21 |
US20180163282A9 (en) | 2018-06-14 |
AR067594A1 (es) | 2009-10-14 |
JP2010533791A (ja) | 2010-10-28 |
KR20100037147A (ko) | 2010-04-08 |
RU2010105699A (ru) | 2011-08-27 |
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