EP3027784B1 - Acier multiphase à haute résistance, micro-allié et contenant du silicium, présentant une résistance minimale à la traction de 750 mpa et des propriétés améliorées et procédé de fabrication d'une bande à partir de cet acier - Google Patents

Acier multiphase à haute résistance, micro-allié et contenant du silicium, présentant une résistance minimale à la traction de 750 mpa et des propriétés améliorées et procédé de fabrication d'une bande à partir de cet acier Download PDF

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Publication number
EP3027784B1
EP3027784B1 EP14741788.5A EP14741788A EP3027784B1 EP 3027784 B1 EP3027784 B1 EP 3027784B1 EP 14741788 A EP14741788 A EP 14741788A EP 3027784 B1 EP3027784 B1 EP 3027784B1
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Prior art keywords
steel
strip
hot
content
mpa
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German (de)
English (en)
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EP3027784A2 (fr
Inventor
Thomas Schulz
Marion CALCAGNOTTO
Sascha KLUGE
Sebastian WESTHÄUSER
Tobias KLINKBERG
Thorsten MICHAELIS
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Salzgitter Flachstahl GmbH
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Salzgitter Flachstahl GmbH
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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
    • 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
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
    • C21D1/76—Adjusting the composition of the atmosphere
    • 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
    • C21D1/84—Controlled slow cooling
    • C—CHEMISTRY; METALLURGY
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • C—CHEMISTRY; METALLURGY
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • 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
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    • 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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    • 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
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    • 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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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0273—Final recrystallisation annealing
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
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    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/573—Continuous furnaces for strip or wire with cooling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
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    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
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    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
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    • 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
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    • 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
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    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
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    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
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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
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    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
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    • 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 high-strength multiphase steel according to the preamble of claim 1.
  • the invention relates to a method for producing a hot and / or cold-rolled strip from such a steel according to claim 13.
  • the invention relates to steels having a tensile strength in the range of at least 750 MPa to at most 920 MPa with low maximum yield ratios of 73% for the production of components that have excellent formability and welding properties, such as weld failure.
  • the highly competitive automotive market is constantly forcing manufacturers to seek solutions to reduce fleet consumption while maintaining maximum comfort and occupant safety.
  • the weight saving of all vehicle components plays a decisive role, but on the other hand also the most favorable possible behavior of the individual components with high static and dynamic stress during operation as well as in the event of a crash.
  • the suppliers of raw material suppliers are trying to meet this need by reducing the weight of the vehicles by providing high-strength to highest-strength steels and reducing the sheet thickness, while at the same time improving forming and component behavior during production and operation.
  • High-strength to ultrahigh-strength steels enable lighter vehicle components, resulting in lower fuel consumption and lower environmental impact due to the reduced CO 2 emissions.
  • These steels must therefore meet comparatively high requirements in terms of their strength and ductility, energy absorption and in their processing, such as stamping, hot and cold forming, welding and / or a surface treatment, e.g. a metallic finish, organic coating, or paint, are sufficient.
  • Newly developed steels must therefore meet the required weight reduction, the increasing material requirements for yield strength, tensile strength, hardening behavior and elongation at break with good formability, as well as the component requirements for high toughness, edge crack resistance, energy absorption and hardenability and the bake hardening effect but also improved Joining suitability in the form of z.
  • Improved edge crack resistance means an increased formability of the sheet edges and can be described for example by an increased Lochetzweitmaschine. This fact is known under the synonyms “Low Edge Crack” (LEC) and “High Hole Expansion” (HHE).
  • LEC Low Edge Crack
  • HHE High Hole Expansion
  • the purpose of the steel according to the invention is also to reduce the thickness of micro-alloyed ferritic steels already used in the automotive industry in terms of component, in order to save weight.
  • the group of multiphase steels is increasingly used, this includes, for. As complex phase steels, ferritic-bainitic steels, TRIP steels, and the previously described dual-phase steels, which are characterized by different structural compositions.
  • Ferritic-bainitic steels are according to EN 10346 steels containing bainite or solidified bainite in a matrix of ferrite and / or solidified ferrite.
  • the strength of the matrix will caused by a high dislocation density, by grain refining and the elimination of micro-alloying elements.
  • Dual- phase steels are, according to EN 10346, steels with a ferritic basic structure in which a martensitic second phase is insular, possibly also with fractions of bainite as a second phase. At high tensile strength, dual phase steels exhibit a low yield ratio and high work hardening.
  • TRIP steels are steels with a predominantly ferritic basic structure, in which bainite and retained austenite are embedded, which can convert to martensite during the transformation (TRIP effect). Because of its high work hardening, the steel achieves high levels of uniform elongation and tensile strength.
  • the high-strength steels with a single-phase structure include, for. B. bainitic and martensitic steels.
  • Bainitic steels are according to EN 10346 steels, which are characterized by a very high yield strength and tensile strength at a sufficiently high elongation for cold forming processes. Due to the chemical composition a good weldability is given.
  • the microstructure typically consists of bainite. Occasionally, small amounts of other phases, such as martensite and ferrite, may be included.
  • Martensitic steels are, according to EN 10346, steels which contain small amounts of ferrite and / or bainite in a matrix of martensite due to thermomechanical rolling. This steel grade is characterized by a very high yield strength and tensile strength at a sufficiently high elongation for cold forming processes. Within the group of multiphase steels, the martensitic steels have the highest tensile strength values.
  • thermoforming is limited.
  • the martensitic steels are mainly suitable for bending forming processes, such as roll forming.
  • high strength steels are, inter alia, in structural, chassis and crash-relevant components, as sheet metal plates, tailored blanks (welded blanks) and cold rolled as flexible bands, so-called TRB ® 's or tailored strips.
  • T Ailor R olled B lank lightweight technology allows a significant weight reduction through a load-adapted material thickness over the length of the component and / or of steel.
  • a special heat treatment for defined microstructure adjustment takes place where z. B. by comparatively soft ingredients such as ferrite or bainitic ferrite, the steel its low yield strength and its hard constituents, such as martensite or carbon-rich bainite, maintains its strength.
  • cold-rolled high-strength to ultra-high-strength steel strips are annealed by recrystallization in a continuous annealing process to produce a readily shapeable thin sheet for economic reasons.
  • the process parameters such as throughput speed, annealing temperatures and cooling rate (cooling gradient), are set according to the required mechanical and technological properties with the necessary structure.
  • the pickled hot strip is heated in typical thicknesses of 1.50 to 4.00 mm or cold strip in typical thicknesses of 0.50 to 3.00 mm in a continuous annealing furnace to a temperature such that during recrystallization and cooling the required structure education sets.
  • a temperature such that during recrystallization and cooling the required structure education sets.
  • Constant temperature is difficult to achieve, especially with different thicknesses in the transition region from one band to the other band. This can lead to alloy compositions with too small process windows in the continuous annealing that z. B. the thinner strip is either driven too slowly through the oven, whereby the productivity is lowered, or that the thicker strip is driven too fast through the oven and the necessary annealing temperatures and cooling gradients to achieve the desired structure can not be achieved. The consequences are increased rejects.
  • Expanded process windows are necessary so that the required strip properties are possible with the same process parameters even with larger cross-sectional changes of the strips to be annealed.
  • TRB ® s with multi-phase structure is not without additional effort, such as with today's known alloys and available continuous annealing plants for widely varying thicknesses.
  • a homogeneous multi-phase microstructure in cold- as well as hot-rolled steel strips can be adjusted due to a temperature gradient occurring in the usual alloy-specific narrow process windows.
  • a method for producing a steel strip with different thickness over the strip length is z. B. in the DE 100 37 867 A1 described.
  • a DP steel for vehicle construction is also in the EP 1 548 142 disclosed.
  • the annealing treatment is usually carried out in a continuous annealing furnace upstream of the galvanizing bath.
  • the required microstructure is occasionally adjusted depending on the alloy concept only during the annealing treatment in the continuous furnace in order to realize the required mechanical properties.
  • Crucial process parameters are thus the setting of the annealing temperatures and the speed, as well as the cooling rate (cooling gradient) in the continuous annealing, since the phase transformation takes place temperature- and time-dependent.
  • the goal of achieving the resulting mechanical and technological properties in a narrow range over bandwidth and strip length through the controlled adjustment of the volume fractions of the structural components has top priority and is therefore only possible through an enlarged process window.
  • the known alloy concepts for multiphase steels are characterized by too narrow a process window and therefore unsuitable for solving the present problem, in particular in flexibly rolled strips.
  • At present, only steels of a strength class with defined cross-sectional areas (strip thickness and strip width) can be represented with the known alloy concepts, so that altered alloy concepts are necessary for different strength classes and / or cross-sectional areas.
  • the state of the art is that an increase in strength is achieved by the quantitative increase of carbon and / or silicon and / or manganese (solid solution hardening) and an increase in the strength via the microstructure settings with adapted temperature control.
  • the ISO 16630 hole expansion test is one of several possible test methods.
  • Silicon plays a subordinate role in the calculation of the carbon equivalent. This is crucial in relation to the invention.
  • the lowering of the carbon equivalent through lower contents of carbon and above all manganese should be compensated by increasing the silicon content. Thus, with the same strengths, the edge crack resistance and the weldability are improved.
  • a low yield ratio (Re / Rm) of less than 65 is typical of a dual phase steel and is particularly useful in stretch and draw formability. It gives the designer information about the distance between the onset of plastic deformation and the failure of the material under quasi-static loading. Accordingly, lower yield ratio ratios provide a greater safety margin to component failure.
  • a higher yield ratio (Re / Rm) of over 65 is also distinguished by resistance to edge cracks. This can be attributed to the smaller differences in the strengths of the individual microstructural constituents and the finer structure lead back, which has a favorable effect on a homogeneous deformation in the region of the cutting edge.
  • the analytical landscape for achieving multiphase steels with minimum tensile strengths of 750 MPa is very diverse and shows very large alloy ranges in the strength-enhancing elements carbon, silicon, manganese, phosphorus, aluminum and chromium and / or molybdenum, as well as in the addition of microalloys, such as titanium , Niobium, vanadium and / or boron, as well as in the material-characterizing properties.
  • the range of dimensions is wide and lies in the thickness range of about 0.50 to 4.00 mm.
  • the invention is therefore based on the object to provide a new alloy concept for a high-strength multiphase steel with a minimum tensile strength of 750 to 920 MPa longitudinal and transverse to the rolling direction, preferably with a dual-phase structure and a yield ratio of at most 73%, with the process window for the Continuous annealing of hot or cold strips can be extended so that in addition to bands with different cross sections and steel bands with tape length and possibly bandwidth varying thickness, and thus correspondingly varying degrees Kaltabwalzgraden, can be produced with the most homogeneous mechanical and technological properties.
  • the H relied (hot dip galvanizing) of the steel is to be ensured and a method for producing a produced from this steel strip can be specified.
  • this object is achieved by a steel with the following contents in% by weight: C ⁇ 0.075 to ⁇ 0.105 Si ⁇ 0.600 to ⁇ 0.800 Mn ⁇ 1.000 to ⁇ 1.90 Cr ⁇ 0.100 to ⁇ 0.700 al ⁇ 0.010 to ⁇ 0.060 N ⁇ 0.0020 to ⁇ 0.0120 S ⁇ 0.0030 Nb ⁇ 0.005 to ⁇ 0.050 Ti ⁇ 0.005 to ⁇ 0.050 B ⁇ 0.0005 to ⁇ 0.0040 Not a word ⁇ 0.200 Cu ⁇ 0.040% Ni ⁇ 0.040%
  • the steel according to the invention is very well suited for hot-dip finishing and has a significantly enlarged process window in comparison to the known steels. This results in increased process reliability in the continuous annealing of cold and hot strip with dual or multi-phase structure. Therefore, for pass-annealed hot or cold strips, more homogeneous mechanical-technological properties in the strip can be set even with different cross-sections and otherwise identical process parameters.
  • processing in selected thickness ranges is possible (e.g., less than 1.00 mm tape thickness, 1.00 mm to 2.00 mm tape thickness, and 2.00 mm to 4.00 mm tape thickness).
  • stress-optimized components can be produced by forming technology.
  • the material produced can be produced both as a cold strip and as a hot strip and as a cold-rolled hot strip via a hot-dip galvanizing line or a pure continuous annealing plant, in the dressed and undressed, in the ironing-stretched and non-stretch-bending and also in the heat-treated (over-aged) state.
  • steel strips can be produced by an intercritical annealing between A c1 and A c3 or at an austenitizing annealing over A c3 with final controlled cooling, which leads to a dual or multi-phase structure.
  • Annealing temperatures of about 700 to 950 ° C have proved to be advantageous. Depending on the overall process, there are different approaches to realize the heat treatment.
  • the strip is cooled starting from the annealing temperature at a cooling rate of about 15 to 100 ° C / s to an intermediate temperature of about 160 to 250 ° C.
  • a cooling rate of about 15 to 100 ° C / s to an intermediate temperature of about 160 to 250 ° C.
  • the cooling to room temperature is finally carried out at a cooling rate of about 2 to 30 ° C / s (variant 1, FIG. 6a ).
  • the second variant of the temperature control in the hot dip finishing includes holding the temperature for about 1 to 20 seconds at the intermediate temperature of about 200 to 350 ° C and then reheating to the temperature required for hot dipping refinement of about 400 to 470 ° C.
  • the strip is cooled after refining to about 200 to 250 ° C.
  • the cooling to room temperature takes place again at a cooling rate of about 2 to 30 ° C / s (variant 3, FIG. 6c ).
  • Material characteristic is also that the addition of manganese with increasing weight percent of the ferrite is shifted to longer times and lower temperatures during cooling. Depending on the process parameters, the proportions of ferrite are more or less reduced by increased amounts of bainite.
  • the carbon equivalent can be reduced, thereby improving weldability and avoiding excessive weld hardening. In resistance spot welding, moreover, the electrode life can be significantly increased.
  • the effect of the elements in the alloy according to the invention is described in more detail below.
  • the multiphase steels are typically chemically designed to combine alloying elements with and without micro-alloying elements.
  • Accompanying elements are unavoidable and are considered in the analysis concept with regard to their effect if necessary.
  • Hydrogen (H) can be the only element that can diffuse through the iron lattice without creating lattice strains. As a result, the hydrogen in the iron grid is relatively mobile and relatively easily absorbed during processing of the steel can be. Hydrogen can only be taken up in atomic (ionic) form in the iron lattice.
  • Hydrogen has a strong embrittlement and preferably diffuses to energy-favorable sites (defects, grain boundaries, etc.). In this case, defects act as hydrogen traps and can significantly increase the residence time of the hydrogen in the material.
  • the hydrogen content in the steel should be as low as possible.
  • Oxygen (O) In the molten state, the steel has a relatively high absorption capacity for gases, but at room temperature, oxygen is only soluble in very small quantities. Similar to hydrogen, oxygen can only diffuse into the material in atomic form. Due to the strong embrittling effect and the negative effects on the aging resistance, as much as possible is attempted during production to reduce the oxygen content.
  • the oxygen content in the steel should be as low as possible.
  • Phosphorus (P) is a trace element from iron ore and is dissolved in the iron lattice as a substitution atom . Phosphorus increases hardness by solid solution strengthening and improves hardenability.
  • the steel according to the invention differs from known analysis concepts which use phosphorus as a mixed crystal former (eg. EP 2 412 842 A1 or EP 2 128 295 A1 ), inter alia by the fact that phosphorus is not alloyed.
  • the phosphorus content is limited to unavoidable amounts in steelmaking.
  • sulfur is bound as a trace element in iron ore. It is undesirable in steel (except free-cutting steels), as it tends to segregate severely and has a strong embrittlement. It is therefore an attempt to achieve the lowest possible amounts of sulfur in the melt (eg by a vacuum treatment). Furthermore, the existing sulfur is converted by adding manganese into the relatively harmless compound manganese sulfide (MnS).
  • the manganese sulfides are often rolled in rows during the rolling process and act as nucleation sites for the transformation. This leads to a line-shaped structure, especially in the case of diffusion-controlled transformation, and can lead to impaired mechanical properties in the case of pronounced bristleness (for example pronounced martensite parts instead of distributed martensite islands, anisotropic material behavior, reduced elongation at break).
  • the sulfur content is limited to ⁇ 0.0030%, advantageously ⁇ 0.0020% or optimally ⁇ 0.0010% or amounts unavoidable in steelmaking.
  • Alloying elements are usually added to the steel in order to specifically influence certain properties.
  • An alloying element in different steels can influence different properties. The effect generally depends strongly on the amount and the solution state in the material.
  • Carbon (C) is considered the most important alloying element in steel. Through its targeted introduction of up to 2.06% iron is only steel. Often the carbon content is drastically lowered during steelmaking. In the case of dual-phase steels for continuous hot-dip refinement, its proportion according to EN 10346 or VDA 239-100 is a maximum of 0.230%; a minimum value is not specified.
  • the steel according to the invention contains carbon contents of less than 0.105%.
  • Carbon also forms carbides.
  • a representative occurring almost in every steel is the cementite (Fe 3 C).
  • significantly harder special carbides may form with other metals such as chromium, titanium, niobium, vanadium.
  • the minimum C content is set at 0.075% and the maximum C content at 0.105%.
  • Silicon (Si) binds oxygen during casting and is therefore used to calm the steel.
  • the Seigerungskostory is significantly lower than z.
  • Seigerept generally lead to a line arrangement of the structural components, which the forming properties, eg. As the hole widening worsen.
  • silicon causes strong solid solution hardening. Approximately, an addition of 0.1% silicon causes an increase in tensile strength of about 10 MPa, with up to 2.2% silicon, the elongation is only slightly deteriorated. Different sheet thicknesses and annealing temperatures were considered. The increase from 0.2% to 0.6% silicon caused an increase in strength of about 20 MPa in the yield strength and about 70 MPa in the tensile strength. The elongation at break only decreases by about 2%. The latter is partly due to the fact that silicon reduces the solubility of carbon in the ferrite, whereby the ferrite is softer, which in turn improves the formability. In addition, silicon prevents the formation of carbides, which reduce the ductility as brittle phases. Due to the low strength-increasing effect of silicon within the range of the steel according to the invention, the basis for a broad process window is created.
  • Another important effect is that silicon shifts the formation of ferrite to shorter times and temperatures, thus allowing the formation of sufficient ferrite before quenching. Hot rolling thereby provides a basis for improved cold rollability.
  • the accelerated ferrite formation enriches the austenite with carbon and thus stabilizes it. Because silicon the Carbide formation impeded, the austenite is additionally stabilized. Thus, the accelerated cooling can suppress the formation of bainite in favor of martensite.
  • silicon has an indirect positive effect on precipitation formation by microalloys, which in turn has a positive effect on the strength of the material. Since increasing the transition temperatures by silicon tends to favor grain coarsening, micro-alloying with niobium, titanium, and boron is particularly useful.
  • the atmospheric conditions during the annealing treatment in a continuous hot-dip coating system cause a reduction of iron oxide, which is present e.g. B. when cold rolling or as a result of storage at room temperature on the surface can form.
  • iron oxide which is present e.g. B. when cold rolling or as a result of storage at room temperature on the surface
  • oxygen-affinity alloy components such as silicon, manganese, chromium, boron
  • the gas atmosphere is oxidizing, with the result that segregation and selective oxidation of these elements can occur.
  • the selective oxidation can take place both externally, that is on the substrate surface, and internally within the metallic matrix.
  • the strip surface is free of scale residues, pickling or rolling oil or other dirt particles by a chemical-mechanical or thermal-hydro-mechanical pre-cleaning.
  • a chemical-mechanical or thermal-hydro-mechanical pre-cleaning In order to prevent silicon oxides from reaching the strip surface, further methods are to be taken which promote the internal oxidation of the alloying elements below the surface of the material. Depending on the system configuration, different measures are used here.
  • the internal oxidation of the alloying elements can be specifically influenced by adjusting the oxygen partial pressure of the furnace atmosphere (N 2 -H 2 protective gas atmosphere).
  • the set oxygen partial pressure must satisfy the following equation, with the furnace temperature between 700 and 950 ° C. - 12 > Log pO 2 ⁇ - 5 * Si - 0 . 25 - 3 * Mn - 0 . 5 - 0 . 1 * Cr - 0 . 5 - 7 * - INB 0 . 5
  • Si, Mn, Cr, B denote the corresponding alloying proportions in the steel in mass% and pO 2 the oxygen partial pressure in mbar.
  • the selective oxidation of the alloying elements can also be influenced by the gas atmospheres of the furnace areas.
  • the combustion reaction in the NOF can be used to adjust the oxygen partial pressure and thus the oxidation potential for iron and the alloying elements. This should be set so that the oxidation of the alloying elements takes place internally, below the steel surface and, if necessary, forms a thin iron oxide layer on the steel surface after passing through the NOF region. This is achieved z. For example, by reducing the CO value below 4%.
  • the optionally formed iron oxide layer is reduced under N 2 -H 2 protective gas atmosphere and likewise the internal oxidation of the alloying elements continues.
  • the set oxygen partial pressure in this furnace area must satisfy the following equation, with the furnace temperature between 700 and 950 ° C. - 18 > Log pO 2 ⁇ - 5 * Si - 0 . 3 - 2 . 2 * Mn - 0 . 45 - 0 . 1 * Cr - 0 . 4 - 12 . 5 * - INB 0 . 25
  • Si, Mn, Cr, B denote the corresponding alloying proportions in the steel in mass% and pO 2 the oxygen partial pressure in mbar.
  • the minimum Si content is set to 0.600% and the maximum silicon content to 0.800%.
  • Manganese (Mn) is added to almost all steels for desulfurization to convert the harmful sulfur into manganese sulphides.
  • manganese increases the strength of the ferrite by solid solution strengthening and shifts the ⁇ / ⁇ conversion to lower temperatures.
  • Dual-phase steels is the significant improvement of hardenability. Due to the diffusion hindrance, the pearlite and bainite transformation is shifted to longer times and the martensite start temperature is lowered.
  • manganese tends to form oxides on the steel surface during annealing.
  • manganese oxides eg MnO
  • / or Mn mixed oxides eg Mn 2 SiO 4
  • manganese is at one low Si / Mn or Al / Mn ratio to be considered as less critical, since forming more globular oxides instead of oxide films.
  • high levels of manganese can negatively affect the appearance of the zinc layer and zinc adhesion.
  • the manganese content is set at 1,000 to 1,900% for the reasons mentioned above.
  • the manganese content is preferably ⁇ 1.500%, for strip thicknesses of 1.00 to 2.00 mm for ⁇ 1.750% and for strip thicknesses> 2.00 mm for ⁇ 1.500%.
  • YS MPa 53 . 9 + 32 . 34 % Mn + 83 . 16 % Si + 354 . 2 % N + 17 . 402 d - 1 / 2
  • the coefficients of manganese and silicon are approximately the same for both yield strength and tensile strength, demonstrating the potential for silicon to be substituted for manganese.
  • chromium Cr
  • Cr chromium
  • chromium causes particle hardening with appropriate temperature control in the form of chromium carbides.
  • the associated increase in the number of seed sites with simultaneously reduced content of carbon leads to a reduction in the hardenability.
  • chromium In dual phase steels, the addition of chromium mainly improves the hardenability. Chromium, when dissolved, shifts perlite and bainite transformation to longer times, while decreasing the martensite start temperature.
  • Chromium is also a carbide former. If chromium-iron mixed carbides are present, the austenitizing temperature must be high enough before curing to dissolve the chromium carbides. Otherwise, the increased germ count may lead to a deterioration of the hardenability.
  • Chromium also tends to form oxides on the steel surface during the annealing process, which may degrade zinc-plating quality.
  • the above-mentioned measures for adjusting the furnace areas during continuous hot-dip coating reduce the formation of Cr oxides or Cr mixed oxides on the steel surface after annealing
  • the chromium content is therefore set to values of 0.100 to 0.700%.
  • the total content of Mn + Si + Cr is likewise advantageously to be adhered to depending on the thickness of the sheet.
  • a sum content of ⁇ 2.40 to ⁇ 2.70% is favorable, and for a sheet thickness of 1.00 to 2.00 mm, a sum content of ⁇ 2.60 to ⁇ 2.90% and for metal thicknesses ⁇ 2.00 mm, a sum content of ⁇ 2.80 to ⁇ 3.10% has been found.
  • Molybdenum (Mo) The addition of molybdenum leads, similar to that of chromium and manganese, to improve hardenability. The pearlite and bainite transformation is postponed to longer times and the martensite start temperature is lowered. At the same time molybdenum is a strong karsentkowner, the finely divided mixed carbides, including titanium, arise. Molybdenum also increases the tempering resistance significantly, so that in the zinc bath no loss of strength can be expected. Molybdenum also works by solid solution hardening, but is less effective than manganese and silicon.
  • molybdenum is usually limited to the unavoidable, steel-accompanying amounts. If additional strength gains are required for certain process parameters, molybdenum can optionally be alloyed up to 0.200%.
  • Copper (Cu): The addition of copper can increase the tensile strength and hardenability. In combination with nickel, chromium and phosphorus, copper can form a protective oxide layer on the surface, which can significantly reduce the corrosion rate.
  • copper When combined with oxygen, copper can form harmful oxides at the grain boundaries, which can be detrimental to hot working processes in particular.
  • the content of copper is therefore limited to quantities that are unavoidable in steel production.
  • Ni nickel
  • Sn tin
  • Aluminum (Al) is usually added to the steel to bind the dissolved oxygen in the iron and nitrogen.
  • the oxygen and nitrogen is thus converted into aluminum oxides and aluminum nitrides. These precipitations can cause a grain refining by increasing the germination sites and thus increase the toughness properties and strength values.
  • Titanium nitrides have a lower formation enthalpy and are formed at higher temperatures.
  • the aluminum content is therefore limited to 0.010 to a maximum of 0.060% and is added to calm the steel.
  • Niobium acts in different ways in steel. During hot rolling in the finishing train, it retards recrystallization by forming finely divided precipitates, increasing the nucleation density and producing a finer grain after conversion. The proportion of dissolved niobium also inhibits recrystallization. The excretions increase the strength of the final product. These can be carbides or carbonitrides. Often these are mixed carbides in which titanium is also incorporated. This effect begins at 0.005% and is most evident at 0.010% niobium. The precipitates also prevent grain growth during (partial) austenitization in the hot dip galvanizing. Above 0.050% niobium, no additional effect is expected, therefore this is the uppermost limit in the invention.
  • Titanium (Ti) Due to its high affinity to nitrogen, titanium is primarily precipitated as TiN during solidification. It also occurs together with niobium as mixed carbide. TiN is of great importance for grain size stability in the blast furnace. The precipitates have a high temperature stability, so that, in contrast to the mixed carbides, at 1200 ° C, they are mostly present as particles that impede grain growth. Titanium also retards recrystallization during hot rolling, but is less effective than niobium. Titanium works by precipitation hardening. The larger TiN particles are less effective than the finely divided mixed carbides. The best effectiveness is achieved in the range of 0.005 to 0.050% titanium, therefore, this represents the alloy span according to the invention. The proportion of titanium is dependent on the addition of boron (see below).
  • Vanadium (V) Since addition of vanadium is not necessary in the present alloy concept, the content of vanadium is limited to unavoidable steel-accompanying amounts.
  • Boron is an extremely effective hardenability enhancer that is effective in very small amounts (from 5 ppm).
  • the martensite start temperature remains unaffected.
  • boron must be in solid solution. Since it has a high affinity for nitrogen, the nitrogen must first be set, preferably by the stoichiometrically necessary amount of titanium. Due to its low solubility in iron, the dissolved boron preferably remains at the austenite grain boundaries. There it partially forms Fe-B carbides, which are coherent and reduce the grain boundary energy. Both effects have a retarding effect on ferrite and pearlite formation and thus increase the hardenability of the steel.
  • the boron content in this invention is limited to 5 to 40 ppm.
  • Nitrogen (N) can be both an alloying element and a companion element from steelmaking. Excessive levels of nitrogen cause an increase in strength associated with rapid loss of toughness and aging effects.
  • a fine grain hardening via titanium nitrides and niobium (karbo) nitrides can be achieved by a targeted addition of nitrogen in conjunction with the micro-alloying elements titanium and niobium. In addition, coarse grain formation upon re-heating before hot rolling is suppressed.
  • the N content is therefore set to values of ⁇ 0.0020% to ⁇ 0.0120%.
  • the content of nitrogen is set to values of ⁇ 0.0020% to ⁇ 0.0100%.
  • the content of nitrogen is set to values of ⁇ 0.00400% to ⁇ 0.0120%.
  • the annealing temperatures for the dual-phase structure to be achieved are between about 700 and 950 ° C. for the steel according to the invention, so that a partially austenitic (two-phase area) or a fully austenitic structure (austenite area) is achieved, depending on the temperature range.
  • the hot-dip coated material can be produced both as a hot strip and as a cold rolled hot strip or cold strip in the dressed (cold rolled) or undressed state and / or in the stretch bending or non-stretch bent state and also in the heat treated state (overaging).
  • Steel strips in the present case as hot strip, cold rolled hot strip or cold strip made of the alloy composition according to the invention, are also distinguished by a high resistance to crack formation at the edge during further processing.
  • the hot strip is produced according to the invention with final rolling temperatures in the austenitic region above A r3 and reel temperatures above the bainite start temperature (variant A).
  • the hot strip is produced according to the invention with final rolling temperatures in the austenitic region above A r3 and coiling temperatures below the bainite start temperature (variant B).
  • FIG. 1 schematically shows the process chain for the production of the steel according to the invention. Shown are the different process routes relating to the invention. Until hot rolling (final rolling temperature), the process route is the same for all steels according to the invention, after which deviating process routes take place, depending on the desired results.
  • the pickled hot strip can be galvanized or cold rolled and galvanized with different degrees of rolling.
  • soft annealed hot strip or soft annealed cold strip can be cold rolled and galvanized.
  • Material can also be optionally processed without zinc pot (continuous annealing) with and without subsequent electrolytic galvanizing.
  • FIG. 2 schematically shows the time-temperature curve of the process steps hot rolling and continuous annealing of strips of the alloy composition according to the invention. Shown is the time- and temperature-dependent conversion for the hot rolling process as well as for a heat treatment after cold rolling.
  • FIG. 3 shows the relevant alloying elements of the steel according to the invention, compared to the comparative quality exemplifies.
  • the steel according to the invention is clearly silicon-alloyed.
  • the difference is still in the carbon content, which is ⁇ 0.120%, but also in the elements titanium and boron.
  • the standard grade like the steel according to the invention, is niobium-microalloyed.
  • FIG. 4 shows examples of mechanical characteristics along the rolling direction of the steel according to the invention.
  • FIG. 5 shows results of the hole expansion tests according to ISO 16630 (absolute values and relative values to the comparison quality). Shown are the results of the hole expansion tests for variant A (reel temperature above bainite start temperature) and variant B (reel temperature below bainite start temperature), in each case for process 2 and process 3.
  • the materials have a sheet thickness of 1.00 or 2.00 mm.
  • the results apply to the test according to ISO 16630. It can be seen that the steels according to the invention achieve better or approximately the same expansion values for punched holes than the comparative grades with the same processing.
  • the method 2 corresponds to an annealing, for example, on a hot-dip galvanizing combined with directly fired furnace and radiant tube furnace, as in FIG. 6b is described.
  • the method 3 corresponds for example to a process control in a continuous annealing plant, as in FIG. 6c is described.
  • a reheating of the steel can optionally be achieved directly in front of the zinc bath by means of an induction furnace.
  • FIGS. 6 show schematically three variants of the temperature-time courses according to the invention in the annealing and cooling and each austenitization different conditions.
  • the method 1 shows the annealing and cooling of the produced cold or hot rolled or cold rolled steel strip in a continuous annealing line.
  • the tape is heated to a temperature in the range of about 700 to 950 ° C.
  • the annealed steel strip is then cooled from the annealing temperature at a cooling rate of between about 15 and 100 ° C / s to an intermediate temperature of about 200 to 250 ° C.
  • a second intermediate temperature (about 300 to 500 ° C) is omitted in this schematic representation.
  • the steel strip is cooled at a cooling rate between about 2 and 30 ° C / s until it reaches room temperature in air or the cooling at a cooling rate between about 15 and 100 ° C / s is maintained up to room temperature.
  • the method 2 ( FIG. 6b ) shows the process according to method 1, but the cooling of the steel strip for the purpose of a hot dip finishing briefly interrupted when passing through the hot dipping vessel, then the cooling at a cooling rate between about 15 and 100 ° C / s up to an intermediate temperature of about 200 continue to 250 ° C. Subsequently, the steel strip is cooled at a cooling rate between about 2 and 30 ° C / s until it reaches room temperature in air.
  • the method 3 ( FIG. 6c ) also shows the process according to method 1 in a hot dip finishing, but the cooling of the steel strip is interrupted by a short break (about 1 to 20 s) at an intermediate temperature in the range of about 200 to 400 ° C and down to the temperature, which is necessary for hot dip refining (about 400 to 470 ° C) reheated. Subsequently, the steel strip is again cooled to an intermediate temperature of about 200 to 250 ° C. With a cooling rate of approx. 2 and 30 ° C / s, the final cooling of the steel strip takes place until the room temperature in air is reached.
  • FIG. 6c stand the following examples:
  • An inventive steel with 0.091% C; 0.705% Si; 1.801% Mn; 0.010% P; 0.0030% S; 0.0054% N; 0.035 Al; 0.344% Cr; 0.012% Mo; 0.016% Ti; 0.001% V; 0.016% Nb; 0.0031% B was melted in a high vacuum melting and casting plant, hot rolled in a hot rolling stand at a final rolling target temperature of 910 ° C and fed to the furnace for simulated coiler cooling at a coiler set temperature of 500 ° C with a thickness of 2.30 mm , After sandblasting, cold rolling was carried out with a cold rolling degree of 15% from 2.30 to 2.00 mm.
  • the steel according to the invention has, after the heat treatment, a microstructure consisting of ferrite, martensite, bainite and retained austenite.
  • An inventive steel with 0.091% C; 0.705% Si; 1.801% Mn; 0.010% P; 0.0030% S; 0.0054% N; 0.035 Al; 0.344% Cr; 0.012% Mo; 0.016% Ti; 0.001% V; 0.016% Nb; 0.0031% B was melted in a high vacuum melting and casting plant, hot rolled in a hot rolling stand at a final rolling target temperature of 910 ° C and fed to the furnace for simulated coiler cooling at a coiler set temperature of 500 ° C with a thickness of 2.30 mm , After sandblasting, cold rolling was carried out with a cold rolling degree of 15% from 2.30 mm to 2.00 mm.
  • the steel according to the invention has, after the heat treatment, a microstructure consisting of ferrite, martensite, bainite and retained austenite.
  • An inventive steel with 0.091% C; 0.705% Si; 1.801% Mn; 0.010% P; 0.0030% S; 0.0054% N; 0.035 Al; 0.344% Cr; 0.012% Mo; 0.016% Ti; 0.001% V; 0.016% Nb; 0.0031% B was melted in a high vacuum melting and casting plant, hot rolled in a hot rolling stand at a final rolling target temperature of 910 ° C and fed to the furnace for a simulated coiler cooling at a coiler set temperature of 710 ° C with a thickness of 2.02 mm , After sandblasting, cold rolling was performed with a cold rolling degree of 50% from 2.02 to 0.99 mm.
  • the steel according to the invention has, after the heat treatment, a microstructure consisting of ferrite, martensite, bainite and retained austenite.
  • An inventive steel with 0.091% C; 0.705% Si; 1.801% Mn; 0.010% P; 0.0030% S; 0.0054% N; 0.035 Al; 0.344% Cr; 0.012% Mo; 0.016% Ti; 0.001% V; 0.016% Nb; 0.0031% B was melted in a high vacuum melting and casting plant, hot rolled in a hot rolling stand at a final rolling target temperature of 910 ° C and fed to the furnace for a simulated coiler cooling at a coiler set temperature of 710 ° C with a thickness of 2.02 mm , After sandblasting, cold rolling was performed with a cold rolling degree of 50% from 2.02 to 0.99 mm.
  • the steel according to the invention has, after the heat treatment, a microstructure consisting of ferrite, martensite, bainite and retained austenite.
  • An inventive steel with 0.091% C; 0.705% Si; 1.801% Mn; 0.010% P; 0.0030% S; 0.0054% N; 0.035 Al; 0.344% Cr; 0.012% Mo; 0.016% Ti; 0.001% V; 0.016% Nb; 0.0031% B was melted in a high vacuum melting and casting plant, hot rolled in a hot rolling stand at a final rolling target temperature of 910 ° C and fed to the furnace for a simulated coiler cooling at a coiler set temperature of 710 ° C with a thickness of 2.02 mm , After sand blasting, the annealing treatment took place.
  • the steel according to the invention has, after the heat treatment, a microstructure consisting of ferrite, martensite, bainite and retained austenite.
  • An inventive steel with 0.091% C; 0.705% Si; 1.801% Mn; 0.010% P; 0.0030% S; 0.0054% N; 0.035 Al; 0.344% Cr; 0.012% Mo; 0.016% Ti; 0.001% V; 0.016% Nb; 0.0031% B was melted in a high vacuum melting and casting plant, hot rolled in a hot rolling stand at a final rolling target temperature of 910 ° C and fed to the furnace for a simulated coiler cooling at a coiler set temperature of 710 ° C with a thickness of 2.02 mm , After sand blasting, the glow simulation took place.
  • the steel according to the invention has, after the heat treatment, a microstructure consisting of ferrite, martensite, bainite and retained austenite.
  • An inventive steel with 0.091% C; 0.705% Si; 1.801% Mn; 0.010% P; 0.0030% S; 0.0054% N; 0.035 Al; 0.344% Cr; 0.012% Mo; 0.016% Ti; 0.001% V; 0.016% Nb; 0.0031% B was melted in a high vacuum melting and casting plant, hot rolled in a hot rolling stand at a final rolling target temperature of 910 ° C and fed to the furnace for simulated coiler cooling at a coiler set temperature of 500 ° C with a thickness of 2.30 mm , After sand blasting, the annealing treatment took place.
  • the steel according to the invention has, after the heat treatment, a microstructure consisting of ferrite, martensite, bainite and retained austenite.
  • An inventive steel with 0.091% C; 0.705% Si; 1.801% Mn; 0.010% P; 0.0030% S; 0.0054% N; 0.035 Al; 0.344% Cr; 0.012% Mo; 0.016% Ti; 0.001% V; 0.016% Nb; 0.0031% B was melted in a high vacuum melting and casting plant, hot rolled in a hot rolling stand at a final rolling target temperature of 910 ° C and fed to the furnace for simulated coiler cooling at a coiler set temperature of 500 ° C with a thickness of 2.30 mm , After sand blasting, the annealing treatment took place.
  • the steel according to the invention has, after the heat treatment, a microstructure consisting of ferrite, martensite, bainite and retained austenite.

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Claims (20)

  1. Acier multiphase à haute résistance avec des résistances minimales à la traction de 750 MPa, de préférence avec une structure double phase pour une bande d'acier laminée à froid ou à chaud avec des propriétés améliorées de formage et un rapport de limites d'élasticité d'un maximum de 73 %, en particulier pour la construction légère d'automobiles, se composant des éléments suivants (teneurs en % en masse) : C ≥ 0,075 à ≤ 0,105 Si ≥ 0,600 à ≤ 0,800 Mn ≥ 1,000 à ≤ 1,900 Cr ≥ 1,100 à ≤ 0,700 Al ≥ 0,010 à ≤ 0,060 N ≥ 0,0020 à ≤ 0,0120 S ≤ 0,0030 Nb ≥ 0,005 à ≤ 0,050 Ti ≥ 0,005 à ≤ 0,050 B ≥ 0,0005 à ≤ 0,0040 Mo ≤ 0,200 Cu ≤ 0,040 % Ni ≤ 0,040 %
    le reste étant du fer, y compris des éléments habituels d'accompagnement de l'acier non mentionnés ci-dessus, lesquels représentent des impuretés dues à la fusion.
  2. Acier selon la revendication 1
    caractérisé en ce
    qu'avec des épaisseurs de bande jusqu'à 1,00 mm, la teneur en Mn est de préférence ≤ 1,500 %.
  3. Acier selon la revendication 1
    caractérisé en ce
    qu'avec des épaisseurs de bande > 1,00 à 2,00 mm, la teneur en Mn est de préférence ≤ 1,750 %.
  4. Acier selon la revendication 1
    caractérisé en ce
    qu'avec des épaisseurs de bande > 2,00 mm, la teneur en Mn est de préférence ≥ 1,500 %.
  5. Acier selon la revendication 1 et 2
    caractérisé en ce
    qu'avec des épaisseurs de bande jusqu'à 1,00 mm, la somme de la teneur en Mn+Si+Cr est de préférence ≥ 2,40 et ≤ 2,70 %.
  6. Acier selon la revendication 1 et 3
    caractérisé en ce
    qu'avec des épaisseurs de bande de 1,00-2,00 mm la somme de la teneur en Mn+Si+Cr est de préférence ≥ 2,60 et ≤ 2,90 %.
  7. Acier selon la revendication 1 et 4
    caractérisé en ce
    qu'avec des épaisseurs de bande > 2,00 mm, la somme de la teneur en Mn+Si+Cr est de préférence ≥ 2,80 et ≤ 3,10 %.
  8. Acier selon l'une des revendications 1 à 7
    caractérisé en ce
    qu'avec la somme de Ti+Nb ≥ 0,010 % et ≤ 0,050 %, la teneur en N est ≥ 0,0020 et ≤ 0,0100 %.
  9. Acier selon l'une des revendications 1 à 7
    caractérisé en ce
    qu'avec la somme de Ti+Nb > 0,050 %, la teneur en N est > 0,0040 et ≤ 0,0120 %.
  10. Acier selon l'une des revendications 1 à 9
    caractérisé en ce
    que la teneur en S est ≤ 0,0020 %.
  11. Acier selon l'une des revendications 1 à 10 caractérisé en ce
    que la teneur en S est ≤ 0,0010 %.
  12. Acier selon l'une des revendications 1 à 11
    caractérisé en ce
    que les additions de silicium et de manganèse sont interchangeables en ce qui concerne les propriétés de résistance mécanique à obtenir conformément au apport : YS MPa = 160 , 7 + 147 , 9 % Si + 161 , 1 % Mn
    Figure imgb0014
     TS MPa = 324 , 8 + 189 , 4 % Si + 174 , 1 % Mn .
    Figure imgb0015
  13. Procédé pour la fabrication d'une bande d'acier laminée à froid ou à chaud en un acier fabriqué selon l'une des revendications 1 à 12, dans lequel une structure double phase est produite pendant un recuit en continu, caractérisé en ce
    que la bande d'acier laminée à froid ou à chaud pendant le recuit en continu est chauffée à une température dans la plage d'environ 700 à 950 °C et que la bande d'acier recuite est ensuite refroidie de la température de recuit à une vitesse de refroidissement comprise entre d'environ 15 et 100 °C/s jusqu'à une première température intermédiaire de d'environ 300 à 500 °C, suite à cela à une vitesse de refroidissement comprise entre environ 15 et 100 °C/s jusqu'à une deuxième température intermédiaire d'environ 160 à 250 °C, qu'ensuite la bande d'acier est refroidie à l'air avec une vitesse de refroidissement d'environ 2 à 30 °C/s jusqu'à l'atteinte de la température ambiante ou bien le refroidissement est maintenu avec une vitesse de refroidissement comprise entre environ 15 et 100 °C/s de la première température intermédiaire jusqu'à la température ambiante.
  14. Procédé selon la revendication 13
    caractérisé en ce
    qu'avec une finition par immersion à chaud après le chauffage et le refroidissement qui s'ensuit, le refroidissement est interrompu avant l'entrée dans le bain de fusion et après la finition par immersion à chaud, le refroidissement se poursuit avec une vitesse de refroidissement comprise entre environ 15 et 100 °C/s jusqu'à une température intermédiaire d'environ 200 à 250 °C, et la bande d'acier est ensuite refroidie à l'air avec une vitesse de refroidissement d'environ 2 et 30 °C/s jusqu'à l'atteinte de la température ambiante.
  15. Procédé selon la revendication 13
    caractérisé en ce
    qu'avec une finition par immersion à chaud après le chauffage et le refroidissement qui s'ensuit à la température intermédiaire d'environ 200 à 250 °C avant l'entrée dans le bain de fusion, la température est maintenue pendant environ 1 à 20 s et la bande d'acier est ensuite de nouveau chauffée à la température d'environ 400 à 470 °C et une fois la finition par immersion à chaud effectuée, un refroidissement avec une vitesse de refroidissement comprise entre environ 15 et 100 °C/s jusqu'à la température intermédiaire d'environ 200 à 250 °C a lieu, et ensuite un refroidissement à l'air jusqu'à la température ambiante avec une vitesse de refroidissement d'environ 2 et 30 °C/s a lieu.
  16. Procédé selon l'une des revendications 13 à 15,
    caractérisé en ce
    que le potentiel d'oxydation en cas d'un recuit avec une configuration d'installation se composant d'une zone de four à chauffage direct (NOF) et d'un four tubulaire en acier (RTF) est augmenté par une teneur en CO dans la zone de four à chauffage direct inférieure à 4 %, dans lequel, dans le four tubulaire en acier, la pression partielle d'oxygène de l'atmosphère du four réductrice pour du fer est réglée conformément à l'équation suivante, − 18 > Log pO 2 ≥ − 5 * Si − 0 , 3 − 2 , 2 * Mn − 0 , 45 − 0 , 1 * Cr − 0 , 4 − 12 , 5 * − In B 0 , 25
    Figure imgb0016
     dans laquelle Si, Mn, Cr, B indiquent les pourcentages d'alliage correspondants dans l'acier en % en masse et po2 la pression partielle d'oxygène en mbars et, pour éviter l'oxydation de la bande directement avant l'immersion dans le bain de fusion, le point de rosée de l'atmosphère gazeuse est réglé à -30 °C ou moins.
  17. Procédé selon l'une des revendications 13 à 15,
    caractérisé en ce
    qu'en cas d'un recuit avec seulement un four tubulaire en acier, la pression partielle d'oxygène de l'atmosphère du four satisfait à l'équation suivante, − 12 > Log pO 2 ≥ − 5 * Si − 0 , 25 − 3 * Mn − 0 , 5 − 0 , 1 * Cr − 0 , 5 − 7 * − In B 0 , 5
    Figure imgb0017
     dans laquelle Si, Mn, Cr, B indiquent les pourcentages d'alliage correspondants dans l'acier en % en masse et po2 la pression partielle d'oxygène en mbars et, pour éviter l'oxydation de la bande directement avant l'immersion dans le bain de fusion, le point de rosée de l'atmosphère gazeuse est réglé à -30 °C ou moins.
  18. Procédé selon l'une des revendications 13 à 17
    caractérisé en ce
    que par adaptation de la vitesse de passage dans l'installation à différentes épaisseurs de bande lors du traitement thermique, des états comparables de structure et de valeurs caractéristiques mécaniques des brandes sont réglés.
  19. Procédé selon l'une des revendications 13 à 18
    caractérisé en ce
    que la bande d'acier est dressée à la suite du traitement thermique.
  20. Procédé selon l'une au moins des revendications 13 à 19
    caractérisé en ce
    que la bande d'acier est soumise à un dressage par traction et flexion à la suite du traitement thermique .
EP14741788.5A 2013-07-30 2014-05-27 Acier multiphase à haute résistance, micro-allié et contenant du silicium, présentant une résistance minimale à la traction de 750 mpa et des propriétés améliorées et procédé de fabrication d'une bande à partir de cet acier Active EP3027784B1 (fr)

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DE102013013067.0A DE102013013067A1 (de) 2013-07-30 2013-07-30 Siliziumhaltiger, mikrolegierter hochfester Mehrphasenstahl mit einer Mindestzugfestigkeit von 750 MPa und verbesserten Eigenschaften und Verfahren zur Herstellung eines Bandes aus diesem Stahl
PCT/DE2014/000295 WO2015014333A2 (fr) 2013-07-30 2014-05-27 Acier multiphase à haute résistance, micro-allié et contenant du silicium, présentant une résistance minimale à la traction de 750 mpa et des propriétés améliorées et procédé de fabrication d'une bande à partir de cet acier

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WO2021185514A1 (fr) 2020-03-19 2021-09-23 Sms Group Gmbh Procédé de fabrication d'une bande d'acier laminée à plusieurs phases présentant des propriétés spéciales
DE102020203564A1 (de) 2020-03-19 2021-09-23 Sms Group Gmbh Verfahren zum Herstellen eines gewalzten Mehrphasenstahlbandes mit Sondereigenschaften
DE102020110319A1 (de) 2020-04-15 2021-10-21 Salzgitter Flachstahl Gmbh Verfahren zur Herstellung eines Stahlbandes mit einem Mehrphasengefüge und Stahlband hinzu
DE102021128327A1 (de) 2021-10-29 2023-05-04 Voestalpine Stahl Gmbh Kaltgewalztes stahlflachprodukt mit metallischer korrosionsschutzschicht und verfahren zur herstellung eines solchen

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RU2666392C2 (ru) 2018-09-07
EP3027784A2 (fr) 2016-06-08
RU2016107030A (ru) 2017-09-01
US10612113B2 (en) 2020-04-07
WO2015014333A3 (fr) 2015-11-05
US20160186298A1 (en) 2016-06-30
RU2016107030A3 (fr) 2018-03-13
KR102196079B1 (ko) 2020-12-29
DE102013013067A1 (de) 2015-02-05
US20180298476A1 (en) 2018-10-18
WO2015014333A2 (fr) 2015-02-05
KR20160039218A (ko) 2016-04-08

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