EP3221484B1 - Procédé de production d'une bande en acier polyphasé, durcissant à l'air, ayant une haute résistance et ayant d'excellentes propriétés de mise en oeuvre - Google Patents

Procédé de production d'une bande en acier polyphasé, durcissant à l'air, ayant une haute résistance et ayant d'excellentes propriétés de mise en oeuvre Download PDF

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Publication number
EP3221484B1
EP3221484B1 EP15831216.5A EP15831216A EP3221484B1 EP 3221484 B1 EP3221484 B1 EP 3221484B1 EP 15831216 A EP15831216 A EP 15831216A EP 3221484 B1 EP3221484 B1 EP 3221484B1
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Prior art keywords
strip
steel
hot
approx
content
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German (de)
English (en)
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EP3221484A1 (fr
Inventor
Thomas Schulz
Joachim SCHÖTTLER
Sascha KLUGE
Christian Meyer
Peter Matthies
Andreas WEDEMEIER
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Salzgitter Flachstahl GmbH
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Salzgitter Flachstahl GmbH
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    • 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
    • C—CHEMISTRY; METALLURGY
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    • C21D1/26—Methods of annealing
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    • 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
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/84—Controlled slow cooling
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
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    • C21D6/00—Heat treatment 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
    • C21D8/0226—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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    • C21D8/0221—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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    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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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
    • C21D8/0263—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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    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • 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
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    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
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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
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
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    • 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
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    • 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
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    • C21D9/562—Details
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    • C21D9/58—Continuous furnaces for strip or wire with heating by baths
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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
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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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
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    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
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    • C21D2211/00—Microstructure comprising significant phases
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the invention relates to a method for producing a cold-rolled or hot-rolled steel strip from a high-strength, air-hardenable multiphase steel according to patent claim 1.
  • Advantageous further developments are the subject matter of dependent claims 2 to 25.
  • the invention relates to steels with a tensile strength in the range of at least 750 MPa in the initial state (not hardened or tempered) for the production of components that have improved formability (such as increased hole expansion and increased bending angle) and improved welding properties.
  • a steel with a lower strength but an addition of alloying elements depending on the sheet thickness is from the DE 10 2012 013 113 A1 known, while a steel with a comparable minimum tensile strength without such a requirement from the DE 10 2011 117 572 A1 is known.
  • a tempering treatment of these steels according to the invention can increase the yield strength and tensile strength, for example through air hardening with optional subsequent tempering.
  • the weight of the vehicles can be reduced while at the same time improving the deformation and component behavior during production and operation.
  • High-strength to ultra-high-strength steels therefore have to meet comparatively high requirements in terms of their strength and ductility, energy absorption and their processing, such as punching, hot and cold forming, thermal quenching and tempering (e.g. air hardening, press hardening), welding and / or surface treatment, e.g. a metallic refinement, organic coating or painting are sufficient.
  • thermal quenching and tempering e.g. air hardening, press hardening
  • welding and / or surface treatment e.g. a metallic refinement, organic coating or painting are sufficient.
  • a high-strength to ultra-high-strength steel with a single or multi-phase structure must therefore be used in order to ensure sufficient strength of the motor vehicle components and to meet the high component requirements in terms of toughness, edge crack resistance, improved bending angle and radius, energy absorption as well as hardening capacity and bake hardening -Effect to suffice.
  • the hole expansion capacity is a material property that describes the resistance of the material to crack initiation and crack propagation during forming operations in areas close to edges, such as when pulling collars.
  • the hole expansion test is regulated in ISO 16630, for example. Then prefabricated holes punched into sheet metal, for example, are widened by means of a mandrel.
  • the measured variable is the change in the hole diameter based on the initial diameter at which the first crack through the sheet occurs at the edge of the hole.
  • Improved edge crack insensitivity means an increased deformability of the sheet metal edges and can be described by an increased hole expansion capacity. This situation is known under the synonyms “L ow E dge C rack” (LEC) or under “H igh E H ole xpansion” (HHE) and xpand®.
  • the bending angle describes a material property that allows conclusions to be drawn about the material behavior during forming operations with dominant bending components (e.g. when folding) or also during crash loads. Increased bending angles thus increase passenger compartment safety.
  • the determination of the bending angle ( ⁇ ) is e.g. Normatively regulated via the plate bending test in VDA 238-100.
  • the above-mentioned properties are important for components that are e.g. can be formed into very complex components by air hardening with optional tempering.
  • AHSS A dvanced H igh S trength S Teels
  • the group of multi-phase steels is used more and more.
  • the multiphase steels include e.g. Complex-phase steels, ferritic-bainitic steels, TRIP steels and the previously described dual-phase steels, which are characterized by different structural compositions.
  • complex- phase steels are steels that contain small proportions of martensite, retained austenite and / or pearlite in a ferritic / bainitic basic structure, whereby a delayed recrystallization or precipitation of micro-alloying elements causes a strong grain refinement.
  • these complex-phase steels Compared to dual-phase steels, these complex-phase steels have higher yield strengths, a higher yield strength ratio, less work hardening and a higher hole expansion capacity.
  • ferritic-bainitic steels are steels that contain bainite or solidified bainite in a matrix of ferrite and / or solidified ferrite.
  • the strength of the matrix is brought about by a high dislocation density, by grain refinement and the precipitation of micro-alloy elements.
  • dual-phase steels are steels with a ferritic basic structure in which a martensitic second phase is embedded in the form of an island, sometimes with a proportion of bainite as the second phase. With a high tensile strength, dual-phase steels show a low yield strength 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 transform to martensite during the forming process (TRIP effect). Because of its strong work hardening, the steel achieves high values of uniform elongation and tensile strength. In connection with the bake hardening effect, high component strengths can be achieved. These steels are suitable for both stretch drawing and deep drawing. When forming the material, however, higher blank holder forces and press forces are required. A comparatively strong springback must be taken into account.
  • the high-strength steels with a single-phase structure include e.g. bainitic and martensitic steels.
  • Bainitic steels in accordance with EN 10346 steels which are characterized by a very high yield and tensile strength at a sufficiently high elongation for cold forming. Due to the chemical composition, it is easy to weld.
  • the structure typically consists of bainite.
  • the structure can contain small proportions of other phases such as martensite and ferrite.
  • martensitic steels are steels which, as a result of thermomechanical rolling, contain small amounts of ferrite and / or bainite in a basic structure of martensite. This type of steel is characterized by a very high yield point and tensile strength with a sufficiently high elongation for cold forming processes. Within the group of multiphase steels, martensitic steels have the highest tensile strength values. The suitability for deep drawing is limited. The martensitic steels are mainly suitable for bending processes such as roll forming.
  • High-strength and ultra-high-strength multiphase steels are used, among others. in structural, chassis and crash-relevant components as sheet metal blanks, tailored blanks (welded blanks) and as flexible cold-rolled strips, 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 takes place for a defined structure adjustment, where, for example, the steel gets its low yield strength from comparatively soft components such as ferrite or bainitic ferrite and its strength from its hard components such as martensite or carbon-rich bainite.
  • cold-rolled high-strength to ultra-high-strength steel strips are usually recrystallized and annealed to form fine sheet metal that is easy to form.
  • the process parameters such as throughput speed, annealing temperatures and cooling speed (cooling gradient) are set according to the required mechanical-technological properties with the necessary structure.
  • the pickled hot strip in typical thicknesses between 1.50 to 4.00 mm or cold strip in typical thicknesses of 0.50 to 3.00 mm is heated in a continuous annealing furnace to such a temperature that during recrystallization and cooling sets the required structure formation.
  • a constant temperature is difficult to achieve, especially with different thicknesses in the transition area from one strip to the other.
  • this can lead to e.g. either the thinner strip is moved too slowly through the furnace, which lowers productivity, or the thicker strip is moved too quickly through the furnace and the necessary annealing temperatures and cooling gradients to achieve the desired structure are not achieved. The consequences are increased rejects and high failure costs.
  • TRB®s with a multiphase structure are not possible with currently known alloys and available continuous annealing systems for widely varying strip thicknesses, however, without additional effort, such as additional heat treatment before cold rolling (hot strip soft annealing).
  • additional heat treatment before cold rolling hot strip soft annealing
  • no homogeneous multi-phase structure can be set in cold as well as hot rolled steel strips.
  • a method for producing a steel strip with different thicknesses over the length of the strip is, for example, in DE 100 37 867 A1 described.
  • the annealing treatment usually takes place in a continuous annealing furnace upstream of the hot-dip bath.
  • the required structure is not set until the annealing treatment in the continuous annealing furnace in order to achieve the required mechanical properties.
  • Decisive process parameters are therefore the setting of the annealing temperature and the speed, as well as the cooling rate (cooling gradient) in continuous annealing, since the phase transition takes place as a function of temperature and time.
  • the goal of achieving the resulting mechanical-technological properties in a narrow range over the bandwidth and length of the belt through the controlled setting of the volume proportions of the structural components has top priority and is only possible through an enlarged process window.
  • the known alloy concepts are characterized by a process window that is too narrow and are therefore unsuitable for solving the problem at hand, particularly in the case of flexibly rolled strips. With the known alloy concepts, only steels of one strength class with defined cross-sectional areas (strip thickness and width) can currently be represented, so that modified alloy concepts are necessary for different strength classes and / or cross-sectional areas.
  • CEV (IIW) C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5
  • CET C + (Mn + Mo) / 10 + (Cr + Cu) / 20 + Ni / 40
  • PCM C + (Mn + Cu + Cr) / 20 + Ni / 60 + Mo / 15 + V / 10 + 5
  • the characteristic standard elements such as carbon and manganese, as well as chromium or molybdenum and vanadium are taken into account (contents in% by weight).
  • the lowering of the Carbon equivalents due to lower levels of carbon and manganese should be compensated for by increasing the silicon content. With the same strength, the insensitivity to edge cracks and the weldability are improved.
  • a low yield strength ratio (Re / Rm) in a strength range above 750 MPa in the initial state is typical for a dual-phase steel and is primarily used for formability in stretching and deep-drawing processes. It provides the designer with information on the distance between the onset of plastic deformation and failure of the material under quasi-static loading. Accordingly, lower yield strength ratios represent a greater safety margin to component failure.
  • a higher yield strength ratio (Re / Rm), as is typical for complex-phase steels, is also characterized by a high resistance to edge cracks. This can be attributed to the smaller differences in the strengths and hardnesses of the individual structural components and the finer structure, which has a favorable effect on a homogeneous deformation in the area of the cut edge.
  • the standards also contain an overlap area, as is the case with the yield point ratio (Re / Rm), in which an assignment to both complex and dual-phase steels is possible and leads to improved material properties.
  • the analytical landscape for the achievement of multiphase steels with minimum tensile strengths of 750 MPa in the initial state is very diverse and shows very large alloy ranges for the strength-increasing elements carbon, silicon, manganese, phosphorus, nitrogen, aluminum as well as chromium and / or molybdenum as well as in the addition of micro-alloys such as titanium, niobium, vanadium and boron.
  • the range of dimensions in this strength range is broad and lies in the thickness range from about 0.50 to about 4.00 mm for strips that are intended for continuous annealing.
  • Hot strip, cold re-rolled hot strip and cold strip can be used as input material.
  • Mainly tapes up to about 1600 mm wide are used, but also split tape dimensions that are created by splitting the tapes lengthways. Sheets or panels are manufactured by dividing the strips transversely.
  • EP 1 807 544 B1 , WO 2011/000351 and EP 2 227 574 B1 known air-hardenable steel grades with minimum tensile strengths in the initial state of 800 (LH®800) or 900 MPa (LH®900) in hot or cold rolled design are particularly characterized by their very good formability in the soft state (deep drawing properties) and their high strength after heat treatment (quenching and tempering).
  • LH®800 initial state of 800
  • 900 MPa LH®900
  • hot or cold rolled design are particularly characterized by their very good formability in the soft state (deep drawing properties) and their high strength after heat treatment (quenching and tempering).
  • the structure of the steel is converted into the austenitic area by heating, preferably to temperatures above 950 ° C under a protective gas atmosphere.
  • a martensitic microstructure is formed for a high-strength component.
  • the invention is therefore based on the object of creating a new cost-effective alloy concept for a high-strength, air-hardenable multiphase steel with excellent processing properties and with a minimum tensile strength of 750 MPa in the initial state, along and across the rolling direction, preferably with a dual-phase structure, with which the process window for the Continuous annealing of hot or cold strips is expanded so that, in addition to strips with different cross-sections, steel strips with a thickness that varies over the length and possibly the width of the strip and the correspondingly varying degrees of cold rolling with the most homogeneous mechanical-technological properties possible can be produced.
  • the hot-dip coating of the steel should be guaranteed. Adequate formability, HFI weldability, excellent general weldability as well as hot-dip and tempering resistance should also be ensured.
  • this object is achieved by a steel of a composition according to claim 1.
  • the structure consists of the main phases ferrite and martensite and the secondary phase bainite, which determines the improved mechanical properties of the steel.
  • the steel is characterized by low carbon equivalents and, with the carbon equivalent CEV (IIW), depends on the sheet thickness on the addition of max. 0.62% so that excellent weldability and the other specific properties described below can be achieved.
  • CEV carbon equivalent
  • the steel according to the invention can be produced in a wide range of hot rolling parameters, for example with coiling temperatures above the bainite start temperature (variant A).
  • a specific process control can be used to set a microstructure that allows the steel to be subsequently cold-rolled without prior soft annealing, with degrees of cold rolling between 10 and 60% per cold rolling pass.
  • the steel is very well suited as a starting material for hot-dip finishing and has a significantly larger process window compared to the known steels due to the total amount of Mn, Si and Cr added according to the invention depending on the strip thickness to be produced.
  • high-strength hot or cold strips are produced from multiphase steel with varying strip thicknesses in the continuous annealing process, components that are optimized in terms of load can advantageously be produced from them.
  • the steel strip according to the invention can be produced as cold and hot strip as well as cold re-rolled hot strip by means of a hot-dip galvanizing line or a pure continuous annealing plant in the passaged and undressing, in the stretch-bend-directed and non-stretch-bend-directed and also in the heat-treated (overaged) state.
  • steel strips can be produced by intercritical annealing between A c1 and A c3 or with austenitizing annealing via A c3 with subsequent controlled cooling, which leads to a dual or multi-phase structure.
  • Annealing temperatures of about 700 to 950 ° C. have proven to be advantageous. Depending on the overall process (only continuous annealing or additional hot-dip refining), there are different approaches to heat treatment.
  • the strip is cooled down from the annealing temperature at a cooling rate of approx. 15 to 100 ° C / s to an intermediate temperature of approx. 160 to 250 ° C.
  • it can be cooled in advance at a cooling rate of approx. 15 to 100 ° C / s to a previous intermediate temperature of 300 to 500 ° C.
  • the cooling down to room temperature then takes place at a cooling rate of approx. 2 to 30 ° C / s (see also method 1, Figure 6a ).
  • the cooling is stopped before entering the molten bath and only continued after exiting the bath until the intermediate temperature of approx. 200 to 250 ° C. is reached.
  • the holding temperature in the melt bath is approx. 400 to 470 ° C.
  • the cooling down to room temperature takes place again at a cooling rate of approx. 2 to 30 ° C / s (see also method 2, Figure 6b ).
  • the second variant of the temperature control in hot-dip refining involves holding the temperature for approx. 1 to 20 s at the intermediate temperature of approx. 200 to 350 ° C and then reheating to the temperature of approx. 400 to 470 ° C required for hot-dip refining.
  • the tape will be back to approx. 200 after finishing cooled to 250 ° C.
  • the cooling to room temperature takes place again at a cooling rate of approx. 2 to 30 ° C / s (see also method 3, Figure 6c ).
  • carbon, manganese, chromium and silicon are also responsible for the conversion of austenite to martensite.
  • carbon, silicon, manganese, nitrogen and chromium as well as niobium, titanium and boron which are added within the specified limits, ensures the required mechanical properties such as minimum tensile strengths of 750 MPa with a significantly wider process window for continuous annealing.
  • the carbon equivalent can be reduced, which improves the weldability and prevents excessive hardening during welding. With resistance spot welding, the electrode life can also be increased significantly.
  • Bealeitiata are elements that are already present in the iron ore or that get into the steel due to production. Due to their predominantly negative influences, they are usually undesirable. Attempts are made to remove them to a tolerable level or to convert them into more harmless forms.
  • Hydrogen (H) is the only element that can diffuse through the iron lattice without creating lattice tension. This means that the hydrogen in the iron lattice is relatively mobile and can be absorbed relatively easily while the steel is being processed. Hydrogen can only be absorbed into the iron lattice in atomic (ionic) form.
  • Hydrogen has a very embrittling effect and diffuses preferentially to energetically favorable locations (defects, grain boundaries, etc.). Defects act as hydrogen traps and can considerably increase the retention time of the hydrogen in the material.
  • Recombination to form molecular hydrogen can cause cold cracks. This behavior occurs with hydrogen embrittlement or with hydrogen-induced stress corrosion cracking. In the case of a delayed crack, the so-called delayed fracture, which occurs without external stresses, hydrogen is often mentioned as the triggering reason. Therefore, the hydrogen content in the steel should be as low as possible.
  • a more uniform structure which in the steel according to the invention et al. is achieved through its expanded process window, also reduces the susceptibility to hydrogen embrittlement.
  • Oxygen (O) In the molten state, the steel has a relatively high absorption capacity for gases. At room temperature, however, oxygen is only soluble in very small amounts. Similar to hydrogen, oxygen can only diffuse into the material in atomic form. Because of the highly embrittling effect and the negative effects on aging resistance, attempts are made as much as possible to reduce the oxygen content during production.
  • the oxygen can be converted into less dangerous conditions.
  • a binding of the oxygen in the course of deoxidation of the steel with manganese, silicon and / or aluminum is usually common.
  • the resulting oxides can cause negative properties as defects in the material.
  • the oxygen content in the steel should therefore 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 through solid solution strengthening and improves hardenability. In general, however, attempts are made to lower the phosphorus content as much as possible, since it has a strong tendency to segregate due to its low solubility in the solidifying medium and, to a large extent, its toughness reduced. Due to the accumulation of phosphorus at the grain boundaries, grain boundary breaks occur. In addition, phosphorus increases the transition temperature from tough to brittle behavior up to 300 ° C. During hot rolling, phosphorus oxides close to the surface can lead to cracks at the grain boundaries.
  • phosphorus is used in small amounts ( ⁇ 0.1% by weight) as a micro-alloy element due to its low cost and high strength increase, for example in higher-strength IF steels (interstitial free), bake hardening steels or in some Alloy concepts for dual-phase steels.
  • the steel according to the invention differs from known analytical concepts which use phosphorus as a mixed crystal former, inter alia, in that phosphorus is not added but is set as low as possible.
  • the phosphorus content in the steel according to the invention is limited to amounts that are unavoidable in steel production.
  • S sulfur
  • MnS manganese sulfide
  • the manganese sulfides are often rolled out in lines during the rolling process and act as nucleation sites for the transformation. In the case of diffusion-controlled transformation in particular, this leads to a lined structure and, if the lined structure is very pronounced, can lead to deteriorated mechanical properties (e.g. pronounced martensite ropes instead of distributed martensite islands, anisotropic material behavior, reduced elongation at break).
  • the sulfur content of the steel according to the invention is limited to 0.0050% by weight, advantageously to 0,00 0.0025% by weight or optimally to 0.0020% by weight or to amounts that are unavoidable in steel production .
  • Leaierunas elements are usually added to the steel in order to specifically influence certain properties.
  • An alloying element can influence different properties in different steels. The effect generally depends heavily on the amount and the state of the solution in the material.
  • Carbon (C) is considered to be the most important alloying element in steel. It is through its targeted introduction of up to 2.06% by weight that iron becomes steel. The carbon content is often drastically reduced during steel production. In the case of dual-phase steels for continuous hot-dip refining, its proportion according to EN 10346 or VDA 239-100 is a maximum of 0.180% by weight; a minimum value is not specified.
  • the steel according to the invention contains carbon contents of less than or equal to 0.115% by weight.
  • Silicon (Si) binds oxygen during casting and is therefore used to calm the steel during deoxidation. It is important for the later steel properties that the segregation coefficient is significantly lower than that of manganese, for example (0.16 compared to 0.87). Segregation generally leads to a linear arrangement of the structural components, which deteriorates the deformation properties, for example the hole expansion and flexibility.
  • the latter is due, among other things, to the fact that silicon reduces the solubility of carbon in ferrite and increases the activity of carbon in ferrite, thus preventing the formation of carbides, which, as brittle phases, reduce ductility, which in turn improves formability.
  • the low strength-increasing effect of silicon within the range of the steel according to the invention creates the basis for a broad process window.
  • silicon in the range according to the invention has led to further surprising effects described below.
  • the retardation of carbide formation described above could e.g. can also be brought about by aluminum.
  • aluminum forms stable nitrides, so that insufficient nitrogen is available for the formation of carbonitrides with micro-alloy elements.
  • This problem does not exist because silicon is alloyed with silicon, since silicon does not form carbides or nitrides.
  • silicon has an indirect positive effect on the formation of precipitates through microalloys, which in turn have a positive effect on the strength of the material. Since the increase in the transformation temperatures caused by silicon tends to increase the grain size, a microalloy with niobium, titanium and boron is particularly useful, as is the targeted adjustment of the nitrogen content in the steel according to the invention.
  • the atmospheric conditions during the annealing treatment in a continuous hot-dip coating system cause a reduction of iron oxide, which e.g. can form on the surface during cold rolling or as a result of storage at room temperature.
  • the gas atmosphere is oxidizing with the consequence that segregation and selective oxidation of these elements can occur.
  • the selective oxidation can take place both externally, that is to say 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 means of a chemical-mechanical or thermal-hydromechanical pre-cleaning.
  • a chemical-mechanical or thermal-hydromechanical pre-cleaning In order to prevent silicon oxides from reaching the strip surface, methods must also be used which promote the internal oxidation of the alloying elements below the material surface. Different measures are used here, depending on the system configuration.
  • the internal oxidation of the alloying elements can be specifically influenced by setting the oxygen partial pressure in the furnace atmosphere (N2-H2 protective gas atmosphere).
  • the set oxygen partial pressure must satisfy the following equation, whereby the furnace temperature is between 700 and 950 ° C.
  • Si, Mn, Cr, B denote the corresponding alloy proportions in the steel in% by weight and pO 2 denotes the partial pressure of oxygen in mbar.
  • the Selective oxidation of the alloying elements can also be influenced via the gas atmosphere in the furnace area.
  • the oxygen partial pressure and thus the oxidation potential for iron and the alloying elements can be adjusted via the combustion reaction in the NOF. This is to be set in such a way that the oxidation of the alloying elements takes place internally below the steel surface and, if necessary, a thin iron oxide layer is formed on the steel surface after passing through the NOF area. This is achieved e.g. by reducing the CO value below 4% by volume.
  • the iron oxide layer that may have formed is reduced under an N2-H2 protective gas atmosphere and the alloying elements are further oxidized internally.
  • the set oxygen partial pressure in this furnace area must satisfy the following equation, the furnace temperature being between 700 and 950 ° C.
  • Si, Mn, Cr, B denote the corresponding alloy proportions in the steel in% by weight and pO 2 denotes the partial pressure of oxygen in mbar.
  • the dew point of the gas atmosphere N 2 -H 2 protective gas atmosphere
  • the oxygen partial pressure must be set so that oxidation of the strip is avoided before it is immersed in the weld pool. Dew points in the range from -30 to -40 ° C have proven to be advantageous.
  • hot-dip coating here e.g. hot-dip galvanizing
  • the process route chosen is continuous annealing with subsequent electrolytic galvanizing (see method 1 in Figure 6a )
  • electrolytic galvanizing pure zinc is deposited directly on the strip surface.
  • pure zinc is deposited directly on the strip surface.
  • it In order not to hinder the flow of electrons between the steel strip and the zinc ions and thus the galvanization, it must be ensured that there is no extensive oxide layer on the strip surface. This condition is usually ensured by a standard reducing atmosphere during the annealing and a pre-cleaning before the electrolysis.
  • the minimum silicon content is set at 0.200% by weight and the maximum silicon content at 0.300% by weight.
  • Manganese (Mn) is added to almost all steels for desulphurization in order to convert the harmful sulfur into manganese sulphides. Manganese also increases the strength of the ferrite through solid solution strengthening and shifts the ⁇ - / ⁇ -conversion to lower temperatures.
  • manganese tends to form oxides on the steel surface during the annealing treatment.
  • manganese oxides eg MnO
  • Mn mixed oxides eg Mn 2 SiO 4
  • manganese with a low Si / Mn or Al / Mn ratio is to be regarded as less critical, since globular oxides rather than oxide films are formed. Nevertheless, high manganese contents can negatively affect the appearance of the zinc layer and the zinc adhesion.
  • the manganese content is set at 1.700 to 2.300% by weight.
  • the manganese content is preferably in a range between ⁇ 1.700 and ⁇ 2.000% by weight, with strip thicknesses of 1.00 to 2.00 mm between ⁇ 1.850 and ⁇ 2.150% by weight for strip thicknesses over 2.00 mm between ⁇ 2.000 and ⁇ 2.300% by weight.
  • YS MPa 53.9 + 32.34 Weight . - % Mn + 83.16 Weight . - % Si + 354.2 Weight . - % N + 17.402 d - 1 / 2
  • the coefficients of manganese and silicon are approximately the same for both the yield point and the tensile strength, which means that manganese can be substituted by silicon.
  • chromium (Cr) in dissolved form can considerably increase the hardenability of steel, even in small quantities.
  • chromium causes particles to solidify in the form of chromium carbides if the temperature is controlled accordingly. The associated increase in the number of nucleation sites while at the same time reducing the carbon content leads to a reduction in hardenability.
  • chromium In dual-phase steels, the addition of chromium mainly improves the hardenability. In the dissolved state, chromium shifts the pearlite and bainite transformation for longer times and at the same time lowers the martensite start temperature.
  • chromium significantly increases the tempering resistance, so that there is almost no loss of strength in the hot-dip bath.
  • Chromium is also a carbide former. If chromium-iron mixed carbides are present, the austenitizing temperature must be selected high enough before hardening to loosen the chromium carbides. Otherwise, the increased number of germs can lead to a deterioration in hardenability.
  • Chromium also tends to form oxides on the steel surface during the annealing treatment, which can degrade the hot-dip quality.
  • the above-mentioned measures for setting 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 contents of 0.280 to 0.480% by weight.
  • Molybdenum (Mo) Since the addition of molybdenum is not necessary with the present alloy concept, the molybdenum content is limited to the unavoidable amounts accompanying the steel.
  • 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 rate of corrosion.
  • copper In connection with oxygen, copper can form harmful oxides at the grain boundaries, which can have negative effects, especially for hot forming processes.
  • the copper content is therefore set at 0.050% by weight and is therefore limited to quantities that are unavoidable in steel production.
  • Nickel (Ni) In combination with oxygen, nickel can form harmful oxides at the grain boundaries, which can have negative effects, especially for hot forming processes.
  • the nickel content is therefore set at 0.050% by weight and is therefore limited to quantities that are unavoidable in steel production.
  • Vanadium (V) Since the present alloy concept does not require the addition of vanadium, the vanadium content is limited to the unavoidable amounts accompanying the steel.
  • Aluminum (Al) is usually added to steel in order to bind the oxygen and nitrogen dissolved in the iron. Oxygen and nitrogen are converted into aluminum oxides and aluminum nitrides. By increasing the nucleation sites, these precipitates can bring about grain refinement and thus increase the toughness properties and strength values.
  • Titanium nitrides have a lower enthalpy of formation and are formed at higher temperatures.
  • the aluminum content is therefore limited to 0.020 to a maximum of 0.060% by weight and is added to calm the steel.
  • Niobium works in steel in different ways. During hot rolling in the finishing train, it delays recrystallization through the formation of finely distributed precipitates, which increases the density of nuclei and results in a finer grain after conversion. The proportion of dissolved niobium also has a recrystallization-inhibiting effect. The precipitates 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 from 0.005% by weight and is most evident from 0.010 to 0.050% by weight of niobium. The precipitates also prevent grain growth during (partial) austenitization in hot-dip galvanizing. No additional effect is to be expected above 0.050% by weight of niobium. With regard to the effect to be achieved by niobium, contents of 0.020 to 0.040% by weight have proven to be advantageous.
  • Titanium (Ti) Due to its high affinity for nitrogen, titanium is primarily precipitated as TiN during solidification. It also occurs together with niobium as mixed carbide. TiN is of great importance for the grain size stability in the pusher 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 hinder the grain growth. Titanium also has a retarding effect on recrystallization during hot rolling, but is less effective than niobium. Titanium works by precipitation hardening. The larger TiN particles are less effective than the more finely divided mixed carbides. The best effectiveness is achieved in the range from 0.005 to 0.050% by weight and advantageously in the range from 0.020 to 0.050% by weight of titanium.
  • Boron is an extremely effective alloying agent for increasing hardenability, which is already effective in very small amounts (from 5 ppm). The martensite start temperature remains unaffected.
  • boron must be in a solid solution. Since it has a high affinity for nitrogen, the nitrogen must first be bound, preferably by the stoichiometrically necessary amount of titanium. Because of its low solubility in iron, the dissolved boron is preferentially deposited on the austenite grain boundaries. There it partially forms Fe-B carbides, which are coherent and reduce the grain boundary energy. Both effects delay the formation of ferrite and pearlite and thus increase the hardenability of the steel.
  • boron contents are harmful, however, as iron boride can form, which has a negative effect on the hardenability, formability and toughness of the material affects. Boron also tends to form oxides or mixed oxides during annealing during continuous hot-dip coating, which deteriorate the galvanizing quality.
  • the above-mentioned measures for setting the furnace areas during continuous hot dip coating reduce the formation of oxides on the steel surface.
  • the boron content for the alloy concept according to the invention is set at values of 5 to 60 ppm, advantageously at 40 or optimally at 20 ppm.
  • Nitrogen (N) can be both an alloying element and an accompanying element from steel production.
  • the N content is therefore set at values from 0.0020 to 0.0120% by weight. It has proven to be advantageous for maintaining the required properties of the steel if the nitrogen content is added as a function of the sum of Ti + Nb + B.
  • the nitrogen content should be maintained at values of ⁇ 20 to ⁇ 90 ppm.
  • nitrogen contents of 40 to 120 ppm have proven to be advantageous.
  • niobium and titanium contents of 0.01 0.100% by weight have proven to be advantageous and, due to the basic interchangeability of niobium and titanium, up to a minimum niobium content of 10 ppm and for cost reasons of 0.090% by weight are particularly advantageous .
  • Calcium (Ca) An addition of calcium in the form of calcium-silicon mixed compounds causes deoxidation and desulfurization of the molten phase in steel production. In this way, reaction products are transferred to the slag and the steel is cleaned. The increased purity leads to better properties according to the invention in the end product.
  • the annealing temperatures for the dual-phase structure to be achieved are between approx. 700 and 950 ° C. for the steel according to the invention, so that, depending on the temperature range, a partially austenitic (two-phase region) or a fully austenitic structure (austenitic region) is achieved.
  • the tests also showed that the set structural proportions after the intercritical annealing between A c1 and A c3 or the austenitizing annealing via A c3 with subsequent controlled cooling even after a further process step of hot-dip refining at temperatures between 400 and 470 ° C, for example with zinc or Zinc-magnesium are preserved.
  • hot-dip refined material can be used both as hot strip and as cold, post-rolled hot strip or cold strip in the passivated form (cold re-rolled) or untreated condition and / or in the stretch-bent or non-stretch-bent condition and also in the heat-treated condition (overaging).
  • This state is referred to below as the initial state.
  • Steel strips in the present case as hot strip, cold re-rolled hot strip or cold strip, made from the alloy composition according to the invention, are also distinguished during further processing by a high degree of resistance to edge cracks.
  • the hot strip is produced according to the invention with final rolling temperatures in the austenitic region above A r3 and at coiling temperatures above the bainite start temperature (variant A).
  • the hot strip is produced according to the invention with final rolling temperatures in the austenitic area above A r3 and coiling temperatures below the bainite start temperature (variant B).
  • Figure 1 shows schematically the process chain for the production of a strip from the steel according to the invention.
  • the different process routes relating to the invention are shown.
  • the process route is the same for all steels according to the invention up to the hot rolling (final rolling temperature), after which there are different process routes 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-rolled strip or soft-annealed cold-rolled strip can also be cold-rolled and galvanized.
  • Material can also optionally be processed without hot-dip finishing, i.e. only in the context of continuous annealing with and without subsequent electrolytic galvanizing.
  • a complex component can now be manufactured from the optionally coated material. This is followed by the hardening process, during which, according to the invention, cooling is carried out in air.
  • a tempering stage can complete the thermal treatment of the component.
  • Figure 2 shows schematically the time-temperature profile of the process steps of hot rolling and continuous annealing of strips made from the alloy composition according to the invention. It shows the time and temperature-dependent conversion for the hot rolling process as well as for heat treatment after cold rolling, component production, tempering and optional tempering.
  • Figure 3 shows the chemical composition of the examined steels in the upper half of the table. Alloys according to the invention LH®1000 were compared with the reference grades LH®800 / LH®900.
  • the alloys according to the invention have, in particular, significantly increased contents of Nb and lower contents of Cr and no additional alloying of V and Mo.
  • Figure 4 shows the mechanical parameters along the rolling direction of the steels examined, with target parameters to be achieved for the air-hardened state ( Figure 4a ), the determined values in the non-air-hardened initial state ( Figure 4b ) and in the air-hardened state ( Figure 4c ).
  • the specified values to be achieved are reliably achieved.
  • Figure 5 shows the results of the hole expansion tests according to ISO 16630 (absolute values).
  • the results of the hole expansion tests for variant A are shown, each for process 2 ( Figure 6b , 2.0 mm, example 1) and procedure 3 ( Figure 6c , 2.0 mm, example 2).
  • the examined materials have a sheet thickness of 2.0 mm.
  • the results apply to the test according to ISO 16630.
  • Method 2 corresponds to annealing, for example, on a hot-dip galvanizing with a combined directly fired furnace and radiant tube furnace, as shown in FIG Figure 6b is described.
  • the method 3 corresponds, for example, to a process control in a continuous annealing plant, as shown in FIG Figure 6c is described.
  • an induction furnace can be used to reheat the steel directly in front of the zinc bath.
  • the Figure 6 shows schematically three variants of the temperature-time curves according to the invention in the annealing treatment and cooling and in each case different austenitizing conditions.
  • Procedure 1 shows the annealing and cooling of the cold or hot rolled or cold re-rolled steel strip produced in a continuous annealing plant.
  • the tape is heated to a temperature in the range of about 700 to 950 ° C (Ac1 to Ac3).
  • the annealed steel strip is then cooled from the annealing temperature at a cooling rate between approx. 15 and 100 ° C / s to an intermediate temperature (ZT) of approx. 200 to 250 ° C.
  • ZT intermediate temperature
  • a second intermediate temperature (approx. 300 to 500 ° C) is not shown in this schematic illustration.
  • the steel strip is then cooled in air at a cooling rate between approx. 2 and 30 ° C / s until room temperature (RT) is reached, or the cooling is maintained at a cooling rate between approx. 15 and 100 ° C / s down to room temperature .
  • RT room temperature
  • Procedure 2 shows the process according to method 1, but the cooling of the steel strip for the purpose of hot-dip finishing is briefly interrupted when passing through the hot-dip vessel, in order to then cool down at a cooling rate of between approx. 15 and 100 ° C / s up to an intermediate temperature of approx. 200 to continue up to 250 ° C.
  • the steel strip is then cooled in air at a cooling rate between approx. 2 and 30 ° C./s until room temperature is reached.
  • Procedure 3 ( Figure 6c ) also shows the process according to method 1 for a hot dip refinement, but the cooling of the steel strip is interrupted by a short pause (approx. 1 to 20 s) at an intermediate temperature in the range of approx. 200 to 400 ° C and down to the temperature ( ST), which is necessary for hot dip refining (approx. 400 to 470 ° C), is reheated.
  • the steel strip is then cooled again to an intermediate temperature of approx. 200 to 250 ° C.
  • a cooling rate of approx. 2 and 30 ° C / s the steel strip is finally cooled in air until room temperature is reached.
  • Example 1 (cold strip) (alloy composition in% by weight)
  • a hot-dip refined, air-hardened steel strip with the following parameters was processed in an annealing simulator.
  • the steel according to the invention After the tempering, the steel according to the invention has a structure which consists of martensite, bainite and retained austenite.
  • This steel shows the following characteristics after air hardening (initial values in brackets, non-tempered condition): - yield strength (Rp0.2) 814 MPa (530 MPa) - tensile strength (Rm) 1179 MPa (855 MPa) - elongation at break (A80) 5.8% (16.1%) - A5 stretch 12.9% (-) - Bake hardening index (BH2) 58 MPa - Hole expansion ratio according to ISO 16630 - (21%) - Bending angle according to VDA 238-100 (lengthways, crossways) - (88 ° / 77 °) along the rolling direction and would correspond to an LH®1000, for example.
  • the yield strength ratio Re / Rm in the longitudinal direction was 62% in the initial state.
  • Example 2 (cold strip) (alloy composition in% by weight)
  • the material was previously hot-rolled at a final rolling target temperature of 910 ° C and coiled to a thickness of 4.09 mm at a target reel temperature of 650 ° C and, after pickling, cold-rolled without additional heat treatment (e.g. hood annealing).
  • the hot-dip coated steel was processed in an annealing simulator in the same way as a tempering process (air hardening) with the following parameters. Annealing temperature 870 ° C Hold time 120 s Transport time max. 5 s (without energy supply) Subsequent cooling in the air
  • the steel according to the invention After the tempering, the steel according to the invention has a structure which consists of martensite, bainite and retained austenite.
  • This steel shows the following characteristics after air hardening (initial values in brackets, non-tempered condition): - yield strength (Rp0.2) 803 MPa (502 MPa) - tensile strength (Rm) 1113 MPa (815 MPa) - elongation at break (A80) 13.1% (18.9%) - A5 stretch 7.1% (-) - Bake hardening index (BH2) 53 MPa - Hole expansion ratio according to ISO 16630 - (31%) - Bending angle according to VDA 238-100 (lengthways, crossways) - (95 ° / 90 °) along the rolling direction and would correspond to an LH®1000, for example.
  • the yield strength ratio Re / Rm in the longitudinal direction was 62% in the initial state.

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Claims (25)

  1. Procédé de fabrication d'une bande en acier laminée à froid ou à chaud, à partir d'un acier à plusieurs phases, à très haute résistance, autotrempant, présentant des résistances minimales à la traction dans le sens longitudinal et dans le sens transversal par rapport à la direction du laminage, avant le durcissement à l'air, de 750 MPa, présentant d'excellentes propriétés de façonnage, consistant en les éléments suivants, en les teneurs suivantes en % en poids C ≥ 0,075 jusqu'à ≤ 0,115 Si ≥ 0,200 jusqu'à ≤ 0,300 Mn ≥ 1,700 jusqu'à ≤ 2,300 Cr ≥ 0,280 jusqu'à ≤ 0,480 Al ≥ 0,020 jusqu'à ≤ 0,060 N ≥ 0,0020 jusqu'à ≤ 0,0120 S ≤ 0,0050 Nb ≥ 0,005 jusqu'à ≤ 0,050 Ti ≥ 0,005 jusqu'à ≤ 0,050 B ≥ 0,0005 jusqu'à ≤ 0,0060 Ca ≥ 0,0005 jusqu'à ≤ 0,0060 Cu ≤ 0,050 Ni ≤ 0,050
    le reste étant constitué de fer, y compris les impuretés usuelles d'accompagnement de l'acier, provoquées par l'élaboration, procédé dans lequel, l'objectif étant une fenêtre de procédé aussi large que possible lors du recuit à passage continu de bandes à chaud ou à froid en cet acier, on ajuste la somme des teneurs en Mn+Si+Cr, indépendamment de l'épaisseur de la bande à produire, comme suit :
    jusqu'à 1,00 mm : somme de Mn+Si+Cr ≥ 2,350 et ≤ 2,500 % en poids
    supérieure à 1,00 jusqu'à 2,00 mm : somme de Mn+Si+Cr > 2,500 et ≤ 2,950 % en poids
    supérieure à 2,00 mm : somme de Mn+Si+Cr > 2,950 et ≤ 3,250 % en poids, et
    pour des épaisseurs de bande jusqu'à 1,00 mm, la teneur en Mn est ≥ 1,700 jusqu'à ≤ 2,000 %,
    pour des épaisseurs de bande supérieures 1,00 jusqu'à 2,00 mm, la teneur en Mn est ≥ 1,850 jusqu'à ≤ 2,150 %,
    pour des épaisseurs de bande supérieures à 2,00 mm, la teneur en Mn est ≥ 2,000 jusqu'à ≤ 2,300 %,
    dans lequel la structure recherchée est produite pendant un recuit à passage continu,
    dans lequel la bande en acier laminée à froid ou à chaud est, pendant le recuit à passage continu, chauffée à une température dans la plage de 700 à 950 °C, et la bande en acier recuite est ensuite refroidie à partir de la température de recuit, à une vitesse de refroidissement entre environ 15 et 100 °C/s, jusqu'à une première température intermédiaire d'environ 300 à 500 °C, puis à une vitesse de refroidissement entre environ 15 et 100 °C/s jusqu'à une deuxième température intermédiaire d'environ 160 à 250 °C, puis la bande en acier est refroidie à une vitesse de refroidissement d'environ 2 à 30 °C/s jusqu'à atteindre la température ambiante dans l'air, ou le refroidissement est maintenu à une vitesse de refroidissement entre environ 15 et 100 °C/s de la première température intermédiaire jusqu'à la température ambiante.
  2. Procédé selon la revendication 1, caractérisé en ce que, pour des épaisseurs de bande de 1,00 mm, la teneur en C est ≤ 0,100 % et l'équivalent carbone CEV(IIW) est ≤ 0,56 %.
  3. Procédé selon la revendication 1, caractérisé en ce que, pour des épaisseurs de bande supérieures à 1,00 jusqu'à 2,00 mm, la teneur en C est ≤ 0,105 % et l'équivalent carbone CEV(IIW) est ≤ 0,59 %.
  4. Procédé selon la revendication 1, caractérisé en ce que, pour des épaisseurs de bande supérieures à 2,00 mm, la teneur en C est ≤ 0,115 % et l'équivalent carbone CEV(IIW) est ≤ 0,62 %.
  5. Procédé selon l'une des revendications 1 à 4, caractérisé en ce que, pour une somme de Ti+Nb+B ≥ 0,010 jusqu'à ≤ 0,050 %, la teneur en N est ≥ 0,0020 à ≤ 0,0090 %.
  6. Procédé selon l'une des revendications 1 à 5, caractérisé en ce que, pour la somme de Ti+Nb+B > 0,050 %, la teneur en N est ≥ 0,0040 jusqu'à ≤ 0,0120 %.
  7. Procédé selon l'une des revendications 1 à 6, caractérisé en ce que la teneur en S est ≤ 0,0025 %.
  8. Procédé selon l'une des revendications 1 à 7, caractérisé en ce que la teneur en S est ≤ 0,0020 %.
  9. Procédé selon l'une des revendications 1 à 8, caractérisé en ce que la teneur en Ti est ≥ 0,020 ≤ 0,050 %.
  10. Procédé selon l'une des revendications 1 à 9, caractérisé en ce que la teneur en Nb est ≥ 0,020 jusqu'à ≤ 0,040 %.
  11. Procédé selon l'une des revendications 1 à 10, caractérisé en ce que la somme Nb+Ti est ≥ 0,01 jusqu'à ≤ 0,100 %.
  12. Procédé selon l'une des revendications 1 à 10, caractérisé en ce que la somme Nb+Ti est ≥ 0,01 jusqu'à ≤ 0,090 %.
  13. Procédé selon l'une des revendications 1 à 12, caractérisé en ce que la somme Ti+Nb+B est ≥ 0,01 jusqu'à ≤ 0,106 %.
  14. Procédé selon la revendication 13, caractérisé en ce que la somme Ti+Nb+B est ≥ 0,01 jusqu'à ≤ 0,097 %.
  15. Procédé selon l'une des revendications 1 à 14, caractérisé en ce que la teneur en Ca est ≥ 0,005 ≤ 0,0030 %.
  16. Procédé selon l'une des revendications 1 à 15, caractérisé en ce que les additions de silicium et de manganèse sont interchangeables, eu égard aux propriétés de résistance mécanique à atteindre, selon la relation suivante : YS MPa = 160,7 + 147,9 % Si + 161,1 % Mn
    Figure imgb0014
     TS MPa = 324,8 + 189,4 % Si + 174,1 % Mn
    Figure imgb0015
     (YS = limite élastique ; TS = résistance à la traction)
  17. Procédé de fabrication d'une bande en acier laminée à froid ou à chaud à partir d'un acier à plusieurs phases pouvant subir une trempe et un revenu à l'air selon l'une des revendications 1 à 16, dans lequel la structure souhaitée est produite pendant un recuit à passage continu,
    caractérisé en ce que,
    lors d'un affinage par métallisation au trempé, après le chauffage puis le refroidissement, on maintient le refroidissement avant immersion dans le bain de fusion et, après l'affinage par métallisation au trempé, on poursuit le refroidissement à une vitesse de refroidissement entre environ 15 et 100 °C/s jusqu'à une température intermédiaire d'environ 200 à 250 °C, puis on refroidit la bande en acier à une vitesse de refroidissement d'environ 2 à 30 °C/s jusqu'à atteindre la température ambiante à l'air.
  18. Procédé de fabrication d'une bande en acier laminée à froid ou à chaud à partir d'un acier à plusieurs phases pouvant subir une trempe et un revenu à l'air selon l'une des revendications 1 à 16, dans lequel la structure souhaitée est produite pendant un recuit à passage continu,
    caractérisé en ce que,
    lors d'un affinage par métallisation au trempé, après le chauffage puis le refroidissement à la température ambiante d'environ 200 à 250 °C avant immersion dans le bain de fusion, on maintient la température pendant environ 1 à 20 s, puis on chauffe de nouveau la bande en acier à une température d'environ 400 à 470 °C et, après la fin d'un affinage par métallisation au trempé, on procède à un refroidissement à une vitesse de refroidissement entre environ 15 et 100°C/s jusqu'à une température intermédiaire d'environ 200 à 250 °C, puis on refroidit jusqu'à la température ambiante à l'air avec une vitesse de refroidissement d'environ 2 à 30 °C/s.
  19. Procédé selon l'une des revendications 1 à 18,
    caractérisé en ce que,
    lors du recuit à passage continu, on augmente le potentiel d'oxydation lors d'un recuit avec une configuration d'installation consistant en une section de four à chauffe directe (NOF) et un four à tubes radiants (RTF) grâce à une teneur en CO dans le NOF inférieure à 4 % en volume, la pression partielle d'oxygène de l'atmosphère du four, réductrice pour le fer, étant ajustée, pour une température du four de 700 à 950 °C, selon 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 représentent les proportions correspondantes d'alliage dans l'acier en % en poids et pO2 représente la pression partielle d'oxygène en mbar, et, pour éviter l'oxydation de la bande, on ajuste directement avant immersion dans le bain de fusion le point de rosée de l'atmosphère gazeuse à -30 °C ou moins.
  20. Procédé selon l'une des revendications 1 à 18, caractérisé en ce que, dans un recuit utilisant uniquement un four à tubes radiants, la pression partielle d'oxygène de l'atmosphère du four, pour une température du four de 700 à 950 °C, satisfait à l'équation suivante − 12 > Log pO 2 ≥ − 5 * Si − 0,25 − 3 * Mn − 0,5 − 0,1 * Cr − 0,5 − 7 * − ln B 0,5
    Figure imgb0017
     dans laquelle Si, Mn, Cr, B représentent les proportions correspondantes d'alliage dans l'acier en % en poids et pO2 représente la pression partielle d'oxygène en mbar, et, pour éviter l'oxydation de la bande, on ajuste directement avant immersion dans le bain de fusion le point de rosée de l'atmosphère gazeuse à -30 °C ou moins.
  21. Procédé selon l'une des revendications 1 à 20, caractérisé en ce que la bande en acier est dressée après le traitement thermique ou l'affinage par métallisation au trempé.
  22. Procédé selon au moins l'une des revendications 1 à 21, caractérisé en ce que la bande en acier est dressée par traction et flexion après le traitement thermique ou l'affinage par métallisation au trempé.
  23. Procédé selon au moins l'une des revendications 17 à 22, caractérisé en ce que la bande en acier présente une valeur minimale du rapport d'expansion de trou selon ISO 16630 de 20 % dans son état avant le durcissement à l'air.
  24. Procédé selon au moins l'une des revendications 17 à 22, caractérisé en ce que la bande en acier présente une valeur minimale du rapport d'expansion de trou selon ISO 16630 de 30 % dans son état avant le durcissement à l'air.
  25. Procédé selon au moins l'une des revendications 17 à 22, caractérisé en ce que la bande en acier présente une valeur minimale du produit Rm x α (résistance à la traction x angle de pliage selon VDA 238-100) de 60 000 MPa.° dans son état avant le durcissement à l'air.
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US10640855B2 (en) 2020-05-05
US20180347018A1 (en) 2018-12-06
DE102014017273A1 (de) 2016-05-19
WO2016078643A9 (fr) 2016-07-14
RU2707769C2 (ru) 2019-11-29
KR20170084209A (ko) 2017-07-19
RU2017120940A (ru) 2018-12-20
RU2017120940A3 (fr) 2018-12-20
EP3221484A1 (fr) 2017-09-27

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