EP1929053A1 - Verfahren zur herstellung eines stahlteils mit mehrphasiger mikrostruktur - Google Patents

Verfahren zur herstellung eines stahlteils mit mehrphasiger mikrostruktur

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Publication number
EP1929053A1
EP1929053A1 EP06808157A EP06808157A EP1929053A1 EP 1929053 A1 EP1929053 A1 EP 1929053A1 EP 06808157 A EP06808157 A EP 06808157A EP 06808157 A EP06808157 A EP 06808157A EP 1929053 A1 EP1929053 A1 EP 1929053A1
Authority
EP
European Patent Office
Prior art keywords
steel
microstructure
blank
ferrite
cooling
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP06808157A
Other languages
English (en)
French (fr)
Other versions
EP1929053B1 (de
Inventor
Jacques Corquillet
Jacques Devroc
Jean-Louis Hochard
Jean-Pierre Laurent
Antoine Moulin
Nathalie Romanowski
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
ArcelorMittal France SA
Original Assignee
ArcelorMittal France SA
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Filing date
Publication date
Application filed by ArcelorMittal France SA filed Critical ArcelorMittal France SA
Priority to EP06808157A priority Critical patent/EP1929053B1/de
Priority to EP10010435A priority patent/EP2287344A1/de
Priority to PL06808157T priority patent/PL1929053T3/pl
Publication of EP1929053A1 publication Critical patent/EP1929053A1/de
Application granted granted Critical
Publication of EP1929053B1 publication Critical patent/EP1929053B1/de
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/185—Hardening; Quenching with or without subsequent tempering from an intercritical temperature
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • C21D1/673—Quenching devices for die quenching
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/12—Aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/26—After-treatment
    • C23C2/261—After-treatment in a gas atmosphere, e.g. inert or reducing 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets

Definitions

  • the present invention relates to a method of manufacturing a multi-phased microstructure steel piece homogeneous in each of the zones of said part, and having high mechanical characteristics.
  • TRIP steels this term means transformation induced plasticity
  • dual phase steels which combine a very high mechanical strength with very high possibilities of deformation.
  • TRIP steels have a microstructure composed of ferrite, residual austenite, and possibly bainite and martensite, which enables them to reach tensile strengths ranging from 600 to 1000 MPa.
  • the dual-phase steels have a microstructure composed of ferrite and martensite, which enables them to reach tensile strengths ranging from 400 MPa to more than 1200 MPa.
  • this type of parts it is cold forming, for example by stamping between tools, a blank cut in a cold rolled strip of dual phase steel or TRIP steel.
  • the deformation is not homogeneous throughout the room, some areas of the room will still contain residual austenite not transformed into martensite and therefore having a significant residual ductility, while other areas of the room having undergone significant deformation will present a ferrito- martensitic structure optionally comprising ductile bainite.
  • the object of the present invention is therefore to overcome the aforementioned drawbacks, and to propose a method of manufacturing a steel part comprising ferrite and having a homogeneous multi-phased microstructure in each of the zones of said part, and not exhibiting resilient return after forming a blank from a steel strip whose composition is typical of that of multi-phase microstructure steels.
  • the invention firstly provides a method for producing a steel having a multiphase microstructure, said microstructure comprising ferrite and being homogeneous in each of the regions of said part, comprising the steps of at :
  • V 1 0%, optionally, one or more elements such as Ni ⁇ 2.0% Cu ⁇ 2.0% S ⁇ 0.05%
  • the area of the different phases is measured in a section made along a plane perpendicular to the plane of the strip (this plane may be parallel to to the rolling direction, or parallel to the direction transverse to the rolling).
  • the different phases sought are revealed by a chemical attack adapted according to their nature.
  • the term "forming tool” means any tool that makes it possible to obtain a part from a blank, such as for example a stamping tool. This excludes cold or hot rolling tools.
  • the inventors have demonstrated that heating the blank to a holding temperature T1 between Ad and Ac3 gives, provided that the cooling rate is sufficient, a multi-phase microstructure comprising ferrite having mechanical properties. homogeneous regardless of the cooling rate of the blank between the tools.
  • the homogeneity of the mechanical properties is defined in the sense of the invention by a dispersion of the tensile strength Rm in a range of cooling rates ranging from 10 to 100 0 CVs less than 25%.
  • the invention has as its second object a steel part comprising ferrite and having a homogeneous multi-phased microstructure in each zone of said part, obtainable by said method.
  • the third object of the invention is a motorized land vehicle comprising said part.
  • FIG. 1 in which:
  • FIG. 1 is a photograph of a part obtained by cold forming (reference G) and a workpiece obtained by hot forming (reference A).
  • the method according to the invention consists in shaping hot, in a certain temperature range, a blank previously cut in a steel strip whose composition is typical of that of multi-phase microstructure steels, but which initially does not does not necessarily have a multi-phased structure, to form a steel part that acquires a multi-phase microstructure during its cooling between the formatting tools.
  • the inventors have furthermore demonstrated that, provided that the cooling rate is sufficient, a homogeneous multi-phased microstructure could be obtained whatever the rate of cooling of the blank between the tools.
  • the advantage of this invention lies in the fact that it is not necessary to form the multi-phased microstructure at the stage of manufacture of the hot sheet, or of its coating, and that forming it at The stage of manufacture of the part, by hot forming, ensures a homogeneous final multi-phased microstructure in each of the zones of the part, which is advantageous in the case of a use for absorption parts. energy, because the microstructure is not altered as is the case when cold forming of dual-phase steel or steel parts
  • the inventors have indeed verified that the energy absorption capacity of a part, determined by the tensile strength multiplied by the elongation (Rm ⁇ A), is greater when the part has been obtained. according to the invention than when it was obtained by cold forming of a dual phase steel blank or TRIP steel. Indeed, cold forming consumes some of the energy absorption capacity.
  • Another advantage of the invention lies in the fact that the hot shaping leads to a much higher shaping ability than cold.
  • a variety of wider shapes can be accessed and new designs of parts can be envisaged while retaining steel compositions whose characteristics, such as weldability, are known.
  • the part obtained has a multi-phase microstructure comprising ferrite at a proportion preferably greater than or equal to 25% by surface, and at least one of the following phases: martensite, bainite, residual austenite.
  • a proportion of at least 25% ferrite surface area makes it possible to give the steel ductility sufficient for the formed parts to have a high energy absorption capacity.
  • the steel blank to be shaped, for example by stamping, is previously cut either in a hot-rolled steel strip or in a cold rolled steel strip, the steel consisting of the following elements:
  • Manganese also plays a role in the inter-diffusion of iron and aluminum, when steel is coated with aluminum or an aluminum alloy.
  • silicon with a content of between 0.001 and 3.0% by weight. Silicon improves the elasticity limit Re of steel. However, above 3.0% by weight, the hot dipping of the steel becomes difficult, and the appearance of the zinc coating is unsatisfactory.
  • Aluminum with a content of between 0.005 and 3.0% by weight. Aluminum stabilizes ferrite. Its content must remain below 3.0% by weight to avoid damaging the weldability due to the presence of aluminum oxide in the welded zone. However, a minimum of aluminum is required to deoxidize the steel.
  • molybdenum at a content of less than or equal to 1.0% by weight. Molybdenum promotes the formation of martensite and increases the resistance to corrosion. However, an excess of molybdenum can promote the phenomenon of cold cracking in welded areas, and reduce the toughness of the steel.
  • chromium at a content of less than or equal to 1.5% by weight.
  • the chromium content must be limited to avoid surface appearance problems when galvanizing the steel.
  • phosphorus at a content less than or equal to 0.10% by weight. Phosphorus is added to reduce the amount of carbon and improve weldability, while maintaining an equivalent level of steel yield strength Re. However, beyond 0.10% by weight, it weakens the steel because of the increased risk of segregation defects, and the weldability is deteriorated.
  • titanium at a content of less than or equal to 0.20% by weight. Titanium improves the yield strength Re, however its content must be limited to 0.20% by weight to avoid the degradation of toughness.
  • Vanadium at a content of less than or equal to 1.0% by weight. Vanadium improves the yield strength Re by grain refinement and promotes the weldability of steel. However, above 1.0% by weight, the toughness of the steel is deteriorated and cracks may appear in the welded areas.
  • nickel at a content less than or equal to 2.0% by weight. Nickel increases the yield strength Re. Its content is generally limited to 2.0% by weight because of its high cost.
  • copper at a content less than or equal to 2.0% by weight. Copper increases the yield strength Re, however an excess of copper promotes the appearance of cracks during hot rolling, and degrades the hot formability of the steel.
  • sulfur at a content less than or equal to 0.05% by weight.
  • Sulfur is a segregating element whose content must be limited in order to avoid cracks during hot rolling.
  • niobium at a content less than or equal to 0.15% by weight.
  • Niobium promotes the precipitation of carbonitride, which increases the yield strength Re.
  • the weldability and hot formability are degraded.
  • the remainder of the composition is iron and other elements that are usually expected to be found as impurities resulting from steel making, in proportions that do not affect the properties of the steel. sought.
  • this metal coating is chosen from zinc or zinc alloy coatings (zinc-aluminum for example), and if it is also desired to withstand good heat resistance, the coatings of aluminum or aluminum alloy (aluminum-silicon for example). These coatings are deposited in a conventional manner either by hot dipping in a bath of liquid metal, by electrodeposition, or under vacuum.
  • the steel blank is heated to bring it to a holding temperature T1 greater than Ad but less than Ac3, and is maintained at this temperature T1 for a holding time M that is adjusted so that steel, after heating the blank, comprises a proportion of austenite greater than or equal to 25% by surface.
  • the heated blank is transferred into a forming tool to form a part, and cool it.
  • the cooling of the workpiece within the shaping tool is performed with a cooling rate V sufficient to prevent all of the austenite from becoming ferrite, and so that the microstructure of the steel after cooling the piece is a multi-phase microstructure comprising ferrite, and which is homogeneous in each of the areas of the room.
  • Homogeneous multi-phased microstructure in each of the zones of the part is understood to mean a microstructure having constancy in terms of proportion and morphology in each zone of the part, and in which the different phases are uniformly distributed.
  • the shaping tools can be cooled, for example by fluid circulation.
  • the clamping force of the shaping tool must be sufficient to ensure intimate contact between the blank and the tool, and ensure efficient and homogeneous cooling of the room.
  • Cold pre-deformation of the blank for example by profiling or cold stamping of the blank, before hot forming is advantageous insofar as it allows access to parts that may have a more complex geometry .
  • the method according to the invention is used to manufacture a steel part having a multi-phase microstructure comprising either ferrite and aluminum. martensite, either ferrite and bainite, or ferrite, martensite and bainite.
  • steel includes the following elements:
  • carbon having a content preferably of between 0.01 and 0.25% by weight, and more preferentially of between 0.08 and 0.15%.
  • the carbon content is limited to 0.25% by weight to limit the formation of martensite and thus avoid deterioration of ductility and formability.
  • silicon at a content preferably between 0.01 and 2.0% by weight, and more preferably between 0.01 and 0.50% by weight.
  • aluminum at a content preferably between 0.005 and 1.5% by weight, and more preferably between 0.005 and 1.0% by weight. It is preferable that the aluminum content is less than 1.5% by weight, so as to avoid the degradation of the spark weldability due to the formation of Al 2 O 3 aluminum oxide inclusions.
  • Molybdenum at a content preferably between 0.001 and 0.50% by weight, and more preferably between 0.001 and 0.10% by weight.
  • chromium at a content preferably less than or equal to 1.0% by weight, and more preferably less than or equal to 0.50% by weight.
  • phosphorus at a content preferably less than or equal to 0.10% by weight.
  • titanium at a content preferably less than or equal to 0.15% by weight.
  • niobium at a content preferably less than or equal to 0.15% by weight.
  • the blank is heated to a holding temperature T1 greater than Ad but lower than Ac3, so as to to control the proportion of austenite formed during the heating of the blank, and not to exceed the preferential upper limit of 75% of austenite surface area.
  • a proportion of austenite in the steel heated to a holding temperature T1 during a holding time M of between 25 and 75% by weight offers a good compromise in terms of the mechanical strength of the steel after shaping and regularity. mechanical characteristics of the steel thanks to the robustness of the process. Indeed, beyond 25% of austenite surface, sufficient hardening phases, such as for example martensite and / or bainite, are formed during the cooling of the steel so that the yield strength Re of the steel after shaping is sufficient.
  • the holding time of the steel blank at the holding temperature T1 depends essentially on the thickness of the strip.
  • the thickness of the strip is typically between 0.3 and 3 mm. Therefore, to form a proportion of austenite between 25 and 75% by surface, the holding time M is preferably between 10 and 1000 s. If the steel blank is maintained at a holding temperature T1 for a holding time M greater than 1000 s, the austenite grains increase and the elastic limit Re of the steel after forming will be limited. In addition, the hardenability of the steel is reduced and the surface of the steel oxidizes.
  • the cooling rate V of the steel part in the forming tool depends on the deformation and the quality of the contact between the tool and the steel blank. However, the cooling rate V must be sufficiently high for the desired multi-phased microstructure to be obtained, and is preferably greater than 10 ° C./s. With a cooling rate V less than or equal to 10 0 CVs, it is likely to form carbides that will contribute to degrade the mechanical characteristics of the part.
  • a multi-phase steel piece comprising more than 25% ferrite surface area is formed, the rest being martensite and / or bainite, the various phases being homogeneously distributed in each of the zones of the In a preferred embodiment of the invention, 25 to 75% ferrite surface area and 25 to 75% surface area of martensite and / or bainite are preferably formed.
  • the method according to the invention is used to manufacture a TRIP steel part.
  • TRIP steel a multiphase microstructure comprising ferrite, residual austenite, and possibly martensite and / or bainite.
  • steel includes the following elements:
  • the carbon plays a very important role on the formation of the microstructure and the mechanical properties: according to the invention, a bainitic transformation occurs from a high temperature austenitic structure, and bainitic ferrite slats are formed . Given the very solubility lower carbon in ferrite compared to austenite, the carbon of the austenite is rejected between the slats.
  • the precipitation of carbides, in particular of cementite intervenes very little.
  • the austenite interlatte is progressively enriched in carbon without the precipitation of carbides intervening. This enrichment is such that the austenite is stabilized, that is to say that the martensitic transformation of this austenite does not occur during cooling to room temperature.
  • Manganese at a content preferably between 0.50 and 3.0% by weight, and more preferably between 0.60 and 2.0% by weight.
  • Manganese promotes the formation of austenite, helps to reduce the martensitic transformation start temperature Ms and to stabilize the austenite. This addition of manganese also contributes to an effective hardening in solid solution and thus to obtaining a yield strength Re high.
  • the manganese content is more preferably between 0.60 and 2.0% by weight. In this way, the effects sought above are obtained without risk of formation of a harmful band structure that would come from a possible segregation of manganese during solidification.
  • silicon at a content preferably between 0.001 and 3.0% by weight, and more preferably between 0.01 and 2.0% by weight. Silicon stabilizes the ferrite and stabilizes the residual austenite at room temperature. Silicon inhibits the precipitation of cementite during cooling from austenite by considerably retarding the growth of carbides: this is because the solubility of silicon in cementite is very low and this element increases the activity of the cementite. carbon in the austenite. In this way, an eventual germ of cementite forming will be surrounded by a zone austenitic silicon-rich which will have been rejected at the precipitated-matrix interface.
  • This silicon-enriched austenite is also richer in carbon and the growth of cementite is slowed down because of the small diffusion resulting from the reduced carbon gradient between the cementite and the surrounding austenitic zone.
  • This addition of silicon thus contributes to stabilizing a sufficient amount of residual austenite to obtain a TRIP effect.
  • this addition of silicon makes it possible to increase the yield strength Re by means of hardening in solid solution.
  • an excessive addition of silicon causes the formation of strongly adherent oxides, which are difficult to eliminate during a stripping operation, and the possible appearance of surface defects due in particular to a lack of wettability in dip galvanizing operations.
  • the silicon content is preferably between 0.01 and 2.0% by weight.
  • aluminum with a content preferably of between 0.005 and 3.0% by weight. Like silicon, aluminum stabilizes ferrite and increases the formation of ferrite during the cooling of the blank. It is very slightly soluble in cementite and can be used as such to prevent the precipitation of cementite during maintenance at bainitic transformation temperature and stabilize the residual austenite.
  • molybdenum at a content preferably less than or equal to 1.0% by weight, and more preferably less than or equal to 0.60% by weight.
  • chromium at a content preferably less than or equal to 1.50% by weight.
  • the chromium content is limited to avoid surface appearance problems when galvanizing steel.
  • nickel at a content preferably less than or equal to 2.0% by weight.
  • Phosphorus in combination with silicon increases the stability of residual austenite by suppressing the precipitation of carbides.
  • sulfur at a content preferably less than or equal to 0.05% by weight.
  • titanium at a content preferably less than or equal to 0.20% by weight.
  • vanadium at a content preferably less than or equal to 1.0% by weight, and more preferably less than or equal to 0.60% by weight.
  • the remainder of the composition is iron and other elements that are usually expected to be found as impurities resulting from steel making, in proportions that do not affect the properties of the steel. sought.
  • the holding time of the steel blank at a holding temperature T1 greater than A1c1 but less than Ac3 essentially depends on the thickness of the strip.
  • the thickness of the strip is typically between 0.3 and 3 mm. Therefore, to form a proportion of austenite greater than or equal to 25% by surface, the holding time M is preferably between 10 and 1000 s. If the steel blank is maintained at a holding temperature T1 for a holding time M greater than 1000 s, the austenite grains increase and the elastic limit Re of the steel after forming will be limited. In addition, the hardenability of the steel is reduced and the surface of the steel oxidizes. On the other hand, if the blank is held for a holding time M less than 10 s, the proportion of austenite formed will be insufficient, and sufficient residual austenite and bainite will not be formed during the cooling of the part between the tool.
  • the cooling rate V of the steel part in the forming tool depends on the deformation and the quality of the contact between the tool and the steel blank. To obtain a steel part having a multi-phased microstructure TRIP, it is preferable that the cooling rate V is between 10 ° C./s and 200 ° C./s. In fact, below 10 ° C / s, ferrite and carbide will be essentially formed, and insufficient residual austenite and martensite, and above 200 ° C / s, essentially martensite will be formed. insufficient residual austenite.
  • the TRIP effect can advantageously be used to absorb energy in the event of high speed shocks. Indeed, during a significant deformation of a TRIP steel part, the residual austenite is gradually transformed into martensite by selecting the orientation of the martensite. This has the effect of reducing the residual stresses in the martensite, reducing the internal stresses in the part, and finally limiting the damage of the part, because the rupture thereof will take place for an elongation A more important than if it was not TRIP steel.
  • the inventors have carried out tests both on steels presenting on the one hand a composition typical of that of mutlphase microstructure steels comprising ferrite and martensite and / or bainite (point 1), and of on the other hand a composition typical of that of TRIP mutli-phased microstructure steels (point 2).
  • Blanks 400 x 600 mm in size are cut from a steel strip whose composition, indicated in Table I, is that of a steel grade DP780 (Dual Phase 780).
  • the strip has a thickness of 1.2 mm.
  • the temperature Ad of this steel is 705 0 C and the temperature Ac3 is 815 ° C.
  • the blanks are brought to a variable holding temperature T1, during a holding period of 5 minutes. Then, they are immediately transferred to a stamping tool in which they are both shaped and cooled with variable cooling rates V, keeping them in the tool for a period of 60 s.
  • the stamped parts are similar to an Omega shape structure
  • Table I chemical composition of the steel according to the invention, expressed in% by weight, the balance being iron or impurities.
  • Table II Mechanical characteristics and microstructure of stamped parts.
  • the purpose of this test is to show the interest of a hot shaping compared to a cold shaping, and to evaluate the elastic return.
  • a piece of DP780 grade steel is manufactured by cold stamping a blank cut from a 1.2 mm thick steel strip, the composition of which is indicated in Table I, but which, unlike the strip used in point 1, already has before stamping a multi-phased microstructure comprising 70% ferrite surface, 15% martensite surface, and 15% bainite surface.
  • Figure 1 shows that the coin formed by cold stamping (marked in the figure by the letter
  • G has a strong springback, compared to the piece A (see Table II) formed by hot stamping (marked by the letter A).
  • Blanks of dimension 200 X 500 mm are cut from a steel strip whose composition, indicated in Table III, is that of a TRIP 800 grade steel. a thickness of 1.2 mm.
  • the temperature Ad of this steel is 751 ° C. and the temperature Ac3 is 875 ° C.
  • the blanks are brought to a variable holding temperature T1, during a hold time of 5 minutes, and then immediately transferred to a stamping tool in which they are both shaped and cooled with a cooling rate V of 45 ° C / s, keeping them in the tool for 60 s.
  • the stamped parts are similar to an Omega shape structure.
  • Table III chemical composition of the steel according to the invention, expressed in% by weight, the balance being iron or impurities

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  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
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  • Heat Treatment Of Steel (AREA)
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EP06808157A 2005-09-21 2006-09-18 Verfahren zur herstellung eines stahlteils mit mehrphasiger mikrostruktur Active EP1929053B1 (de)

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EP1929053B1 (de) 2011-06-22
US20120211128A1 (en) 2012-08-23
ZA200802385B (en) 2009-01-28
EP1767659A1 (de) 2007-03-28
BRPI0616261B1 (pt) 2014-02-04
KR101453697B1 (ko) 2014-10-22
CA2623146C (fr) 2011-03-22
US10294557B2 (en) 2019-05-21
ATE513932T1 (de) 2011-07-15
CN101292049A (zh) 2008-10-22
RU2008115444A (ru) 2009-10-27
KR20130017102A (ko) 2013-02-19
RU2403291C2 (ru) 2010-11-10
MA29790B1 (fr) 2008-09-01
CN101292049B (zh) 2011-12-14
UA96739C2 (ru) 2011-12-12
CA2623146A1 (fr) 2007-03-29
KR20080053312A (ko) 2008-06-12
WO2007034063A1 (fr) 2007-03-29
KR20110121657A (ko) 2011-11-07
KR20120099526A (ko) 2012-09-10
JP5386170B2 (ja) 2014-01-15
US8114227B2 (en) 2012-02-14
ES2366133T3 (es) 2011-10-17
EP2287344A1 (de) 2011-02-23
JP2009508692A (ja) 2009-03-05
PL1929053T3 (pl) 2011-10-31
US20080308194A1 (en) 2008-12-18
BRPI0616261A2 (pt) 2011-06-14

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