EP2817428B2 - Acier haute résistance à faible densité durcissable par cuisson et procédé de production de cet acier - Google Patents

Acier haute résistance à faible densité durcissable par cuisson et procédé de production de cet acier Download PDF

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Publication number
EP2817428B2
EP2817428B2 EP13704616.5A EP13704616A EP2817428B2 EP 2817428 B2 EP2817428 B2 EP 2817428B2 EP 13704616 A EP13704616 A EP 13704616A EP 2817428 B2 EP2817428 B2 EP 2817428B2
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steel
strip
hot
ppm
cold
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EP2817428B1 (fr
EP2817428A1 (fr
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Cheng Liu
Radhakanta RANA
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Tata Steel Nederland Technology BV
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Tata Steel Nederland Technology BV
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
    • C21D8/0284—Application of a separating or insulating coating
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/49—Method of mechanical manufacture
    • Y10T29/4998—Combined manufacture including applying or shaping of fluent material
    • Y10T29/49988—Metal casting
    • Y10T29/49991—Combined with rolling

Definitions

  • the invention relates to a high strength bake-hardenable low density steel and to a method for producing said steel.
  • ferritic steel strip or sheet comprising, in weight percent
  • the steel according to the invention has a tailored chemical composition to allow the steel to contain carbon in solid solution (C_solute) after the annealing and optional galvanising step.
  • This carbon in solid solution allows the steel to be bake-hardenable e.g. in a paint-baking cycle.
  • the car component is formed from the steel coming of the mill, and the component is painted and baked after it has been formed into its final shape.
  • the steel according to the invention combines the good formability prior to forming a car component, i.e. before the paint-baking operation, with a higher strength after the paint-baking operation.
  • solute carbon solute carbon
  • the level of solute carbon may also not exceed a critical upper value because the steel is preferably free from natural ageing.
  • Natural ageing is the spontaneous ageing of a supersaturated solid solution at room temperature and involves a spontaneous change in the physical properties of the steel, which occurs on being held at atmospheric temperatures after hot- or cold rolling or after a final heat treatment, e.g. during transport to or storage at a customers prior to processing the strip. This natural ageing involves changes of the mechanical properties which are considered undesirable as they lead to unpredictable variations in processability during the forming of the car components. Also, the surface quality may be adversely affected due to the formation of so-called Lüder-lines. Also, too high a carbon level in solid solution may result in a deterioration of the formability prior to bake-hardening.
  • solute carbon For that reason a maximum value of 50 ppm of solute carbon is preferable. A more suitable maximum is 40 ppm of solute carbon (i.e. 0.004%).
  • C_solute is at least 0.0010 (10 ppm) and/or at most 0.0030 (30 ppm). This achieves a stable process and reproducible properties.
  • Nitrogen in particularly free nitrogen (i.e. nitrogen in solid solution), is not desirable but unavoidable in steel making. Titanium can be optionally added to bound nitrogen into TiN. The large amount of aluminium in the steel can also ensure that all nitrogen is bound. This means that the matrix is substantially free of nitrogen in solid solution.
  • Boron is optionally added to the steel. Its presence is not mandatory, but it may help to suppress any tendency for secondary work embrittlement. If added, a minimum amount of 5 ppm boron is required.
  • the manganese content is at least 0.1%.
  • the aluminium content is at least 6 % and/or at most 9%, preferably at most 8%.
  • the steel is preferably calcium treated.
  • the chemical composition may therefore also contain calcium in an amount consistent with a calcium treatment.
  • the amount of carbon in solid solution is controlled by the addition of microalloying elements (Ti, Nb, V, Zr) in combination with excellent control of the total carbon content in the steel.
  • Ti or Nb should be strictly controlled. Too much titanium or niobium will combine with carbon to form carbides or, in the presence of sulphur, carbosulphides. As a consequence of this, no solute carbon is available and no bake-hardenability.
  • Ti is beneficial for binding nitrogen, but not strictly necessary. Up to 0.019% Ti can be added into the steel, mainly to bind nitrogen into TiN and secondarily to control the amount of solute carbon. The titanium content must 0.019% or lower, e.g. at most 0.018% or 0.015% or even at most 0.012%.
  • titanium is added as an alloying element, a suitable minimum value for the titanium content is 0.005%. If added, then a suitable minimum value for Nb is 0.008%. If added, then for V and Zr suitable minimum values are 0.002 and 0.004 respectively.
  • the composition of the ferritic steel according to the invention has a base composition where no titanium is added to the steel, and any titanium present is an unavoidable impurity.
  • Titanium as an alloying element or as an inevitable impurity, will first form TiN. If there is excess nitrogen, then the remaining nitrogen will be bound to aluminium. If there is excess titanium, then the remaining titanium will form Ti 4 C 2 S 2 until all titanium is consumed.
  • the factor Minimum[X,Y] calculates how much carbon is consumed by the formation of Ti 4 C 2 S 2 after all free nitrogen was bound to TiN. If the calculation results in a negative value for Y, then the factor is to be set to zero.
  • solute carbon available for bake hardening.
  • level of solute carbon below 50 ppm, and preferably below 40 ppm, the steel according to the invention is bake hardenable and nature-aging resistant.
  • a method for producing a ferritic steel strip comprising the steps of:
  • the coiling temperature is at least 600°C and/or the hot rolling finishing temperature is at least 900°C.
  • This hot-rolled strip can be subsequently further processed in a process comprising the steps of:
  • the hot-rolled strip is usually pickled and cleaned prior to the cold-rolling step.
  • the peak metal temperature in the continuous annealing process is at least 750°C, preferably at least 800°C.
  • the cold rolling reduction is at least 50%.
  • the thickness of the hot-rolled strip is between 1 and 5 mm and/or the thickness of the cold-rolled strip is between 0.4 and 2 mm.
  • the hot-rolled strip is annealed in a continuous annealing step and optionally galvanised in a hot-dip galvanising step.
  • the annealing may also take place in a so called heat-to-coat cycle.
  • a heat-to-coat cycle the hot-rolled steel is reheated to a temperature sufficient for performing the hot-dip galvanising, but not to a temperature as high as the conventional continuous annealing step.
  • the carbon which may have precipitated during the slow cooling of the hot rolled coil after hot rolling is brought into solid solution again.
  • After annealing and/or galvanising the steel has to be fast cooled to avoid precipitation of the carbon in solid solution.
  • this galvanised steel sheet for producing a car component or other product by forming, followed by painting and baking, then the paint-baking also ensures the strength increase associated with the paint-baking cycle.
  • the steels were produced by casting a slab and reheating the slab at a temperature of at most 1250°C. This temperature is the maximum temperature, because at higher reheating temperatures excessive grain growth may occur.
  • the finishing temperature during hot rolling was 900°C, coiling temperature 650°C followed by pickling and cold rolling (67%) and continuous annealing at a peak metal temperature of 800°C and hot-dip-galvanising.
  • Steel 3a also contained 16 ppm B.

Claims (13)

  1. Bande ou feuille d'acier ferritique comprenant en pourcentage de poids jusqu'à 0.01 % du total de C (C_total);
    au plus de 0.2 % de Si;
    0.1 à 1.0 % de Mn;
    de 5 à 10 % d'Al;
    jusqu'à 0.010 % de N;
    jusqu'à 0.01 % de S;
    jusqu'à 0.1 % de P;
    au moins un élément parmi
    - 0.005 à 0.019 % de Ti;
    - 0.008 à 0.08 % de Nb;
    - 0.002 à 0.1% de V;
    - 0.004 à 0.1 % de Zr;
    éventuellement entre 5 et 50 ppm de B;
    le reste étant composé de fer et des inévitables impuretés;
    où C_soluté = total de C
    - Minimum[X,Y]
    - Maximum[Z,0]
    - (12/93)*Nb
    - (12/91)*Zr
    - (12/51)*V;
    où, X = 2 ⋅ 12 2 ⋅ 32 ⋅ S
    Figure imgb0014
     Y = 2 ⋅ 12 4 ⋅ 48 ⋅ Ti − 48 14 ⋅ N
    Figure imgb0015
     Z = 12 48 ⋅ Ti − 48 14 ⋅ N − 4 ⋅ 48 2 ⋅ 32 ⋅ S
    Figure imgb0016
     où,
    Minimum[X,Y] = valeur inférieure de X et Y et Minimum[X,Y] = zéro si Y est négatif;
    Maximum[Z,0] = valeur supérieure de zéro et Z;
    et où C_soluté est d'au moins 0.0005 (5 ppm).
  2. Acier selon la revendication 1 où C_soluté est au plus de 0.0050 (50 ppm).
  3. Acier selon l'une quelconque des revendications précédentes, où Al est au moins de 6 % et/ou au plus de 9%, de préférence au plus de 8%.
  4. Acier selon l'une quelconque des revendications précédentes, où le total de C est au moins de 0.0010 % (10 ppm).
  5. Acier selon l'une quelconque des revendications précédentes, où C_soluté est au moins de 0.0010% (10 ppm) et/ou au plus de 0.0040% (40 ppm), de préférence au plus de 0.0030% (30 ppm).
  6. Acier selon l'une quelconque des revendications précédentes, où N est au plus de 0.005% (50 ppm).
  7. Acier selon l'une quelconque des revendications précédentes, où le poids spécifique de l'acier est compris entre 6800 et 7300 kg/m3.
  8. Procédé de production d'une bande d'acier ferritique selon l'une quelconque des revendications 1 à 7 comprenant les phases consistant à :
    • fournir une brame d'acier ou une bande épaisse d'acier par ;
    ∘ coulage continu, ou
    ∘ coulage à brames minces, ou
    ∘ coulage à bandes continues ou
    ∘ coulage en bandes minces ;
    • suivi éventuellement du réchauffage de la brame ou de la bande d'acier à une température de réchauffage d'au plus 1250°C ;
    • laminage à chaud de la brame ou de la bande épaisse et finition du procédé de laminage à chaud à une température de finition de laminage à chaud d'au moins 850°C ;
    • bobinage de la bande laminée à chaud à une température de bobinage comprise entre 550 et 750°C.
  9. Procédé selon la revendication 8 où le carbone en bandes laminées à chaud est réchauffé lors :
    • d'une phase de recuit continue, éventuellement suivie d'une galvanisation par immersion à chaud, avant refroidissement rapide ou
    • une phase de chauffage et d'enrobage, suivie d'une galvanisation par immersion à chaud et refroidissement rapide.
  10. Procédé de production de la bande d'acier ferritique comprenant les phases suivantes :
    • laminage à froid de la bande d'acier ferritique selon la revendication 8 dans une réduction par laminage à froid de 40-90% pour obtenir une bande laminé à froid ;
    • recuit de la bande laminée à froid dans un procédé de recuit continu pour avoir un pic de température de métal compris entre 700 et 900°C ;
    • éventuellement galvanisation de la bande recuite dans une galvanisation par immersion à chaud ou électrozingage ou un procédé de chauffage et d'enrobage.
  11. Procédé selon la revendication 10, où le pic de température de métal dans le procédé de recuit continu est d'au moins 750°C, de préférence d'au moins 800°C.
  12. Procédé selon l'une quelconque des revendications 10 à 11, où la réduction par laminage à froid est d'au moins 50 %.
  13. Procédé selon l'une quelconque des revendications 9 à 12, où l'épaisseur de la bande laminée à chaud est comprise entre 1 et 5 mm et/où l'épaisseur de la bande laminée à froid est comprise entre 0.4 et 2 mm.
EP13704616.5A 2012-02-20 2013-02-19 Acier haute résistance à faible densité durcissable par cuisson et procédé de production de cet acier Active EP2817428B2 (fr)

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Application Number Priority Date Filing Date Title
EP12156180 2012-02-20
EP12160499 2012-03-21
PCT/EP2013/053257 WO2013124264A1 (fr) 2012-02-20 2013-02-19 Acier pouvant être durci par cuisson, à faible densité et à haute résistance et son procédé de production
EP13704616.5A EP2817428B2 (fr) 2012-02-20 2013-02-19 Acier haute résistance à faible densité durcissable par cuisson et procédé de production de cet acier

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EP2817428A1 EP2817428A1 (fr) 2014-12-31
EP2817428B1 EP2817428B1 (fr) 2016-04-20
EP2817428B2 true EP2817428B2 (fr) 2019-06-19

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US (1) US20150027597A1 (fr)
EP (1) EP2817428B2 (fr)
JP (1) JP6342336B2 (fr)
KR (1) KR20140129150A (fr)
CN (1) CN104126023B (fr)
WO (1) WO2013124264A1 (fr)

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US9777350B2 (en) 2012-04-11 2017-10-03 Tata Steel Nederland Technology B.V. High strength interstitial free low density steel and method for producing said steel
MX2017010539A (es) 2015-02-17 2017-12-14 Jfe Steel Corp Lamina de acero delgada laminada en frio de alta resistencia y metodo para la produccion de la misma.
WO2023148087A1 (fr) 2022-02-03 2023-08-10 Tata Steel Ijmuiden B.V. Procédé de fabrication d'une bande d'acier à faible teneur en carbone ayant une aptitude au formage améliorée

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EP2817428B1 (fr) 2016-04-20
US20150027597A1 (en) 2015-01-29
WO2013124264A1 (fr) 2013-08-29
CN104126023B (zh) 2017-02-22
KR20140129150A (ko) 2014-11-06
CN104126023A (zh) 2014-10-29
JP6342336B2 (ja) 2018-06-13
EP2817428A1 (fr) 2014-12-31

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