EP3292228B1 - PRODUIT EN ACIER PLAT ET PROCÉDÉ DE FABRICATION DE
CELLE-CI - Google Patents

PRODUIT EN ACIER PLAT ET PROCÉDÉ DE FABRICATION DE
CELLE-CI Download PDF

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EP3292228B1
EP3292228B1 EP16723293.3A EP16723293A EP3292228B1 EP 3292228 B1 EP3292228 B1 EP 3292228B1 EP 16723293 A EP16723293 A EP 16723293A EP 3292228 B1 EP3292228 B1 EP 3292228B1
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steel
content
temperature
flat steel
flat
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EP3292228A1 (fr
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Richard G. Thiessen
Thomas Heller
Karsten MACHALITZA
Roland Sebald
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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ThyssenKrupp Steel Europe AG
ThyssenKrupp AG
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    • C—CHEMISTRY; METALLURGY
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    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
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    • 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
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/22—Martempering
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
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    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—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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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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    • C22C—ALLOYS
    • 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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    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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    • 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
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    • 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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • 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
    • C23C2/02—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
    • C23C2/04—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
    • C23C2/26—After-treatment
    • C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
    • C23C2/29—Cooling or quenching
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    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
    • C23C2/36—Elongated material
    • C23C2/40—Plates; Strips
    • C—CHEMISTRY; METALLURGY
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    • C23F—NON-MECHANICAL REMOVAL OF METALLIC MATERIAL FROM SURFACE; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL; MULTI-STEP PROCESSES FOR SURFACE TREATMENT OF METALLIC MATERIAL INVOLVING AT LEAST ONE PROCESS PROVIDED FOR IN CLASS C23 AND AT LEAST ONE PROCESS COVERED BY SUBCLASS C21D OR C22F OR CLASS C25
    • C23F17/00—Multi-step processes for surface treatment of metallic material involving at least one process provided for in class C23 and at least one process covered by subclass C21D or C22F or class C25
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
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    • C21D2211/002—Bainite
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • a flat steel product which has a tensile strength R m of at least 1200 MPa and consists of a steel which, in addition to Fe and unavoidable impurities (in% by weight), C: 0.10-0.50%, Si: 0 , 1 - 2.5%, Mn: 1.0 - 3.5%, Al: up to 2.5%, P: up to 0.020%, S: up to 0.003%, N: up to 0.02% , and optionally one or more of the elements "Cr, Mo, V, Ti, Nb, B and Ca" in the following contents: Cr: 0.1-0.5%, Mo: 0.1-0.3%, V : 0.01-0.1%, Ti: 0.001-0.15%, Nb: 0.02-0.05%.
  • Typical tensile strengths Rm of flat steel products according to the invention are 950-1300 MPa with a yield strength which is at least 800 MPa and can reach the respective tensile strength.
  • the elongation A 50 of flat steel products according to the invention is typically 8-20%.
  • a flat steel product according to the invention regularly achieves hole expansion ratios of at least 30% in the hole expansion test according to ISO 16630.
  • the setting of a suitable ratio between the elements which influence the austenite formation and hardenability of the steel and the elements which suppress the carbide formation is of essential importance here.
  • This ratio is set in an alloy according to the invention using the factor ⁇ in which the respective C, Mn, Cr, Al and Si content of the steel is incorporated.
  • the factor ⁇ should not be less than 1.5. Too high a content of silicon or aluminum would have a negative effect on the coatability (silicon) or the castability (aluminum) of the steel. If the carbon, manganese or chromium content is insufficient, the required strength would not be achieved.
  • the values for the factor ⁇ are at least 1.6.
  • Al is added to the steel of a flat steel product according to the invention for deoxidation and for binding any nitrogen that may be present.
  • Al can also be used to suppress cementite.
  • the Al content of a steel intended for a flat steel product according to the invention is therefore limited to 0.01-1.5% by weight. If low austenitizing temperatures are to be guaranteed, it can be expedient to limit the Al content to a maximum of 0.44% by weight, in particular to 0.1% by weight.
  • higher Al contents have a negative effect on castability in steel production. Al contents of at most 1.0% by weight, in particular at most 0.44% by weight, have proven to be favorable for ensuring particularly good castability.
  • Chromium in contents of up to 1.0% by weight can optionally be used as an effective inhibitor of pearlite in the steel provided according to the invention and also contributes to strength. With contents of more than 1.0 wt.% Cr, there is a risk of pronounced grain boundary oxidation. To be able to use the positive effects of Cr are at least 0.05% by weight is required.
  • the presence of Cr in the steel of a flat steel product according to the invention has a particularly favorable effect if at least 0.15% by weight of Cr is present, an optimal effect being achieved with contents of up to 0.8% by weight.
  • the Ti content of the steel of a steel flat product according to the invention is limited to a maximum of 0.2% by weight and its Nb content to a maximum of 0.05% by weight, whereby the presence of micro-alloying elements has proven to be advantageous in order to avoid negative influences, when the sum of the contents of Nb and Ti does not exceed 0.2% by weight.
  • the steels E, F and G therefore did not meet the requirements determined according to the invention by the factor ⁇ for the coordination of the alloying elements essential for austenite formation and hardenability.
  • samples 1 - 7, 11, 12, 16 - 23, 28 - 31, 33 - 35, 39, 40, 43-60 for a holding period t Q of 10-60 s.
  • Samples 1-7, 11, 12, 16, 17, 19-23, 28-31, 33-35, 39, 40, 43-48 were then heated to a treatment temperature T B at a heating rate ⁇ B1 over a heating time t BR heated, on which they have been held for an additional holding period t BI in some attempts.
  • Sample 18 was cooled to the treatment temperature T B analogously. It was then cooled to room temperature at a cooling rate ⁇ B2 .
  • Comparative examples A3 and C19 show that if the cooling speeds ⁇ Q are too low, the desired yield strength is not achieved, which is due to the fact that the formation of ferrite could not be prevented sufficiently.

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Claims (7)

  1. Produit plat en acier qui a une résistance à la traction Rm au moins de 950 MPa, une limite d'élasticité au moins de 800 MPa et un allongement à la rupture A50 au moins de 8 %, et la résistance à la traction, la limite d'élasticité et l'allongement à la rupture ont été déterminés conformément à la norme DIN EN ISO 6892, forme d'échantillons 1, où le produit plat en acier est fabriqué dans un acier qui, en plus du fer et d'impuretés inévitables, se compose, suivant un pourcentage (%) en poids, des éléments suivants : C : de 0,05 % à 0,20 %, Si : de 0,2 % à 1,5 %, Al : de 0,01 % à 1,5 %, Mn : de 1,0 % à 3,0 %, P : jusqu'à 0,02 %, S : jusqu'à 0,005 %, N : jusqu'à 0,008 %,
    ledit acier se composant aussi, de façon facultative, d'un ou de plusieurs éléments parmi le groupe "Cr, Mo, Ti, Nb, B", cet élément ou ces éléments ayant les teneurs suivantes : Cr : de 0,05 % à 1,0 %, Mo : de 0,05 % à 0,2 %, Ti : de 0,005 % à 0,2 %, Nb : de 0,001 % à 0,05 %, B : de 0,0001 % à 0,005 %,
    où pour le rapport ψ = % C + % Mn / 5 + % Cr / 6 / % Al + % Si
    Figure imgb0023
    ayant %C : teneur respective de l'acier en C
    %Mn : teneur respective de l'acier en Mn
    %Cr : teneur respective de l'acier en Cr
    %Al : teneur respective de l'acier en Al
    %Si : teneur respective de l'acier en Si
    s'applique la relation 1,6 ≤ ψ ≤ 3 ;
    Figure imgb0024
     et où le produit plat en acier présente une structure qui se compose :
    - au maximum de 5 % en surface de bainite,
    - au maximum de 5 % en surface de ferrite polygonale,
    - au maximum de 2 % en volume d'austénite résiduelle, et
    - au moins de 90 % en surface de martensite, où au moins la moitié de la martensite est de la martensite revenue, et pour l'équivalent carbone CE = % C + % Si + % Mn / 5 + % Cr + % Mo / 6
    Figure imgb0025
     ayant
    %C : teneur respective de l'acier en C
    %Si : teneur respective de l'acier en Si
    %Mn : teneur respective de l'acier en Mn
    %Cr : teneur respective de l'acier en Cr
    %Mo : teneur respective de l'acier en Mo
    s'applique la relation
    0,254 ≤ CE ≤ 1,1 % en poids.
  2. Produit plat en acier selon la revendication 1, caractérisé en ce que l'équivalent carbone CE est au maximum égal à 1,0 % en poids.
  3. Produit plat en acier selon l'une des revendications précédentes, caractérisé en ce que la somme des teneurs en Ti et en Nb est au maximum égale à 0,2 % en poids.
  4. Produit plat en acier selon l'une quelconque des revendications précédentes, caractérisé en ce que ledit produit plat en acier est doté d'un revêtement de protection métallique à base de Zn, ledit revêtement de protection étant appliqué par la mise en œuvre d'un processus de revêtement par immersion dans un bain en fusion.
  5. Procédé de fabrication d'un produit plat en acier selon l'une quelconque des revendications 1 à 4, ledit procédé de fabrication comprenant les étapes de travail suivantes consistant :
    a) à fournir un produit plat en acier, sans revêtement, ledit produit plat étant fabriqué dans un acier qui, en plus du fer et d'impuretés inévitables, se compose, suivant un pourcentage (%) en poids, des éléments suivants : C : de 0,05 % à 0,20 %, Si : de 0,2 % à 1,5 %, Al : de 0,01 % à 1,5 %, Mn : de 1,0 % à 3,0 %, P : jusqu'à 0,02 %, S : jusqu'à 0,005 %, N : jusqu'à 0,008 %,
    ledit acier se composant aussi, de façon facultative, d'un ou de plusieurs éléments parmi le groupe "Cr, Mo, Ti, Nb, B", cet élément ou ces éléments ayant les teneurs suivantes : Cr : de 0,05 % à 1,0 %, Mo : de 0,05 % à 0,2 %, Ti : de 0,005 % à 0,2 %, Nb : de 0,001 % à 0,05 %, B : de 0,0001 % à 0,005 %,
    où pour le rapport ψ = % C + % Mn / 5 + % Cr / 6 / % Al + % Si
    Figure imgb0026
    ayant %C : teneur respective de l'acier en C
    %Mn : teneur respective de l'acier en Mn
    %Cr : teneur respective de l'acier en Cr
    %Al : teneur respective de l'acier en Al
    %Si : teneur respective de l'acier en Si
    s'applique la relation 1,6 ≤ ψ ≤ 3 ;
    Figure imgb0027
     et pour l'équivalent carbone CE = % C + % Si + % Mn / 5 + % Cr + % Mo / 6
    Figure imgb0028
    ayant %C : teneur respective de l'acier en C
    %Si : teneur respective de l'acier en Si
    %Mn : teneur respective de l'acier en Mn
    %Cr : teneur respective de l'acier en Cr
    %Mo : teneur respective de l'acier en Mo
    s'applique la relation
    0,254 ≤ CE ≤ 1,1 % en poids ;
    b) à chauffer le produit plat en acier à une température d'austénitisation THZ qui est supérieure à la température A3 de l'acier du produit plat en acier et au maximum égale à 950°C, où le chauffage se produit jusqu'à une température de point d'inflexion Tw se situant entre 200°C et 400°C, à une vitesse de chauffage θH1 comprise entre 5 K/s et 25 K/s, ledit chauffage se produisant ensuite jusqu'à atteindre la température d'austénitisation THZ, à une vitesse de chauffage θH2 comprise au moins entre 2 K/s et 10 K/s,
    ayant T HZ > A c 3 ° C = 910 − 203 √ % C − 15,2 % Ni + 44,7 % Si + 31,5 % Mo − 21,1 % Mn
    Figure imgb0029
    ayant %C : teneur de l'acier en C,
    %Ni : teneur de l'acier en Ni,
    %Si : teneur de l'acier en Si,
    %Mo : teneur de l'acier en Mo,
    %Mn : teneur de l'acier en Mn ;
    c) à maintenir le produit plat en acier à la température d'austénitisation THZ sur une durée d'austénitisation tHZ comprise entre 5 s et 15 s ;
    d) à effectuer un premier refroidissement du produit plat en acier ayant lieu sur une durée de refroidissement tk comprise entre 50 s et 300 s, ledit premier refroidissement étant effectué à une température intermédiaire TK non inférieure à 680°C ;
    e) à effectuer, à partir de la température intermédiaire TK, une trempe du produit plat en acier à une vitesse de refroidissement θQ de plus de 30 K/s, jusqu'à une température d'arrêt de refroidissement TQ pour laquelle s'applique la relation : (TMS - 175°C) < TQ < TMS
    ayant T MS ° C = 539 ° C + − 423 % C − 30,4 % Mn − 7,5 % Si + 30 % Al ° C / % en poids
    Figure imgb0030
    ayant %C : teneur de l'acier en C
    %Mn : teneur de l'acier en Mn
    %Si : teneur de l'acier en Si
    %Al : teneur de l'acier en Al ;
    f) à maintenir le produit plat en acier à la température d'arrêt de refroidissement TQ pour une durée de maintien tQ comprise 10 s et 60 s ;
    g) à traiter le produit plat en acier ayant été trempé à la température d'arrêt de refroidissement TQ,
    g.1) où le produit plat en acier, sur une durée totale de traitement tBT comprise entre 10 s et 1000 s, est maintenu à une température de traitement TB qui est au moins égale à la température d'arrêt de refroidissement TQ et non supérieure à 550°C,
    ou bien
    g.2) où le produit plat en acier, à partir de la température d'arrêt de refroidissement TQ, est chauffé à une température de traitement TB comprise entre 450°C et 500°C, où le produit plat en acier est maintenu ensuite, de façon facultative, à cette température de traitement TB, de manière à être isotherme sur une durée de maintien tBI, où le chauffage à la température de traitement TB se produit à une vitesse de chauffage θB1 inférieure à 80 K/s, et la durée totale de traitement tBT formée comme étant la somme du temps de chauffage tBR nécessaire pour le chauffage, et de la durée de maintien tBI, est comprise entre 10 s et 1000 s, et où, après le traitement, on fait passer le produit plat en acier dans un bain en fusion, afin de recouvrir ledit produit plat en acier d'un revêtement de protection métallique à base de Zn ;
    h) à effectuer un refroidissement à partir de la température de traitement TB, à une vitesse de refroidissement θB2 de plus de 5 K/s.
  6. Procédé selon la revendication 5, caractérisé en ce que, au cours de l'étape de travail b), les vitesses de chauffage θH1 et θH2 sont identiques.
  7. Procédé selon la revendication 5 ou 6, caractérisé en ce que le produit plat en acier, au cours de l'étape de travail g.1), est chauffé à la température de traitement TB, à partir de la température d'arrêt de refroidissement TQ, à une vitesse de chauffage θB1 inférieure à 80 K/s.
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