EP1485511B1 - High-resistant, low-density hot laminated steel sheet and method for the production thereof - Google Patents

High-resistant, low-density hot laminated steel sheet and method for the production thereof Download PDF

Info

Publication number
EP1485511B1
EP1485511B1 EP03725278A EP03725278A EP1485511B1 EP 1485511 B1 EP1485511 B1 EP 1485511B1 EP 03725278 A EP03725278 A EP 03725278A EP 03725278 A EP03725278 A EP 03725278A EP 1485511 B1 EP1485511 B1 EP 1485511B1
Authority
EP
European Patent Office
Prior art keywords
phase
sheet according
hot
ferrite phase
silicon
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.)
Expired - Lifetime
Application number
EP03725278A
Other languages
German (de)
French (fr)
Other versions
EP1485511A2 (en
Inventor
Xavier Bano
Christian Giraud
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
USINOR SA
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=27763686&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=EP1485511(B1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by USINOR SA filed Critical USINOR SA
Publication of EP1485511A2 publication Critical patent/EP1485511A2/en
Application granted granted Critical
Publication of EP1485511B1 publication Critical patent/EP1485511B1/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

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
    • C21D8/04—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
    • 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
    • C22C38/02—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

Definitions

  • the invention relates to a hot-rolled steel sheet with very high strength and low density, resulting from a band rolling mill, as well as its method of manufacturing.
  • the object of the invention is to propose to the users of steel sheet rolled hot sheet of low density and with comparable resistance levels to the high strength steel plate currently used or even higher, and that, in order to cumulate the two advantages of low density and resistance high mechanical
  • the sheet according to the invention is such that the silicon content is between 3 and 6%, and that the aluminum content is between 1 and 2%.
  • the sheet according to the invention is such that the silicon content is between 2 and 3%, and that the aluminum content is between 7 and 10%.
  • the silicon and aluminum contents of the sheet according to the invention are such that: % Si +% Al ⁇ 9
  • the hot rolled steel on a belt train according to the invention has a high mechanical strength and low density.
  • the carbon content of the sheet according to the invention is between 0.04 and 0.5% by weight, preferably between 0.04 and 0.3% by weight.
  • the evolution of the structure of the steel as a function of the carbon content is presented in Figures 2 to 5 and shows that the structure of the steel according to the invention (FIGS. 2 to 4) consists of coarse grain primary ferrite, and a mixture of carbide phase and ferrite fine secondary to smaller grains. If the carbon content falls below 0.04%, the microstructure does not include any carbureted phases and loses mechanical characteristics. On the other hand, if the carbon content exceeds 0.5% weight, the structure becomes very fragile, and it is observed that the microstructure does not include more primary ferrite (see Figure 5).
  • the steel according to the invention can reach levels of mechanical resistance ranging from 620 MPa at over 1000 MPa and densities in the order of 7.55 and down to 7 g / cm 3 according to the contents of silicon and aluminum and addition elements, as shown in Figure 1.
  • the mechanical characteristics can be reinforced by addition of element micro-alloy such as niobium, titanium, vanadium, the last two, less dense than iron.
  • element micro-alloy such as niobium, titanium, vanadium, the last two, less dense than iron.
  • the sheet according to the invention may be manufactured by any suitable method.
  • This process firstly comprises reheating of the slab at high temperature (preferably greater than 900 ° C), prior to hot rolling.
  • high temperature preferably greater than 900 ° C
  • the slab has a microstructure composed of a so-called primary ferritic phase which is formed at high temperature, and which co-exists with an austenitic phase.
  • the austenitic phase is then completely transformed into a carburized phase mixture and secondary ferrite, the average grain size is lower than that of the primary ferritic phase that remains.
  • Castings A, C, F, H and L are given for comparison, while castings B, D, E, G, I, J and K are according to the invention.
  • VS% mn% Yes% al% Rm (MPa) Density AT 0.24 2.46 1.83 ⁇ 0,1 1423 7.74 B 0.23 2.53 3.06 1.28 902 7.54 VS 0.12 2.55 4.09 ⁇ 0,1 1296 7.55 D 0.07 2.67 5.28 5 1400 7.14 E 0.068 1.29 3.23 1,423 750 7.52 F 0.079 1.21 1.44 3.25 587 7.44 BOY WUT 0,042 1.37 3.27 1.43 760 7.51 H 0,204 2.62 ⁇ 0,1 8.05 673 7.02 I 0,040 1,688 3.66 1,075 621 7.55 J 0,160 1,270 3.69 1,153 835 7.52 K 0.268 1,155 3.59 1,435 949 7.51 The 0,505 0,167 3.48 1,041 1134 7.54
  • the rolling temperature is 895 ° C. and the winding temperature of 600 ° C, with a cooling rate of 49 ° C / s, which gives the steel a mechanical strength of 750 MPa. lowering the winding temperature makes it possible to increase the level of mechanical resistance.
  • the level of mechanical resistance can also be adjusted by carbon and manganese and / or other addition elements as presented above. Some operations, such as re-rolling or heat treatment such as annealing, can be used to modify or adjust the level of properties mechanical.
  • the proposed steel meets two contradictory needs of the hot-rolled steels on the one hand, high mechanical properties and on the other hand, a low density.
  • Existing solutions for making very steels high levels of mechanical resistance are based on the use of elements of addition not allowing a strong variation of the density, and the existing solutions to achieve low density steels are based on the use of elements addition does not achieve a high level of mechanical strength.
  • the steel of the invention combines these two properties, namely, a high level of mechanical strength and very low density for usable part lightening in the automobile.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
  • Laminated Bodies (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)

Abstract

The invention relates to a high-resistant, low-density hot laminated sheet steel comprising the following elements expressed in weight per cent: 0.04%:9 carbon<=0.5%; 0.05%<=manganese<=3%, being able to contain hardening elements: 0.01%<=niobium<=0.1 0.01%<=titanium<=0.2% 0.01<=vanadium<=0.2%, either individually or combined, and/or elements acting on the transformation temperatures, 0.0005%<=boron<=0.005%; 0.05%<=nickel<=2%; 0.05%<=chrome<=2%; 0.05%<=molybdenum<=2%, either individually or combined, the remainder being iron and elements which are inherent to production, characterized in that it comprises: 2%<=silicon<=10%; 1%<=aluminium<=10%. The invention also relates to the production thereof.

Description

L'invention concerne une tôle d'acier laminé à chaud, à très haute résistance et de faible densité, issu d'un train de laminage à bande, ainsi que son procédé de fabrication.The invention relates to a hot-rolled steel sheet with very high strength and low density, resulting from a band rolling mill, as well as its method of manufacturing.

L'allègement des véhicules automobiles devient une nécessité de par l'imposition de diminuer les émissions de CO2 à 140g /Km en 2008. Cet allègement ne peut être réalisé qu'en augmentant le niveau de résistance mécanique des aciers pour compenser la diminution d'épaisseur des tôles. Il est donc nécessaire d'augmenter les caractéristiques mécaniques tout en réduisant les épaisseurs des tôles avec lesquelles sont réalisées les pièces utilisées. Cette démarche trouve ses limites avec la diminution de la rigidité des pièces et l'apparition de vibrations et de bruits rédhibitoires dans les applications visées du domaine de l'automobile où le bruit est un élément d'inconfort.The lightening of motor vehicles becomes a necessity due to taxation to reduce CO2 emissions to 140g / Km in 2008. This reduction can not be realized that by increasing the level of mechanical strength of steels for to compensate for the decrease in the thickness of the sheets. It is therefore necessary to increase the mechanical characteristics while reducing the thickness of the sheets with which the parts used are made. This approach finds its limits with the decrease the rigidity of the parts and the appearance of vibrations and unacceptable noises in the targeted automotive applications where noise is an element of discomfort.

Dans le domaine des aciers plats laminés à chaud, dont les caractéristiques mécaniques sont obtenues par laminage contrôlé sur train à large bande, le niveau de résistance le plus élevé est obtenu avec les aciers THR de structure bainitique, qui permettent d'atteindre un niveau de résistance mécanique compris entre 800 MPa et 1000 MPa, mais leur densité est celle d'un acier courant, c'est-à-dire une densité de 7,8 g/cm3.In the field of hot-rolled flat steels, whose mechanical characteristics are obtained by controlled rolling on a wideband gear, the highest level of resistance is obtained with THR steels of bainitic structure, which make it possible to reach a level of mechanical strength between 800 MPa and 1000 MPa, but their density is that of a common steel, that is to say a density of 7.8 g / cm 3 .

Il est par ailleurs possible d'obtenir un acier de plus faible densité en utilisant un élément d'addition tel que l'aluminium, acier dans lequel un ajout de 8,5% d'aluminium permet d'abaisser la densité jusqu'à 7g/cm3. Cette solution ne permet pas d'atteindre des niveaux de résistance mécanique supérieure à 480 MPa. L'ajout d'autres éléments d'addition comme le chrome, le vanadium et le niobium, à des teneurs allant respectivement jusqu'à 1%, 0,1%, 0,4%, ne permet pas de dépasser en résistance mécanique un niveau de 580 MPa. Dans cette démarche, le gain en densité est annihilé par la faiblesse des caractéristiques en résistance mécanique obtenues.It is also possible to obtain a lower density steel by using a addition element such as aluminum, steel in which an addition of 8.5% aluminum allows to lower the density up to 7g / cm3. This solution does not achieve levels of mechanical strength greater than 480 MPa. Addition of other elements addition, such as chromium, vanadium and niobium, at levels up to 1%, 0.1%, 0.4%, can not exceed resistance mechanical a level of 580 MPa. In this process, the gain in density is annihilated by the weakness of the mechanical strength characteristics obtained.

Le but de l'invention est de proposer aux utilisateurs de tôles d'acier laminées à chaud une tôle de faible densité et comportant des niveaux de résistance comparables aux tôles d'acier à haute résistance mécanique actuellement utilisé voire d'un niveau supérieur, et cela, afin de cumuler les deux avantages de faible densité et de résistance mécanique élevée. The object of the invention is to propose to the users of steel sheet rolled hot sheet of low density and with comparable resistance levels to the high strength steel plate currently used or even higher, and that, in order to cumulate the two advantages of low density and resistance high mechanical

L'invention a pour premier objet une tôle d'acier laminé à chaud à très haute résistance et de faible densité, caractérisé en ce que sa composition en % en poids comprend :

  • 0,04% ≤ carbone ≤ 0,5%
  • 0,05% ≤ manganèse ≤ 3%
    • pouvant contenir les éléments de durcissement :
  • 0,01 %≤ niobium ≤ 0,1%
  • 0,01% ≤ titane ≤ 0,2%
  • 0,01 ≤ vanadium ≤ 0,2%, pris seul ou en combinaison,
    •  et/ou les éléments agissant sur les températures de transformation,
  • 0,0005% ≤ bore ≤ 0,005%
  • 0,05% ≤ nickel ≤ 2%
  • 0,05% ≤ chrome ≤ 2%
  • 0,05% ≤ molybdène ≤ 2%, pris seul ou en combinaison,
    •  le reste étant du fer et des éléments inhérents à l'élaboration, caractérisé en ce qu'il comporte :
  • 2% ≤ silicium ≤ 10%,
  • 1% ≤ aluminium ≤ 10%.
    •  et en ce que la tôle présente une microstructure constituée d'une phase de ferrite primaire, et d'une phase de ferrite secondaire, la taille moyenne de grains de ladite ferrite primaire étant supérieure à la taille moyenne de grains de ladite ferrite secondaire, ladite microstructure contenant également des phases carburées.The invention firstly relates to a hot rolled steel sheet with very high strength and low density, characterized in that its composition in% by weight comprises:
  • 0.04% ≤ carbon ≤ 0.5%
  • 0.05% ≤ manganese ≤ 3%
    • which may contain the curing elements:
  • 0.01% ≤ niobium ≤ 0.1%
  • 0.01% ≤ titanium ≤ 0.2%
  • 0.01 ≤ vanadium ≤ 0.2%, alone or in combination,
    • and / or the elements acting on the transformation temperatures,
  • 0.0005% ≤ boron ≤ 0.005%
  • 0.05% ≤ nickel ≤ 2%
  • 0.05% ≤ chromium ≤ 2%
  • 0.05% ≤ molybdenum ≤ 2%, taken alone or in combination,
    • the rest being iron and elements inherent in the preparation, characterized in that it comprises:
  • 2% ≤ silicon ≤ 10%,
  • 1% ≤ aluminum ≤ 10%.
    • and in that the sheet has a microstructure consisting of a primary ferrite phase, and a secondary ferrite phase, the average grain size of said primary ferrite being greater than the average grain size of said secondary ferrite, said microstructure also containing carburized phases.

    Dans un mode de réalisation préféré de l'invention, l'acier comporte dans sa composition, en % en poids :

  • 0,04% ≤ carbone ≤ 0,3%
  • 0.08% ≤ manganèse ≤ 3%
  • 2% ≤ silicium ≤ 6%,
  • 1% ≤ aluminium ≤ 10%.
    • In a preferred embodiment of the invention, the steel comprises in its composition, in% by weight:
  • 0.04% ≤ carbon ≤ 0.3%
  • 0.08% ≤ manganese ≤ 3%
  • 2% ≤ silicon ≤ 6%,
  • 1% ≤ aluminum ≤ 10%.

    • Dans un autre mode de réalisation préféré, la tôle selon l'invention est telle que la teneur en silicium est comprise entre 3 et 6%, et que la teneur en aluminium est comprise entre 1 et 2 %.In another preferred embodiment, the sheet according to the invention is such that the silicon content is between 3 and 6%, and that the aluminum content is between 1 and 2%.

    Dans un autre mode de réalisation préféré, la tôle selon l'invention est telle que la teneur en silicium est comprise entre 2 et 3 %, et que la teneur en aluminium est comprise entre 7 et 10 %. In another preferred embodiment, the sheet according to the invention is such that the silicon content is between 2 and 3%, and that the aluminum content is between 7 and 10%.

    Dans un autre mode de réalisation préféré, les teneurs en silicium et en aluminium de la tôle selon l'invention sont telles que : %Si + %Al ≥ 9 In another preferred embodiment, the silicon and aluminum contents of the sheet according to the invention are such that: % Si +% Al ≥ 9

    La tôle selon l'invention peut également présenter les caractéristiques suivantes, seules ou en combinaison :

    • la tôle présente une phase de ferrite primaire obtenue lors du réchauffage de l'acier effectué préalablement au laminage à chaud, et une phase de ferrite secondaire obtenue à l'issue du laminage à chaud, ainsi que des phases carburées,
    • la tôle comprend une phase de ferrite primaire dont la taille moyenne de grains est supérieure à 5 µm, et une phase de ferrite secondaire dont la taille moyenne de grains est inféneure à 2 µm.
    The sheet according to the invention may also have the following characteristics, alone or in combination:
    • the sheet has a primary ferrite phase obtained during reheating of the steel carried out prior to hot rolling, and a secondary ferrite phase obtained at the end of the hot rolling, as well as the carburized phases,
    • the sheet comprises a primary ferrite phase whose average grain size is greater than 5 μm, and a secondary ferrite phase whose average grain size is less than 2 μm.

    L'invention a pour second objet un procédé de fabrication d'une tôle laminée à chaud qui comprend les étapes consistant à :

    • réchauffer une brame dont la composition est conforme à l'invention, formant ainsi une brame dont la microstructure comprend une phase de ferrite primaire et une phase d'austénite,
    • puis à laminer à chaud ladite brame, la température de fin de laminage à chaud étant supérieure à la température AR3 de la phase austénitique formée lors du réchauffage, afin de réaliser un laminage dans des conditions austénitiques, transformant ainsi la phase austénitique en une phase de ferrite secondaire et des phases carburées.
    The subject of the invention is a process for producing a hot-rolled sheet which comprises the steps of:
    • heating a slab whose composition is in accordance with the invention, thus forming a slab whose microstructure comprises a primary ferrite phase and an austenite phase,
    • and then hot rolling said slab, the hot rolling end temperature being higher than the AR3 temperature of the austenitic phase formed during reheating, in order to carry out a rolling under austenitic conditions, thus transforming the austenitic phase into a phase of secondary ferrite and carburized phases.

    La description qui suit fera bien comprendre l'invention en référence aux figures annexées, qui représentent :

    • en figure 1 : une courbe présentant l'évolution de la densité d'un acier en fonction de la teneur en silicium, en aluminium et/ou silicium plus aluminium,
    • en figure 2 : la microstructure d'un acier selon l'invention comprenant 0,04% de carbone (coulée I),
    • en figure 3 : la microstructure d'un acier selon l'invention comprenant 0,160% de carbone (coulée J),
    • en figure 4 : la microstructure d'un acier selon l'invention comprenant 0,268% de carbone (coulée K),
    • en figure 5 : la microstructure d'un acier comprenant 0,505% de carbone, montré à titre de comparaison (coulée L).
    The description which follows will make the invention clearly understood with reference to the appended figures, which represent:
    • in FIG. 1: a curve showing the evolution of the density of a steel as a function of the content of silicon, aluminum and / or silicon plus aluminum,
    • in FIG. 2: the microstructure of a steel according to the invention comprising 0.04% carbon (casting I),
    • in FIG. 3: the microstructure of a steel according to the invention comprising 0.160% of carbon (casting J),
    • in FIG. 4: the microstructure of a steel according to the invention comprising 0.268% of carbon (casting K),
    • in FIG. 5: the microstructure of a steel comprising 0.505% of carbon, shown for comparison (casting L).

    L'acier laminé à chaud sur train à bande selon l'invention présente une résistance mécanique élevée et une faible densité.The hot rolled steel on a belt train according to the invention has a high mechanical strength and low density.

    L'acier à la composition générale pondérale suivante :

  • 0,04% ≤ carbone ≤ 0,5%
  • 0,05% ≤ manganèse ≤ 3%
    • pouvant contenir les éléments de durcissement :
  • 0,01 % ≤ niobium ≤ 0,1%
  • 0,01% ≤ titane ≤ 0,2%
  • 0,01 ≤ vanadium ≤ 0,2%, pris seul ou en combinaison,
    •  et/ou les éléments agissant sur les températures de transformation,
  • 0,0005% ≤ bore ≤ 0,005%
  • 0,05% ≤ nickel ≤ 2%
  • 0,05% ≤ chrome ≤ 2%
  • 0,05% ≤ molybdène ≤ 2%,
    •  pris seul ou en combinaison, le reste étant du fer et des éléments inhérents à l'élaboration, comporte :
  • 2% ≤ silicium ≤ 10%,
  • 1%≤ aluminium ≤ 10%.
    •  Steel with the following general weight composition:
  • 0.04% ≤ carbon ≤ 0.5%
  • 0.05% ≤ manganese ≤ 3%
    • which may contain the curing elements:
  • 0.01% ≤ niobium ≤ 0.1%
  • 0.01% ≤ titanium ≤ 0.2%
  • 0.01 ≤ vanadium ≤ 0.2%, alone or in combination,
    • and / or the elements acting on the transformation temperatures,
  • 0.0005% ≤ boron ≤ 0.005%
  • 0.05% ≤ nickel ≤ 2%
  • 0.05% ≤ chromium ≤ 2%
  • 0.05% ≤ molybdenum ≤ 2%,
    • taken alone or in combination, the rest being iron and elements inherent to the elaboration, comprises:
  • 2% ≤ silicon ≤ 10%,
  • 1% ≤ aluminum ≤ 10%.

    • La teneur en carbone de la tôle selon l'invention est comprise entre 0,04 et 0,5% en poids, de préférence entre 0,04 et 0,3% en poids. L'évolution de la structure de l'acier en fonction de la teneur en carbone est présentée dans les figures 2 à 5 et montre que la structure de l'acier selon l'invention (figures 2 à 4) est constituée de ferrite primaire à gros grains, et d'un mélange de phase carburées et de ferrite secondaire fine à plus petits grains. Si la teneur en carbone tombe en dessous de 0,04%, la microstructure ne comprend pas de phases carburées et perd en caractéristiques mécaniques. Par contre, si la teneur en carbone dépasse 0,5% en poids, la structure devient très fragile, et on observe que la microstructure ne comprend plus de ferrite primaire (cf. Figure 5).The carbon content of the sheet according to the invention is between 0.04 and 0.5% by weight, preferably between 0.04 and 0.3% by weight. The evolution of the structure of the steel as a function of the carbon content is presented in Figures 2 to 5 and shows that the structure of the steel according to the invention (FIGS. 2 to 4) consists of coarse grain primary ferrite, and a mixture of carbide phase and ferrite fine secondary to smaller grains. If the carbon content falls below 0.04%, the microstructure does not include any carbureted phases and loses mechanical characteristics. On the other hand, if the carbon content exceeds 0.5% weight, the structure becomes very fragile, and it is observed that the microstructure does not include more primary ferrite (see Figure 5).

    Sans vouloir être lié par une théorie, on pense que l'obtention de cette microstructure originale est due à la combinaison des teneurs en carbone, silicium et aluminium. Elle permet d'atteindre d'excellentes caractéristiques mécaniques. En effet, l'acier selon l'invention peut atteindre des niveaux de résistance mécanique allant de 620 MPa à plus de 1000 MPa et des densités de l'ordre de 7,55 et descendant jusqu'à 7 g/cm3 suivant les teneurs en silicium et en aluminium et en éléments d'addition, comme le montre la figure 1.Without wishing to be bound by a theory, it is thought that obtaining this original microstructure is due to the combination of carbon, silicon and aluminum. It achieves excellent mechanical characteristics. Indeed, the steel according to the invention can reach levels of mechanical resistance ranging from 620 MPa at over 1000 MPa and densities in the order of 7.55 and down to 7 g / cm 3 according to the contents of silicon and aluminum and addition elements, as shown in Figure 1.

    Les caractéristiques mécaniques peuvent être renforcées par addition d'élément de micro alliage comme le niobium, le titane, le vanadium, les deux derniers, moins denses que le fer.The mechanical characteristics can be reinforced by addition of element micro-alloy such as niobium, titanium, vanadium, the last two, less dense than iron.

    La tôle selon l'invention pourra être fabriquée par tout procédé adapté.The sheet according to the invention may be manufactured by any suitable method.

    Néanmoins, on préfère employer le procédé selon l'invention. Ce procédé comprend tout d'abord un réchauffage de la brame à haute température (de préférence supérieure à 900°C), préalablement au laminage à chaud. Les présents inventeurs ont découvert que lors de cette étape de réchauffage, la brame présente une microstructure composée d'une phase ferritique dite primaire qui se forme à haute température, et qui co-existe avec une phase austénitique.Nevertheless, it is preferred to employ the method according to the invention. This process firstly comprises reheating of the slab at high temperature (preferably greater than 900 ° C), prior to hot rolling. The present inventors discovered that during this heating step, the slab has a microstructure composed of a so-called primary ferritic phase which is formed at high temperature, and which co-exists with an austenitic phase.

    En laminant à chaud de telle sorte que la température de fin de laminage reste supérieure à la valeur de AR3 calculée pour la phase austénitique seule, on réalise un laminage dans des conditions austénitiques.By hot rolling so that the end of rolling temperature remains greater than the value of AR3 calculated for the austenite phase alone, a rolling under austenitic conditions.

    On observe que la phase austénitique se transforme alors complètement en un mélange de phase carburées et de ferrite secondaire, dont la taille de grains moyenne est inférieure à celle de la phase ferritique primaire qui subsiste.It is observed that the austenitic phase is then completely transformed into a carburized phase mixture and secondary ferrite, the average grain size is lower than that of the primary ferritic phase that remains.

    On choisira avantageusement un couple carbone-manganèse afin d'avoir une température de transformation AR3 telle qu'on puisse garantir un laminage dans des conditions austénitiques. We will advantageously choose a carbon-manganese pair in order to have a transformation temperature AR3 such that it can guarantee a rolling in austenitic conditions.

    Le tableau 1 suivant, présentant différentes analyses selon l'invention, montre l'influence des différents éléments sur les caractéristiques des aciers.The following Table 1, presenting different analyzes according to the invention, shows the influence of the different elements on the characteristics of the steels.

    TABLEAU 1TABLE 1

    Les coulées A, C, F, H et L sont données à titre de comparaison, tandis que les coulées B, D, E, G, I, J et K sont selon l'invention. C% Mn% Si% Al% Rm (MPa) Densité A 0,24 2,46 1,83 < 0,1 1423 7,74 B 0,23 2,53 3,06 1,28 902 7,54 C 0,12 2,55 4,09 < 0,1 1296 7,55 D 0,07 2,67 5,28 5 1400 7,14 E 0,068 1,29 3,23 1,423 750 7,52 F 0,079 1,21 1,44 3,25 587 7,44 G 0,042 1,37 3,27 1,43 760 7,51 H 0,204 2,62 < 0,1 8,05 673 7,02 I 0,040 1,688 3,66 1,075 621 7,55 J 0,160 1,270 3,69 1,153 835 7,52 K 0,268 1,155 3,59 1,435 949 7,51 L 0,505 0,167 3,48 1,041 1134 7,54 Castings A, C, F, H and L are given for comparison, while castings B, D, E, G, I, J and K are according to the invention. VS% mn% Yes% al% Rm (MPa) Density AT 0.24 2.46 1.83 <0,1 1423 7.74 B 0.23 2.53 3.06 1.28 902 7.54 VS 0.12 2.55 4.09 <0,1 1296 7.55 D 0.07 2.67 5.28 5 1400 7.14 E 0.068 1.29 3.23 1,423 750 7.52 F 0.079 1.21 1.44 3.25 587 7.44 BOY WUT 0,042 1.37 3.27 1.43 760 7.51 H 0,204 2.62 <0,1 8.05 673 7.02 I 0,040 1,688 3.66 1,075 621 7.55 J 0,160 1,270 3.69 1,153 835 7.52 K 0.268 1,155 3.59 1,435 949 7.51 The 0,505 0,167 3.48 1,041 1134 7.54

    Les données, présentées que le tableau 1, montrent que l'aluminium seul ne permet pas d'obtenir à la fois une faible densité de l'acier et un haut niveau de résistance dudit acier.The data presented in Table 1 show that aluminum alone not allow to obtain both a low density of steel and a high level of resistance of said steel.

    Dans l'exemple de l'acier référencé E, la température de laminage est de 895°C, et la température de bobinage de 600°C, avec une vitesse de refroidissement de 49°C/s, ce qui donne à l'acier une résistance mécanique de 750 MPa. L'abaissement de la température de bobinage permet d'augmenter le niveau de résistance mécanique. In the example of the steel referenced E, the rolling temperature is 895 ° C. and the winding temperature of 600 ° C, with a cooling rate of 49 ° C / s, which gives the steel a mechanical strength of 750 MPa. lowering the winding temperature makes it possible to increase the level of mechanical resistance.

    C'est le cas de l'exemple de l'acier référencé B, dont la température de bobinage est de 20°C avec une vitesse de refroidissement de 5°C/s, ce qui permet d'atteindre un niveau de résistance mécanique de 902 MPa.This is the case of the example of the steel referenced B, whose winding temperature is 20 ° C with a cooling rate of 5 ° C / s, which makes it possible to reach a mechanical strength level of 902 MPa.

    Si on augmente la vitesse de refroidissement pour un acier référencé C réalisé avec un laminage à une température de 870°C, un bobinage à une température de 120°C et une vitesse de refroidissement de 130°C/s, on obtient un acier avec une résistance mécanique de 1296 MPa.If we increase the cooling speed for a steel referenced C realized with a rolling at a temperature of 870 ° C., a winding at a temperature of 120 ° C and a cooling rate of 130 ° C / sec, a steel with a mechanical strength of 1296 MPa.

    Le niveau de résistance mécanique peut aussi être ajusté par des teneurs en carbone et manganèse et/ou d'autres éléments d'addition comme présentés ci-dessus. Certaines opérations, comme par exemple un re-laminage ou un traitement thermique tel q'un recuit, peuvent être utilisées pour modifier ou ajuster le niveau des propriétés mécaniques.The level of mechanical resistance can also be adjusted by carbon and manganese and / or other addition elements as presented above. Some operations, such as re-rolling or heat treatment such as annealing, can be used to modify or adjust the level of properties mechanical.

    Selon l'invention, l'acier proposé répond à deux besoins contradictoires du domaine des aciers laminés à chaud d'une part, des propriétés mécaniques élevées et d'autre part, une faible densité. Les solutions existantes pour réaliser des aciers de très hauts niveaux de résistance mécanique sont basées sur l'utilisation d'éléments d'addition ne permettant pas une forte variation de la densité, et les solutions existantes pour réaliser des aciers de faible densité sont basées sur l'utilisation d'éléments d'addition ne permettant pas d'atteindre de haut niveau de résistance mécanique.According to the invention, the proposed steel meets two contradictory needs of the hot-rolled steels on the one hand, high mechanical properties and on the other hand, a low density. Existing solutions for making very steels high levels of mechanical resistance are based on the use of elements of addition not allowing a strong variation of the density, and the existing solutions to achieve low density steels are based on the use of elements addition does not achieve a high level of mechanical strength.

    L'acier de l'invention combine ces deux propriétés, à savoir, un haut niveau de résistance mécanique et une très faible densité pour un allègement de pièce utilisable dans l'automobile.The steel of the invention combines these two properties, namely, a high level of mechanical strength and very low density for usable part lightening in the automobile.

    Claims (9)

    1. Very-high-strength and low-density, hot-rolled steel sheet, characterized in that its composition in % by weight comprises:
      0.04% ≤ carbon ≤ 0.5%
      0.05% ≤ manganese ≤ 3%
      and optionally the following hardening elements:
      0.01% ≤ niobium ≤ 0.1%
      0.01% ≤ titanium ≤ 0.2%
      0.01% ≤ vanadium ≤ 0.2%, taken individually or in combination,
      and optionally elements that act on the transformation temperatures:
      0.0005% ≤ boron ≤ 0.005%
      0.05% ≤ nickel ≤ 2%
      0.05% ≤ chromium ≤ 2%
      0.05% ≤ molybdenum ≤ 2%, taken individually or in combination,
      the balance being iron and elements inherent in smelting, characterized in that it includes:
      2% ≤ silicon ≤ 10%,
      1% ≤ aluminium ≤ 10%,
      and in that said sheet further has a microstructure consisting of a primary ferrite phase and of a secondary ferrite phase, the mean grain size of said primary ferrite being greater than the mean grain size of said secondary ferrite, said microstructure also containing carbide phases.
    2. Sheet according to Claim 1, further characterized in that said composition comprises:
      0.04% ≤ carbon ≤ 0.3%
      0.08% ≤ manganese ≤ 3%
      2% ≤ silicon ≤ 6%
      1% ≤ aluminium ≤ 10%.
    3. Sheet according to either of Claims 1 and 2, further characterized in that the silicon content is between 3 and 6% and in that the aluminium content is between 1 and 2%.
    4. Sheet according to either of Claims 1 and 2, further characterized in that the silicon content is between 2 and 3% and in that the aluminium content is between 7 and 10%.
    5. Sheet according to any one of Claims 1, 2 and 4, further characterized in that the silicon and aluminium contents are such that: %Si + %Al ≥ 9.
    6. Sheet according to any one of Claims 1 to 5, further characterized in that said primary ferrite phase is obtained during the reheating of the steel carried out prior to the hot rolling, and said secondary ferrite phase is obtained after the hot rolling.
    7. Sheet according to any one of Claims 1 to 6, characterized in that said primary ferrite phase has a mean grain size of greater than 5 µm and in that said secondary ferrite phase has a mean grain size of less than 2 µm.
    8. Process for manufacturing a hot-rolled sheet according to any one of Claims 1 to 7, characterized in that it comprises the steps consisting in:
      reheating a slab, the composition of which is in accordance with that of any one of Claims 1 to 5, thus forming a slab whose microstructure comprises a primary ferrite phase and an austenite phase; and then
      hot-rolling said slab, the temperature at the end of hot rolling being above the AR3 temperature of the austenitic phase formed during the reheat, so as to carry out rolling under austenitic conditions, thus transforming the austenitic phase into a secondary ferrite phase and carbide phases.
    9. Use of a hot-rolled steel sheet according to any one of Claims 1 to 7 or obtained by the process according to Claim 8 for the manufacture of motor vehicles.
    EP03725278A 2002-03-11 2003-03-10 High-resistant, low-density hot laminated steel sheet and method for the production thereof Expired - Lifetime EP1485511B1 (en)

    Applications Claiming Priority (3)

    Application Number Priority Date Filing Date Title
    FR0202998 2002-03-11
    FR0202998A FR2836930B1 (en) 2002-03-11 2002-03-11 HOT ROLLED STEEL WITH HIGH RESISTANCE AND LOW DENSITY
    PCT/FR2003/000765 WO2003076673A2 (en) 2002-03-11 2003-03-10 High-resistant, low-density hot laminated sheet steel and method for the production thereof

    Publications (2)

    Publication Number Publication Date
    EP1485511A2 EP1485511A2 (en) 2004-12-15
    EP1485511B1 true EP1485511B1 (en) 2005-12-07

    Family

    ID=27763686

    Family Applications (1)

    Application Number Title Priority Date Filing Date
    EP03725278A Expired - Lifetime EP1485511B1 (en) 2002-03-11 2003-03-10 High-resistant, low-density hot laminated steel sheet and method for the production thereof

    Country Status (15)

    Country Link
    US (1) US7416615B2 (en)
    EP (1) EP1485511B1 (en)
    JP (1) JP4638152B2 (en)
    KR (1) KR100986697B1 (en)
    CN (1) CN1306046C (en)
    AT (1) ATE312206T1 (en)
    AU (1) AU2003227824A1 (en)
    BR (1) BR0308328B1 (en)
    CA (1) CA2478123C (en)
    DE (1) DE60302659T2 (en)
    ES (1) ES2252671T3 (en)
    FR (1) FR2836930B1 (en)
    MX (1) MXPA04008717A (en)
    RU (1) RU2323983C2 (en)
    WO (1) WO2003076673A2 (en)

    Families Citing this family (21)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    JP5042694B2 (en) * 2007-04-13 2012-10-03 新日本製鐵株式会社 High strength low specific gravity steel plate excellent in ductility and workability and method for producing the same
    EP1995336A1 (en) * 2007-05-16 2008-11-26 ArcelorMittal France Low-density steel with good suitability for stamping
    KR101008117B1 (en) 2008-05-19 2011-01-13 주식회사 포스코 High strength thin steel sheet for the superier press formability and surface quality and galvanized steel sheet and method for manufacturing the same
    KR101027250B1 (en) * 2008-05-20 2011-04-06 주식회사 포스코 High strength steel sheet and hot dip galvanized steel sheet having high ductility and excellent delayed fracture resistance and method for manufacturing the same
    KR100985298B1 (en) * 2008-05-27 2010-10-04 주식회사 포스코 Low Density Gravity and High Strength Hot Rolled Steel, Cold Rolled Steel and Galvanized Steel with Excellent Ridging Resistibility and Manufacturing Method Thereof
    US9970073B2 (en) * 2010-10-18 2018-05-15 Nippon Steel & Sumitomo Metal Corporation Hot-rolled, cold rolled, and plated steel sheet having improved uniform and local ductility at a high strain rate
    TWI447236B (en) 2011-03-28 2014-08-01 Nippon Steel & Sumitomo Metal Corp Hot rolled steel sheet and manufacturing method thereof
    KR101634776B1 (en) 2011-05-25 2016-06-30 신닛테츠스미킨 카부시키카이샤 Hot-rolled steel sheet and process for producing same
    WO2013178887A1 (en) 2012-05-31 2013-12-05 Arcelormittal Investigación Desarrollo Sl Low-density hot- or cold-rolled steel, method for implementing same and use thereof
    DE102012013113A1 (en) * 2012-06-22 2013-12-24 Salzgitter Flachstahl Gmbh High strength multiphase steel and method of making a strip of this steel having a minimum tensile strength of 580 MPa
    CN103215516B (en) 2013-04-09 2015-08-26 宝山钢铁股份有限公司 A kind of 700MPa grade high-strength hot-rolled Q & P steel and manufacture method thereof
    TWI519650B (en) * 2013-05-01 2016-02-01 新日鐵住金股份有限公司 Zn-coated steel sheet and method of manufacturing the same
    MX2015014879A (en) 2013-05-01 2016-03-21 Nippon Steel & Sumitomo Metal Corp High-strength, low-specific gravity steel plate having excellent spot welding properties.
    UA117592C2 (en) * 2013-08-01 2018-08-27 Арселорміттал PAINTED GALVANIZED STEEL SHEET AND METHOD OF MANUFACTURING
    KR102021687B1 (en) 2015-04-08 2019-09-16 닛폰세이테츠 가부시키가이샤 Hot Rolled Steel Sheets For Heat Treatment
    KR102034129B1 (en) 2015-04-08 2019-10-18 닛폰세이테츠 가부시키가이샤 Heat-treated steel sheet member and manufacturing method thereof
    CN107532255B (en) 2015-04-08 2019-06-28 日本制铁株式会社 Heat- treated steel board member and its manufacturing method
    RU2615667C1 (en) * 2015-12-09 2017-04-06 Публичное акционерное общество "Северсталь" Method of producing hot-rolled sheets of low-alloyed steel of k65 strength grade for longitudinal electric-welded pipes
    RU2627079C1 (en) * 2016-11-17 2017-08-03 Федеральное Государственное Унитарное Предприятие "Центральный научно-исследовательский институт черной металлургии им. И.П. Бардина" (ФГУП "ЦНИИчермет им. И.П. Бардина") Method of manufacture of high-strengthen corrosive-resistant hot-rolled steel with low specific weight
    CN112481555B (en) * 2020-11-27 2022-01-04 马鞍山市鑫龙特钢有限公司 Low-density steel resistant to high-temperature oxidation corrosion
    WO2023105271A1 (en) * 2021-12-10 2023-06-15 Arcelormittal Low density hot rolled steel, method of production thereof and use of such steel to produce vehicle parts

    Family Cites Families (28)

    * Cited by examiner, † Cited by third party
    Publication number Priority date Publication date Assignee Title
    JPS60204833A (en) * 1984-03-29 1985-10-16 Sumitomo Metal Ind Ltd Manufacture of "sendust(r)" plate having superior magnetic characteristic
    JPH07115041B2 (en) * 1987-03-11 1995-12-13 日本鋼管株式会社 Method for manufacturing non-oriented high Si steel sheet
    JPH03291360A (en) 1990-04-06 1991-12-20 Tohoku Tokushuko Kk Alloy for magnetic head
    JP2536255B2 (en) * 1990-08-04 1996-09-18 日本鋼管株式会社 Damping alloy
    JP2536256B2 (en) * 1990-08-04 1996-09-18 日本鋼管株式会社 High strength damping alloy
    JP2503125B2 (en) * 1991-05-09 1996-06-05 新日本製鐵株式会社 Manufacturing method of good electromagnetic plate
    JP2708682B2 (en) * 1991-12-27 1998-02-04 新日本製鐵株式会社 Non-oriented electrical steel sheet having extremely excellent magnetic properties and method for producing the same
    JP3168665B2 (en) * 1992-01-18 2001-05-21 住友金属工業株式会社 Hot-rolled high-strength steel sheet with excellent workability and its manufacturing method
    JP3011538B2 (en) * 1992-05-25 2000-02-21 新日本製鐵株式会社 Manufacturing method for structural steel with low yield strength.
    US5445685A (en) * 1993-05-17 1995-08-29 The Regents Of The University Of California Transformation process for production of ultrahigh carbon steels and new alloys
    JP3386514B2 (en) * 1993-06-16 2003-03-17 川崎製鉄株式会社 Damping alloy steel sheet and method of manufacturing the same
    EP0681032A4 (en) * 1993-11-22 1996-03-20 Nippon Steel Corp Continuously cast slab of extremely low carbon steel and thin extremely low carbon steel sheet in which surface defect rarely occurs during steel sheet manufacturing step, and method of manufacturing the same slab and steel sheet.
    JPH07252592A (en) * 1994-03-15 1995-10-03 Nippon Steel Corp Hot rolled high strength steel sheet excellent in formability, low temperature toughness and fatigue property
    JPH07300655A (en) 1994-04-28 1995-11-14 Nippon Steel Corp Nonoriented silicon steel sheet excellent in magnetic/ calking properties and its production
    JP3348365B2 (en) * 1994-08-19 2002-11-20 新日本製鐵株式会社 Hot-rolled high-strength steel sheet for processing having excellent heat-softening property and excellent fatigue properties, and method for producing the same
    JPH09241745A (en) * 1996-03-01 1997-09-16 Nkk Corp Production of pc steel rod excellent in uniform elongation and high temperature relaxation characteristic
    JPH1025543A (en) * 1996-07-15 1998-01-27 Nkk Corp Pc steel bar excellent in uniform elongation and high temperature relaxation characteristic in as-spot-welded state
    JPH10212522A (en) 1997-01-30 1998-08-11 Nippon Steel Corp Manufacture of hot rolled steel sheet excellent in pickling property
    EP1025543A1 (en) 1997-10-28 2000-08-09 Hide and Seek Technologies, Inc. Optical disc authentication and data storage
    JPH11189850A (en) * 1997-12-24 1999-07-13 Sumitomo Metal Ind Ltd Non-oriented silicon steel sheet and its production
    JP3401427B2 (en) * 1998-03-12 2003-04-28 株式会社神戸製鋼所 High-strength steel sheet with excellent impact resistance
    JPH11323489A (en) 1998-05-13 1999-11-26 Nippon Steel Corp High strength cold rolled steel sheet having superior workability and excellent in shape fixability and its production
    JP4184481B2 (en) * 1998-06-11 2008-11-19 新日本製鐵株式会社 Corrosion resistant steel
    JP2000160249A (en) * 1998-11-26 2000-06-13 Kawasaki Steel Corp Manufacture of hot rolled silicon steel sheet excellent in magnetic property in l-direction and c-direction
    JP3447233B2 (en) * 1998-12-11 2003-09-16 新日本製鐵株式会社 Method for producing thin steel sheet and high-strength pressed body excellent in heat-hardening ability
    JP3962186B2 (en) * 1998-12-11 2007-08-22 新日本製鐵株式会社 Thin steel plate excellent in heat treatment hardening ability and method for producing high-strength press-formed body using the steel plate
    FR2796966B1 (en) * 1999-07-30 2001-09-21 Ugine Sa PROCESS FOR THE MANUFACTURE OF THIN STRIP OF TRIP-TYPE STEEL AND THIN STRIP THUS OBTAINED
    JP3924108B2 (en) 2000-03-13 2007-06-06 新日本製鐵株式会社 Manufacturing method of high strength steel sheet with excellent hydroformability after pre-processing

    Also Published As

    Publication number Publication date
    WO2003076673A8 (en) 2004-09-30
    BR0308328B1 (en) 2011-11-01
    CA2478123A1 (en) 2003-09-18
    ES2252671T3 (en) 2006-05-16
    CN1306046C (en) 2007-03-21
    BR0308328A (en) 2004-12-28
    AU2003227824A8 (en) 2003-09-22
    FR2836930A1 (en) 2003-09-12
    JP4638152B2 (en) 2011-02-23
    MXPA04008717A (en) 2004-12-06
    DE60302659T2 (en) 2006-07-20
    AU2003227824A1 (en) 2003-09-22
    CN1688725A (en) 2005-10-26
    ATE312206T1 (en) 2005-12-15
    US7416615B2 (en) 2008-08-26
    US20060231177A1 (en) 2006-10-19
    FR2836930B1 (en) 2005-02-25
    KR100986697B1 (en) 2010-10-08
    EP1485511A2 (en) 2004-12-15
    KR20040088583A (en) 2004-10-16
    DE60302659D1 (en) 2006-01-12
    RU2004129774A (en) 2005-08-20
    RU2323983C2 (en) 2008-05-10
    WO2003076673A3 (en) 2004-04-22
    CA2478123C (en) 2011-01-25
    JP2005527701A (en) 2005-09-15
    WO2003076673A2 (en) 2003-09-18

    Similar Documents

    Publication Publication Date Title
    EP1485511B1 (en) High-resistant, low-density hot laminated steel sheet and method for the production thereof
    EP1649069B1 (en) Method of producing austenitic iron/carbon/manganese steel sheets having a high strength and excellent toughness and being suitable for cold forming, and sheets thus produced
    AU2005200300C1 (en) High strength steel sheet and method for manufacturing same
    CA2873578C (en) Low-density hot- or cold-rolled steel, method for implementing same and use thereof
    CA2514736C (en) Method of producing a cold-rolled band of dual-phase steel with a ferritic/martensitic structure and band thus obtained
    EP2245203B1 (en) Austenitic stainless steel sheet and method for obtaining this sheet
    WO2012127136A2 (en) Hot-rolled steel sheet and associated production method
    JP2020509151A (en) High-strength dual-phase steel sheet having a minimum tensile strength of 600 MPa, hot-rolled, precipitation-strengthened and crystal grains refined, and method for producing the same
    FR2480311A1 (en) COLD LAMINATED STEEL SHEET WITH LOW ELIMINATION LIMIT AND HIGH RESISTANCE FOR DEEP TIPPING
    JP4380471B2 (en) High carbon hot rolled steel sheet and manufacturing method thereof
    CA2325892C (en) Process for producing high resistance rolled metal sheet suitable for forming and cupping
    FR2833617A1 (en) PROCESS FOR MANUFACTURING COLD ROLLED SHEATHES WITH HIGH RESISTANCE OF MICRO-ALLOY DUAL PHASE STEELS
    JP4380469B2 (en) High carbon hot rolled steel sheet and manufacturing method thereof
    EP1138796B1 (en) High strength hot rolled steel with high yield strength for use in the car industry
    EP1587963A2 (en) Ultrahigh strength hot-rolled steel and method of producing bands
    FR3026748A1 (en) METAL ALLOY, METALLIC PART AND PROCESS FOR OBTAINING
    JP2005133200A (en) High carbon cold rolled steel sheet, and method of manufacturing the same
    BE1007790A6 (en) Method for manufacturing a thin strip rolled mild steel for cold stamping.
    EP0748877A1 (en) Process for manufacturing a hot rolled steel sheet with very high elastic limit and steel sheet produced accordingly

    Legal Events

    Date Code Title Description
    PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

    Free format text: ORIGINAL CODE: 0009012

    AK Designated contracting states

    Kind code of ref document: A2

    Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

    AX Request for extension of the european patent

    Extension state: AL LT LV MK

    17P Request for examination filed

    Effective date: 20041022

    17Q First examination report despatched

    Effective date: 20041126

    RIN1 Information on inventor provided before grant (corrected)

    Inventor name: BANO, XAVIER

    Inventor name: GIRAUD, CHRISTIAN

    GRAP Despatch of communication of intention to grant a patent

    Free format text: ORIGINAL CODE: EPIDOSNIGR1

    RTI1 Title (correction)

    Free format text: HIGH-RESISTANT, LOW-DENSITY HOT LAMINATED STEEL SHEET AND METHOD FOR THE PRODUCTION THEREOF

    GRAS Grant fee paid

    Free format text: ORIGINAL CODE: EPIDOSNIGR3

    GRAA (expected) grant

    Free format text: ORIGINAL CODE: 0009210

    AK Designated contracting states

    Kind code of ref document: B1

    Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HU IE IT LI LU MC NL PT RO SE SI SK TR

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: FI

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20051207

    Ref country code: SI

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20051207

    Ref country code: IE

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20051207

    Ref country code: AT

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20051207

    Ref country code: RO

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20051207

    REG Reference to a national code

    Ref country code: GB

    Ref legal event code: FG4D

    Free format text: NOT ENGLISH

    REG Reference to a national code

    Ref country code: CH

    Ref legal event code: EP

    REG Reference to a national code

    Ref country code: IE

    Ref legal event code: FG4D

    Free format text: LANGUAGE OF EP DOCUMENT: FRENCH

    REF Corresponds to:

    Ref document number: 60302659

    Country of ref document: DE

    Date of ref document: 20060112

    Kind code of ref document: P

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: BG

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20060307

    Ref country code: DK

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20060307

    Ref country code: GR

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20060307

    REG Reference to a national code

    Ref country code: SE

    Ref legal event code: TRGR

    GBT Gb: translation of ep patent filed (gb section 77(6)(a)/1977)

    Effective date: 20060306

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: MC

    Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

    Effective date: 20060331

    Ref country code: LU

    Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

    Effective date: 20060331

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: PT

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20060508

    REG Reference to a national code

    Ref country code: ES

    Ref legal event code: FG2A

    Ref document number: 2252671

    Country of ref document: ES

    Kind code of ref document: T3

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: HU

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20060608

    RAP2 Party data changed (patent owner data changed or rights of a patent transferred)

    Owner name: ARCELOR FRANCE

    REG Reference to a national code

    Ref country code: IE

    Ref legal event code: FD4D

    NLT2 Nl: modifications (of names), taken from the european patent patent bulletin

    Owner name: ARCELOR FRANCE

    Effective date: 20060614

    PLBI Opposition filed

    Free format text: ORIGINAL CODE: 0009260

    PLAX Notice of opposition and request to file observation + time limit sent

    Free format text: ORIGINAL CODE: EPIDOSNOBS2

    26 Opposition filed

    Opponent name: THYSSEN KRUPP STAHL AG

    Effective date: 20060907

    NLR1 Nl: opposition has been filed with the epo

    Opponent name: THYSSEN KRUPP STAHL AG

    PLAF Information modified related to communication of a notice of opposition and request to file observations + time limit

    Free format text: ORIGINAL CODE: EPIDOSCOBS2

    PLBB Reply of patent proprietor to notice(s) of opposition received

    Free format text: ORIGINAL CODE: EPIDOSNOBS3

    REG Reference to a national code

    Ref country code: CH

    Ref legal event code: PL

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: LI

    Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

    Effective date: 20070331

    Ref country code: CH

    Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

    Effective date: 20070331

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: EE

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20051207

    PLCK Communication despatched that opposition was rejected

    Free format text: ORIGINAL CODE: EPIDOSNREJ1

    PLBN Opposition rejected

    Free format text: ORIGINAL CODE: 0009273

    STAA Information on the status of an ep patent application or granted ep patent

    Free format text: STATUS: OPPOSITION REJECTED

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: CY

    Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

    Effective date: 20051207

    27O Opposition rejected

    Effective date: 20080710

    REG Reference to a national code

    Ref country code: FR

    Ref legal event code: PLFP

    Year of fee payment: 14

    REG Reference to a national code

    Ref country code: FR

    Ref legal event code: PLFP

    Year of fee payment: 15

    REG Reference to a national code

    Ref country code: FR

    Ref legal event code: PLFP

    Year of fee payment: 16

    PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

    Ref country code: GB

    Payment date: 20220225

    Year of fee payment: 20

    Ref country code: DE

    Payment date: 20220217

    Year of fee payment: 20

    PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

    Ref country code: TR

    Payment date: 20220221

    Year of fee payment: 20

    Ref country code: SK

    Payment date: 20220224

    Year of fee payment: 20

    Ref country code: SE

    Payment date: 20220217

    Year of fee payment: 20

    Ref country code: NL

    Payment date: 20220217

    Year of fee payment: 20

    Ref country code: IT

    Payment date: 20220217

    Year of fee payment: 20

    Ref country code: FR

    Payment date: 20220221

    Year of fee payment: 20

    Ref country code: CZ

    Payment date: 20220223

    Year of fee payment: 20

    Ref country code: BE

    Payment date: 20220217

    Year of fee payment: 20

    PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

    Ref country code: ES

    Payment date: 20220401

    Year of fee payment: 20

    REG Reference to a national code

    Ref country code: DE

    Ref legal event code: R071

    Ref document number: 60302659

    Country of ref document: DE

    REG Reference to a national code

    Ref country code: NL

    Ref legal event code: MK

    Effective date: 20230309

    REG Reference to a national code

    Ref country code: BE

    Ref legal event code: MK

    Effective date: 20230310

    Ref country code: GB

    Ref legal event code: PE20

    Expiry date: 20230309

    Ref country code: SK

    Ref legal event code: MK4A

    Ref document number: E 445

    Country of ref document: SK

    Expiry date: 20230310

    REG Reference to a national code

    Ref country code: ES

    Ref legal event code: FD2A

    Effective date: 20230427

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: CZ

    Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

    Effective date: 20230310

    REG Reference to a national code

    Ref country code: SE

    Ref legal event code: EUG

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: SK

    Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

    Effective date: 20230310

    Ref country code: GB

    Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

    Effective date: 20230309

    PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

    Ref country code: ES

    Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

    Effective date: 20230311