EP1138796B1 - High strength hot rolled steel with high yield strength for use in the car industry - Google Patents

High strength hot rolled steel with high yield strength for use in the car industry Download PDF

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Publication number
EP1138796B1
EP1138796B1 EP01400777A EP01400777A EP1138796B1 EP 1138796 B1 EP1138796 B1 EP 1138796B1 EP 01400777 A EP01400777 A EP 01400777A EP 01400777 A EP01400777 A EP 01400777A EP 1138796 B1 EP1138796 B1 EP 1138796B1
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Prior art keywords
vanadium
steel
strength
hot
yield strength
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EP01400777A
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German (de)
French (fr)
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EP1138796A1 (en
Inventor
Xavier Bano
Jacques Devroc
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ArcelorMittal France SA
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Arcelor France SA
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite

Definitions

  • the invention relates to a hot-rolled steel with a very high yield strength and a mechanical strength that can be used in particular for producing automotive parts.
  • the service life of the parts obtained by shaping from these sheets is an important criterion since it defines the service life of shaped parts, as for example by stamping, profiling or hydroforming.
  • the service life associated with the fatigue behavior defines the service life for specific loads.
  • one solution consists of the use of very high strength steels which have significant fatigue properties because, as a first approximation, there is a proportional relationship between the limit of endurance and mechanical resistance. Nevertheless, the steel must be suitable for stamping. However, in general, the shaping properties decrease with the increase of the mechanical strength thus limiting the possibilities of shaping workable parts with high strength steels.
  • Shock resistance is also an important property for safety reasons, particularly in automotive applications, since the impact strength defines the abrupt breaking strength of the parts.
  • the impact strength defines the abrupt breaking strength of the parts.
  • one solution consists of the use of steels with a very high yield strength because there is, as a first approximation, a linear relationship between the impact resistance and the yield strength. .
  • the shaping properties decrease with increasing yield strength.
  • HLE steels high yield strength steels, are micro alloyed steels with a yield strength of 315 MPa to 700 MPa, but which have a limited formability due, in particular, to a ratio of Re / Rm higher than 0.85. These steels have a ferrite-carbide phase structure of the cementite type.
  • the level of yield strength is obtained by controlled rolling and a precipitation of the micro-alloy elements such as niobium, vanadium, titanium during the ferritic transformation.
  • Dual-Phase steels are steels of ferrite-martensite structure with remarkable shaping properties.
  • the mechanical strength levels are generally between 550 MPa and 800 MPa.
  • the highest level is achieved by precipitation of micro-alloy elements during ferritic transformation that complements the hardening effect of martensite.
  • HR steels are so-called high-strength steels, carbon and manganese, undergoing after rolling, a relatively fast cooling associated with a low temperature winding to give them a ferritic-bainitic structure. They have an intermediate formability characteristic between HLE steels and Dual-Phase steels. The resistance level varies between 450 MPa and 800 MPa.
  • Martensitic steels with the highest resistance levels. These steels have a martensitic structure obtained by heat treatment after rolling. The realization of this type of structure on a broadband train is difficult because of the fragility of martensite which leads to breaks in the strip after rolling. Martensitic steels allow to reach resistance levels higher than 1000 MPa but with a very low level of ductility and elongations of less than 8%. It is also necessary to carry out a heat treatment after rolling.
  • DE 197 10 125 discloses a hot rolled steel having a bainitic structure and its method of manufacture.
  • the object of the invention is to present a hot rolled steel with a very high yield strength and mechanical strength having good forming properties for the production of parts by stamping, profiling, hydroforming especially for the automotive industry.
  • the cooling cycle from a temperature between 400 ° C and 600 ° C, and preferably to a temperature between 450 ° C and 500 ° C is performed in coil.
  • Table 1 shows the results obtained for an application example B according to the invention, framed by two comparison examples A and C, the analyzes of the two comparison examples comprising, one, a low vanadium content, the other a high vanadium content.
  • Table 1 Steel VS mn Cr MB Yes NOT V P AT 0.11 1.58 0.51 0.33 0.2 0.0035 0 0.02 B 0.11 1.58 0.51 0.32 0.2 0.0040 0.2 0.02 VS 0.11 1.58 0.51 0.34 0.2 0.0050 0.45 0.02
  • Table 2 gives the conditions of the heat treatment after hot rolling. Steel Tem rolling ° C Cooling speed. ° C / s Winding time.
  • Table 3 presents the mechanical characteristics in mechanical strength Rm, yield strength Re, and elongation A, of the three exemplary embodiments.
  • vanadium increases mechanical strength and reduces elongation. Vanadium is the necessary element in bainitic steel for the realization of a hardening effect, which is unexpected because the micro-alloy elements have a precipitation-hardening effect but this precipitation is completely finished to higher. temperature and must be in the ferritic field to be hardening.
  • the final structure of the steel according to the invention is a bainitic structure. This structure makes it possible to obtain a yield strength greater than 700 MPa, a resistance mechanical greater than 1000 MPa and an elongation greater than 10%. These values show the good shaping properties of the steel according to the invention.
  • the invention allows the rolling of a steel having a thickness of between 1.4 and 5 mm which has both a high mechanical strength, that is to say greater than 1000 MPa and shaping properties remarkable, thanks to an elongation greater than 10%.
  • the surface state, without defects, after stripping of the hot-rolled sheet is ensured in the composition of the steel by a silicon content of less than 0.5%.
  • the strip of hot-rolled steel sheet of the invention has an advantage in its use in sectors of activity such as for example the automobile and mechanical engineering in general, for stamped, folded, profiled or hydroformed parts, parts that can be lightened while ensuring fatigue performance, improved impact performance and a combination of these benefits.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Laminated Bodies (AREA)
  • Heat Treatment Of Steel (AREA)
  • Body Structure For Vehicles (AREA)

Description

L'invention concerne un acier laminé à chaud à très haute limite d'élasticité et résistance mécanique utilisable notamment pour la réalisation de pièce de véhicules automobiles.The invention relates to a hot-rolled steel with a very high yield strength and a mechanical strength that can be used in particular for producing automotive parts.

Dans le domaine de la réalisation de tôles d'acier laminées à chaud, acier dont les caractéristiques sont obtenues par un laminage contrôlé, il est connu des produits à limite d'élasticité élevée, c'est à dire comprise entre 315 MPa et 700 MPa.In the field of producing hot-rolled steel sheet, steel whose characteristics are obtained by controlled rolling, it is known products with high yield strength, that is to say between 315 MPa and 700 MPa .

Dans le domaine des tôles laminées à chaud issues d'un train à bande, la tenue en service des pièces obtenues par mise en forme à partir de ces tôles est un critère important puisqu'elle définit la durée de vie des pièces mises en forme, comme par exemple par emboutissage, profilage ou hydroformage.In the field of hot rolled sheet from a belt train, the service life of the parts obtained by shaping from these sheets is an important criterion since it defines the service life of shaped parts, as for example by stamping, profiling or hydroforming.

La tenue en service liée à la tenue en fatigue définit la durée de vie pour des charges déterminées.The service life associated with the fatigue behavior defines the service life for specific loads.

Afin d'améliorer la tenue en fatigue de pièces mises en forme, une solution consiste en l'utilisation d'aciers à très haute résistance qui présentent des propriétés en fatigue importantes car il existe en première approximation, une relation proportionnelle entre la limite d'endurance et la résistance mécanique. Il faut néanmoins que l'acier soit apte à l'emboutissage. Or, en général, les propriétés de mise en forme diminuent avec l'augmentation de la résistance mécanique limitant ainsi les possibilités de mise en forme de pièces réalisables avec les aciers à haute résistance.In order to improve the fatigue strength of shaped parts, one solution consists of the use of very high strength steels which have significant fatigue properties because, as a first approximation, there is a proportional relationship between the limit of endurance and mechanical resistance. Nevertheless, the steel must be suitable for stamping. However, in general, the shaping properties decrease with the increase of the mechanical strength thus limiting the possibilities of shaping workable parts with high strength steels.

La tenue au choc est également une propriété importante pour des raisons de sécurité notamment dans des applications concernant l'automobile, puisque la tenue au choc définit la résistance à la rupture brutale des pièces. Afin d'améliorer cette propriété des pièces mises en forme, une solution consiste en l'utilisation d'aciers à très haute limite d'élasticité car il existe en première approximation, une relation linéaire entre la résistance au choc et la limite d'élasticité. Cependant, en général, les propriétés de mise en forme diminuent avec l'augmentation de la limite d'élasticité.Shock resistance is also an important property for safety reasons, particularly in automotive applications, since the impact strength defines the abrupt breaking strength of the parts. In order to improve this property of shaped parts, one solution consists of the use of steels with a very high yield strength because there is, as a first approximation, a linear relationship between the impact resistance and the yield strength. . However, in general, the shaping properties decrease with increasing yield strength.

Dans la gamme des produits plats courants laminés à chaud, dont les caractéristiques mécaniques sont obtenues par laminage contrôlé sur un train à large bande, il existe notamment quatre familles principales d'aciers à caractéristiques mécaniques élevées.In the range of hot-rolled flat products, whose mechanical characteristics are obtained by controlled rolling on a broadband train, there are in particular four main families of steels with high mechanical characteristics.

Les aciers HLE, aciers à haute limite d'élasticité, sont des aciers micro alliés qui présentent une limite d'élasticité comprise entre 315 MPa et 700 MPa, mais qui possèdent une aptitude au formage limitée du fait, en particulier, d'un rapport Re/Rm élevé supérieur à 0,85. Ces aciers présentent une structure ferrite-phase carburée du type cémentite. Le niveau de limite d'élasticité est obtenu par un laminage contrôlé et une précipitation des éléments de micro alliage tels que niobium, vanadium, titane lors de la transformation ferritique.HLE steels, high yield strength steels, are micro alloyed steels with a yield strength of 315 MPa to 700 MPa, but which have a limited formability due, in particular, to a ratio of Re / Rm higher than 0.85. These steels have a ferrite-carbide phase structure of the cementite type. The level of yield strength is obtained by controlled rolling and a precipitation of the micro-alloy elements such as niobium, vanadium, titanium during the ferritic transformation.

Les aciers Dual-Phase sont des aciers de structure ferrite-martensite ayant une propriété de mise en forme remarquable. Les niveaux de résistance mécanique sont généralement compris entre 550 MPa et 800 MPa. Le niveau le plus élevé est obtenu par précipitation d'éléments de micro alliage lors de la transformation ferritique qui vient compléter l'effet durcissant de la martensite.Dual-Phase steels are steels of ferrite-martensite structure with remarkable shaping properties. The mechanical strength levels are generally between 550 MPa and 800 MPa. The highest level is achieved by precipitation of micro-alloy elements during ferritic transformation that complements the hardening effect of martensite.

Les aciers HR sont des aciers dits haute résistance, au carbone et au manganèse, subissant après laminage, un refroidissement relativement rapide associé à un bobinage à basse température pour leur conférer une structure ferrito-bainitique. Ils ont une caractéristique de formabilité intermédiaire entre les aciers HLE et les aciers Dual-Phase. Le niveau de résistance varie entre 450 MPa et 800 MPa.HR steels are so-called high-strength steels, carbon and manganese, undergoing after rolling, a relatively fast cooling associated with a low temperature winding to give them a ferritic-bainitic structure. They have an intermediate formability characteristic between HLE steels and Dual-Phase steels. The resistance level varies between 450 MPa and 800 MPa.

Les aciers martensitiques dont les niveaux de résistance sont les plus élevés. Ces aciers ont une structure martensitique obtenue par traitement thermique après laminage. La réalisation de ce type de structure sur un train à large bande est difficile de par la fragilité de la martensite qui conduit à des ruptures de la bande après laminage. Les aciers martensitiques permettent d'atteindre des niveaux de résistance supérieurs à 1000 MPa mais avec un niveau de ductilité très faible et des allongements inférieurs à 8%. Il est de plus nécessaire de réaliser un traitement thermique après laminage.Martensitic steels with the highest resistance levels. These steels have a martensitic structure obtained by heat treatment after rolling. The realization of this type of structure on a broadband train is difficult because of the fragility of martensite which leads to breaks in the strip after rolling. Martensitic steels allow to reach resistance levels higher than 1000 MPa but with a very low level of ductility and elongations of less than 8%. It is also necessary to carry out a heat treatment after rolling.

DE 197 10 125 décrit un acier laminé à chaud ayant une structure bainitique et son procédé de fabrication.DE 197 10 125 discloses a hot rolled steel having a bainitic structure and its method of manufacture.

L'augmentation du niveau de résistance de l'ensemble des aciers ci-dessus cités s'accompagne d'une augmentation des efforts de laminage qui limite la réduction d'épaisseur ne permettant pas de bénéficier complètement des possibilités d'allègement.The increase in the level of resistance of all the aforementioned steels is accompanied by an increase in rolling forces which limits the thickness reduction that does not fully benefit from the lightening possibilities.

Le but de l'invention est de présenter un acier laminé à chaud à très haute limite d'élasticité et résistance mécanique présentant de bonnes propriétés de mise en forme pour la réalisation de pièces par emboutissage, profilage, hydroformage notamment pour l'industrie automobile.The object of the invention is to present a hot rolled steel with a very high yield strength and mechanical strength having good forming properties for the production of parts by stamping, profiling, hydroforming especially for the automotive industry.

L'objet de l'invention est un acier laminé à chaud à très haute limite d'élasticité et résistance mécanique présentant une structure entièrement bainitique, utilisable notamment pour la réalisation de pièce de véhicules automobiles caractérisée en la composition pondérale suivante :

  • 0,08% < carbone < 0,2%
  • 1% < manganèse < 2%
  • 0,02% < aluminium < 0,1%
  • silicium < 0,5%
  • phosphore < 0,03%
  • soufre < 0,01%
  • 0,1% < vanadium < 0,3%
  • chrome < 1%
  • azote < 0,015%
  • Molybdène < 0,6%
le reste étant du fer et des impuretés inhérentes à l'élaboration.The object of the invention is a hot rolled steel with a very high yield strength and mechanical strength having a completely bainitic structure, usable in particular for the production of motor vehicle parts characterized by the following weight composition:
  • 0.08% <carbon <0.2%
  • 1% <manganese <2%
  • 0.02% <aluminum <0.1%
  • silicon <0.5%
  • phosphorus <0.03%
  • sulfur <0.01%
  • 0.1% <vanadium <0.3%
  • chrome <1%
  • nitrogen <0.015%
  • Molybdenum <0.6%
the rest being iron and impurities inherent in the elaboration.

De préférence, l'acier est caractérisé en la composition pondérale suivante :

  • 0,1% < carbone < 0,14%
  • 1,4% < manganèse < 1,8%
  • 0,02% < aluminium < 0,08%
  • 0,15% < silicium < 0,3%
  • phosphore < 0,03%
  • soufre < 0,008%
  • 0,1% < vanadium < 0,3%
  • 0,3% < chrome < 0,6%
  • azote < 0,012%
  • 0,15 < molybdène < 0,4
le reste étant du fer et des impuretés inhérentes à l'élaboration. L'invention concerne également un procédé de réalisation d'une bande de tôle d'acier laminée à chaud à très haute résistance présentant une structure entièrement bainitique, utilisable notamment pour la réalisation de pièce de véhicules automobiles caractérisée en ce que l'acier de composition pondérale suivante
  • 0,08% < carbone < 0,2%
  • 1% < manganèse < 2%
  • 0,02% < aluminium < 0,1%
  • silicium < 0,5%
  • phosphore < 0,03%
  • soufre < 0,01%
  • 0,1% < vanadium < 0,3%
  • chrome < 1%
  • azote < 0,015%
  • molybdène < 0,6%
le reste étant du fer et des impuretés inhérentes à l'élaboration est soumis à
  • un laminage à une température inférieure à 950°C et de préférence inférieure à 880°C,
  • un refroidissement effectué à une vitesse supérieure à 20°C par seconde, et de préférence à une vitesse comprise entre 100°C et 200°C par seconde jusqu'à une température comprise entre 400°C et 600°C, et de préférence jusqu'à une température comprise entre 450°C et 500°C.
Preferably, the steel is characterized in the following composition by weight:
  • 0.1% <carbon <0.14%
  • 1.4% <manganese <1.8%
  • 0.02% <aluminum <0.08%
  • 0.15% <silicon <0.3%
  • phosphorus <0.03%
  • sulfur <0.008%
  • 0.1% <vanadium <0.3%
  • 0.3% <chromium <0.6%
  • nitrogen <0.012%
  • 0.15 <molybdenum <0.4
the rest being iron and impurities inherent in the elaboration. The invention also relates to a method for producing a strip of hot-rolled steel sheet with a very high strength having a completely bainitic structure, used in particular for the production of motor vehicle parts characterized in that the composition steel following weight
  • 0.08% <carbon <0.2%
  • 1% <manganese <2%
  • 0.02% <aluminum <0.1%
  • silicon <0.5%
  • phosphorus <0.03%
  • sulfur <0.01%
  • 0.1% <vanadium <0.3%
  • chrome <1%
  • nitrogen <0.015%
  • molybdenum <0.6%
the rest being iron and impurities inherent in the making is subject to
  • rolling at a temperature below 950 ° C and preferably below 880 ° C,
  • cooling carried out at a rate greater than 20 ° C per second, and preferably at a rate of between 100 ° C and 200 ° C per second to a temperature between 400 ° C and 600 ° C, and preferably up to at a temperature between 450 ° C and 500 ° C.

La description qui suit et les figures annexées, le tout donné à titre d'exemple non limitatif, fera bien comprendre l'invention.

  • La figure 1 est un schéma présentant la variation de température en fonction de temps lors du refroidissement de la bande d'acier laminé à chaud.
  • La figure 2 présente une courbe d'allongement en fonction de la contrainte pour un acier selon l'invention.
L'acier selon l'invention, dont la composition pondérale est la suivante :
  • 0,08% < carbone < 0,2%
  • 1% < manganèse < 2%
  • 0,02% < aluminium < 0,1%
  • silicium < 0,5%
  • phosphore < 0,03%
  • soufre < 0,01%
  • 0,1% < vanadium < 0,3%
  • chrome < 1%
  • azote < 0,015%
  • molybdène < 0,6%
le reste étant du fer et des impuretés inhérentes à l'élaboration, possède une structure entièrement bainitique. Sous cette forme, il est possible d'atteindre un niveau de résistance supérieur à 1000 MPa avec un allongement supérieur à 10%.
L'acier mis sous forme d'une bande laminée à chaud selon l'invention est soumis à:
  • un laminage à une température inférieure à 950°C et de préférence inférieure à 880°C,
  • un refroidissement effectué à une vitesse supérieure à 20°C par seconde, et de préférence à une vitesse comprise entre 100°C et 200°C par seconde jusqu'à une température comprise entre 400°C et 600°C, et de préférence jusqu'à une température comprise entre 450°C et 500°C.
The description which follows and the appended figures, all given by way of non-limiting example, will make the invention clear.
  • Fig. 1 is a diagram showing temperature variation as a function of time during cooling of the hot rolled steel strip.
  • FIG. 2 shows an elongation curve as a function of the stress for a steel according to the invention.
The steel according to the invention, whose weight composition is as follows:
  • 0.08% <carbon <0.2%
  • 1% <manganese <2%
  • 0.02% <aluminum <0.1%
  • silicon <0.5%
  • phosphorus <0.03%
  • sulfur <0.01%
  • 0.1% <vanadium <0.3%
  • chrome <1%
  • nitrogen <0.015%
  • molybdenum <0.6%
the rest being iron and impurities inherent in the elaboration, has a completely bainitic structure. In this form, it is possible to achieve a level of resistance greater than 1000 MPa with an elongation greater than 10%.
The steel formed into a hot-rolled strip according to the invention is subjected to:
  • rolling at a temperature below 950 ° C and preferably below 880 ° C,
  • cooling carried out at a rate greater than 20 ° C per second, and preferably at a rate of between 100 ° C and 200 ° C per second to a temperature between 400 ° C and 600 ° C, and preferably up to at a temperature between 450 ° C and 500 ° C.

Comme représenté sur le schéma de la figure 1, le cycle de refroidissement à partir d'une température comprise entre 400°C et 600°C, et de préférence jusqu'à une température comprise entre 450°C et 500°C est effectué en bobine.As shown in the diagram of Figure 1, the cooling cycle from a temperature between 400 ° C and 600 ° C, and preferably to a temperature between 450 ° C and 500 ° C is performed in coil.

Du point de vue de la composition de l'acier selon l'invention :

  • le carbone limité à 0,2% permet d'assurer une bonne soudabilité tout en permettant un durcissement par précipitation avec le vanadium.
  • le manganèse permet d'abaisser les points de transformation AR3, Bs et Ms qui correspondent respectivement, à la température de début de la transformation ferritique, à la température de début de la transformation bainitique et à la température de début de la transformation martensitique. Il permet de par cet effet d'augmenter la trempabilité en évitant de former de la ferrite du fait des vitesses de refroidissement élevées et d'obtenir une structure entièrement bainitique. Le début de transformation bainitique (Bs) abaissé permet d'augmenter les propriétés mécaniques.
  • l'aluminium est utilisé pour calmer l'acier.
  • le silicium est conservé à des teneurs relativement faibles pour bénéficier du pouvoir durcissant en solution solide qu'il apporte sans dégrader l'état de surface après décapage, ni la revêtabilité du produit sur ligne de galvanisation ou d'électrozingage en continue. Le silicium est connu pour dégrader d'une part, l'aspect de surface des produits décapés par la formation de Fe2O3SiO4 et d'autre part, la mouillabilité et donc, l'adhérence des revêtements.
  • le molybdène, par son effet de trempabilité notamment une diminution de Bs, permet d'augmenter les propriétés mécaniques et cela par la formation d'une structure entièrement bainitique.
  • le vanadium est l'élément nécessaire à la formation de précipité de type nitrures et carbures qui se forment à différentes températures au cours du traitement thermomécanique. Ces précipités très durcissants permettent d'atteindre le niveau de propriétés mécaniques très élevé. Cet élément permet ce durcissement par précipitation sans augmentation de la dureté à chaud. Cet effet est contradictoire avec les effets connus des éléments de micro alliage qui, par précipitation induite au cours du laminage, conduisent à une augmentation de ladite dureté à chaud. Cette constatation a permis aux inventeurs d'obtenir, avec l'élément vanadium contenu dans l'acier selon l'invention, de laminer de fines épaisseurs de tôle jusqu'à 1,4 mm d'épaisseur sans augmentation des efforts de laminage.
From the point of view of the composition of the steel according to the invention:
  • the carbon limited to 0.2% ensures good weldability while allowing precipitation hardening with vanadium.
  • the manganese makes it possible to lower the transformation points AR3, Bs and Ms which respectively correspond, at the start temperature of the ferritic transformation, to the start temperature of the bainitic transformation and to the start temperature of the martensitic transformation. It allows for this effect to increase the quenchability avoiding the formation of ferrite due to high cooling rates and to obtain a completely bainitic structure. The beginning of bainitic transformation (Bs) lowered allows to increase the mechanical properties.
  • aluminum is used to calm the steel.
  • the silicon is stored at relatively low levels to benefit from the solid solution hardening power that it provides without degrading the surface state after pickling, nor the coating of the product on continuous galvanizing line or electrogaling. Silicon is known to degrade, on the one hand, the surface appearance of the products stripped by the Fe 2 O 3 SiO 4 formation and, on the other hand, the wettability and therefore the adhesion of the coatings.
  • molybdenum, by its quenching effect, in particular a decrease in Bs, makes it possible to increase the mechanical properties and this by the formation of an entirely bainitic structure.
  • vanadium is the element necessary for the formation of nitride and carbide precipitates which form at different temperatures during the thermomechanical treatment. These very hardening precipitates make it possible to reach the level of very high mechanical properties. This element allows this hardening by precipitation without increasing the hardness when hot. This effect is contradictory with the known effects of micro-alloy elements which, by precipitation induced during rolling, lead to an increase in said hardness when hot. This finding allowed the inventors to obtain, with the vanadium element contained in the steel according to the invention, laminating thin sheet thicknesses up to 1.4 mm thick without increasing the rolling forces.

Les exemples ci-dessous présentent les résultats obtenus pour un exemple B d'application selon l'invention encadrée par deux exemples de comparaison A et C, les analyses des deux exemples de comparaison comportant, l'une, une teneur en vanadium faible, l'autre une teneur en vanadium élevée.
Les compositions des exemples sont présentées sur le tableau 1 suivant : Tableau 1. Acier C Mn Cr Mo Si N V P A 0,11 1,58 0,51 0,33 0,2 0,0035 0 0,02 B 0,11 1,58 0,51 0,32 0,2 0,0040 0,2 0,02 C 0,11 1,58 0,51 0,34 0,2 0,0050 0,45 0,02 Le tableau 2 suivant donne les conditions du traitement thermique après le laminage à chaud. Tableau 2. Acier Tem de laminage °C Vitesse de refroidissement. °C/s Temps de bobinage. °C A 900 65 450 B 885 40 450 C 890 50 450 Le tableau 3 suivant présente les caractéristiques mécaniques en résistance mécanique Rm, limite d'élasticité Re, et allongement A, des trois exemples de réalisation. Tableau 3. Acier Rm (MPa) Re (MPa) A (%) A 790 670 14 B 1090 990 10,4 C 1125 1015 8,9 On peut remarquer que le vanadium augmente la résistance mécanique et réduit l'allongement. Le vanadium est l'élément nécessaire, dans l'acier à structure bainitique, pour la réalisation d'un effet durcissant, ce qui est inattendu car les éléments de micro alliage ont un effet durcissant par précipitation mais cette précipitation est complètement terminée à plus haute température et doit se faire dans le domaine ferritique pour pouvoir être durcissante. Cet effet ne peut être obtenu par d'autres éléments de micro alliage comme le titane ou le niobium car ces éléments conduisent à une augmentation de la dureté à chaud qui limite les taux de réduction en laminage à chaud et donc l'épaisseur minimale réalisable pour ce type de tôle. Il s'avère que le vanadium n'a pas d'effet sur la dureté à chaud.The examples below show the results obtained for an application example B according to the invention, framed by two comparison examples A and C, the analyzes of the two comparison examples comprising, one, a low vanadium content, the other a high vanadium content.
The compositions of the examples are presented in the following Table 1: Table 1. Steel VS mn Cr MB Yes NOT V P AT 0.11 1.58 0.51 0.33 0.2 0.0035 0 0.02 B 0.11 1.58 0.51 0.32 0.2 0.0040 0.2 0.02 VS 0.11 1.58 0.51 0.34 0.2 0.0050 0.45 0.02 Table 2 below gives the conditions of the heat treatment after hot rolling. Steel Tem rolling ° C Cooling speed. ° C / s Winding time. ° C AT 900 65 450 B 885 40 450 VS 890 50 450 Table 3 below presents the mechanical characteristics in mechanical strength Rm, yield strength Re, and elongation A, of the three exemplary embodiments. Steel Rm (MPa) Re (MPa) AT (%) AT 790 670 14 B 1090 990 10.4 VS 1125 1015 8.9 It can be noted that vanadium increases mechanical strength and reduces elongation. Vanadium is the necessary element in bainitic steel for the realization of a hardening effect, which is unexpected because the micro-alloy elements have a precipitation-hardening effect but this precipitation is completely finished to higher. temperature and must be in the ferritic field to be hardening. This effect can not be obtained by other micro-alloy elements such as titanium or niobium because these elements lead to an increase in the hot hardness which limits the reduction rates in hot rolling and therefore the minimum thickness achievable for this type of sheet. It turns out that vanadium has no effect on hot hardness.

D'autres éléments résiduels peuvent être présents et utilisés en fonction de leurs propriétés connues comme le Cu, Ni. L'ajout d'éléments d'alliage comme le titane ou le bore peuvent être utilisés pour favoriser la précipitation des carbures de vanadium au dépend des nitrures de vanadium. Le titane et le bore forment des nitrures à haute température qui restent stables au cours du traitement thermomécanique ultérieur.Other residual elements may be present and used depending on their known properties such as Cu, Ni. The addition of alloying elements such as titanium or boron can be used to promote the precipitation of vanadium carbides at the expense of vanadium nitrides. Titanium and boron form high temperature nitrides which remain stable during subsequent thermomechanical treatment.

Des essais industriels ont été réalisés sur la base de l'analyse B présentée dans le tableau n°4.
Tableau n°4 C% Mn% Cr% N% V % Mo % Al % Si % 0,124 1,560 0,389 0,0051 0,189 0,280 0,031 0,185 Un exemple de propriété mécanique obtenue pour une épaisseur de 1,7 mm est présenté sur la figure 2 à travers une courbe de traction.
Les caractéristiques de l'acier sont une résistance mécanique de 1015 MPa, une limite d'élasticité de 880 MPa, un allongement de 12%.Industrial tests were carried out on the basis of the analysis B presented in Table 4.
Table n ° 4 VS% mn% Cr% NOT% V% Mo% Al% Yes % 0.124 1,560 0.389 0.0051 0.189 0,280 0.031 0.185 An example of mechanical property obtained for a thickness of 1.7 mm is presented in Figure 2 through a tensile curve.
The characteristics of the steel are a mechanical strength of 1015 MPa, a yield strength of 880 MPa, an elongation of 12%.

La structure finale de l'acier selon l'invention est une structure bainitique. Cette structure permet d'obtenir une limite d'élasticité supérieure à 700 MPa, une résistance mécanique supérieure à 1000 MPa et un allongement supérieur à 10%. Ces valeurs montrent les bonnes propriétés de mise en forme de l'acier selon l'invention.The final structure of the steel according to the invention is a bainitic structure. This structure makes it possible to obtain a yield strength greater than 700 MPa, a resistance mechanical greater than 1000 MPa and an elongation greater than 10%. These values show the good shaping properties of the steel according to the invention.

L'invention permet le laminage d'un acier ayant une épaisseur comprise entre 1,4 et 5 mm qui possède à la fois, une résistance mécanique élevée, c'est-à-dire supérieure à 1000 MPa et des propriétés de mise en forme remarquables, grâce à un allongement supérieur à 10%.The invention allows the rolling of a steel having a thickness of between 1.4 and 5 mm which has both a high mechanical strength, that is to say greater than 1000 MPa and shaping properties remarkable, thanks to an elongation greater than 10%.

L'état de surface, sans défaut, après le décapage de la tôle laminée à chaud est assuré, dans la composition de l'acier, par une teneur en silicium inférieure à 0,5%.The surface state, without defects, after stripping of the hot-rolled sheet is ensured in the composition of the steel by a silicon content of less than 0.5%.

La bande de tôle d'acier laminée à chaud de l'invention présente un avantage dans son utilisation dans des secteurs d'activité comme par exemple l'automobile et la construction mécanique en général, pour des pièces embouties, pliées, profilées ou hydroformées, pièces pouvant être allégées tout en assurant des performances en fatigue, une amélioration des performances au choc et une combinaison de ces avantages.The strip of hot-rolled steel sheet of the invention has an advantage in its use in sectors of activity such as for example the automobile and mechanical engineering in general, for stamped, folded, profiled or hydroformed parts, parts that can be lightened while ensuring fatigue performance, improved impact performance and a combination of these benefits.

Claims (3)

  1. Hot-rolled steel of very high yield strength and tensile strength, having an entirely bainitic structure, which can be used in particular for the production of motor vehicle parts, characterized by the following composition by weight:
    0.08% < carbon < 0.2%;
    1% < manganese < 2%;
    0.02% < aluminium < 0.1%;
    silicon < 0.5%;
    phosphorus < 0.03%;
    sulphur < 0.01%;
    0.1% < vanadium < 0.3%;
    chromium < 1%;
    nitrogen < 0.015%;
    molybdenum < 0.6%,
    the balance being iron and impurities inherent in the smelting operation.
  2. Steel according to Claim 1, characterized by the following composition by weight:
    0.1% < carbon < 0.14%;
    1.4% < manganese < 1.8%;
    0.02% < aluminium < 0.08%;
    0.15% < silicon < 0.3%;
    phosphorus < 0.03%;
    sulphur < 0.008%;
    0.1% < vanadium < 0.3%;
    0.3% < chromium < 0.6%;
    nitrogen < 0.012%;
    0.15% < molybdenum < 0.4%,
    the balance being iron and impurities inherent in the smelting operation.
  3. Process for producing a hot-rolled strip of steel sheet of very high strength, having an entirely bainitic structure, which can be used in particular for the production of motor vehicle parts, characterized in that steel, of the following composition by weight:
    0.08% < carbon < 0.20%;
    1% < manganese < 2%;
    0.02 < aluminium < 0.1%;
    silicon < 0.5%;
    phosphorus < 0.03%;
    sulphur < 0.01%;
    0.1% < vanadium < 0.3%;
    chromium < 1%;
    nitrogen < 0.15%;
    molybdenum < 0.6%,
    the balance being iron and impurities inherent in the smelting operation,
    is subjected to:
    - a rolling step at a temperature below 950°C and preferably below 880°C; and
    - a cooling step carried out at a rate of greater than 20°C per second, and preferably at a rate between 100°C and 200°C per second, down to a temperature lying between 400°C and 600°C, and preferably down to a temperature lying between 450°C and 500°C
EP01400777A 2000-03-29 2001-03-27 High strength hot rolled steel with high yield strength for use in the car industry Expired - Lifetime EP1138796B1 (en)

Applications Claiming Priority (2)

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FR0003958 2000-03-29
FR0003958A FR2807068B1 (en) 2000-03-29 2000-03-29 HOT ROLLED STEEL WITH VERY HIGH LIMIT OF ELASTICITY AND MECHANICAL STRENGTH FOR USE IN PARTICULAR FOR THE PRODUCTION OF PARTS OF MOTOR VEHICLES

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US20030172512A1 (en) * 2002-03-12 2003-09-18 Suarez Carlos Infanzon Process for manufacturing fuel tanks by blast shaping of steel
FI114484B (en) † 2002-06-19 2004-10-29 Rautaruukki Oyj Hot rolled strip steel and its manufacturing process
CN101469403B (en) * 2003-02-18 2011-11-23 松下电器产业株式会社 Process for manufacturing plasma display panel and substrate holder
EP2020451A1 (en) * 2007-07-19 2009-02-04 ArcelorMittal France Method of manufacturing sheets of steel with high levels of strength and ductility, and sheets produced using same
FI20095528A (en) * 2009-05-11 2010-11-12 Rautaruukki Oyj Process for producing a hot rolled strip steel product and hot rolled strip steel product
FI122313B (en) * 2010-06-07 2011-11-30 Rautaruukki Oyj Process for the production of hot rolled steel product and hot rolled steel
CN110643894B (en) * 2018-06-27 2021-05-14 宝山钢铁股份有限公司 Ultra-high strength hot rolled steel sheet and steel strip having good fatigue and hole expansion properties, and method for manufacturing same
US20220056543A1 (en) 2018-09-20 2022-02-24 Arcelormittal Hot rolled steel sheet with high hole expansion ratio and manufacturing process thereof
WO2020065381A1 (en) 2018-09-28 2020-04-02 Arcelormittal Hot rolled steel sheet and a method of manufacturing thereof

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US5900075A (en) * 1994-12-06 1999-05-04 Exxon Research And Engineering Co. Ultra high strength, secondary hardening steels with superior toughness and weldability
US5743972A (en) * 1995-08-29 1998-04-28 Kawasaki Steel Corporation Heavy-wall structural steel and method
DE19719546C2 (en) * 1996-07-12 1998-12-03 Thyssen Stahl Ag Hot steel strip and process for its manufacture
JP3635803B2 (en) * 1996-09-10 2005-04-06 Ｊｆｅスチール株式会社 Method for producing high-tensile steel with excellent toughness
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ES2267692T3 (en) 2007-03-16
AR027746A1 (en) 2003-04-09
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CA2342256A1 (en) 2001-09-29
US6554919B2 (en) 2003-04-29
EP1138796A1 (en) 2001-10-04
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CA2342256C (en) 2009-10-06

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