EP0474530A1 - Process for manufacturing products with very high tensile strength from unstable austenitic steel, and products obtained - Google Patents

Process for manufacturing products with very high tensile strength from unstable austenitic steel, and products obtained Download PDF

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Publication number
EP0474530A1
EP0474530A1 EP91402232A EP91402232A EP0474530A1 EP 0474530 A1 EP0474530 A1 EP 0474530A1 EP 91402232 A EP91402232 A EP 91402232A EP 91402232 A EP91402232 A EP 91402232A EP 0474530 A1 EP0474530 A1 EP 0474530A1
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Prior art keywords
steel
deformation
temperature
martensite
composition
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German (de)
French (fr)
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EP0474530B1 (en
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Jean-Michel Hauser
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Ugitech SA
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Ugine Savoie SA
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    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • 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
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys

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  • the present invention relates to a process for producing products with a very high breaking load from an unstable austenitic steel, and the product obtained by this process, in particular in the form of a wire or strip.
  • This process is of the type in which the steel is subjected to a first plastic deformation at a temperature higher than the limit temperature (Md) for the formation of martensite by deformation and lower than the recrystallization temperature and then a second deformation of said steel to a temperature lower than said temperature (Md).
  • hot rolled steel prior to the first deformation, is subjected to a standard annealing heat treatment called hyper-tempering consisting in placing said steel under a temperature between 1000 and 1100 ° C for about 30 minutes.
  • the object of the invention is to control the formation of martensite so as to obtain products with particularly high tensile characteristics.
  • the steel is subjected to plastic deformation at a temperature above the limit temperature (Md) for forming martensite by deformation and below the recrystallization temperature.
  • Md limit temperature
  • the breaking load of the steel is greater than 1000 MPa, preferably greater than 1300 MPa.
  • the steel is deformed at a temperature below (Md), in a determined range of martensite formation temperature so that for an additional rational deformation of 0.1, the increase in the rate of martensite formed does not exceed 20% at any time.
  • the steel is deformed at a temperature below (Md) with a cumulative rational deformation of between 0.7 and 3, which corresponds to a section reduction rate included between 50 and 95%.
  • a minimum cumulative rational deformation of 0.7 is necessary to reach or slightly exceed the breaking loads envisaged in the drawing processes of the prior art.
  • the steel is subjected to an aging treatment.
  • a rational deformation greater than 1.65 corresponding to a reduction rate of section greater than 80% introduces into the steel a quantity of crystallographic defects sufficient in the form of dislocations to promote accommodation, that is to say the development of martensite platelets under the effect of cold deformation.
  • the reduction rate can be much higher than this minimum rate.
  • the products with very high breaking load according to the invention in particular in the form of wire or strip, are obtained by a plasticity effect induced by deformation.
  • Aging of steels subjected to warm work hardening, followed by cold work hardening according to the process can increase the breaking load by around 200 MPa and sometimes more depending on the grade of steel used.
  • the conditions for obtaining high tensile strengths are attached on the one hand to the mechanical characteristics obtained during lukewarm hardening, the steel having to have at least one tensile strength greater than 1000 MPa and on the other hand to the conditions of cold work hardening, according to which the work hardening of the steel is carried out in a determined range of temperature, called critical field of temperature of deformation of martensite, so that for an additional rational formation of 0.1, the increase in the rate of martensite formed does not exceed, at any time, 20%.
  • rational deformation is meant the logarithm of the ratio of the surface S of the section after deformation on the surface So of the initial section (In S / So).
  • the determined range of martensite formation temperature is, for the steels taken as an example, included in the range -20 ° C. + 180 ° C. Indeed, beyond + 180 ° C there is no longer an appreciable amount of martensite, while below -20 ° C the formation of martensite is excessive.
  • the basic thread used in these three examples is a wire rod about 5.6mm in diameter; the wire is cold-worked at 250 ° C in several passes up to a diameter of approximately 2mm, then this wire is cold drawn at room temperature of 20 ° C in order to obtain a wire of approximately 0.5mm in diameter, the section reduction rates per drawing pass being approximately 25%. After each drawing pass the wire returns to room temperature before another pass.
  • the number of lukewarm passes is approximately 20, the number of cold passes being approximately 10.
  • the steel used for the implementation of the process is a steel referenced 1, having the following weight composition: 0.08% carbon, 18.6% chromium, 8.5% nickel, 0.3% manganese , 0.5% silicon, 0.04% nitrogen.
  • Curve 1A represents, for the steel referenced 1, the evolution of the rate of martensite as a function of the rational deformation, this rate of martensite reaching approximately 60% after cold drawing.
  • Curve 1B represents the evolution of the load at break during lukewarm hardening up to 1400 MPa then the evolution of the load at break during cold drawing thus reaching 2500 MPa; aging provides a breaking load of approximately 2700 Mpa.
  • the increase in breaking load is obtained by controlling the increase in the formation of martensite from one wire drawing pass to another.
  • the steel used is a steel referenced 2, having the following composition by weight: 0.09% carbon, 17.3% chromium, 8.3% nickel, 0.9% manganese, 0.8% silicon , 0.06% nitrogen.
  • Curve 2A illustrates for the steel referenced 2 the evolution of the rate of martensite as a function of the cumulative rational deformation, the rate of martensite reached being approximately 45%.
  • Curve 2B represents the evolution of the breaking load during lukewarm hardening, up to a breaking load of 1600 MPa, then the evolution of said breaking load during cold drawing, reaching about 2500 MPa.
  • the steel used is a steel referenced 3 and having the following composition: 0.09% carbon, 17.3% chromium, 7.7% nickel, 0.5% manganese, 0.8% silicon, 0.15% nitrogen, 1% aluminum.
  • the curve 3A represents for the steel referenced 3 the evolution of the rate of martensite as a function of the rational deformation, the rate of martensite being able to reach 95%.
  • Curve 3B represents the evolution of the load at break during lukewarm hardening, up to the load at rupture of approximately 1600 MPa, then the evolution of said load at break during cold drawing, reaching around 2300 Mpa.
  • the gain after heat treatment at 480 ° C. for 45 minutes is in this example approximately 300 MPa.
  • Such characteristics are obtained by the formation of martensite during cold drawing, slower formation on a product previously cold-worked at lukewarm than by direct cold drawing of the wire rod.
  • the first "lukewarm" deformation or work hardening operation may be a wire drawing, as described in the examples, but also a rolling, hammering or forging, twisting, alternating bending, or the like.
  • the second cold deformation operation can also take various aspects: drawing, rolling or other.

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  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
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Abstract

According to this process the steel is subjected to a first plastic deformation at a temperature above the limiting temperature (Md) of the formation of martensite by deformation and lower than the recrystallisation temperature, and then to a second deformation at a temperature lower than the said temperature (Md). During the second deformation the steel is deformed in a determined range of temperature of the formation of martensite so that, in the case of an additional rational deformation of 0.1, the increase in the content of martensite formed does not at any time exceed 20%.

Description

La présente invention concerne un procédé d'élaboration de produits à très haute charge à la rupture à partir d'un acier austénitique instable, et le produit obtenu par ce procédé, notamment sous forme de fil ou de bande. Ce procédé est du type dans lequel on soumet l'acier à une première déformation plastique à une température supérieure à la température limite (Md) de formation de la martensite par déformation et inférieure à la température de recristallisation puis à une seconde déformation dudit acier à une température inférieure à ladite température (Md).The present invention relates to a process for producing products with a very high breaking load from an unstable austenitic steel, and the product obtained by this process, in particular in the form of a wire or strip. This process is of the type in which the steel is subjected to a first plastic deformation at a temperature higher than the limit temperature (Md) for the formation of martensite by deformation and lower than the recrystallization temperature and then a second deformation of said steel to a temperature lower than said temperature (Md).

Généralement, l'acier laminé à chaud, préalablement à la première déformation, est soumis à un traitement thermique de recuit standard dit hyper-trempe consistant à placer ledit acier sous une température comprise entre 1000 et 1100°C pendant environ 30 minutes.Generally, hot rolled steel, prior to the first deformation, is subjected to a standard annealing heat treatment called hyper-tempering consisting in placing said steel under a temperature between 1000 and 1100 ° C for about 30 minutes.

Un tel procédé est connu. Un grand nombre d'études ont été faites sur le comportement en traction, au-dessous de la température limite (Md) de formation de la martensite par déformation, tant à la température ambiante qu'en dessous de la température ambiante, de matériaux à l'austénite instable, préalablement écrouis au-dessus de ladite température limite (Md) qui peut varier en fonction de la composition de l'acier austénitique entre -150°C et +250°C.Such a method is known. A large number of studies have been made on the tensile behavior, below the limit temperature (Md) of formation of martensite by deformation, both at room temperature and below room temperature, of materials to unstable austenite, previously hardened above said limit temperature (Md) which can vary depending on the composition of the austenitic steel between -150 ° C and + 250 ° C.

On peut citer le brevet US n° 4 415 377 décrivant un procédé et un dispositif pour laminer des aciers à austénite instable et particulièrement un acier inoxydable, procédé selon lequel l'acier est soumis :

  • à un premier laminage au-dessus de la température limite (Md) puis,
  • à un second laminage au-dessous de la température limite (Md).
Mention may be made of US Pat. No. 4,415,377 describing a process and a device for rolling unstable austenite steels and particularly stainless steel, process according to which the steel is subjected:
  • to a first rolling above the limit temperature (Md) then,
  • to a second rolling below the limit temperature (Md).

Ces deux laminages permettent d'obtenir de manière plus aisée des produits déterminés en dimension, c'est-à-dire de réduire le nombre de passes de laminage comparativement à l'obtention desdits produits par un laminage à froid, tout en conservant aux produits des caractéristiques mécaniques analogues.These two rolling operations make it possible to obtain products determined in size more easily, that is to say to reduce the number of rolling passes compared to obtaining said products by cold rolling, while keeping the products similar mechanical characteristics.

Le procédé décrit dans le brevet cité ne permet pas l'obtention de caractéristiques mécaniques particulières en comparaison avec un laminage à froid.The process described in the cited patent does not make it possible to obtain particular mechanical characteristics in comparison with cold rolling.

Le but de l'invention est de contrôler la formation de martensite de façon à obtenir des produits de caractéristiques en traction particulièrement élevées.The object of the invention is to control the formation of martensite so as to obtain products with particularly high tensile characteristics.

A cet effet, dans une première étape, on soumet l'acier à une déformation plastique à une température supérieure à la température limite (Md) de formation de la martensite par déformation et inférieure à la température de recristallisation. Afin d'obtenir des caractéristiques mécaniques en traction très élevées, on s'assure qu'après déformation plastique, la charge à la rupture de l'acier est supérieure à 1000 MPa, de préférence supérieure à 1300 MPa.To this end, in a first step, the steel is subjected to plastic deformation at a temperature above the limit temperature (Md) for forming martensite by deformation and below the recrystallization temperature. In order to obtain very high tensile mechanical characteristics, it is ensured that after plastic deformation, the breaking load of the steel is greater than 1000 MPa, preferably greater than 1300 MPa.

Dans une seconde étape, on déforme l'acier à une température inférieure à (Md), dans un domaine déterminé de température de formation de la martensite de façon que pour une déformation rationnelle supplémentaire de 0,1, l'augmentation du taux de martensite formée ne dépasse pas, à tout instant, 20%.In a second step, the steel is deformed at a temperature below (Md), in a determined range of martensite formation temperature so that for an additional rational deformation of 0.1, the increase in the rate of martensite formed does not exceed 20% at any time.

De préférence, on déforme l'acier à une température inférieure à (Md) avec une déformation rationnelle cumulée comprise entre 0,7 et 3, ce qui correspond à un taux de réduction de section compris entre 50 et 95%.Preferably, the steel is deformed at a temperature below (Md) with a cumulative rational deformation of between 0.7 and 3, which corresponds to a section reduction rate included between 50 and 95%.

Une déformation rationnelle cumulée minimale de 0,7 est nécessaire pour atteindre ou dépasser légèrement des charges à la rupture envisagées dans les procédés de tréfilage de l'art antérieur.A minimum cumulative rational deformation of 0.7 is necessary to reach or slightly exceed the breaking loads envisaged in the drawing processes of the prior art.

D'autre part, une déformation rationnelle cumulée ne peut dépasser 3, valeur correspondant à un seuil maximum admissible de fragilité de l'acier déformé.On the other hand, a cumulative rational deformation cannot exceed 3, a value corresponding to a maximum admissible threshold of brittleness of the deformed steel.

De préférence après la seconde déformation, on soumet l'acier à un traitement de vieillissement.Preferably after the second deformation, the steel is subjected to an aging treatment.

Une déformation rationnelle supérieure à 1,65 correspondant à un taux de réduction de section supérieure à 80% introduit, au sein de l'acier, une quantité de défauts cristallographiques suffisante sous forme de dislocations pour favoriser l'accommodation, c'est à dire le développement de plaquettes de martensite sous l'effet de la déformation à froid. Le taux de réduction peut être largement supérieur à ce taux minimum.A rational deformation greater than 1.65 corresponding to a reduction rate of section greater than 80% introduces into the steel a quantity of crystallographic defects sufficient in the form of dislocations to promote accommodation, that is to say the development of martensite platelets under the effect of cold deformation. The reduction rate can be much higher than this minimum rate.

L'invention concerne également un produit à très haute charge à la rupture obtenu par déformation, à partir d'un acier austénitique instable, sous forme notamment de fil ou de bande. Les caractéristiques du produit sont les suivantes :

  • l'acier austénitique est un acier comprenant dans sa composition :
    de 0,01 à
    0,15% de carbone
    de 13 à
    22 % de chrome
    de 5 à
    13 % de nickel
    de 0,2 à
    2,5 % de manganèse
    de 0,2 à
    3 % de silicium
    de 0,01 à
    0,15% d'azote,
    le reste étant du fer;
  • l'acier comprend en outre dans sa composition de 0,5 à 2% d'aluminium;
  • l'acier comprend en outre dans sa composition moins de 2% de molybdène;
  • l'acier austénitique est un acier comprenant dans sa composition :
    de 0,2 à
    1 % de carbone
    de 15 à
    30 % de manganèse
    de 0,01 à
    0,7% d'azote,
    le reste étant du fer;
  • l'acier comprend en outre moins de 5% de chrome et moins de 7% d'aluminium;
  • la charge à la rupture, avant vieillissement est supérieure à 2300 MPa;
  • l'acier austénitique est un acier com-prenant dans sa composition :
    de 0,1 à
    0,6 % de carbone
    de 6 à
    25 % de nickel
    de 0 à
    13 % de chrome
    de 0 à
    4 % de molybdène
    de 0 à
    3 % de silicium;
  • la charge à la rupture après vieillissement est supérieure à 2500 Mpa.
The invention also relates to a product with very high breaking load obtained by deformation, from an unstable austenitic steel, in the form in particular of wire or strip. The product features are:
  • Austenitic steel is a steel comprising in its composition:
    from 0.01 to
    0.15% carbon
    from 13 to
    22% chromium
    from 5 to
    13% nickel
    0.2 to
    2.5% manganese
    0.2 to
    3% silicon
    from 0.01 to
    0.15% nitrogen,
    the rest being iron;
  • the steel further comprises in its composition from 0.5 to 2% aluminum;
  • the steel further comprises in its composition less than 2% molybdenum;
  • Austenitic steel is a steel comprising in its composition:
    0.2 to
    1% carbon
    from 15 to
    30% manganese
    from 0.01 to
    0.7% nitrogen,
    the rest being iron;
  • the steel further comprises less than 5% chromium and less than 7% aluminum;
  • the breaking load, before aging, is greater than 2300 MPa;
  • Austenitic steel is a steel including in its composition:
    0.1 to
    0.6% carbon
    from 6 to
    25% nickel
    from 0 to
    13% chromium
    from 0 to
    4% molybdenum
    from 0 to
    3% silicon;
  • the breaking load after aging is greater than 2500 Mpa.

La description qui suit, ainsi que les dessins annexés, le tout donné à titre d'exemple non limitatif, feront bien comprendre l'invention.The following description, as well as the appended drawings, all given by way of nonlimiting example, will make the invention easier to understand.

Sur ces dessins:

  • les courbes 1A à 3A représentent dans deux opérations de laminage à tiède puis à froid pour trois aciers pris en exemple, le taux de martensite obtenu en fonction de différentes déformations rationnelles cumulées;
  • les courbes 1B à 3B représentent les caractéristiques en traction pour les trois aciers pris en exemple, en fonction de la déformation rationnelle cumulée, dans différentes conditions de traitement.
In these drawings:
  • curves 1A to 3A represent, in two lukewarm and then cold rolling operations for three steels taken as an example, the rate of martensite obtained as a function of different cumulative rational strains;
  • curves 1B to 3B represent the tensile characteristics for the three steels taken as an example, as a function of the cumulated rational deformation, under different processing conditions.

Les produits à très haute charge à la rupture selon l'invention, notamment sous la forme de fil ou de bande, sont obtenus par un effet de plasticité induite par déformation.The products with very high breaking load according to the invention, in particular in the form of wire or strip, are obtained by a plasticity effect induced by deformation.

Les aciers écrouis à une température supérieure à la température limite (Md) de formation de la martensite par déformation, appelés aussi écrouis "à tiède" ne présentent pas de propriétés d'usage particulières.Steels hardened at a temperature above the limit temperature (Md) for forming martensite by deformation, also called "warm" hardened, have no particular properties of use.

Lorsque les aciers sont soumis à un écrouissage à tiède puis à un écrouissage à froid, on observe, dans certaines conditions, une plasticité particulièrement élevée, qui permet une transformation mécanique à froid par passes successives, par exemple avec des taux de réduction de 25% et l'obtention de niveaux de charge à la rupture de plus de 2300 Mpa, le produit conservant d'une passe à l'autre une ductilité acceptable.When the steels are subjected to lukewarm hardening and then to cold hardening, we observe, under certain conditions, a particularly high plasticity, which allows a cold mechanical transformation by successive passes, for example with reduction rates of 25% and obtaining load levels at break of more than 2300 Mpa, the product retaining an acceptable ductility from one pass to the next.

L'effet de plasticité à froid après un écrouissage à tiède est d'autant plus important que la charge à la rupture de l'acier écroui à tiède est élevée.The effect of cold plasticity after lukewarm hardening is all the more important the higher the breaking load of the cold worked steel.

Un vieillissement des aciers soumis à un écrouissage à tiède, suivi d'un écrouissage à froid selon le procédé peut augmenter la charge à la rupture d'environ 200 MPa et parfois plus en fonction de la nuance d'acier utilisée.Aging of steels subjected to warm work hardening, followed by cold work hardening according to the process can increase the breaking load by around 200 MPa and sometimes more depending on the grade of steel used.

Les conditions d'obtention des hautes charges à la rupture sont attachées d'une part aux caractéristiques mécaniques obtenues lors de l'écrouissage à tiède, l'acier devant avoir au moins une charge à la rupture supérieure à 1000 MPa et d'autre part aux conditions d'écrouissage à froid, selon lesquelles l'écrouissage de l'acier est réalisé dans un domaine de température déterminé, appelé domaine critique de température de déformation de la martensite, de façon que pour une formation rationnelle supplémentaire de 0,1, l'augmentation du taux de martensite formé ne dépasse pas, à tout instant, 20%.The conditions for obtaining high tensile strengths are attached on the one hand to the mechanical characteristics obtained during lukewarm hardening, the steel having to have at least one tensile strength greater than 1000 MPa and on the other hand to the conditions of cold work hardening, according to which the work hardening of the steel is carried out in a determined range of temperature, called critical field of temperature of deformation of martensite, so that for an additional rational formation of 0.1, the increase in the rate of martensite formed does not exceed, at any time, 20%.

On entend par déformation rationnelle le logarithme du rapport de la surface S de la section après déformation sur la surface So de la section initiale (In S/So).By rational deformation is meant the logarithm of the ratio of the surface S of the section after deformation on the surface So of the initial section (In S / So).

Il est à noter qu'en fonction de la nuance d'acier ou d'alliage austénitique instable considérée, la vitesse de formation de la martensite, liée au domaine critique de température de formation de la martensite et à la déformation rationnelle cumulée comprise entre 0,7 et 3, doit être contrôlée pour l'obtention de caractéristiques mécaniques élevées, en d'autres termes il est nécessaire de ne pas former trop rapidement la martensite lors de l'écrouissage à froid.It should be noted that depending on the grade of steel or unstable austenitic alloy considered, the rate of formation of martensite, linked to the critical range of temperature of formation of martensite and to the cumulative rational deformation of between 0 , 7 and 3, must be checked to obtain high mechanical characteristics, in other words it is necessary not to form the martensite too quickly during cold work hardening.

Le domaine déterminé de température de formation de la martensite est, pour les aciers pris en exemple, compris dans l'intervalle -20°C +180°C. En effet, au-delà de +180°C il ne se forme plus de martensite en quantité appréciable alors qu'en deçà de -20°C la formation de martensite est excessive.The determined range of martensite formation temperature is, for the steels taken as an example, included in the range -20 ° C. + 180 ° C. Indeed, beyond + 180 ° C there is no longer an appreciable amount of martensite, while below -20 ° C the formation of martensite is excessive.

Des essais de tréfilage ont été réalisés et ont permis de mettre en évidence l'effet surprenant de la plasticité induite dans les aciers austénitiques instables, traités selon le procédé de l'invention.Wire drawing tests were carried out and made it possible to highlight the surprising effect of the plasticity induced in unstable austenitic steels, treated according to the method of the invention.

Trois exemples de réalisation mettant en évidence l'invention vont être décrits ci-après :Three exemplary embodiments highlighting the invention will be described below:

Le fil de base utilisé dans ces trois exemples est un fil-machine d'environ 5,6mm de diamètre ; le fil est écroui à tiède à 250°C en plusieurs passes jusqu'à un diamètre d'environ 2mm, puis ce fil est tréfilé à froid à la température ambiante de 20°C afin d'obtenir un fil d'environ 0,5mm en diamètre, les taux de réduction de section par passe de tréfilage étant d'environ 25%. Après chaque passe de tréfilage le fil reprend la température ambiante avant une autre passe. Le nombre de passe à tiède est d'environ 20, le nombre de passe à froid étant d'environ 10.The basic thread used in these three examples is a wire rod about 5.6mm in diameter; the wire is cold-worked at 250 ° C in several passes up to a diameter of approximately 2mm, then this wire is cold drawn at room temperature of 20 ° C in order to obtain a wire of approximately 0.5mm in diameter, the section reduction rates per drawing pass being approximately 25%. After each drawing pass the wire returns to room temperature before another pass. The number of lukewarm passes is approximately 20, the number of cold passes being approximately 10.

Exemple 1 :Example 1:

L'acier utilisé pour la mise en oeuvre du procédé est un acier référencé 1, ayant la composition pondérale suivante : 0,08% de carbone, 18,6% de chrome, 8,5% de nickel, 0,3% de manganèse, 0,5% de silicium, 0,04% d'azote.The steel used for the implementation of the process is a steel referenced 1, having the following weight composition: 0.08% carbon, 18.6% chromium, 8.5% nickel, 0.3% manganese , 0.5% silicon, 0.04% nitrogen.

Pendant l'écrouissage à tiède, il n'y a pas formation de martensite et la charge à la rupture atteinte est d'environ 1500 Mpa; après le tréfilage à froid la charge à la rupture du fil d'acier est d'environ 2500 MPa.During lukewarm hardening, there is no formation of martensite and the breaking load reached is approximately 1500 Mpa; after cold drawing the breaking load of the steel wire is around 2500 MPa.

Un traitement de vieillissement à 400°C pendant une heure lui confère alors une charge à la rupture d'environ 2700 MPa.An aging treatment at 400 ° C for one hour then gives it a breaking load of approximately 2700 MPa.

La courbe 1A représente, pour l'acier référencé 1, l'évolution du taux de martensite en fonction de la déformation rationnelle, ce taux de martensite atteignant environ 60% après tréfilage à froid.Curve 1A represents, for the steel referenced 1, the evolution of the rate of martensite as a function of the rational deformation, this rate of martensite reaching approximately 60% after cold drawing.

La courbe 1B représente l'évolution de la charge à la rupture lors de l'écrouissage à tiède jusqu'à 1400 MPa puis l'évolution de la charge à la rupture lors du tréfilage à froid atteignant alors 2500 MPa; un vieillissement permet d'obtenir une charge à la rupture d'environ 2700 Mpa.Curve 1B represents the evolution of the load at break during lukewarm hardening up to 1400 MPa then the evolution of the load at break during cold drawing thus reaching 2500 MPa; aging provides a breaking load of approximately 2700 Mpa.

L'augmentation de la charge à la rupture est obtenue en contrôlant l'augmentation de la formation de la martensite d'une passe de tréfilage à l'autre.The increase in breaking load is obtained by controlling the increase in the formation of martensite from one wire drawing pass to another.

Exemple 2 :Example 2:

L'acier utilisé est un acier référencé 2, ayant la composition pondérale suivante : 0,09% de carbone, 17,3% de chrome, 8,3% de nickel, 0,9% de manganèse, 0,8% de silicium, 0,06% d'azote.The steel used is a steel referenced 2, having the following composition by weight: 0.09% carbon, 17.3% chromium, 8.3% nickel, 0.9% manganese, 0.8% silicon , 0.06% nitrogen.

La courbe 2A illustre pour l'acier référencé 2 l'évolution du taux de martensite en fonction de la déformation rationnelle cumulée, le taux de martensite atteint étant de 45% environ.Curve 2A illustrates for the steel referenced 2 the evolution of the rate of martensite as a function of the cumulative rational deformation, the rate of martensite reached being approximately 45%.

La courbe 2B représente l'évolution de la charge à la rupture lors de l'écrouissage à tiède, jusqu'à une charge à la rupture de 1600 MPa, puis l'évolution de ladite charge à la rupture lors du tréfilage à froid, atteignant environ 2500 MPa.Curve 2B represents the evolution of the breaking load during lukewarm hardening, up to a breaking load of 1600 MPa, then the evolution of said breaking load during cold drawing, reaching about 2500 MPa.

Un vieillissement à 400°C pendant 1 heure améliore la valeur de la charge à la rupture d'environ 200 MPa.Aging at 400 ° C for 1 hour improves the value of the breaking load by around 200 MPa.

Exemple 3 :Example 3:

L'acier utilisé est un acier référencé 3 et ayant la composition suivante : 0,09% de carbone, 17,3% de chrome, 7,7% de nickel, 0,5% de manganèse, 0,8% de silicium, 0,15% d'azote, 1% d'aluminium.The steel used is a steel referenced 3 and having the following composition: 0.09% carbon, 17.3% chromium, 7.7% nickel, 0.5% manganese, 0.8% silicon, 0.15% nitrogen, 1% aluminum.

La courbe 3A représente pour l'acier référencé 3 l'évolution du taux de martensite en fonction de la déformation rationnelle, le taux de martensite pouvant atteindre 95%.The curve 3A represents for the steel referenced 3 the evolution of the rate of martensite as a function of the rational deformation, the rate of martensite being able to reach 95%.

La courbe 3B représente l'évolution de la charge à la rupture lors de l'écrouissage à tiède, jusqu'à la charge à la rupture d'environ 1600 MPa, puis l'évolution de ladite charge à la rupture lors du tréfilage à froid, atteignant environ 2300 Mpa.Curve 3B represents the evolution of the load at break during lukewarm hardening, up to the load at rupture of approximately 1600 MPa, then the evolution of said load at break during cold drawing, reaching around 2300 Mpa.

Le gain après traitement thermique à 480°C pendant 45 minutes est dans cet exemple d'environ 300 MPa.The gain after heat treatment at 480 ° C. for 45 minutes is in this example approximately 300 MPa.

De telles caractéristiques sont obtenues par la formation de martensite lors du tréfilage à froid, formation plus lente sur un produit préalablement écroui à tiède que par un tréfilage à froid direct du fil machine.Such characteristics are obtained by the formation of martensite during cold drawing, slower formation on a product previously cold-worked at lukewarm than by direct cold drawing of the wire rod.

On peut obtenir des caractéristiques encore plus élevées :

  • en optimisant l'écrouissage à tiède;
  • par addition dans les compositions d'éléments tels que molybdène, silicium, ... pour durcir la martensite formée;
  • par addition d'éléments tels que cuivre, aluminium, ... favorisant des précipitations durcissantes lors du vieillissement final.
Even higher characteristics can be obtained:
  • optimizing the warm-up;
  • by adding elements such as molybdenum, silicon, etc. to the compositions to harden the martensite formed;
  • by adding elements such as copper, aluminum, ... favoring hardening precipitation during final aging.

La première opération de déformation ou d'écrouissage "à tiède" peut être un tréfilage, comme décrit dans les exemples, mais aussi un laminage, un martelage ou un forgeage, une torsion, une flexion alternée, ou autre.The first "lukewarm" deformation or work hardening operation may be a wire drawing, as described in the examples, but also a rolling, hammering or forging, twisting, alternating bending, or the like.

La deuxième opération de déformation à froid peut également prendre divers aspects : tréfilage, laminage ou autre.The second cold deformation operation can also take various aspects: drawing, rolling or other.

Claims (14)

Procédé d'élaboration de produits à très haute charge à la rupture, à partir d'un acier austénitique instable, selon lequel on soumet l'acier à une première déformation plastique à une température supérieure à la température limite (Md) de formation de la martensite par déformation et inférieure à la température de recristallisation, puis on soumet cet acier à une seconde déformation à une température inférieure à ladite température limite (Md), caractérisé en ce que lors de la seconde déformation, on déforme l'acier dans un domaine déterminé de température de formation de la martensite de façon que pour une déformation rationnelle supplémentaire de 0,1, l'augmentation du taux de martensite formée ne dépasse pas, à tout instant, 20%.Process for the preparation of products with a very high breaking load, from an unstable austenitic steel, according to which the steel is subjected to a first plastic deformation at a temperature above the limit temperature (Md) for forming the martensite by deformation and below the recrystallization temperature, then this steel is subjected to a second deformation at a temperature below said limit temperature (Md), characterized in that during the second deformation, the steel is deformed in one area determined martensite formation temperature so that for an additional rational deformation of 0.1, the increase in the rate of martensite formed does not at any time exceed 20%. Procédé selon la revendication 1, caractérisé en ce qu'on déforme l'acier à une température inférieure à (Md) avec une déformation rationnelle cumulée comprise entre 0,7 et 3.Method according to claim 1, characterized in that the steel is deformed at a temperature below (Md) with a cumulative rational deformation of between 0.7 and 3. Procédé selon la revendication 1, caractérisé en ce qu'après la seconde déformation, on soumet l'acier à un traitement de vieillissement.Method according to claim 1, characterized in that after the second deformation, the steel is subjected to an aging treatment. Procédé selon la revendication 1, caractérisé en ce que la première déformation plastique est assurée avec une déformation rationnelle supérieure à 1,65.Method according to claim 1, characterized in that the first plastic deformation is ensured with a rational deformation greater than 1.65. Procédé selon les revendications 1 et 4, caractérisé en ce qu'après la première déformation plastique, la charge à la rupture de l'acier est supérieure à 1300 MPa.Process according to Claims 1 and 4, characterized in that after the first plastic deformation, the breaking load of the steel is greater than 1300 MPa. Produit à très haute charge à la rupture, obtenu à partir d'un acier austénitique instable, sous forme notamment de fil ou de bande, caractérisé en ce qu'il est élaboré par le procédé selon l'une quelconque des revendications 1 à 5.Product with very high breaking load, obtained from an unstable austenitic steel, in the form in particular of wire or strip, characterized in that that it is produced by the process according to any one of claims 1 to 5. Produit selon la revendication 6, caractérisé en ce que l'acier austénitique est un acier comprenant dans sa composition :
   de 0,01 à 0,15% de carbone
   de 13 à 23 % de chrome
   de 5 à 13 % de nickel
   de 0,2 à 2,5 % de manganèse
   de 0,2 à 3 % de silicium
   de 0,01 à 0,15% d'azote,
   le reste étant du fer.Product according to claim 6, characterized in that the austenitic steel is a steel comprising in its composition:
from 0.01 to 0.15% carbon
13 to 23% chromium
5 to 13% nickel
0.2 to 2.5% manganese
0.2 to 3% silicon
from 0.01 to 0.15% nitrogen,
the rest being iron. Produit selon la revendication 7, caractérisé en ce que l'acier comprend en outre dans sa composition de 0,5 à 2% d'aluminium.Product according to claim 7, characterized in that the steel further comprises in its composition from 0.5 to 2% aluminum. Produit selon la revendication 7, caractérisé en ce que l'acier comprend en outre dans sa composition moins de 2% de molybdène.Product according to claim 7, characterized in that the steel further comprises in its composition less than 2% molybdenum. Produit selon la revendication 6, caractérisé en ce que l'acier austénitique est un acier comprenant dans sa composition :
   de 0,2 à 1 % de carbone
   de 15 à 30 % de manganèse
   de 0,01 à 0,7% d'azote
   le reste étant du fer.Product according to claim 6, characterized in that the austenitic steel is a steel comprising in its composition:
0.2 to 1% carbon
15 to 30% manganese
from 0.01 to 0.7% nitrogen
the rest being iron. Produit selon la revendication 10, caractérisé en ce que l'acier comprend en outre moins de 5% de chrome et moins de 7% d'aluminium.Product according to claim 10, characterized in that the steel further comprises less than 5% of chromium and less than 7% of aluminum. Produit selon la revendication 6, caractérisé en ce que l'acier austénitique est un acier comprenant en sa composition :
   de 0,1 à 0,6% de carbone
   de 6 à 25 % de nickel
   de 0 à 13 % de chrome
   de 0 à 4 % de molybdène
   de 0 à 3 % de silicium,
   le reste étant du fer.Product according to claim 6, characterized in that the austenitic steel is a steel comprising in its composition:
0.1 to 0.6% carbon
6 to 25% nickel
0 to 13% chromium
0 to 4% molybdenum
from 0 to 3% silicon,
the rest being iron. Produit selon l'une quelconque des revendications 6 à 12, caractérisé en ce que la charge à la rupture, avant vieillissement, est supérieure à 2300 MPa.Product according to any one of Claims 6 to 12, characterized in that the breaking load, before aging, is greater than 2300 MPa. Produit selon l'une quelconque des revendications 6 à 13, caractérisé en ce que la charge à la rupture après vieillissement est supérieure à 2500 MPa.Product according to any one of Claims 6 to 13, characterized in that the breaking load after aging is greater than 2500 MPa.
EP91402232A 1990-08-30 1991-08-12 Process for manufacturing products with very high tensile strength from unstable austenitic steel, and products obtained Expired - Lifetime EP0474530B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9010828 1990-08-30
FR9010828A FR2666352B1 (en) 1990-08-30 1990-08-30 PROCESS FOR THE PRODUCTION OF HIGHLY LOADED RUPTURE PRODUCTS FROM UNSTABLE AUSTHENIC STEEL, AND PRODUCTS THEREFROM.

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EP0474530A1 true EP0474530A1 (en) 1992-03-11
EP0474530B1 EP0474530B1 (en) 1995-12-13

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JP (1) JPH0681033A (en)
AT (1) ATE131539T1 (en)
CA (1) CA2050208C (en)
DE (1) DE69115392T2 (en)
ES (1) ES2083543T3 (en)
FR (1) FR2666352B1 (en)
GR (1) GR3019185T3 (en)
PT (1) PT98792B (en)
TW (1) TW226033B (en)

Cited By (2)

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Publication number Priority date Publication date Assignee Title
EP0953651A1 (en) * 1998-04-29 1999-11-03 Ugine-Savoie Imphy Stainless steel for manufacturing drawn wire, especially tyre reinforcement wire, and wire manufactured by said process
EP4198363A1 (en) * 2021-12-14 2023-06-21 Vallourec Tube-Alloy, LLC High strength insulated tube

Families Citing this family (5)

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Publication number Priority date Publication date Assignee Title
JPS62275035A (en) * 1985-05-07 1987-11-30 Sumitomo Electric Ind Ltd Production of base material for optical fiber
JP3542239B2 (en) * 1996-10-15 2004-07-14 新日本製鐵株式会社 High-strength stainless wire with excellent resistance to longitudinal cracking and its wire
JP4519513B2 (en) * 2004-03-08 2010-08-04 新日鐵住金ステンレス株式会社 High-strength stainless steel wire with excellent rigidity and manufacturing method thereof
DE102004051885A1 (en) * 2004-10-26 2006-04-27 Fag Kugelfischer Ag & Co. Ohg Mechanically load-bearing actuator or bearing component made of mechanically hardened steel
KR101330903B1 (en) * 2008-11-05 2013-11-18 혼다 기켄 고교 가부시키가이샤 High-strength steel sheet and the method for production therefor

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FR1550475A (en) * 1966-11-22 1968-12-20
FR2207992A1 (en) * 1972-11-29 1974-06-21 Brunswick Corp
US4265679A (en) * 1979-08-23 1981-05-05 Kawasaki Steel Corporation Process for producing stainless steels for spring having a high strength and an excellent fatigue resistance
US4415377A (en) * 1982-06-28 1983-11-15 Olin Corporation Duplex rolling process and apparatus

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US3296846A (en) * 1964-06-05 1967-01-10 Crucible Steel Co America Method of rolling steel
FR1550475A (en) * 1966-11-22 1968-12-20
FR2207992A1 (en) * 1972-11-29 1974-06-21 Brunswick Corp
US4265679A (en) * 1979-08-23 1981-05-05 Kawasaki Steel Corporation Process for producing stainless steels for spring having a high strength and an excellent fatigue resistance
US4415377A (en) * 1982-06-28 1983-11-15 Olin Corporation Duplex rolling process and apparatus

Cited By (5)

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Publication number Priority date Publication date Assignee Title
EP0953651A1 (en) * 1998-04-29 1999-11-03 Ugine-Savoie Imphy Stainless steel for manufacturing drawn wire, especially tyre reinforcement wire, and wire manufactured by said process
FR2778188A1 (en) * 1998-04-29 1999-11-05 Ugine Savoie Sa STAINLESS STEEL FOR THE PREPARATION OF TREWNED WIRE, ESPECIALLY OF PNEUMATIC REINFORCEMENT WIRE AND PROCESS FOR MAKING THE SAID WIRE
US6048416A (en) * 1998-04-29 2000-04-11 Ugine-Savoie Imphy Steel, steel wire, and process for forming drawn wire of steel
EP4198363A1 (en) * 2021-12-14 2023-06-21 Vallourec Tube-Alloy, LLC High strength insulated tube
WO2023110731A1 (en) * 2021-12-14 2023-06-22 Vallourec Tube Alloy, Llc High strength insulated tube

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CA2050208A1 (en) 1992-03-01
CA2050208C (en) 2002-08-20
DE69115392T2 (en) 1996-05-30
PT98792A (en) 1992-07-31
EP0474530B1 (en) 1995-12-13
ES2083543T3 (en) 1996-04-16
DE69115392D1 (en) 1996-01-25
ATE131539T1 (en) 1995-12-15
TW226033B (en) 1994-07-01
GR3019185T3 (en) 1996-06-30
FR2666352B1 (en) 1992-12-11
PT98792B (en) 1999-01-29
FR2666352A1 (en) 1992-03-06
JPH0681033A (en) 1994-03-22

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