EP0571521B1 - Metal wire consisting of a steel substrate with a cold hardened annealed martensitic structure, and a coating - Google Patents

Abstract

In a metal wire consisting of a substrate and a coating, the substrate is steel with a carbon content of at least 0.05 % and at most 0.6 %, said steel having a structure with over 90 % cold hardened annealed martensite. The substrate is coated with a metal alloy other than steel. A method for obtaining this wire involves cold drawing a steel wire rod containing 28 % to 96 % proeutectoid ferrite and 72 % to 4 % perlite. It is then hardened to obtain a structure containing over 90 % martensite. Metals are then deposited thereon and the wire is heated to produce the formation of an alloy and the formation of a structure consisting of over 90 % annealed martensite. The wire is cooled and cold drawn. This wire is used, form example, to reinforce tyre casings.

Description

The invention relates to steel wires and methods for obtaining these wires. These threads are used, for example, to reinforce plastic or rubber articles, in particular pipes, belts, plies, tire casings.

The son of this type commonly used today are made of steel containing at least 0.6% carbon, this steel having a hardened pearlitic structure. The breaking strength of these wires is around 2800 MPa (megapascals), their diameter generally varies from 0.15 to 0.35 mm, and their elongation at break is between 0.4 and 2%. These wires are produced by drawing a starting wire, known as a "machine wire", the diameter of which is around 5 to 6 mm, the structure of this machine wire being a hard structure, made up of perlite and ferrite. with a high rate of perlite which is generally greater than 72%. During the production of this wire, the drawing operation is interrupted at least once to carry out one or more heat treatments which make it possible to regenerate the initial structure. After the last heat treatment, an alloy deposit, for example brass, on the wire is necessary for the last drawing operation to be carried out correctly.

• la matière première est coûteuse, car le taux de carbone est relativement élevé ;
• les paramètres ne peuvent pas être modifiés facilement, en particulier le diamètre du fil machine et le diamètre final sont maintenus dans des limites rigides, le procédé manquant donc de souplesse ;
• la grande dureté du fil machine due à sa structure fortement perlitique rend le tréfilage difficile, avant le traitement thermique, de telle sorte que le taux de déformation ε de ce tréfilage est nécessairement inférieur à 3 ; d'autre part les vitesses de ce tréfilage sont faibles et il peut y avoir des casses du fil lors de cette opération ;
• l'opération d'un dépôt d'alliage, par exemple de laiton, est une étape nécessaire au procédé et n'est pas intégrée à l'étape de traitement thermique qui la précède.

This process has the following drawbacks:

• the raw material is expensive because the carbon content is relatively high;
• parameters cannot be changed easily, in particular the diameter of the wire rod and the final diameter are kept within rigid limits, the process therefore lacking flexibility;
• the high hardness of the wire rod due to its highly pearlitic structure makes wire drawing difficult, before the heat treatment, so that the rate of deformation ε of this wire drawing is necessarily less than 3; on the other hand, the speeds of this drawing are low and there may be breaks in the wire during this operation;
• the operation of depositing an alloy, for example brass, is a necessary step in the process and is not integrated into the heat treatment step which precedes it.

On the other hand, the wires themselves have a resistance to breakage and a ductility at break which is sometimes insufficient, and they exhibit significant damage as a result of the drawing before heat treatment, because of the great hardness of the machine wire.

Document EP-A-213 917 describes a two-phase wire rod containing from 10 to 70% by volume of martensite and / or bainite and 90 to 30% by volume of ferrite. The wire obtained by transformation of this machine wire also has a structure with these two phases.

The object of the invention is to provide a hardened steel wire coated with a metal alloy, the steel of this wire having a hardened non-pearlitic structure and having a breaking strength and an elongation at break at least as high as the known hardened pearlitic steel wires, and less damage by wire drawing than the known wires.

Another object of the invention is to propose, for producing this yarn, a process which does not have the abovementioned drawbacks.

In the following, the contents of the steel used in alloying elements are expressed in weight percentages.

• a) il comporte un substrat en acier ayant une teneur en carbone au moins égale à 0,05 % et au plus égale à 0,6 % ;
• b) cet acier présente une structure comportant plus de 90 % de martensite revenue écrouie ;
• c) le substrat est revêtu d'un alliage métallique autre que l'acier ;
• d) le diamètre du fil est au moins égal à 0,10 mm et au plus égal à 0,40 mm ;
• e) la résistance à la rupture du fil est au moins égale à 2800 MPa ;
• f) l'allongement à la rupture du fil est au moins égal à 0,4 %.

The metal wire according to the invention, comprising a substrate and a coating, has the following characteristics:

• a) it comprises a steel substrate having a content of carbon at least equal to 0.05% and at most equal to 0.6%;
• b) this steel has a structure comprising more than 90% of hardened returned martensite;
• c) the substrate is coated with a metal alloy other than steel;
• d) the diameter of the wire is at least equal to 0.10 mm and at most equal to 0.40 mm;
• e) the breaking strength of the wire is at least equal to 2800 MPa;
• f) the elongation at break of the wire is at least equal to 0.4%.

• a) on écrouit un fil machine en acier, cet acier ayant une teneur en carbone au moins égale à 0,05 % et au plus égale à 0,6 %, cet acier comportant de 28 % à 96 % de ferrite proeutectoïde et de 72 % à 4 % de perlite ; le taux de déformation ε de cet écrouissage étant au moins égal à 3 ;
• b) on arrête l'écrouissage et on effectue un traitement thermique de trempe sur le fil écroui, ce traitement consistant à chauffer le fil au-dessus du point de transformation AC3 pour lui donner une structure d'austénite homogène, puis à le refroidir rapidement au dessous du point de fin de transformation martensitique M_F, la vitesse de ce refroidissement étant au moins égale à 150°C/seconde, de façon à obtenir une structure comportant plus de 90 % de martensite ;
• c) on effectue ensuite sur le fil un dépôt d'au moins deux métaux susceptibles de former par diffusion un alliage, l'acier servant ainsi de substrat ;
• d) on chauffe ensuite le fil à une température au moins égale à 0,3 T_F et au plus égale à 0,5 T_F, de façon à provoquer la formation, par diffusion, d'un alliage de ces métaux déposés, ainsi que la formation, pour l'acier, d'une structure comportant plus de 90 % de martensite revenue, T_F étant la température de fusion de l'acier, exprimée en Kelvin ;
• e) on refroidit ensuite le fil à une température inférieure à 0,3 T_F ;
• f) on effectue ensuite un écrouissage sur le fil, la température du fil lors de cet écrouissage étant inférieure à 0,3 T_F, le taux de déformation ε de cet écrouissage étant au moins égal à 1.

The process according to the invention for producing this coated steel wire is characterized by the following points:

• a) a steel wire rod is hardened, this steel having a carbon content at least equal to 0.05% and at most equal to 0.6%, this steel comprising from 28% to 96% of proeutectoid ferrite and 72 % to 4% perlite; the rate of deformation ε of this work hardening being at least equal to 3;
• b) the work hardening is stopped and a hardening heat treatment is carried out on the work hardened wire, this treatment consisting in heating the wire above the transformation point AC3 to give it a homogeneous austenite structure, then in rapidly cooling it below the end point of martensitic transformation M _F , the speed of this cooling being at least equal to 150 ° C / second, so as to obtain a structure comprising more than 90% of martensite;
• c) a deposit is then made on the wire of at least two metals capable of forming by diffusion an alloy, the steel thus serving as a substrate;
• d) the wire is then heated to a temperature at least equal to 0.3 T _F and at most equal to 0.5 T _F , so as to cause the formation, by diffusion, of an alloy of these deposited metals, as well as the formation, for steel, of a structure comprising more than 90% of returned martensite, T _F being the melting temperature of steel, expressed in Kelvin;
• e) the wire is then cooled to a temperature below 0.3 T _F ;
• f) a work hardening is then carried out on the wire, the temperature of the wire during this work hardening being less than 0.3 T _F , the rate of deformation ε of this work hardening being at least equal to 1.

The invention also relates to assemblies comprising at least one wire according to the invention.

The invention also relates to articles reinforced at least in part by wires or assemblies in accordance with the preceding definitions, such articles being, for example, hoses, belts, plies, tire casings.

The invention will be easily understood with the aid of the following embodiment examples, and all schematic figures relating to these examples.

• la figure 1 représente la structure de l'acier d'un fil avant les traitements thermiques, lors de la mise en oeuvre du procédé conforme à l'invention ;
• la figure 2 représente la structure de l'acier d'un fil après le traitement thermique de trempe, lors de la mise en oeuvre du procédé conforme à l'invention ;
• la figure 3 représente la structure de l'acier d'un fil laitonné, lors de la mise en oeuvre du procédé conforme à l'invention ;
• la figure 4 représente la structure de l'acier d'un fil conforme à l'invention.

On the drawing :

• FIG. 1 represents the structure of the steel of a wire before the heat treatments, during the implementation of the method according to the invention;
• FIG. 2 represents the structure of the steel of a wire after the quenching heat treatment, during the implementation of the method according to the invention;
• FIG. 3 represents the structure of the steel of a wire brassy, during the implementation of the process according to the invention;
• FIG. 4 represents the structure of the steel of a wire according to the invention.

In the following, all the percentages indicated are by weight and the measurements of breaking strength and elongation at break are carried out according to the AFNOR NFA 03-151 method.

, Ln étant le logarithme népérien, So étant la section initiale du fil avant cet écrouissage et Sf étant la section du fil après cet écrouissage.By definition, the rate of strain ε of a hardening is given by the formula $$\text{ε = Ln}\frac{\text{So}}{\text{Sf}}$$

, Ln being the natural logarithm, So being the initial section of the wire before this hardening and Sf being the section of the wire after this hardening.

The purpose of the examples which follow is to describe the preparation and the properties of three wires in accordance with the invention.

• teneur en carbone : 0,4 % ;
• teneur en manganèse : 0,5 % ;
• teneur en silicium : 0,2 % ;
• teneur en phospore : 0,015 % ;
• teneur en soufre : 0,02 % ;
• teneur en aluminium : 0,015 % ;
• teneur en azote : 0,005 % ;
• teneur en chrome : 0,05 % ;
• teneur en nickel : 0,10 % ;
• teneur en cuivre : 0,10 % ;
• teneur en molybdène : 0,01 % ;
• teneur en ferrite proeutectoïde : 53 % ;
• teneur en perlite : 47 % ;
• température de fusion de l'acier, T_F : 1795 K ;
• point de fin de transformation martensitique M_F : 150°C ;
• résistance à la rupture R_m : 700 MPa ;
• allongement à la rupture A_r: 17 % ;

On réalise avec ce fil machine trois fils conformes à l'invention de la façon suivante :In these examples, an unworked wire rod 5.5 mm in diameter is used. This wire rod is made of steel, the characteristics of which are as follows:

• carbon content: 0.4%;
• manganese content: 0.5%;
• silicon content: 0.2%;
• phosphate content: 0.015%;
• sulfur content: 0.02%;
• aluminum content: 0.015%;
• nitrogen content: 0.005%;
• chromium content: 0.05%;
• nickel content: 0.10%;
• copper content: 0.10%;
• molybdenum content: 0.01%;
• proeutectoid ferrite content: 53%;
• perlite content: 47%;
• melting temperature of steel, T _F : 1795 K;
• martensitic transformation end point M _F : 150 ° C;
• breaking strength R _m : 700 MPa;
• elongation at break A _r : 17%;

Three wire in accordance with the invention are produced with this wire rod as follows:

Example 1 :

The machine wire is descaled, it is coated with a drawing soap, for example borax, and it is drawn dry to obtain a wire with a diameter of 1.1 mm, which corresponds to a rate of deformation ε slightly greater than 3.2.

The drawing is easily carried out thanks to the relatively ductile structure of the wire rod. For example, a steel with 0.7% carbon not hardened has a breaking strength R _m of approximately 900 MPa and an elongation at break A _r of approximately 8%, that is to say that it is much less ductile.

For example, this drawing is carried out at a temperature below 0.3 T _F , for the purpose of simplification, although this is not essential, the drawing temperature possibly being equal to or exceeding 0.3 T _F.

Figure 1 shows the section of a portion 1 of the structure of the wire thus obtained. This structure consists of elongated blocks 2 of cementite and elongated blocks 3 of ferrite, the largest dimension of these blocks being oriented in the drawing direction.

• on chauffe le fil par convection dans un four à mouffle pour le porter à 950°C, c'est-à-dire au dessus du point de transformation AC3, et on le maintient pendant 30 secondes à cette température de façon à obtenir une structure d'austénite homogène ;
• on refroidit ensuite le fil, dans un anneau gazeux, produit par une turbine, jusqu'à une température de 75°C, c'est-à-dire en dessous du point de fin de transformation martensitique M_F (Martensite Finish) en moins de 3,5 secondes de façon à obtenir une structure comportant plus de 90 % de martensite en lattes.

The following heat treatments are then carried out on the wire thus obtained:

• the wire is heated by convection in a muffle furnace to bring it to 950 ° C., that is to say above the transformation point AC3, and it is maintained for 30 seconds at this temperature so as to obtain a structure homogeneous austenite;
• the wire is then cooled, in a gas ring, produced by a turbine, to a temperature of 75 ° C, that is to say below the martensitic transformation end point M _F (Martensite Finish) less 3.5 seconds to obtain a structure with more than 90% martensite in slats.

FIG. 2 represents a section of a portion 4 of the structure thus obtained, the martensite slats being represented by the reference 5.

The wire is then degreased. Then it is copper, then it is coated with zinc electrolytically at room temperature. It is then heat treated by Joule effect at 540 ° C (813 K) for 2.5 seconds, then cooled to room temperature (about 20 ° C, or 293 K).

This latter treatment makes it possible to obtain brass by diffusion of copper and zinc, as well as, for steel, a structure comprising more than 90% of returned martensite. The thickness of this layer of brass is small (of the order of a micrometer) and it is negligible compared to the diameter of the wire.

FIG. 3 represents a section of a portion 6 of the structure of the wire thus obtained. This structure comprises precipitates of carbides 7, distributed almost homogeneously in a matrix 8 of ferritic type. This structure is obtained thanks to heat treatments previous, and it is kept when cooling to room temperature. The precipitates 7 generally have dimensions at least equal to 0.005 "m (micrometer) and at most equal to 1" m.

A wet wire drawing of this wire is then carried out so as to obtain a final diameter of 0.2 mm, which practically corresponds to ε = 3.4. The temperature of the wire, during this drawing, is necessarily less than 0.3 T _F. The brass thickness of the wire thus drawn is very small, of the order of a tenth of a micrometer.

FIG. 4 represents a longitudinal section of the portion 9 of the steel of this wire according to the invention thus obtained. This portion 9 has a structure of the hardened returned martensite type consisting of carbides 10 of elongated shape which are practically parallel to each other and whose largest dimension is oriented along the axis of the wire, that is to say according to the direction of drawing shown schematically by the arrow F in FIG. 4. These carbides 10 are arranged in a hardened die 11.

This wire according to the invention has a breaking strength of 3000 MPa and an elongation at break of 0.7%.

Example 2

The machine wire is descaled, it is coated with a layer of wire-drawing soap, for example borax, and it is drawn dry to obtain a wire with a diameter of 0.9 mm, which corresponds to a rate of deformation ε slightly higher than 3.6. The structure obtained is similar to that shown in FIG. 1. The following heat treatments are then carried out on the wire thus obtained:
The wire is heated by the Joule effect to bring it to 1000 ° C. for 3 seconds, that is to say above the transformation point AC3 so as to obtain a homogeneous austenite structure. The wire is then cooled in an oil bath to a temperature of 100 ° C., that is to say below the end point of transformation M _F , in less than 3 seconds so as to obtain a structure comprising more than 90% martensite in slats, the structure of the wire obtained being in accordance with FIG. 2.

The wire is then degreased. Then it is copper, then it is coated with zinc electrolytically at room temperature. It is then heat treated by Joule effect at 540 ° C (813 K) for 2.5 seconds, then it is cooled to room temperature, these treatments being identical to Example 1.

The structure obtained for this brass-plated wire is similar to that shown in FIG. 3. The wire is then drawn by the wet method so as to obtain a final diameter of 0.17 mm, which corresponds practically to ε = 3.3. The temperature of the wire during this drawing is less than 0.3 T _F. The steel of the wire according to the invention thus obtained has a structure similar to that shown in FIG. 4.

This wire has a breaking strength equal to 2850 MPa and an elongation at break equal to 1%.

Example 3

A wire of 1.1 mm diameter obtained in the same way as in Example 1 by drawing the machine wire is heated by Joule effect at 1000 ° C for 3 seconds, that is to say above the point of transformation AC3 so as to obtain a homogeneous austenite structure.

The wire is then cooled, in a gas ring produced by a turbine, to a temperature of 100 ° C., that is to say below the end point of transformation M _F , in less than 3 seconds, so as to obtain a structure comprising more than 90% martensite in slats.

The wire is then copper-plated then galvanized by electrolytic means, at room temperature then heat treated by Joule effect at 500 ° C (773 K) for 5 seconds. It is then cooled to room temperature, the strand thus braided is then drawn by the wet method at a temperature below 0.3 T _{F up} to the diameter 0.17 mm, which corresponds practically to ε = 3.7. This wire, according to the invention has a breaking strength equal to 3200 MPa and an elongation at break equal to 0.6%.

The intermediate structures and the final structure are analogous to the structures previously described.

• on part d'un fil machine à faible taux de carbone, et donc d'un coût peu élevé :
• on bénéficie d'une grande souplesse dans le choix des diamètres des fils, c'est ainsi par exemple qu'on peut utiliser des fils machines dont le diamètre est notablement supérieur à 6 mm, ce qui réduit encore les coûts, et on peut réaliser des fils très variés en diamètre ;
• le tréfilage avant les traitements thermiques est relativement aisé, de telle sorte que le taux de déformation ε de ce tréfilage peut être supérieur à 3 ; d'autre part, ce tréfilage peut être réalisé avec des vitesses élevées ; enfin on réduit la fréquence des casses de fils et des changements de filières, ce qui réduit encore les coûts ;
• le traitement de diffusion pour obtenir l'alliage est effectué en même temps que le revenu du fil, ce qui évite une opération supplémentaire de diffusion et limite donc les coûts de fabrication tout en permettant un traitement global en ligne du fil, depuis le fil machine jusqu'au fil final ;
• le fil obtenu présente une résistance à la rupture et un allongement à la rupture de valeurs au moins égales à celles des fils classiques, ce qui se traduit donc par une énergie de rupture au moins égale à celle des fils classiques ;
• le fil est moins endommagé lors du tréfilage avant traitement thermique ;
• le fil obtenu présente une meilleure résistance à la corrosion que les fils classiques par suite de sa faible teneur en carbone.

The invention has the following advantages:

• we start with a low carbon wire rod, and therefore of a low cost:
• there is great flexibility in the choice of wire diameters, this is for example that we can use machine wires whose diameter is significantly greater than 6 mm, which further reduces costs, and we can achieve wires very varied in diameter;
• the wire drawing before the heat treatments is relatively easy, so that the rate of deformation ε of this wire drawing can be greater than 3; on the other hand, this wire drawing can be carried out with high speeds; finally we reduce the frequency of breaks threads and die changes, which further reduces costs;
• the diffusion treatment to obtain the alloy is carried out at the same time as the tempering of the wire, which avoids an additional diffusion operation and therefore limits the manufacturing costs while allowing overall online treatment of the wire, from the wire rod until the final thread;
• the wire obtained has a breaking strength and an elongation at break of values at least equal to those of conventional wires, which therefore results in a breaking energy at least equal to that of conventional wires;
• the wire is less damaged during the drawing before heat treatment;
• the wire obtained has better resistance to corrosion than conventional wires due to its low carbon content.

During the quenching treatment carried out using homogeneous austenite, from a temperature above the AC3 transformation point to a temperature below M _F , since the cooling rate is at least 150 ° C, in accordance In the invention, less than 10% of the homogeneous austenite is transformed before reaching the temperature corresponding to the point of the start of martensitic transformation (M _S ), so that the structure, at the end of this quenching, comprises more than 90% martensite, this structure can be made up entirely of martensite. Preferably, the martensite obtained after quenching has a slatted structure, as described in the examples.

Preferably, the steel of the wire according to the invention, and therefore the starting machine wire, has a carbon content at least equal to 0.2% and at most equal to 0.5%.

Preferably, in the steel of the wire according to the invention and therefore in the starting machine wire, there are the following compositions: 0.3% ≦ Mn ≦ 0.6%; 0.1% ≦ Si ≦ 0.3%; P ≦ 0.02%; S ≦ 0.02%; Al ≦ 0.02%; N ≦ 0.006%.

Advantageously, in the steel of the wire according to the invention and therefore in the starting machine wire, there are the following compositions: Cr ≦ 0.06%; Ni ≦ 0.15%; Cu ≦ 0.15%;

• le fil machine de départ a une teneur en ferrite proeutectoïde au moins égale à 41 %, et au plus égale à 78 % et une teneur en perlite au moins égale à 22 % et au plus égale à 59 % ;
• le taux de déformation ε lors de l'écrouissage avant les traitements thermiques est au moins égal à 3,2 et au plus égal à 6 ;
• le taux de déformation ε lors de l'écrouissage final après les traitements thermiques est au moins égal à 3 et au plus égal à 5 ;
• le traitement thermique de trempe est effectué avec une vitesse de refroidissement au moins égale à 250°C/seconde.

Preferably, in the process according to the invention, there is at least one of the following characteristics:

• the starting wire rod has a proeutectoid ferrite content at least equal to 41%, and at most equal to 78% and a perlite content at least equal to 22% and at most equal to 59%;
• the rate of deformation ε during work hardening before the heat treatments is at least equal to 3.2 and at most equal to 6;
• the rate of deformation ε during the final work hardening after the heat treatments is at least equal to 3 and at most equal to 5;
• the quenching heat treatment is carried out with a cooling rate at least equal to 250 ° C / second.

The wire work hardening in the previous examples is carried out by drawing, but other techniques are possible, for example rolling, possibly associated with drawing, for at least one of the work hardening operations. Of course, the invention is not limited to the embodiments described above, this is for example the case that the invention applies to cases where an alloy other than the brass, with two metals, or more than two metals, for example ternary copper - zinc - nickel, copper - zinc - cobalt, copper - zinc - tin alloys, the main thing being that the metals used are capable of forming an alloy, by diffusion, at a temperature at least equal to 0.3 T _F and at most equal to 0.5 T _F.

Claims (20)

1. A metal wire which comprises a substrate and a coating, said wire having the following characteristics:

   (a) it comprises a substrate of steel having a carbon content of at least 0.05% by weight and of at most 0.6% by weight;

   (b) this steel has a structure comprising more than 90% work-hardened tempered martensite;

   c) the substrate is coated with a metal alloy other than steel;

   d) the diameter of the wire is at least 0.10 mm and at most 0.40 mm;

   e) the rupture strength of the wire is at least 2800 MPa;

   f) the elongation upon rupture of the wire is at least 0.4%.
2. A wire according to Claim 1, characterised in that the steel has a carbon content of at least 0.2% by weight and at most 0.5% by weight.
3. A metal wire according to any one of Claims 1 or 2, characterised in that the steel satisfies the following relationships: 0.3% ≦ Mn ≦ 0.6%; 0.1% ≦ Si ≦ 0.3%; P ≦ 0.02%; S ≦ 0.02%; Al ≦ 0.02%; N ≦ 0.006% (% by weight).
4. A metal wire according to Claim 3, characterised in that the steel satisfies the following relationships: Cr ≦ 0.06%; Ni ≦ 0.15%; Cu ≦ 0.15% (% by weight).
5. A wire according to any one of Claims 1 to 4, characterised in that the metal alloy is a brass.
6. A method of obtaining the wire according to any one of Claims 1 to 5, characterised by the following features:

   (a) a steel machine wire is work-hardened, this steel having a carbon content of at least 0.05% by weight and at most 0.6% by weight, this steel comprising 28% to 96% proeutectoid ferrite and 72% to 4% pearlite; the deformation ratio ε of this work-hardening being at least 3;

   (b) the work-hardening is stopped and a hardening heat treatment is carried out on the work-hardened wire, this treatment consisting of heating the wire to above the AC3 transformation point in order to impart to it a homogenous austenite structure, then cooling it rapidly to below the martensite transformation finish point M_F, the rate of this cooling being at least 150°C/second, so as to obtain a structure comprising more than 90% martensite;

   c) at least two metals capable of forming an alloy by diffusion are then deposited on the wire, the steel thus serving as substrate;

   d) the wire is then heated to a temperature of at least 0.3 T_F and at most 0.5 T_F so as to cause the formation by diffusion of an alloy of these deposited metals, as well as the formation, for the steel, of a structure comprising more than 90% tempered martensite, T_F being the melting point of the steel, expressed in Kelvin;

   (e) the wire is then cooled to a temperature below 0.3 T_F;

   (f) work-hardening is then carried out on the wire, the temperature of the wire upon this work-hardening being less than 0.3 T_F, the deformation ratio ε of this work-hardening being at least 1.
7. A method according to Claim 6, characterised in that the initial machine wire has a carbon content of at least 0.2% by weight and at most 0.5% by weight.
8. A method according to any one of Claims 6 or 7, characterised in that the machine wire satisfies the following relationships: 0.3% ≦ Mn ≦ 0.6%; 0.1% ≦ Si ≦ 0.3%; P ≦ 0.02%; S ≦ 0.02%; Al ≦ 0.02%; N ≦ 0.006% (% by weight).
9. A method according to Claim 8, characterised in that the machine wire satisfies the following relationships: Cr ≦ 0.06%; Ni ≦ 0.15%; Cu ≦ 0.15% (% by weight).
10. A method according to any one of Claims 6 to 9, characterised in that the initial machine wire has a proeutectoid ferrite content of at least 41% and at most 78%, and a pearlite content of at least 22% and at most 59%.
11. A method according to any one of Claims 6 to 10, characterised in that the deformation ratio ε upon the work-hardening before the heat treatments is at least 3.2 and at most 6.
12. A method according to any one of Claims 6 to 11, characterised in that the deformation ratio ε upon the final work-hardening after the heat treatments is at least 3 and at most 5.
13. A method according to any one of Claims 6 to 12, characterised in that the deposit effected on the wire after the hardening heat treatment is a deposit of copper and zinc.
14. A method according to any one of Claims 6 to 13, characterised in that at least one work-hardening is carried out at least in part by drawing.
15. A method according to any one of Claims 6 to 14, characterised in that the hardening heat treatment is carried out with a speed of cooling of at least 250°C/second.
16. A method according to Claim 15, characterised in that the hardening heat treatment imparts to the wire a structure comprising more than 90% martensite in laths.
17. An assembly comprising at least one wire according to any one of Claims 1 to 5.
18. An article reinforced with at least one wire according to any one of Claims 1 to 5.
19. An article reinforced with at least one assembly according to Claim 17.
20. An article according to any one of Claims 18 or 19, characterised in that it is a tyre.

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