EP1466024B1 - Procede de fabrication d un produit siderurgique en acier au carbone riche en cuivre, et produit siderurgique ainsi obtenu - Google Patents

Procede de fabrication d un produit siderurgique en acier au carbone riche en cuivre, et produit siderurgique ainsi obtenu Download PDF

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EP1466024B1
EP1466024B1 EP03712234A EP03712234A EP1466024B1 EP 1466024 B1 EP1466024 B1 EP 1466024B1 EP 03712234 A EP03712234 A EP 03712234A EP 03712234 A EP03712234 A EP 03712234A EP 1466024 B1 EP1466024 B1 EP 1466024B1
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Prior art keywords
strip
copper
temperature
process according
steel
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German (de)
English (en)
French (fr)
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EP1466024A1 (fr
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Nicolas Patrice Guelton
Michel Faral
Jean=Pierre Birat
Catherine Juckum
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ArcelorMittal France SA
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Arcelor France 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
    • C21D8/0415—Rapid solidification; Thin strip casting
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0473—Final recrystallisation annealing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • C21D2211/005—Ferrite

Definitions

  • the invention relates to the field of the production of ferrous alloys, and more specifically the field of the production of steels with high levels of copper.
  • Copper is generally regarded as an undesirable element in carbon steels, because by favoring hot cracking, on the one hand it makes the hot working of steel difficult, and on the other hand it degrades the quality and the appearance of the surface of the products. For these reasons, it is customary to limit the copper content of high quality carbon steels to levels of less than 0.05%. Since it is not possible to remove the copper present in the molten steel, obtaining these low levels of copper is possible only by producing the steel from molten iron, which is economically viable only for production in large quantities, or by producing steel in electric furnace by melting carefully selected scrap, thus expensive.
  • the curing power of the copper by precipitation is optimal when the copper is maintained completely in solid solution before the precipitation treatment by quenching. Indeed, the contribution of the precipitation to curing is even lower than the precipitation temperature is high. Copper should not be allowed to precipitate on cooling until the tempering temperature is reached. The conventional production line does not allow the execution of such a quenching necessary to maximize the hardening power.
  • EP-A-1 072 689 discloses a method of manufacturing TRIP type steel thin strips by direct casting of liquid steel optionally containing between 0.5 and 2% copper.
  • the cast strip is hot rolled and undergoes two forced cooling separated by a residence at temperatures between 55 ° and 400 ° C for there to occur a bainitic transformation.
  • the object of the invention is to provide complete production processes for hot-rolled or cold-rolled carbon steel sheets having high mechanical properties, in particular high strength, good anisotropy of the deformations, as well as good welding properties, in which a high copper content is tolerated or even desired.
  • the Mn / Si ratio is greater than or equal to 3.
  • the casting of the thin strip can be carried out on a casting installation between two internally cooled rolls rotating in opposite directions.
  • the hot rolling of the strip is preferably carried out in line with the casting of the strip.
  • the speed V of forced cooling following hot rolling is generally such that V ⁇ e 1 , 98 ( % Cu ) - 0 , 08 with V expressed in ° C / s and% Cu in% by weight.
  • the carbon content of the steel is between 0.1 and 1%, and the winding of the strip is carried out at a temperature above the martensitic transformation start temperature M s .
  • the winding of the strip is carried out at less than 300 ° C., and the strip then undergoes a copper precipitation heat treatment between 400 and 700 ° C. Under these conditions, if the carbon content is between 0.1 and 1%, there is preferably no unwinding before the heat treatment.
  • the winding of the strip is carried out at a temperature that is both greater than the temperature M s of beginning of martensitic transformation and less than 300 ° C., and then a cold rolling, an annealing of recrystallization in a temperature range where the copper is in supersaturated solid solution, a forced cooling maintaining the copper in solid solution, and a precipitation income.
  • Said precipitation income is carried out in a continuous annealing plant between 600 and 700 ° C, or in a base annealing plant between 400 and 700 ° C.
  • the winding of the strip is carried out at a temperature that is both greater than the temperature M s of martensite transformation start and less than 300 ° C., and then a cold rolling and a base annealing are carried out. between 400 and 700 ° C serving both recrystallization annealing and precipitation income.
  • the carbon content of the steel is preferably between 0.1 and 1%, or between 0.01 and 0.2%, or between 0.0005% and 0%. , 05%. In the latter case, its copper content is preferably between 0.5 and 1.8%.
  • a final treatment of the strip can be carried out in a cold-rolling mill.
  • the invention also relates to a steel product obtained by one of the preceding methods.
  • the invention essentially consists in directly casting a steel having the specified composition in a thin strip, and then imposing on it conditions which avoid the rapid cooling chipping of the strip at the outlet of the ingot mold, bringing it below 1000 ° C., and possibly keeping the strip in a non-oxidizing atmosphere at least until this temperature is reached), then hot rolling the strip, preferably in line, followed by forced cooling. now the copper in supersaturated solid solution.
  • the tape is then wound. It can then undergo various thermal or mechanical treatments that will give it its thickness and its final properties.
  • a liquid metal is produced having the following composition (all the contents are expressed in percentages by weight).
  • the carbon content may range from 0.0005% to 1%, depending in particular on the applications envisaged for the final product.
  • the lower limit of 0.0005% corresponds to practically the minimum that can be obtained by conventional methods of decarburizing the liquid metal.
  • the upper limit of 1% is justified by the gamma-carbon effect. Indeed, beyond 1%, carbon excessively reduces the solubility of copper in ferrite. In addition, beyond 1%, the weldability of the steel is significantly degraded, which makes it unsuitable for many preferred applications of sheets obtained from the steels of the invention.
  • carbon provides a hardening effect, as well as the precipitation of titanium and / or niobium carbides used for texture control, if titanium and / or niobium are present in significant amounts in the steel. .
  • a carbon content of the order of 0.02% is typical of the steels of the invention, except very high strength steels hot rolled or cold.
  • the copper content of the steel is between 0.5 and 10%, preferably between 1 and 10%.
  • the copper has no precipitation hardening effect or, more accurately, the driving force of precipitation is too low to achieve precipitation hardening under reasonable time and temperature conditions in the process. perspective of an industrial application. Practically, it is better to have at least 1% copper in the steel to take advantage of its hardening effect.
  • the end of rolling temperature is conditioned by the solubility limit of the copper in the austenite. But levels of the order of 4% of copper, imposing to hot roll above 1000 ° C and then cool the band to more than 2500 ° C / s, are still accessible by the technology of casting thin strips, provided to impose a low speed of scrolling of the hot product, of the order of a few m / s.
  • the first variant it is decided to dissociate the recrystallization treatment from the precipitation treatment (case of high-strength cold-rolled sheet for stamping).
  • the copper At the recrystallization temperature, the copper must be completely in solid solution in the single-phase ferritic domain.
  • the maximum copper content is then given by the solubility limit of the copper in the ferrite at the recrystallization temperature considered. It is at most 1.8% at the maximum allowable recrystallization temperature of 840 ° C (see Figure 1b).
  • the second variant it is chosen to couple the recrystallization treatment and the precipitation treatment (case of high-strength cold-rolled sheets). Very high levels of copper, up to 10%, are tolerable by basic annealing. Nevertheless, the recrystallization optimum may not coincide with the precipitation optimum, and the treatment parameters must then be chosen so as to achieve the best compromise for the intended application.
  • copper contents of the order of 3% and 1.8% depending on the application may be recommended.
  • the manganese content must be kept below or equal to 2%. Like carbon, manganese has a hardening effect. In addition, it is gammagenic, so it decreases the solubility of copper in ferrite by reducing the extent of the ferritic domain. Typically, it is recommended a manganese content of the order of 0.3%.
  • the silicon content can be up to 5%, without a minimum content must imperatively impose. Its alphagenic character makes it advantageous, however, because it allows to remain in the ferritic domain even with the preferred copper contents of 1.8 or even 3% of the steels of the invention. It is recommended to adjust the ratio Mn / Si to a value preferably greater than 3, to control, during the transformation ⁇ ⁇ ⁇ , the transfer of roughness of the surface of the cylinders on the solidified skins and the regularity of attachment of the solidified skins, to avoid the formation of cracks on the band during solidification and cooling.
  • Niobium and titanium may, preferably but not necessarily, be present at levels up to 0.5% each. They produce carbides favorable to texture control, and when they are over-stoichiometric with respect to carbon, they increase the temperature A C1 of the steel, thus the solubility of copper in ferrite. Typically, each of these elements may be present at a level of about 0.05%.
  • the nickel content can be up to 5%, this element being only optional. Nickel is often added to copper steels to combat hot cracking. His action is double. On the one hand, by increasing the solubility of copper in austenite, nickel delays the segregation of copper at the metal-oxide interface. On the other hand, since it is miscible with copper in any proportion, nickel increases the melting point of the segregating phase. It is usually considered that a nickel addition of the order of copper is sufficient to prevent hot cracking. The rapid cooling and possibly the inerting after casting of the process according to the invention prevents hot cracking, which reduces the interest of adding nickel with this objective in view. However, it is possible to add nickel to facilitate hot rolling.
  • the aluminum content can be up to 2% without damaging the properties of the steel, but this element is not necessarily present. However, it is advantageous for its alphagenic role comparable to that of silicon. Typically, aluminum is present at a level of about 0.05%.
  • the other chemical elements are present as residual elements at levels resulting from the production of steel according to conventional methods.
  • the tin content is less than 0.03%
  • the nitrogen content is less than 0.02%
  • the sulfur content is less than 0.05%
  • the phosphorus content is less than 0.05%.
  • the liquid steel whose composition has just been exposed is then continuously cast directly as a thin strip of thickness less than or equal to 10 mm.
  • the steel is typically poured into a bottomless mold, the casting space of which is limited by the internally cooled side walls of two cylinders rotated in opposite directions, and by two refractory side walls pressed against the ends. planes of cylinders.
  • This process is now well known in the literature (it is described in EP-A-0 641 867 in particular), and we will not talk about it further. It would also be conceivable to use a method of casting by solidification of the steel on a single cylinder, which would give access to thinner strips than the casting between two rolls.
  • the strip then undergoes hot rolling.
  • This can be carried out on a separate installation of the casting installation, after reheating of the strip at a temperature not exceeding 1000 ° C to avoid cracking (unless this reheating is performed in a non-heated atmosphere. oxidant).
  • In-line rolling also makes it possible to dispense with a sequence of winding / uncoiling / reheating operations between casting and hot rolling, which may present metallurgical risks: surface cracking, and incrustation of scale on winding in particular.
  • This hot rolling is carried out, with a reduction rate of at least 10%, in one pass or more. It basically has three functions.
  • the recrystallization it causes suppresses the solidification structure, which is unfavorable to the shaping of the sheet. Moreover, this recrystallization leads to a refinement of the grain which is necessary for the simultaneous improvement of the strength and tenacity properties of the strip, if it is intended to be used in the state of hot-rolled sheet.
  • the end of rolling temperature must be such that the copper is still at this stage in solid solution in ferrite and / or austenite. Indeed, the precipitation of the copper before the end of the rolling would not allow to draw the maximum of hardening. This maximum is of the order of 300 MPa per 1% copper, when the precipitation conditions are well controlled. This end of rolling temperature to be respected therefore depends on the composition of the steel, in particular its copper and carbon contents.
  • the end-of-lamination temperature must be greater than 1094 ° C, this temperature being approximately the temperature of the peritectic bearing that the Fe-Cu phase diagram exhibits. shown in Figure 1a, for very low carbon contents.
  • This also implies that the hot rolling is carried out in a non-oxidizing atmosphere, and that if the strip is cooled immediately after its solidification, this cooling is stopped at a sufficiently high temperature to then allow hot rolling of the strip. strip under conditions resulting in a rolling end temperature greater than 1094 ° C.
  • the end-of-lamination temperature must be higher than the solubility limit of the copper in the austenite, as given by the Fe-Cu phase diagram, for the carbon content considered.
  • the end-of-lamination temperature must be higher than 840 ° C for the very low carbon contents, this temperature corresponding to the eutectoid plateau (see Fig. 1b).
  • the end-of-lamination temperature must be higher than the solubility limit of the copper in the ferrite, as given by the Fe-Cu phase diagram for the carbon content considered.
  • the above figures are also modified because the carbon has a gamma-effect, as seen in the Fe-Cu phase diagram extract of Figure 2, established for a carbon content of 0.2%.
  • the temperature of the eutectoid bearing is lowered compared to the case of very low carbon contents, and is often below 800 ° C. We can then afford to lower the end of rolling temperature compared to previously described cases.
  • structural hardening is also achieved by the action of quenching precipitating constituents, such as bainite or martensite, in addition to hardening due to copper precipitation.
  • this end-of-lamination temperature must not be lower than the temperature for which, given the composition of the steel, precipitation of the copper would be observed.
  • the determination of this temperature for a given steel composition can be made at of current experiments by metallurgists, in case a measurement of this temperature would not be available in the literature.
  • the cooling rate V of the band is as V ⁇ e 1 , 98 % Cu - 0 , 08 with V in ° C / s and% Cu in% by weight.
  • V For a copper content of 1%, V must therefore be greater than or equal to 7 ° C / s, which is easily accessible. For a copper content of 3%, V must be greater than or equal to 350 ° C / s. This high speed is however accessible on a thin strip casting installation.
  • the winding of the band then takes place.
  • t HV , T the preferred combinations (t HV , T) compatible with the industrial tool used.
  • t HV is imposed (greater than 1 h); we can only play on the winding temperature.
  • the value of the maximum hardness that can be obtained increases as the temperature of the precipitation of precipitation decreases, provided that the band is allowed enough time to reach this maximum hardness.
  • the choice of the winding temperature of the strip and the choice of subsequent operations depend on the type of product that it is desired to manufacture.
  • the winding of the strip is carried out after hot rolling at an elevated temperature, for example that (calculated as a function of the copper content according to formula (2) above) which makes it possible to reach the maximum hardness in 1h (time from which, as said, the temperature of the coil usually starts to decrease).
  • the period during which the strip undergoes a stay at high temperature is therefore the initial phase of its stay in the form of coil following rapid cooling.
  • the hot-rolled sheet After complete cooling of the coil (which, depending on requirements, can be carried out in a completely natural way or be carried out in a forced manner after the lapse of the time required to obtain the desired hardness), the hot-rolled sheet is ready to use.
  • the germination rate of copper precipitates is an increasing exponential function of the degree of cooling of the band. Under these conditions, it is advisable, in order to obtain a maximum precipitation hardening effect, to complete the germination phase at a temperature lower than that at which the growth of the grains will take place. It is therefore possible to propose a second operating mode for the manufacture of hot-rolled strips. According to this second operating mode, the strip is wound at a sufficiently low temperature so that, during the natural cooling of the coil, there is no precipitation of the copper, the latter remaining in supersaturated solid solution. It is estimated that a winding temperature of less than 300 ° C is sufficient for this purpose. There is, in this case, no problem in winding the band in the martensitic transformation field.
  • the band (always wound, at least in the case where the winding took place below M s ) then undergoes a heat treatment of income between 400 and 700 ° C which makes it possible to remove the martensite.
  • the main role of this income is to precipitate the copper, so as to obtain the desired properties for the hot sheet.
  • the parameters of this treatment (temperature and duration) can be determined using equation (2) previously given.
  • the winding temperature must be greater than M s for steels whose carbon content is between 0.1 and 1%, since there is no heat treatment that would eliminate the martensite between winding and unwinding before cold rolling. But the In any case, the coiling temperature must also be less than 300 ° C. so that the cold rolling and subsequent recrystallization annealing take place on a steel in which the copper is in a supersaturated solid solution.
  • the cold rolling (typically at a reduction rate of 40 to 80% and at room temperature) is first carried out on the strip whose copper is in supersaturated solid solution and then on a recrystallization annealing carried out in the high temperature range where copper is also in solid solution in ferrite and / or austenite. It has already been seen in connection with the choice of the end temperature of hot rolling what could be the conditions adapted for this purpose, depending on the copper content of the strip.
  • the duration of this recrystallization annealing depends on the ability to have previously preserved the copper in solid solution. In fact, at the recrystallization temperature of 840 ° C., where up to 1.8% of copper can be converted into solid solution, the growth of the grains may be excessive. If the copper is already in solid solution before recrystallization, the annealing time is fixed not by the kinetics of dissolution of the copper precipitates, but by the kinetics of growth of the grains. The dissolution of the copper before recrystallization thus facilitates the optimization of the texture, and this situation is the most advantageous for the metallurgist.
  • the recrystallization annealing if carried out at 840 ° C, has a duration that can vary from 20s to 5mn. It can advantageously be executed in an installation of "Compact annealing" giving access in a short time to high temperatures that allow to resubmit large amounts of copper.
  • the precipitation income when very high levels of resistance are sought, it is preferable to achieve the precipitation income at relatively low temperature (400 to 700 ° C), but for a prolonged period determined, preferably, by the equation (2) above, in a base annealing installation where the band stays in the coil state.
  • the rapid cooling following treatment should bring the band below 300 ° C to keep the copper in supersaturated solids.
  • a procedure which comprises, as previously, a cold rolling (typically at a rate of reduction of 40 to 80% and at ambient temperature) carried out on the strip where the copper is in supersaturated solid solution, a recrystallization annealing and a precipitation income.
  • the recrystallization In order for the sheet to retain good stamping properties, the recrystallization must take place in the ferritic field and must not allow the copper to precipitate.
  • the recrystallization temperature is therefore determined by the solubility limit of the copper in the ferrite as seen above. Practically, it is advisable to carry out the recrystallization annealing at the eutectoid temperature (of the order of 840 ° C for low-carbon copper steels), where the solubility of copper in ferrite is maximum (1.8% ).
  • the hot or cold rolled strip can undergo a final treatment in a skin-pass mill to give it its final surface and flatness and adjust its mechanical properties.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatments In General, Especially Conveying And Cooling (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Metal Rolling (AREA)
  • Continuous Casting (AREA)
  • Superconductors And Manufacturing Methods Therefor (AREA)
EP03712234A 2002-01-14 2003-01-13 Procede de fabrication d un produit siderurgique en acier au carbone riche en cuivre, et produit siderurgique ainsi obtenu Revoked EP1466024B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR0200387A FR2834722B1 (fr) 2002-01-14 2002-01-14 Procede de fabrication d'un produit siderurgique en acier au carbone riche en cuivre, et produit siderurgique ainsi obtenu
FR0200387 2002-01-14
PCT/FR2003/000088 WO2003057928A1 (fr) 2002-01-14 2003-01-13 Procede de fabrication d'un produit siderurgique en acier au carbone riche en cuivre, et produit siderurgique ainsi obtenu

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EP1466024A1 EP1466024A1 (fr) 2004-10-13
EP1466024B1 true EP1466024B1 (fr) 2007-07-25

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EP03712234A Revoked EP1466024B1 (fr) 2002-01-14 2003-01-13 Procede de fabrication d un produit siderurgique en acier au carbone riche en cuivre, et produit siderurgique ainsi obtenu

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US (2) US7425240B2 (es)
EP (1) EP1466024B1 (es)
JP (1) JP2005514518A (es)
KR (1) KR20040069357A (es)
CN (1) CN100334235C (es)
AT (1) ATE368132T1 (es)
AU (1) AU2003216715A1 (es)
BR (1) BR0307165A (es)
CA (1) CA2473050A1 (es)
DE (1) DE60315129T2 (es)
ES (1) ES2289270T3 (es)
FR (1) FR2834722B1 (es)
WO (1) WO2003057928A1 (es)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2690184A1 (de) 2012-07-27 2014-01-29 ThyssenKrupp Steel Europe AG Kaltgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung
EP2690183A1 (de) 2012-07-27 2014-01-29 ThyssenKrupp Steel Europe AG Warmgewalztes Stahlflachprodukt und Verfahren zu seiner Herstellung

Families Citing this family (18)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US7618503B2 (en) * 2001-06-29 2009-11-17 Mccrink Edward J Method for improving the performance of seam-welded joints using post-weld heat treatment
FR2834722B1 (fr) * 2002-01-14 2004-12-24 Usinor Procede de fabrication d'un produit siderurgique en acier au carbone riche en cuivre, et produit siderurgique ainsi obtenu
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CN100334235C (zh) 2007-08-29
US7425240B2 (en) 2008-09-16
BR0307165A (pt) 2004-11-03
DE60315129D1 (de) 2007-09-06
FR2834722A1 (fr) 2003-07-18
US20080257456A1 (en) 2008-10-23
DE60315129T2 (de) 2008-04-10
FR2834722B1 (fr) 2004-12-24
US20050028898A1 (en) 2005-02-10
CN1633509A (zh) 2005-06-29
ATE368132T1 (de) 2007-08-15
KR20040069357A (ko) 2004-08-05
CA2473050A1 (fr) 2003-07-17
EP1466024A1 (fr) 2004-10-13
JP2005514518A (ja) 2005-05-19
AU2003216715A1 (en) 2003-07-24
ES2289270T3 (es) 2008-02-01
WO2003057928A1 (fr) 2003-07-17

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