EP1819461B1 - Procede de fabrication de toles d' acier austenitique , fer-carbone-manganese a tres hautes caracteristiques de resistance et excellente homogénéité. - Google Patents

Procede de fabrication de toles d' acier austenitique , fer-carbone-manganese a tres hautes caracteristiques de resistance et excellente homogénéité. Download PDF

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Publication number
EP1819461B1
EP1819461B1 EP05814950.1A EP05814950A EP1819461B1 EP 1819461 B1 EP1819461 B1 EP 1819461B1 EP 05814950 A EP05814950 A EP 05814950A EP 1819461 B1 EP1819461 B1 EP 1819461B1
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Prior art keywords
steel
mpa
equal
sheet
cold
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German (de)
English (en)
French (fr)
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EP1819461A2 (fr
Inventor
Philippe Cugy
Nicolas Guelton
Colin Scott
François Stouvenot
Marie-Christine Theyssier
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ArcelorMittal SA
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ArcelorMittal 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling

Definitions

  • the present invention relates to the manufacture of hot-rolled and cold-rolled sheets of austenitic iron-carbon-manganese steels having very high mechanical characteristics, and in particular a very advantageous combination of mechanical strength and elongation at break combined with excellent homogeneity. mechanical properties.
  • hot-rolled sheets that is to say of thickness ranging from from 1 to 10 mm
  • such characteristics are used to lighten ground connection parts, wheels, reinforcement parts such as door intrusion bars, or those intended for heavy vehicles (trucks , bus).
  • trucks trucks , bus
  • cold-rolled sheets ranging from approximately 0.2 mm to 6 mm
  • the applications are aimed at manufacturing parts contributing to the safety and durability of motor vehicles or even external parts.
  • steels with an austenitic structure such as Fe-C steels (up to 1.5%) - Mn (15 to 35%) (contents expressed by weight) and possibly containing other elements such as silicon, aluminum or chromium:
  • EDE energy of stacking defect
  • the mechanical twinning makes it possible to obtain a great capacity of work hardening: by obstructing the propagation of the dislocations, the twins participate in the increase of the flow limit.
  • the EDE increases in particular with the carbon and manganese content.
  • Austenitic steels Fe-0.6% C-22% Mn are thus known which are capable of deformation by twinning: Depending on the grain size, these steel compositions lead to tensile strength values ranging from 900 to 1150 MPa approximately. , in combination with a breaking strain ranging from 50 to 80%. There is, however, an unresolved need for hot or cold rolled steel sheets, with a strength significantly greater than 1150 MPa, also having good deformation capacity, and this without the addition of expensive alloys. It is sought to have steel sheets having a very homogeneous behavior during subsequent mechanical stresses.
  • FR-A-2 829 775 describes a process for manufacturing a welded tube, of the type comprising a final stretching or hydroforming step, characterized in that: an alloy is produced; a semi-finished product is then cast from this alloy, a) either in the form of an ingot which is then roughed by hot rolling to transform it into a slab, or directly in the form of a slab said slab then being hot rolled in the form of a strip and then wound, b) either in the form of a thin strip; the strip is then stripped if the strip is oxidized at the surface; we then proceed to manufacture the welded tube by progressive forming of a sheet metal cut from the previous strip to bring its edges until docking, then by welding of said edges, then by elimination of the weld bead, then by cold drawing or hydroforming.
  • the object of the invention is therefore to dispose of a sheet or a hot or cold rolled steel product, of economical manufacture, having a resistance greater than or equal to 1200 or even 1400 MPa in combination with a elongation such as product P: resistance (MPa) x elongation at rupture (%) is greater than 60,000 or 50,000 MPa% respectively at the resistance level mentioned above, a great homogeneity of mechanical properties during deformations or subsequent mechanical stresses and a structure free of martensite at any point during or after the deformation cold from this sheet or this product.
  • the subject of the invention is a hot-rolled sheet of austenitic iron-carbon-manganese steel whose resistance is greater than 1200 MPa, the product P of which (resistance (MPa) x elongation at break (%)) is greater than 65,000 MPa%, the nominal chemical composition of which includes, the contents being expressed by weight: 0.85% ⁇ C ⁇ 1.05%, 16% ⁇ Mn ⁇ 19%, Si ⁇ 2%, Al ⁇ 0.050%, S ⁇ 0.030%, P ⁇ 0.050%, N ⁇ 0.1%, and optionally, one or more elements chosen from: Cr ⁇ 1%, Mo ⁇ 1.50%, Ni ⁇ 1%, Cu ⁇ 5% , Ti ⁇ 0.50%, Nb ⁇ 0.50%, V ⁇ 0.50%, the rest of the composition consisting of iron and unavoidable impurities resulting from the production, the surface fraction recrystallized from steel being equal to 100%, the surface fraction of precipitated carbides of the steel being equal to
  • the invention also relates to a cold-rolled and annealed sheet of austenitic iron-carbon-manganese steel whose strength is greater than 1250 MPa, whose product P (strength (MPa) x elongation at break (%)) is greater at 65,000 MPa%, the nominal chemical composition of which includes, the contents being expressed by weight: 0.85% ⁇ C ⁇ 1.05%, 16% ⁇ Mn ⁇ 19%, Si ⁇ 2%, Al ⁇ 0.050%, S ⁇ 0.030%, P ⁇ 0.050%, N ⁇ 0.1%, and optionally, one or more elements chosen from: Cr ⁇ 1%, Mo ⁇ 1.50%, Ni ⁇ 1%, Cu ⁇ 5%, Ti ⁇ 0.50%, Nb ⁇ 0.50%, V ⁇ 0.50%, the rest of the composition consisting of iron and unavoidable impurities resulting from the production, the recrystallized surface fraction of the steel being equal to 100%, the average grain size of the steel being less than 3 microns
  • the local carbon content C L of the steel, and the local manganese content Mn L , expressed by weight, at all points of the austenitic steel sheet, are such that:% Mn L + 9.7% C L ⁇ 21.66
  • the nominal silicon content of the steel is less than or equal to 0.6%
  • the nominal nitrogen content of the steel is less than or equal to 0.050%.
  • the nominal aluminum content of the steel is less than or equal to 0.030%.
  • the invention also relates to a process for manufacturing a cold-rolled and annealed sheet of austenitic iron-carbon-manganese steel, the strength of which is greater than 1250 MPa, of which the product P (resistance (MPa) x elongation at rupture (%)) is greater than 60,000 MPa%, characterized in that a hot-rolled sheet obtained by the above process is supplied, at least one cycle is carried out, each cycle consisting of cold rolling the sheet in one or several successive passes and then perform recrystallization annealing, the average austenitic grain size before the last cold rolling cycle followed by recrystallization annealing, being less than 15 microns.
  • a hot-rolled sheet obtained by the above process is supplied, at least one cycle is carried out, each cycle consisting of cold rolling the sheet in one or several successive passes and then perform recrystallization annealing, the average austenitic grain size before the last cold rolling cycle followed by recrystallization annealing, being less than 15 microns.
  • the invention also relates to a process for manufacturing a cold-rolled and annealed sheet of austenitic iron-carbon-manganese steel whose resistance is greater than 1400 MPa, of which the product P (resistance (MPa) x elongation at break (%)) is greater than 50,000 MPa%, characterized in that, after the final recrystallization annealing, cold deformation is carried out with an equivalent deformation rate greater than or equal to 6%, and less than or equal to 17%.
  • MPa resistance
  • % x elongation at break
  • the subject of the invention is also a method of manufacturing a cold-rolled sheet of austenitic iron-carbon-manganese steel whose resistance i is greater than 1400 MPa, of which the product P (resistance (MPa) x elongation at break ( %)) is greater than 50,000 MPa%, characterized in that a cold rolled and annealed sheet is supplied according to the invention, and that a cold deformation of this sheet is carried out with a higher equivalent deformation rate or equal to 6%, and less than or equal to 17%.
  • the invention also relates to a process for manufacturing an austenitic steel sheet, characterized in that the conditions for casting or heating said semi-finished product, such as the temperature for casting said semi-finished product.
  • semi-finished product the mixing of the liquid metal by electromagnetic forces, the heating conditions leading to a homogenization of carbon and manganese by diffusion, are chosen so that, at any point on the sheet, the local carbon content C L and the local manganese content Mn L , expressed by weight, are such that:% Mn L + 9.7% C L ⁇ 21.66
  • the casting of the semi-finished product is carried out in the form of casting slabs or thin strips between counter-rotating steel cylinders.
  • the invention also relates to the use of an austenitic sheet steel for the manufacture of reinforcing or structural elements or of external parts, in the automotive field.
  • the invention also relates to the use of an austenitic steel sheet manufactured by means of a process described above, for the manufacture of reinforcing or structural elements or external parts, in the automotive field.
  • Manganese is also an essential element for - increasing resistance, increasing the energy of stacking defect and stabilizing the austenitic phase. If its nominal content is less than 16%, there is, as will be seen below, a risk of formation of martensitic phase which decreases most notably the ability to deform. Furthermore, when the nominal manganese content is greater than 19%, the twinning deformation mode is less favored compared to the sliding mode of perfect dislocations. In addition, for cost reasons, it is undesirable that the manganese content is high.
  • Aluminum is a particularly effective element for the deoxidation of steel. Like carbon, it increases the stacking fault energy. However, its excessive presence in steels with a high manganese content has a drawback. Manganese increases the solubility of nitrogen in liquid iron, and if too much aluminum is present in the steel, the nitrogen combining with the aluminum precipitates in the form of aluminum nitrides. interfering with the migration of grain boundaries during hot processing and very significantly increases the risk of cracks appearing.
  • a nominal content of Al less than or equal to 0.050% makes it possible to avoid precipitation of AIN. Correlatively, the nominal nitrogen content must be less than or equal to 0.1% in order to avoid this precipitation and the formation of volume defects during solidification. This risk is particularly reduced when the nominal aluminum content is less than 0.030% as well as when the nominal nitrogen content is less than 0.050%.
  • Silicon is also an effective element for deoxidizing steel as well as for hardening in the solid phase. However, beyond a nominal content of 2%, it reduces the elongation and tends to form undesirable oxides during certain assembly processes and must therefore be kept below this limit. This phenomenon is greatly reduced when the nominal silicon content is less than 0.6%.
  • Sulfur and phosphorus are impurities which weaken grain boundaries. Their respective nominal content must be less than or equal to 0.030 and 0.050% in order to maintain sufficient hot ductility. When the nominal phosphorus content is less than 0.040%, the risk of brittleness is particularly reduced.
  • Chromium can be used as an option to increase the strength of the steel by hardening in solid solution. However, since chromium decreases the stacking defect energy, its nominal content must be lower or equal to 1%. Nickel increases the stacking defect energy and contributes to obtaining a significant elongation at break. However, it is also desirable, for cost reasons, to limit the nominal nickel content to a maximum content less than or equal to 1%. Molybdenum can also be used for similar reasons, this element further delaying the precipitation of carbides. For efficiency and cost reasons, it is desirable to limit its nominal content to 1.5%, and preferably to 0.4%.
  • adding copper to a nominal content less than or equal to 5% is a means of hardening the steel by precipitation of metallic copper.
  • copper is responsible for the appearance of hot sheet surface defects.
  • Titanium, niobium and vanadium are also elements which can be used optionally to obtain hardening by precipitation of carbonitrides.
  • the nominal Nb or V or Ti content is greater than 0.50%, excessive precipitation of carbonitrides can cause a reduction in ductility and drawability, which should be avoided.
  • a steel is produced, the composition of which has been set out above. This production can be followed by casting in ingots, or continuously in the form of slabs with a thickness of the order of 200 mm. The casting can also be carried out in the form of thin slabs a few tens of millimeters thick, or of thin strips, between counter-rotating steel cylinders.
  • the present description illustrates the application of the invention to flat products, it can be applied in the same way to the manufacture of long products made of Fe-C-Mn steel.
  • These cast semi-finished products are first brought to a temperature of between 1100 and 1300 ° C. This is intended to reach at all points the temperature ranges favorable to the high deformations that the steel will undergo during rolling. However, the temperature should not be higher than 1300 ° C, on pain of being too close to the solidus temperature which could be reached in possible areas segregated into manganese and / or carbon, and of causing a start of local passage by a liquid state which would be harmful for hot forming.
  • the stage of hot rolling of these semi-finished products starting between 1300 and 1100 ° C. can be done directly after casting so that a stage of reheating intermediary is not necessary in this case.
  • the semi-finished product is hot rolled, for example to obtain a thickness of hot rolled strip of a few millimeters.
  • the low aluminum content of the steel according to the invention makes it possible to avoid excessive precipitation of AIN which would harm hot deformability during rolling.
  • the end of rolling temperature In order to avoid any cracking problem due to lack of ductility, the end of rolling temperature must be greater than or equal to 900 ° C.
  • the inventors have demonstrated that the ductility properties of the sheets obtained are reduced when the recrystallized surface fraction of the steel is less than 100%. Consequently, if the hot rolling conditions have not led to a total recrystallization of the austenite, the inventors have demonstrated that it is necessary to observe, after the hot rolling phase, a time of waiting so that the recrystallized surface fraction is equal to 100%. This isothermal high-temperature maintenance phase after rolling thus causes total recrystallization.
  • the inventors have used evidence that particularly high strength and elongation at break properties are obtained when the average austenitic grain size was less than or equal to 10 microns. Under these conditions, the breaking strength of the hot sheets thus obtained is greater than 1200 MPa and the product P (resistance x elongation at break) is greater than 65000 MPa%.
  • the process includes a cold deformation step
  • the sheet produced can be qualified as “hot rolled sheet” insofar as the rate of cold deformation is very minimal in comparison with the usual rates achieved during rolling. cold before annealing for the production of thin sheets, and insofar as the thickness of the sheet thus produced is within the usual range of thicknesses of hot-rolled sheets.
  • the equivalent cold deformation rate is greater than 17%
  • the reduction in elongation becomes such that the parameter P (resistance R x elongation at break A) cannot reach 50,000 MPa%.
  • the sheet retains a good elongation capacity since the product P of the sheet thus obtained is greater than or equal to 50,000 MPa%.
  • the inventors have also demonstrated that the structure must be completely recrystallized after annealing in order to achieve the desired properties. Simultaneously, when the average grain size is less than 5 microns, the resistance exceeds 1200 MPa, and the product P is greater than 65000 MPa%. When the average grain size obtained after annealing is less than 3 microns, the resistance exceeds 1250 MPa, the product P always being greater than 65000MPa%.
  • FIG. 1 presents, in a carbon-manganese diagram (and iron complement) the calculated iso-energy curves of stacking defect whose values range from 5 to 30mJ / m 2 .
  • the deformation mode is theoretically identical for any Fe-C-Mn alloy having the same EDE.
  • the area of occurrence of martensite has also been shown in this diagram.
  • the inventors have shown that, in order to assess the mechanical behavior, it is necessary to consider not only the nominal chemical composition of the alloy, for example its nominal or average content. carbon and manganese, but also its local content.
  • local content is meant here the content measured by means of a device such as an electronic probe.
  • a linear or surface scan using such a device makes it possible to appreciate the variation in the local content.
  • the inventors have sought the specific conditions for obtaining very high mechanical characteristics simultaneously with a great homogeneity of these characteristics within a steel sheet.
  • the combination of carbon (0.85% -1.05%) and manganese (16-19%) associated with the other characteristics of the invention leads to resistance values greater than 1200MPa and to a product (resistance x elongation at break) greater than 60,000, or even 65,000 MPa%.
  • these steel compositions are in a field where the EDE is of the order of 19-24 mJ / m 2 , that is to say favorable to deformation by twinning.
  • the inventors have also demonstrated that a variation in the local carbon or manganese content has a much smaller influence than that mentioned in the previous example.
  • the inventors have shown that it was absolutely necessary to avoid the formation of martensite during deformation operations or the use of sheets under penalty of heterogeneity of mechanical characteristics on the parts.
  • the inventors have determined that this condition is satisfied when, at any point on the sheets, the local carbon and manganese contents of the sheet are such that:% Mn L + 9.7% C L ⁇ 21.66.
  • austenitic steel sheets are produced which not only have very high mechanical characteristics but also a very low dispersion of these characteristics.
  • the person skilled in the art will adapt the manufacturing conditions so as to satisfy this relationship concerning the local contents, in particular by means of the casting conditions (casting temperature, stirring of the liquid metal by electromagnetic forces) or heating conditions leading to homogenization of carbon and manganese by diffusion.
  • a semi-finished product of steel I according to the invention was reheated to a temperature of 1180 ° C and hot rolled to a temperature above 900 ° C to reach a thickness of 3 mm.
  • a waiting time of 2 s was observed after rolling for complete recrystallization, then cooling was carried out at a speed greater than 20 ° C / s, followed by winding at room temperature.
  • the reference steels were reheated to a temperature above 1150 ° C, rolled to a rolling end temperature above 940 ° C and then coiled at a temperature below 450 ° C.
  • the recrystallized surface fraction is 100% for all steels, the fraction of precipitated carbides is equal to 0%, the average grain size between 9 and 10 microns.
  • the steel according to the invention makes it possible to obtain an increased resistance of approximately 200 MPa with very comparable elongation.
  • the steel sheet according to the invention was then subjected to a slight cold deformation by rolling with an equivalent deformation of 14%.
  • This product with exceptionally high mechanical characteristics offers great possibilities of subsequent deformation due to its reserve of plasticity and its low anisotropy.
  • the steel sheet produced according to the invention whose average grain size is 4 microns, therefore offers a particularly advantageous resistance-elongation combination and a significant increase in resistance compared to the reference steel. As with hot rolled sheets, these characteristics are obtained with very high homogeneity on the product, no trace of martensite is present after deformation.
  • Equibiaxial expansion tests on a hemispherical punch 75 mm in diameter carried out on a cold-rolled and annealed sheet 1.6 mm thick according to the invention reveal a limit stamping height of 33 mm, which highlights a excellent deformability. Bending tests carried out on this same sheet also show that the critical deformation before the appearance of cracks is greater than 50%.
  • the steel sheet produced according to the invention was subjected to cold deformation by rolling with an equivalent deformation rate of 8%:
  • hot-rolled or cold-rolled steels according to the invention will be used with advantage for applications where capacity is sought. significant deformation and very high strength.
  • advantage will be taken of their advantages for the manufacture of structural parts, reinforcing elements or even external parts.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
EP05814950.1A 2004-11-24 2005-11-04 Procede de fabrication de toles d' acier austenitique , fer-carbone-manganese a tres hautes caracteristiques de resistance et excellente homogénéité. Active EP1819461B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL05814950T PL1819461T3 (pl) 2004-11-24 2005-11-04 Sposób wytwarzania blach ze stali austenitycznych żelazo-węgiel-mangan o bardzo wysokich właściwościach wytrzymałościowych i doskonałej jednorodności

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR0412477A FR2878257B1 (fr) 2004-11-24 2004-11-24 Procede de fabrication de toles d'acier austenitique, fer-carbone-manganese a tres hautes caracteristiques de resistance et d'allongement, et excellente homogeneite
PCT/FR2005/002740 WO2006056670A2 (fr) 2004-11-24 2005-11-04 Procede de fabrication de toles d'acier austenitique, fer-carbone-manganese a tres hautes caracteristiques de resistance et d'allongement, et excellente homogeneite

Publications (2)

Publication Number Publication Date
EP1819461A2 EP1819461A2 (fr) 2007-08-22
EP1819461B1 true EP1819461B1 (fr) 2020-04-15

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EP05814950.1A Active EP1819461B1 (fr) 2004-11-24 2005-11-04 Procede de fabrication de toles d' acier austenitique , fer-carbone-manganese a tres hautes caracteristiques de resistance et excellente homogénéité.

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US (1) US7794552B2 (ko)
EP (1) EP1819461B1 (ko)
JP (2) JP5142101B2 (ko)
KR (3) KR20070091300A (ko)
CN (1) CN101090982B (ko)
BR (1) BRPI0517890B1 (ko)
CA (1) CA2587858C (ko)
ES (1) ES2791675T3 (ko)
FR (1) FR2878257B1 (ko)
HU (1) HUE050022T2 (ko)
MX (1) MX2007006240A (ko)
PL (1) PL1819461T3 (ko)
RU (1) RU2366727C2 (ko)
UA (1) UA90873C2 (ko)
WO (1) WO2006056670A2 (ko)
ZA (1) ZA200703890B (ko)

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EP1878811A1 (en) * 2006-07-11 2008-01-16 ARCELOR France Process for manufacturing iron-carbon-manganese austenitic steel sheet with excellent resistance to delayed cracking, and sheet thus produced
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US20080035248A1 (en) 2008-02-14
CN101090982B (zh) 2010-09-08
KR20100084570A (ko) 2010-07-26
US7794552B2 (en) 2010-09-14
HUE050022T2 (hu) 2020-11-30
RU2007123594A (ru) 2008-12-27
KR20070091300A (ko) 2007-09-10
JP2008520830A (ja) 2008-06-19
BRPI0517890A (pt) 2008-10-21
KR101275895B1 (ko) 2013-06-17
JP5142101B2 (ja) 2013-02-13
PL1819461T3 (pl) 2020-10-05
ZA200703890B (en) 2008-05-28
CA2587858A1 (fr) 2006-06-01
EP1819461A2 (fr) 2007-08-22
UA90873C2 (ru) 2010-06-10
WO2006056670A2 (fr) 2006-06-01
BRPI0517890B1 (pt) 2014-12-23
ES2791675T3 (es) 2020-11-05
CN101090982A (zh) 2007-12-19
FR2878257A1 (fr) 2006-05-26
RU2366727C2 (ru) 2009-09-10
CA2587858C (fr) 2011-10-25
FR2878257B1 (fr) 2007-01-12
WO2006056670A3 (fr) 2007-07-05
MX2007006240A (es) 2007-10-08
KR20120014070A (ko) 2012-02-15
JP2012072499A (ja) 2012-04-12

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