EP0877824B1 - Gebrauchtsfertiges metalldraht und verfahren zu dessen herstellung - Google Patents

Gebrauchtsfertiges metalldraht und verfahren zu dessen herstellung Download PDF

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Publication number
EP0877824B1
EP0877824B1 EP97900245A EP97900245A EP0877824B1 EP 0877824 B1 EP0877824 B1 EP 0877824B1 EP 97900245 A EP97900245 A EP 97900245A EP 97900245 A EP97900245 A EP 97900245A EP 0877824 B1 EP0877824 B1 EP 0877824B1
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EP
European Patent Office
Prior art keywords
wire
steel
alloying element
weight
microalloyed
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
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EP97900245A
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English (en)
French (fr)
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EP0877824A1 (de
Inventor
Jean-Claude Arnaud
Eric Depraetere
Marc Francois
Raoul Serre
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Compagnie Generale des Etablissements Michelin SCA
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Compagnie Generale des Etablissements Michelin SCA
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • 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
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C21D2211/008—Martensite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12354—Nonplanar, uniform-thickness material having symmetrical channel shape or reverse fold [e.g., making acute angle, etc.]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12375—All metal or with adjacent metals having member which crosses the plane of another member [e.g., T or X cross section, etc.]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12431—Foil or filament smaller than 6 mils

Definitions

  • the invention relates to ready-to-use metal wires and methods for obtaining these sons. These ready-made threads are used for example to reinforce articles of plastics or rubber, in particular pipes, belts, tablecloths, tire covers.
  • ready-to-use yarn used in the present application means, in a way known in the art, that this wire can be used, for the intended application, without the to undergo a heat treatment likely to modify its structure metallurgical and without subjecting it to a deformation of its metallic material, by example a wire drawing, likely to modify its diameter.
  • Patent application WO-A-92/14811 describes a method for obtaining a wire ready for the use comprising a steel substrate whose structure comprises more than 90% of hardened returned martensite, the steel having a carbon content at least equal to 0.05% and at most equal to 0.6%, this substrate being coated with a metal alloy other than steel, for example brass.
  • the process for obtaining this thread comprises a quenching treatment on a work hardened wire by heating the wire above the point of AC3 transformation to give it a homogeneous austenite structure and then rapidly cooling, at a speed at least equal to 150 ° C / second, at below the end point of martensitic transformation. After this treatment of quenching at least two metals are deposited on the wire, the wire is heated to cause by diffusion the formation of an alloy of these metals, generally brass, we then cool the wire and we work harden it.
  • EP-A-330752 describes a steel wire (carbon from 0.01 to 0.5%) for be used as tire reinforcement and which may contain Nb, V and / or Ti for obtaining a special structure or for regulating the content of carbon and nitrogen.
  • the starting steel contains (in a way optional) Cr and / or Mo to provide improved corrosion resistance.
  • the purpose of the method followed by EP-A-330752 is directed purely to obtaining of a mixed structure of ferrite and martensite and / or bainite.
  • the ready-to-use wire has a coating of metal alloy other than steel disposed on a microalloyed steel substrate having the characteristics mentioned above.
  • a deposition is carried out on the wire.
  • the invention also relates to assemblies comprising at least one wire ready for the use according to the invention.
  • assemblies are for example strands, wire cables, especially cables with wire layers or cables made up of strands of wires.
  • the invention also relates to articles reinforced at least in part by threads. ready to use or by assemblies conforming to the preceding definitions, such articles being for example pipes, belts, tablecloths, envelopes tires.
  • returned martensite structure means that this structure contains less than 1% of non-martensitic phase (s). this other phase, or these other phases, being due to inevitable heterogeneities of steel.
  • breaking strength measurements are carried out in tension according to the method described in French standard AFNOR NF A 03-151 of June 1978.
  • the structure of steels is determined visually with a microscope optical with a magnification of 400.
  • the preparation of samples by chemical attack as well as structural examination are carried out according to the following reference: De Ferri Metallographica vol. No. II, A. Schrader, A. Rose, Edition Verlay Stahleisen GmbH. Düsseldorf.
  • C, Mn, Ni, Cr, Mo. Si and Co represent the% by weight, that is to say % by weight, of chemical bodies of which they are the symbols.
  • vanadium can be used in this formula having the same effect as molybdenum, while the aforementioned reference does not mention vanadium.
  • T d [area of peak ⁇ ] / [area of peak ⁇ + area of peak ⁇ ]
  • the peak ⁇ corresponds approximately to the angle of 50 ° and the peak ⁇ corresponds approximately to the angle 51 °.
  • the steel of these machine wires has a pearlitic structure.
  • M F and AC3 for these wire rods are given in table 2.
  • M F AC3 Son A and B 123 ° C 769 ° C Wire C 122 ° C 779 ° C Wire D 125 ° C 786 ° C
  • wires A and B are therefore identical and not micro-alloyed, the wires C and D being micro-alloyed and different from each other.
  • the quench cooling conditions are as follows.
  • Wires A, C and D speed of 130 ° C / second using as quench gas mixture of hydrogen and nitrogen (75% by volume of hydrogen, 25% by volume nitrogen volume).
  • Wire B speed of 180 ° C / second using pure hydrogen.
  • the Vickers hardness is measured on each of the wires obtained referenced A1, B1, C1 and D1, the letters A, B, C and D each identifying the starting wire rod cited above.
  • the wire A1 is unusable due to its too low hardness, which is due to the fact that its structure is not made up solely of martensite but contains both martensite and bainite.
  • the wires B1, C1 and D1 each consist almost entirely of martensite and their Vickers hardness is satisfactory.
  • wires C1 and D1 made of microalloyed steel, are obtained with easy quenching perform (relatively low speed, with an inexpensive gas mixture and not dangerous), while wire B1 is obtained with a difficult process and expensive (high quenching speed, using pure hydrogen), this process to obtain sufficient hardness but which is however less than that of the microalloyed wires C1 and D1.
  • vanadium makes it possible to improve the quenchability of steel, i.e. the formation of a single martensite phase during the quenching.
  • control wire B2 is then heated by the Joule effect, for 5 seconds each time, to three tempering temperatures T r (525 ° C, 590 ° C, 670 ° C) and then cooled to room temperature (about 20 ° C) , in order to evaluate the effect of this heat treatment on the tensile strength R m and on the diffusion rate T d of the brass, formed by the alloy of copper and zinc, for the wire thus obtained B3, in each case.
  • the diffusion rate T d is insufficient (less than 0.85) but that the breaking strength is higher than for the other temperatures.
  • a very good diffusion of the brass is obtained for the treatment at 670 ° C (diffusion greater than 0.85) but the resistance to rupture is notably lower than at 525 ° C and is not sufficient to allow obtaining high tensile strength by subsequent drawing.
  • the breaking strength is slightly higher for treatment at 590 ° C than that obtained at 670 ° C, with a slightly lower diffusion of the brass, although satisfactory, but this resistance is also insufficient to guarantee a high resistance after wire drawing. .
  • the diffusion rate of the brass is higher at 0.9, that is to say that the diffusion is very good, and that the resistance to breaking is also very good, much higher than that obtained for the wire witness B3 when the diffusion of the brass is greater than 0.9.
  • the presence of vanadium therefore allows, unexpectedly, to have both a good diffusion of brass and good resistance to breakage thanks to the formation of fine precipitates of carbonitride and / or vanadium carbide, which was in solution after the quenching period, despite the very short income time.
  • T r are those indicated previously for the income and the values of T d are those indicated previously and which were determined after the brass plating operation, before drawing, the values of T d being practically unchanged during the wire drawing.
  • wires C4 and D4 in accordance with the invention are characterized both by a good rate of diffusion of brass (greater than 0.9) and excellent resistance to breakage (greater than 2900 MPa).
  • B4 control wires have resistance to breakage significantly lower than that of wires C4 and D4 conforming to the invention, except for the wire B4 initially treated at a tempering temperature of 525 ° C, but then the diffusion rate of the brass is insufficient (less than 0.85), i.e. drawing is difficult to perform and leads to frequent breaks of the wire during its deformation, which makes obtaining the wire much more difficult than in the case of wires C4 and D4 of the invention.
  • the wire rod usable for the invention is produced in the manner which is usual for a wire rod intended to be transformed into fine wire ready for use to reinforce tire casings.
  • a bath of molten steel having the composition indicated for the wire rod according to the invention.
  • This steel is first produced in an electric oven or oxygen converter then deoxidized in a bag using an oxidant, like silicon, which is not likely to produce inclusions of alumina.
  • the vanadium is then introduced into the bag in the form of loose pieces of ferrovanadium by addition to the metal bath.
  • the process is similar if the alloying element is to be chromium or molybdenum.
  • the steel bath is continuously poured in the form of billets or blooms.
  • These semi-finished products are then conventionally rolled into wires machine with a diameter of 5.5 mm, first in billets, if it is blooms, or directly in the wire rod in the case of billets.
  • the alloying element is vanadium alone, which has the advantage of giving small precipitates, while chromium gives large precipitated and that molybdenum tends to cause segregation. If we uses chromium alone, its content in the steel is advantageously at least equal to 0.2%.
  • deformation of the wire in the previous examples was carried out by drawing. but other techniques are possible, for example rolling, associated possibly to a wire drawing, for at least one of the operations of deformation.
  • the coating of the wire ready for the use according to the invention is an alloy other than brass, this alloy being obtained with two metals, or more than two metals, for example ternary copper - zinc - nickel alloys, copper - zinc - cobalt, copper - zinc - tin, the main thing being that the metals used are likely to form a alloy, by diffusion, at a temperature at most equal to the temperature of annealed.

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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)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Heat Treatment Of Steel (AREA)

Claims (28)

  1. Gebrauchsfertiger mikrolegierter Stahldraht, der die folgenden Eigenschaften aufweist:
    sein Durchmesser liegt im Bereich von 0,10 mm bis 0,50 mm;
    seine Zugfestigkeit beträgt mindestens 2800 MPa;
    der mikrolegierte Stahl weist einen Kohlenstoffgehalt von 0,2 bis 0,6 % und einen Mengenanteil eines Legierungselements, das unter Vanadium (V), Molybdän (Mo), Chrom (Cr) oder einem Gemisch von zwei oder mehreren dieser Elemente ausgewählt ist, im Bereich von 0,08 bis 0,5 % (Gew.-% des Stahls) auf;
    der mikrolegierte Stahl hat eine kaltverfestigte, angelassene Martensit-Struktur.
  2. Draht nach Anspruch 1, dadurch gekennzeichnet, daß er einen Überzug aus einer von dem Stahl verschiedenen Metallegierung aufweist, der auf dem als Substrat dienenden mikrolegierten Stahl abgeschieden wurde.
  3. Draht nach Anspruch 2, dadurch gekennzeichnet, daß es sich bei dem Überzug um Messing handelt.
  4. Draht nach einem der Ansprüche 1 bis 3, dadurch gekennzeichnet, daß der Kohlenstoffgehalt des mikrolegierten Stahls mindestens 0,3 % und höchstens 0,5 % beträgt.
  5. Draht nach Anspruch 4, dadurch gekennzeichnet, daß der Kohlenstoffgehalt etwa 0,4 % ist.
  6. Draht nach einem der Ansprüche 1 bis 5, dadurch gekennzeichnet, daß der Stahl die folgenden Beziehungen (Gew.-%) erfüllt:
    0,3 % ≤ Mn ≤ 0,6 %; 0,1 % ≤ Si ≤ 0,3 %; P ≤ 0,02 %; S ≤ 0,02 %.
  7. Draht nach einem der Ansprüche 1 bis 6, dadurch gekennzeichnet, daß das Legierungselement höchsten 0,3 Gew.-% des mikrolegierten Stahls ausmacht.
  8. Draht nach einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, daß als Legierungselement nur Vanadium verwendet wird.
  9. Draht nach einem der Ansprüche 1 bis 7, dadurch gekennzeichnet, daß als Legierungselement nur Chrom verwendet wird, wobei sein Mengenanteil im Stahl mindestens 0,2 % ist.
  10. Draht nach einem der Ansprüche 1 bis 9, dadurch gekennzeichnet, daß die Zugfestigkeit mindestens 2900 MPa beträgt.
  11. Draht nach einem der Ansprüche 1 bis 10, dadurch gekennzeichnet, daß sein Durchmesser mindestens 0,15 mm und höchstens 0,40 mm beträgt.
  12. Verfahren zur Herstellung eines gebrauchsfertigen Drahts aus mikrolegiertem Stahl nach einem der Ansprüche 1 bis 11, dadurch gekennzeichnet, daß es die folgenden Schritte umfaßt:
    a) es wird von einem Draht-Vormaterial aus mikrolegiertem Stahl ausgegangen, das einen Kohlenstoffgehalt von 0,2 bis 0,6 % und einen Mengenanteil eines Legierungselements, das unter Vanadium (V), Molybdän (Mo), Chrom (Cr) oder einem Gemisch von zwei oder mehreren dieser Elemente ausgewählt ist, im Bereich von 0,08 bis 0,5 % % (Gew.-% des Stahls) aufweist;
    b) das Draht-Vormaterial wird so verformt, daß der Durchmesser des Drahtes nach der Deformation unter 3 mm liegt;
    c) die Deformation wird abgeschlossen und es wird eine Abschreckwärmebehandlung mit dem verformten Draht durchgeführt, wobei die Behandlung darin besteht, den Draht über den Umwandlungspunkt Ac3 zu erwärmen, um ihm eine homogene Austenit-Struktur zu verleihen, und ihn dann mindestens bis zum Endpunkt der Martensitumwandlung MF abzukühlen, wobei die Abkühlgeschwindigkeit mindestens 60 °C/s beträgt, um eine Martensitstruktur zu erhalten;
    d) der Draht wird auf eine Temperatur von mindestens 250 °C und höchstens 700 °C, die auch als Anlaßtemperatur bezeichnet wird, erwärmt, um in dem Stahl die Bildung einer Ausscheidung von mindestens einem Carbonitrid und/oder Carbid des Legierungselements hervorzurufen und eine angelassene Martensitstruktur zu erzeugen;
    e) der Draht wird anschließend auf eine Temperatur unter 250 °C abgekühlt; und
    f) der Draht wird dann verformt, wobei der Deformationsgrad s mindestes 1 ist, so daß eine kaltverfestigte, angelassene Martensitstruktur erhalten wird.
  13. Verfahren nach Anspruch 12, dadurch gekennzeichnet, daß nach Schritt c) auf dem Draht mindestens zwei Metalle abgeschieden werden, die befähigt sind, durch Diffusion eine Legierung zu bilden, die von dem Stahl des als Substrat dienenden Drahts verschieden ist, wobei das Erwärmen auf die Anlaßtemperatur in Schritt d) auch dazu dient, über Diffusion die Bildung einer Legierung aus diesen Metallen hervorzurufen.
  14. Verfahren nach Anspruch 13, dadurch gekennzeichnet, daß Kupfer und Zink abgeschieden werden, um in Schritt d) eine Messinglegierung zu erhalten.
  15. Verfahren nach einem der Ansprüche 12 bis 14, dadurch gekennzeichnet, daß der Kohlenstoffgehalt des Stahls des Draht-Vormaterials mindestens 0,3 % und höchstens 0,5 % beträgt.
  16. Verfahren nach Anspruch 15, dadurch gekennzeichnet, daß der Kohlenstoffgehalt etwa 0,4 % ist.
  17. Verfahren nach einem der Ansprüche 12 bis 16, dadurch gekennzeichnet, daß der Stahl des Draht-Vormaterials die folgenden Beziehungen (Gew.-%) erfüllt:
    0,3 % ≤ Mn ≤ 0,6 %; 0,1 % ≤ Si ≤ 0,3 %; P ≤ 0,02 %; S ≤ 0,02 %.
  18. Verfahren nach einem der Ansprüche 12 bis 17, dadurch gekennzeichnet, daß das Legierungselement (V, Mo, Cr) höchstens 0,3 Gew.-% des mikrolegierten Stahls ausmacht.
  19. Verfahren nach einem der Ansprüche 12 bis 18, dadurch gekennzeichnet, daß als Legierungselement nur Vanadium verwendet wird.
  20. Verfahren nach einem der Ansprüche 12 bis 18, dadurch gekennzeichnet, daß als Legierungselement nur Chrom verwendet wird, wobei sein Mengenanteil im Stahl mindestens 0,2 % ist.
  21. Verfahren nach einem der Ansprüche 12 bis 20, dadurch gekennzeichnet, daß die Abkühlgeschwindigkeit bei der Härtung in Schritt c) unter 150 °C/Sekunde liegt.
  22. Verfahren nach einem der Ansprüche 12 bis 21, dadurch gekennzeichnet, daß die Anlaßtemperatur in Schritt d) mindestens 400 °C und höchstens 650 °C beträgt.
  23. Verfahren nach einem der Ansprüche 12 bis 22, dadurch gekennzeichnet, daß der Draht auf Raumtemperatur abgekühlt wird, nachdem er auf Anlaßtemperatur gebracht wurde.
  24. Verfahren nach einem der Ansprüche 12 bis 23, dadurch gekennzeichnet, daß der Deformationsgrad E nach der Anlaßbehandlung mindestens 3 ist.
  25. Verband zur Verstärkung, die mindestens einen mikrolegierten Stahldraht nach einem der Ansprüche 1 bis 11 enthält.
  26. Verwendung eines mikrolegierten Stahldrahts nach einem der Ansprüche 1 bis 11 oder einer Verband nach Anspruch 25 zur Verstärkung von Gegenständen aus Kunststoff und/oder Kautschuk.
  27. Gegenstand, der zumindest teilweise mit einem mikrolegierten Stahldraht nach einem der Ansprüche 1 bis 11 oder einer Anordnung nach Anspruch 25 verstärkt ist.
  28. Gegenstand nach Anspruch 27, dadurch gekennzeichnet, daß es sich um einen Reifen handelt.
EP97900245A 1996-01-16 1997-01-08 Gebrauchtsfertiges metalldraht und verfahren zu dessen herstellung Expired - Lifetime EP0877824B1 (de)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR9600406 1996-01-16
FR9600406A FR2743573A1 (fr) 1996-01-16 1996-01-16 Fil metallique pret a l'emploi et procede pour obtenir ce fil
PCT/FR1997/000028 WO1997026379A1 (fr) 1996-01-16 1997-01-08 Fil metallique pret a l'emploi et procede pour obtenir ce fil

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EP0877824A1 EP0877824A1 (de) 1998-11-18
EP0877824B1 true EP0877824B1 (de) 2000-09-20

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US (1) US6106637A (de)
EP (1) EP0877824B1 (de)
JP (1) JP2000503724A (de)
KR (1) KR19990077252A (de)
CN (1) CN1079117C (de)
AU (1) AU1383497A (de)
BR (1) BR9706987A (de)
CA (1) CA2243324A1 (de)
DE (1) DE69703149T2 (de)
ES (1) ES2150752T3 (de)
FR (1) FR2743573A1 (de)
RU (1) RU2177510C2 (de)
WO (1) WO1997026379A1 (de)

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US6395109B1 (en) 2000-02-15 2002-05-28 Cargill, Incorporated Bar product, cylinder rods, hydraulic cylinders, and method for manufacturing
CA2303693C (en) * 2000-03-15 2001-12-11 Richard Aaron Barkley Method and apparatus for toughening metal strap buckles
FR2836847B1 (fr) * 2002-03-05 2004-05-14 Coflexip Procede de fabrication de fil d'armure en acier plaque pour conduite tubulaire flexible de transport d'hydrocarbures, et conduite ainsi armee
US7617713B2 (en) * 2004-12-14 2009-11-17 The Goodyear Tire + Rubber Company, Inc. Final die for wire drawing machines
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RU2480852C2 (ru) * 2011-01-17 2013-04-27 Закрытое акционерное общество "Москабельмет" Катанка из алюминиевого сплава
RU2505619C1 (ru) * 2012-11-23 2014-01-27 Открытое акционерное общество "Научно-производственное объединение "Прибор" Малоуглеродистая легированная сталь
FR3013737B1 (fr) * 2013-11-22 2016-01-01 Michelin & Cie Fil d'acier a haute trefilabilite comprenant un taux de carbone en masse compris entre 0,05 % inclus et 0,4 % exclu
WO2015097349A1 (fr) 2013-12-24 2015-07-02 Arcelormittal Wire France Fil laminé à froid en acier à haute résistance à la fatigue et à la fragilisation par l'hydrogène et renfort de conduites flexibles l'incorporant
CN108138276B (zh) * 2015-10-09 2021-05-25 江阴贝卡尔特钢丝制品有限公司 具有用于耐腐蚀的金属涂层的细长钢丝
FR3045671B1 (fr) * 2015-12-16 2017-12-08 Michelin & Cie Pneu renforce par un ruban en acier au carbone
FR3045670A1 (fr) * 2015-12-16 2017-06-23 Michelin & Cie Feuillard en acier au carbone, son utilisation pour le renforcement d'articles en caoutchouc

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KR19990077252A (ko) 1999-10-25
US6106637A (en) 2000-08-22
JP2000503724A (ja) 2000-03-28
EP0877824A1 (de) 1998-11-18
CN1079117C (zh) 2002-02-13
ES2150752T3 (es) 2000-12-01
DE69703149T2 (de) 2001-05-17
RU2177510C2 (ru) 2001-12-27
CN1214085A (zh) 1999-04-14
AU1383497A (en) 1997-08-11
WO1997026379A1 (fr) 1997-07-24
CA2243324A1 (fr) 1997-07-24
BR9706987A (pt) 1999-07-20
FR2743573A1 (fr) 1997-07-18
DE69703149D1 (de) 2000-10-26

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