EP0859064B1 - Acier inoxydable pour l'élaboration de fil tréfilé notamment de fil de renfort de pneumatique et procédé de realisation dudit fil - Google Patents

Acier inoxydable pour l'élaboration de fil tréfilé notamment de fil de renfort de pneumatique et procédé de realisation dudit fil Download PDF

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Publication number
EP0859064B1
EP0859064B1 EP98400241A EP98400241A EP0859064B1 EP 0859064 B1 EP0859064 B1 EP 0859064B1 EP 98400241 A EP98400241 A EP 98400241A EP 98400241 A EP98400241 A EP 98400241A EP 0859064 B1 EP0859064 B1 EP 0859064B1
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EP
European Patent Office
Prior art keywords
wire
less
diameter
steel
inclusions
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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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EP98400241A
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German (de)
English (en)
French (fr)
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EP0859064A1 (fr
Inventor
Jean-Michel Hauser
Joel Marandel
Etienne Havette
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ugitech
Original Assignee
Sprint Metal Societe de Production Internationale de Trefiles
Ugine Savoie Imphy SA
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    • D—TEXTILES; PAPER
    • D07—ROPES; CABLES OTHER THAN ELECTRIC
    • D07B—ROPES OR CABLES IN GENERAL
    • D07B1/00—Constructional features of ropes or cables
    • D07B1/06—Ropes or cables built-up from metal wires, e.g. of section wires around a hemp core
    • D07B1/0606—Reinforcing cords for rubber or plastic articles
    • D07B1/066—Reinforcing cords for rubber or plastic articles the wires being made from special alloy or special steel composition
    • 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
    • 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • D—TEXTILES; PAPER
    • D07—ROPES; CABLES OTHER THAN ELECTRIC
    • D07B—ROPES OR CABLES IN GENERAL
    • D07B2201/00—Ropes or cables
    • D07B2201/20—Rope or cable components
    • D07B2201/2001—Wires or filaments
    • D07B2201/2009—Wires or filaments characterised by the materials used
    • D—TEXTILES; PAPER
    • D07—ROPES; CABLES OTHER THAN ELECTRIC
    • D07B—ROPES OR CABLES IN GENERAL
    • D07B2205/00—Rope or cable materials
    • D07B2205/30—Inorganic materials
    • D07B2205/3021—Metals
    • D07B2205/3025—Steel
    • D07B2205/3028—Stainless steel
    • 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
    • Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10S428/00—Stock material or miscellaneous articles
    • Y10S428/922—Static electricity metal bleed-off metallic stock
    • Y10S428/923—Physical dimension
    • 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
    • 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
    • Y10T428/12438—Composite
    • 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
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, 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
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • 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
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12778—Alternative base metals from diverse categories
    • 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
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • 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
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12903—Cu-base component
    • Y10T428/12917—Next to Fe-base component
    • Y10T428/12924—Fe-base has 0.01-1.7% carbon [i.e., steel]

Definitions

  • the present invention relates to a method for producing yarn drawn, of stainless steel, in particular of tire reinforcement wire of diameter less than 0.3 mm, by drawing of a steel having a adapted composition and inclusive cleanliness.
  • the thread obtained by the method can be used in the field of making parts subject to fatigue.
  • Reinforcing metal wires for elastomers for tires must have a small diameter, generally between 0.1 mm and 0.3 mm and high mechanical characteristics.
  • the charge to the rupture in tension can be higher than 2300 MPa, the ductility residual, measured by tensile necking, torsion or by looping must be non-zero, the limit of endurance in fatigue by bending rotary or alternating must be greater than 1000 MPa.
  • Patent application FR 93 12 528 deals with the use of a wire of stainless steel with a diameter between 0.05 mm and 0.5 mm including the tensile strength Rm is greater than 2000 MPa.
  • the steel of which is composed the thread contains in its composition at least 50% of martensite obtained by wire drawing at a reduction rate greater than 2.11 with intermediate annealing, the sum of the nickel content and chromium being between 20% and 35%.
  • the object of the invention is to produce a drawn wire, in particular a tire reinforcement wire with a diameter less than 0.3 mm by drawing a basic wire rod with a diameter greater than or equal to 5 mm or d '' a previously drawn basic steel wire of given composition, the simplified production process, ensuring on the one hand inclusionary quality which reduces breakages in wire drawing, and on the other hand, improved mechanical properties.
  • the invention also relates to the stainless steel used in the process.
  • the invention also relates to the application of the wire obtained by the process in the field of tire reinforcement.
  • Figure 1 shows the cumulative strain rate ⁇ that it is possible to reach by industrial drawing without annealing between wire drawing operations, according to the IM index defined by the relation satisfying the composition, for alloys containing less than 2% of manganese.
  • Figure 2 shows the martensite content after wire drawing of the diameter 5.5 mm to diameters 0.18 mm, without intermediate annealing, from annealed wires of different compositions, according to the JM index.
  • Figure 3 shows the breaking load after drawing of 5.5 mm to 0.18 mm without intermediate annealing, depending on the JM index.
  • the invention relates to a process for producing a drawn wire, in particular tire reinforcement wire with a diameter of less than 0.3 mm by drawing a basic wire rod with a diameter greater than 5 mm or a previously drawn basic wire.
  • the fine wire is produced by drawing from a machine wire or a previously drawn steel wire. Due to the composition of the steel, after live drawing without intermediate annealing, the final drawn wire has improved tensile strength properties and sufficient residual ductility for assembly, for example, in the form of sheets, cables.
  • This steel whose austenite partially transforms into deformation martensite near room temperature and with controlled inclusions, allows to obtain, by wire drawing, a cumulative deformation capacity ⁇ without intermediate annealing greater than 6.84.
  • This composition condition is intended to ensure the capacity large reductions by wire drawing and hardening by work hardening adequate.
  • annealing means that no reheating of the wire to more than 650 ° C is applied between the start and the end of the drawing operations.
  • a annealing at more than 650 ° C would have the effect of converting martensite into austenite and to eliminate the hardening by recrystallization.
  • the wire drawing is preferably carried out on a machine multipass, the wire being on the one hand lubricated with soap or lubricant liquid, and on the other hand, temperature controlled between 20 ° C and 180 ° C.
  • the wire can also be brass plated before or during wire drawing operations.
  • the brass layer improves the ability to wire drawing and adhesion of the wire with the elastomers of the tires.
  • gamma-genes favor the appearance of austenite phase of metallographic structure of cubic type with faces centered.
  • these elements are carbon, nitrogen, manganese, copper, nickel.
  • compositions forming a quantity excessive wire drawing martensite becomes brittle and brittle when drawing.
  • This limit quantity of martensite is a function of the content total carbon and nitrogen of the steel and is around 90% for a total carbon and nitrogen content of less than 0.030%, of 70% for a total carbon and nitrogen content less than or equal to 0.050%, and 30% for a total carbon and nitrogen content between 0.050% and 0.1%.
  • compositions having an index MI greater than the value determined above and a total content of carbon and nitrogen of the order of 0.040% become brittle before reach the wire drawing to the final diameter.
  • the presence of an excessive amount of silicon i.e. in an amount greater than 1%, has the effect of weaken the wire in the work-hardened state by drawing in the presence of a quantity important martensite.
  • composition of the stainless steel according to the invention containing more than 9% nickel, more than 1.5% copper, more than 15% chromium, a total carbon and nitrogen content of less than 0.050%, a content in Mn less than 2% with an IM index less than -55 ° C or a Mn content greater than or equal to 2% with a JM index less than -55 ° C, can be drawn to the final diameter with a breakage rate reduced, the wire retaining mechanical characteristics which allow its use in the field of tire reinforcement.
  • the IM index When the Mn content is less than 2%, the IM index must be in the range -150 ° C and -55 ° C. Indeed, if IM is lower at -150 ° C, the amount of martensite formed remains small, for example less than 10%, and the breaking load cannot reach values higher than 2200 MPa, even after drawing with a cumulative deformation ⁇ close to 8. In the same way, when the Mn content is greater than or equal to 2%, the JM index must be between - 120 ° C and - 55 ° C. When JM is less than -120 ° C, the amount of martensite is less than 25% and the breaking load does not can exceed 2200 MPa even after a cumulative reduction of around of 8.
  • a copper content greater than 4% generates segregation at solidification and ruptures or defects during hot rolling.
  • the process applied to the drawing of stainless steel according to the invention makes it possible to obtain a wire comprising an excellent fatigue strength measured by rotary bending with an endurance stress of 2.10 6 cycles greater than 1000 MPa.
  • the yarn obtained contains less than 75% of austenite or more than 25% martensite.
  • the steel used is slightly unstable with austenite with a total carbon and nitrogen content of less than 0.050%.
  • stainless steels may, in the liquid state, contain in solution, due to the production processes, oxygen and sulfur contents of less than 1000 ⁇ 10 -4 %. During the cooling of the steel in liquid or solid state, the solubility of the oxygen and sulfur elements decreases and the energy of formation of the oxides or sulphides is reached.
  • inclusions formed on the one hand of oxide type compounds containing oxygen atoms and alloying elements eager to react with oxygen such as calcium, magnesium, aluminum, silicon, manganese, chromium, and on the other hand, sulfur-type compounds containing sulfur atoms and alloying elements eager to react with sulfur such as manganese, chromium, calcium, magnesium. There may also appear inclusions which are mixed compounds of the oxysulfide type.
  • the production of a stainless steel having a selected inclusiveness allows the production of wire rod or basic pre-drawn wire, wire used according to the invention for drawing tire reinforcement wire with a diameter of less than 0.3 mm or the production of parts subject to fatigue.
  • a steel A according to the invention contains in its composition by weight 19.10 -3 % of carbon, 23.10 -3 % of nitrogen, 0.53% of silicon, 0.72% of manganese, 17.3% chromium, 9.3% nickel, 3.1% copper, 0.055% molybdenum, 4.10 -3 % sulfur, 22.10 -3 % phosphorus, 72.10 -4 % total oxygen , 5.10 -4 % total aluminum, 2.10 -4 % magnesium, 2.10 -4 % calcium, 11.10 -4 % titanium.
  • Its IM stability index is -77 ° C.
  • the steel is produced in an electric oven and then in the AOD converter, and continuously cast in 205 mm by 205 mm section then hot rolled into 5.5 mm diameter wire.
  • the steel A was subjected to a metallographic examination by cutting in the longitudinal direction, which revealed the presence, on a surface of 1000 mm 2 , of 8 inclusions of thickness between 5 and 10 ⁇ m and an inclusion of 12 ⁇ m.
  • the wire After recrystallization annealing at 1050 ° C. in a crown and water cooling, the wire is pickled and drawn without annealing intermediate up to the diameter of 0.18 mm successively on several multi-pass machines. The breaking load of the drawn wire is then 2650 MPa and the wire has a necking after traction.
  • Steel C can be drawn to a diameter of 0.4 mm from a wire with a diameter of 5.5 mm. For further drawing, it becomes fragile with the presence in its composition of a large amount of martensite.
  • Steel A according to the invention can be drawn from 5.5 mm to 0.18 mm without the process generating a brittleness of the yarn obtained.
  • the wire thus produced has a breaking load ensuring use in the area of tire reinforcement wire.
  • the wires were drawn in 12 successive passes with soap up to a diameter of 1 mm, then in 6 soap passes with a diameter of 0.48 mm, then in 9 soap passes with a diameter of 0.18 mm, all without any annealing from the initial state. At this point, the final product has been subjected to tensile and martensite rate measurements by the saturation magnetization method.
  • Table 4 presents for each of the compositions the values of the indices IM and JM, as well as the breaking loads Rm and the martensite contents of the final product.
  • Figure 2 shows the martensite content of the diameter wires 0.18 mm depending on JM.
  • Figure 3 shows the breaking loads of the 0.18 mm diameter depending on JM.
  • the JM index is particularly relevant for reporting on changes in breaking loads and martensite contents.
  • Wires with a JM index greater than - 55 ° C will present, for rejection rates ⁇ greater than 6, without intermediate annealing, more 90% martensite and fragile behavior.
  • the wires were drawn in 12 passes, with soap, to the diameter 1mm, without intermediate annealing.
  • the treatment substantially retains the initial amount of martensite and may cause slight hardening for short times.
  • softening becomes more important.
  • martensite mostly tends to disappear and the steel of the wire softens strongly.
  • the wires may be subjected, between several operations of wire drawing, heat treatments at temperatures below 650 ° C and preferably less than 600 ° C without causing excessive disappearance of martensite or softening, which would harm obtaining very high mechanical properties as a wire wireframe having undergone total deformation by wire drawing ⁇ greater than 6.
  • any treatment, even short, at a higher temperature at 650 ° C strongly softens the steel of the drawn wire at an intermediate stage or final, which is considered annealing.
  • Carbon, nitrogen, chromium, nickel, manganese, silicon are the usual elements for obtaining a steel austenitic stainless.
  • the manganese, chromium, sulfur contents in proportion are chosen to generate deformable sulfides of good composition determined.
  • composition intervals of the silicon and manganese elements ensure according to the invention, the presence of inclusions of silicate type, rich in SiO 2 and containing a non-negligible amount of MnO, deformable by hot rolling.
  • the silicon has a content of between 0.2%, which corresponds to a residual due to processing and 1%, which is the content beyond which it appears excessive embrittlement of the cold drawn wire.
  • Mobybdenum can be added to the composition of steel stainless to improve corrosion resistance.
  • Copper is added to the composition of the steel according to the invention because it improves the cold deformation properties and therefore stabilizes the austenite.
  • the copper content is limited to 4% to avoid difficulties of hot transformation because copper significantly lowers the upper heating temperature limit steel before rolling.
  • the intervals in total oxygen, aluminum and calcium make it possible, according to the invention, to obtain inclusions of the manganese silicate type containing a non-zero fraction of Al 2 O 3 and CaO.
  • the overall aluminum and calcium contents are each greater than 0.1 ⁇ 10 -4 % so that the desired inclusions contain more than 1% of CaO and more than 3% of Al 2 O 3 .
  • the values of the total oxygen contents are according to the invention between 40.10 -4 % and 120.10 -4 %.
  • the oxygen fixes the elements magnesium, calcium, aluminum and does not form the inclusion of oxides rich in SiO 2 and MnO.
  • the calcium content is less than 5.10 -4 % so that the desired inclusions do not contain more than 30% CaO.
  • the aluminum content is less than 20.10 -4 % to prevent the desired inclusions from containing more than 25% of Al 2 O 3 , which also promotes crystallization.
  • the invention relates to stainless steel containing inclusions of chosen composition obtained voluntarily, the composition being related to the overall composition of the steel, so that the physical properties of these inclusions favor their deformation during hot transformation of steel.
  • stainless steel contains inclusions of determined composition which have their softening point close to the rolling temperature of the steel and such that the appearance of crystals harder than steel at the rolling temperature.
  • the defined compounds SiO 2 , in the form of tridymite, christobalite, quartz; 3CaO-SiO 2 ; CaO; MgO; Cr 2 O 3 ; anorthite, mullite, gehlenite, corundum, spinel of the Al 2 O 3 -MgO or Al 2 O 3 -Cr 2 O 3 -MnO-MgO type; CaO-Al 2 O 3 ; CaO-6Al 2 O 3 ; CaO-2Al 2 O 3 , TiO 2 is inhibited.
  • the steel mainly contains inclusions of oxide of composition such as this form a vitreous mixture or amorphous during all the successive operations of setting in form of steel.
  • the viscosity of the inclusions chosen is sufficient to that the growth of crystallized oxide particles in the inclusions resulting from the invention is completely inhibited by the fact that, in an oxide inclusion, the short distance diffusion is weak and convective movements are very limited.
  • These inclusions remained glass in the temperature range of hot treatments of steel also have a higher hardness and modulus of elasticity weak than crystallized inclusions of corresponding composition.
  • inclusions can be further distorted, overwritten and lengthened, during wire drawing operations and the concentration of stresses in the vicinity of the inclusions is greatly reduced, which significantly reduces the risk of developing, for example, fatigue cracks or wire drawing breaks.
  • stainless steel contains inclusions of oxides of defined composition such as their viscosity in the temperature range of hot rolling steel is not too high. Therefore, the flow constraint of inclusion is significantly weaker than that of steel under the conditions of hot rolling whose temperatures are generally included between 800 ° C and 1350 ° C. Thus the oxide inclusions deform in same time as steel during hot rolling and therefore after rolling, these inclusions are perfectly elongated, and thick very low which avoids any breakage problem during a wire drawing operation.
  • SiO 2 content is less than 30%, the viscosity of the oxide inclusions is too low and the growth mechanism of oxide crystals is not inhibited. If SiO 2 is greater than 65%, very hard harmful particles of silica are formed in the form of trydimite or christobalite or quartz.
  • the MnO content between 5% and 40% makes it possible to greatly lower the softening point of the mixture of oxides containing in particular SiO 2 , CaO, Al 2 O 3 , and promotes the creation of inclusions which remain in a state vitreous under the rolling conditions of the steel according to the invention.
  • crystals of MnO-Al 2 O 3 or of mullite are formed.
  • the CaO content is greater than 30%, crystals of CaO-SiO 2 or (Ca, Mn) O-SiO 2 are formed .
  • crystals of MgO are formed; 2MgO-SiO 2 ; MgO-SiO 2 ; Al 2 O 3 -MgO, which are extremely hard phases.
  • Al 2 O 3 is less than 3%, wollastonite crystals are formed and when Al 2 O 3 is greater than 25%, crystals of mullite, anorthite, corundum and spinels, especially of the Al 2 type, appear O 3 -MgO or Al 2 O 3 -Cr 2 O 3 -MgO-MnO or alternatively of aluminates of the CaO-6Al 2 O 3 or CaO-2Al 2 O 3 or CaO-Al 2 O 3 type , or of gehlenite .
  • Oxides and sulfides inclusions are generally considered harmful with regard to the properties of use in the in the field of fine wire drawing and in the field of holding fatigue, in particular, in bending and / or torsion.
  • a form factor which is the ratio of length to thickness.
  • the form factor of inclusions in the wires can reach 10 or 20 and as a result, the thickness of the inclusion is extremely small.
  • the inclusive characteristics are materialized by the fact, on a surface of 1000 mm 2 sampled from wire rod with a diameter greater than or equal to 5 mm of less than 5 inclusions of oxides with a thickness of more than 10 ⁇ m.
  • the sulfide inclusions are, in number, less than 10 having a thickness of more than 5 ⁇ m, for an area of 1000 mm 2 .
  • the wire according to the invention can be used, in its hardened state by work hardening due to wire drawing, or else after heat treatment of aging between 300 ° C and 550 ° C, which is likely to harden it again by precipitation of copper epsilon, for the manufacture, by for example, springs or reinforcements of tires.
  • a softening annealing It can also undergo, at the final diameter, a softening annealing and be used for making various objects such as woven threads or knitted, woven hoses, filters, etc.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Steel (AREA)
  • Ropes Or Cables (AREA)
  • Metal Extraction Processes (AREA)
  • Yarns And Mechanical Finishing Of Yarns Or Ropes (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Preventing Corrosion Or Incrustation Of Metals (AREA)
EP98400241A 1997-02-18 1998-02-05 Acier inoxydable pour l'élaboration de fil tréfilé notamment de fil de renfort de pneumatique et procédé de realisation dudit fil Expired - Lifetime EP0859064B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
FR9701858A FR2759709B1 (fr) 1997-02-18 1997-02-18 Acier inoxydable pour l'elaboration de fil trefile notamment de fil de renfort de pneumatique et procede de realisation dudit fil
FR9701858 1997-02-18

Publications (2)

Publication Number Publication Date
EP0859064A1 EP0859064A1 (fr) 1998-08-19
EP0859064B1 true EP0859064B1 (fr) 2003-05-02

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EP98400241A Expired - Lifetime EP0859064B1 (fr) 1997-02-18 1998-02-05 Acier inoxydable pour l'élaboration de fil tréfilé notamment de fil de renfort de pneumatique et procédé de realisation dudit fil

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US (1) US6440579B1 (id)
EP (1) EP0859064B1 (id)
JP (1) JPH10226844A (id)
KR (1) KR19980071473A (id)
CN (1) CN1080773C (id)
AT (1) ATE239098T1 (id)
AU (1) AU734559B2 (id)
BR (1) BR9800640A (id)
CA (1) CA2229693C (id)
DE (1) DE69813923T2 (id)
ES (1) ES2198034T3 (id)
FR (1) FR2759709B1 (id)
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RU2530603C1 (ru) * 2013-08-29 2014-10-10 Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Нижегородский государственный технический университет им. Р.Е. Алексеева", НГТУ Способ изготовления горячекатаного проката под холодную объемную штамповку крепежных изделий
JP6146908B2 (ja) * 2013-10-09 2017-06-14 日本冶金工業株式会社 表面性状に優れたステンレス鋼とその製造方法
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EP0859064A1 (fr) 1998-08-19
ATE239098T1 (de) 2003-05-15
BR9800640A (pt) 1999-09-14
JPH10226844A (ja) 1998-08-25
CA2229693C (fr) 2008-12-30
FR2759709B1 (fr) 1999-03-19
DE69813923T2 (de) 2004-02-26
CA2229693A1 (fr) 1998-08-18
AU5302898A (en) 1998-08-20
CN1199782A (zh) 1998-11-25
ID19904A (id) 1998-08-20
ZA981116B (en) 1998-08-20
PT859064E (pt) 2003-08-29
DE69813923D1 (de) 2003-06-05
FR2759709A1 (fr) 1998-08-21
CN1080773C (zh) 2002-03-13
AU734559B2 (en) 2001-06-14
TW409080B (en) 2000-10-21
KR19980071473A (ko) 1998-10-26
US6440579B1 (en) 2002-08-27
ES2198034T3 (es) 2004-01-16

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