EP0218167A1 - Fil d'acier tréfilé à haute résistance à la rupture et à ductilité modifiée - Google Patents

Fil d'acier tréfilé à haute résistance à la rupture et à ductilité modifiée Download PDF

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Publication number
EP0218167A1
EP0218167A1 EP86113353A EP86113353A EP0218167A1 EP 0218167 A1 EP0218167 A1 EP 0218167A1 EP 86113353 A EP86113353 A EP 86113353A EP 86113353 A EP86113353 A EP 86113353A EP 0218167 A1 EP0218167 A1 EP 0218167A1
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EP
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Prior art keywords
weight
steel wire
kgf
steel
ductility
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EP86113353A
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German (de)
English (en)
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EP0218167B1 (fr
Inventor
Toshihiko Dainigijutsukenkyusho Takahashi
Yoshiuki Dainigijutsukenkyusho Asano
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Nippon Steel Corp
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Nippon Steel Corp
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Priority claimed from JP21497785A external-priority patent/JPH0248605B2/ja
Priority claimed from JP60214770A external-priority patent/JPS6277441A/ja
Priority claimed from JP21477185A external-priority patent/JPS6277442A/ja
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Publication of EP0218167A1 publication Critical patent/EP0218167A1/fr
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Publication of EP0218167B1 publication Critical patent/EP0218167B1/fr
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    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
    • 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
    • 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

Definitions

  • the present invention relates to a high tensile strength steel wire having excellent ductility.
  • an objective of the present inven­tion is to provide a steel wire which has excellent ductility.
  • a steel wire of the present invention contains the following chemical components in amounts described below for the reasons described below.
  • Si is added because it is capable of setting a solid solution hardening, and the amount employed is limited to 2.0% or less, since the ductility becomes decreased when over 2% is contained in a steel wire.
  • Mn is contained to assure hardenability and fix S as MnS, and the amount thereof is set at between 0.2 and 2.0%, since less than 0.2% Mn is not capable of sufficiently fixing S and the hardenability thereof does not increase with a content of over 2% Mn.
  • N is contained in an amount of 0.01% or less, since with a content of over 0.01% thereof a deterioration in the ductility is apparent.
  • the thus-composed steel wire of the present invention contains, in addition to the ingredients described above, at least one ingredient selected from group (A) consisting of 0.05 to 3% of Cr, 0.01 to 1% of Mo, 0.01 to 1% of W, 0.05 to 3% of Cu, 0.1 to 5% of Ni and 0.1 to 5% of Co, and/or at least one ingredient selected from group (B) consisting of 0.001 to 0.1% of Al, 0.001 to 0.1% of Ti, 0.001 to 0.1% of Nb, 0.001 to 0.1% of V, 0.0003 to 0.05% of B, 0.001 to 0.1% of Mg and 0.001 to 0.1% of Ca.
  • group (A) consisting of 0.05 to 3% of Cr, 0.01 to 1% of Mo, 0.01 to 1% of W, 0.05 to 3% of Cu, 0.1 to 5% of Ni and 0.1 to 5% of Co
  • group (B) consisting of 0.001 to 0.1% of Al, 0.001 to 0.1% of Ti, 0.001 to 0.1% of
  • Cr, Mo, W, Cu, Ni and Co are incorporated for the purpose of increasing the stength and corrosion resistance. They are not effective if added in amounts of less than 0.05%, 0.01%, 0.01%, 0.05%, 0.1% and 0.1%, respectively. The lower limit of the specified amounts thereof are therefore set at 0.05%, 0.01%, 0.01%, 0.05%, 0.1% and 0.1%, respectively.
  • Cr, Mo, W, Cu, Ni and Co are incorporated in amounts which are less than or equal to 3%, 1%, 1%, 3%, 5% and 5%, respectively. This is because when the content exceeds these amounts, the ductility of the steel wire is lowered, while the increase in strength and corrosion resistance is saturated. It is preferable for the total amount of these elements to be set at 7% or less from the viewpoint of good ductility.
  • Al, Ti, Nb, V, B, Mg and Ca are added in the steel wire for the purpose of increasing the ductility thereof by fixing N and S. Their effects are not apparent, however, if added in amounts which are less than 0.001%, 0.001%, 0.001%, 0.0003%, 0.001% and 0.001%, respectively. The amounts thereof are therefore set to be at least 0.001%, 0.001%, 0.001%, 0.0003%, 0,001% and 0.001%, respectively.
  • Al, Ti, Nb, V, B, Mg and Ca are added in amounts which are over 0.1%, 0.1%, 0.1%, 0.1%, 0.05%, 0.1% and 0.1%, respectively, the ductility of the steel wire is decreased due to the resulting nitride and sulfide of these elements, while their respective effects are saturated.
  • the amounts thereof to be added are therefore set to be no more than 0.1%, 0.1%, 0.1%, 0.05%, 0.1% and 0.1%, respectively.
  • the total amount of these elements is preferably set at 0.2% at most to ensure the quality in terms of ductility.
  • the steel wire of the present invention has a strength of at least 130 kgf/mm2, since, if the strength is less than 130 kgf/mm2, the ductility does not increase even if there is a residual compression stress on the surface of the steel wire.
  • the steel wire according to the present invention has a residual compression stress of between (0.05 ⁇ + 23) and (0.35 ⁇ + 28) kgf/mm2 on the surface thereof, depending on its strength ⁇ , for the reasons described below.
  • the ductility of steel wire is generally deter­mined by tensile, torsion and bending tests, based on such results as the elongation and reduction of area observed in the tensile test, and the number of turns (torsion number) to fracture and the mode of that fracture ovserved in the torsion test.
  • Figs. 6 and 7 illustrate typical ways in which a steel wire 2 fractures in torsion tests.
  • Fig. 6 shows a normal mode of fracture in steel wire
  • Fig. 7 illustrates an abnormal fracture with cracks 11.
  • the abnormal type of fracutre occurs more frequently as the strength of the steel wire 2 increases. It is caused by the occurence of a longitudinal crack 11 as shown in Fig. 8, in which a wire is twisted by chuching with jig 12. It can therefore be considered that abnormal fracture means a deterioration in the ductility in the circumferential direction of the steel wire.
  • the present inventors have found that the duc­tility of steel wire in the cricumferential direction can be effectively increased by providing its surface with a residual compression stress, and they have studied the appropriate range for the application of this residual compression stress. More specifically, the present inventors set themselves the goal of reducing the incidence of abnormal fracture to 10% or less in torsion tests, and investigated how the level of the surface residual compression stress and the occurrence of abnormal fracture are related, using steel wire having tensile strengths of 152 kgf/mm2, 235 kgf/mm2, 316 kgf/mm2 and 377 kgf/mm2, respectively.
  • the lower limit of the residual compres­sion stress to be applied to the surface of steel wire was set at (0.05 ⁇ + 23) kgf/mm2. This value of course changes as its strength increases.
  • the residual tensile stress at the center of the steel wire increases in proportion to the residual compression stress on the surface, as is generally known, and cracks are thereby occured in the center which lead to abnormal fracture in torsion tests. This determines the maximum allowable residual compression stress which can be applied to the surface.
  • the present inventors have investigated how the occurrence of abnormal fracture due to cracks generated in the center of the steel wire is related to the level of residual compression stress which is applied, using four types of steel wires of the same strengths as those employed before.
  • the present inventors made a quantitative study to clear the appropriate range of application of strain by means of surface machining which is required to maintain the surface residual compression stress in the above-described range, and found that the strain should be limited to between 0.2 and 10% to do so. This is because, if the strain is less than 0.2%, residual compression stress within the above-described range cannot be applied on the surface. On the other hand, fine cracks are appeared on the surface of a steel wire and the ductility thereof tends to decrease when the strain exceeds 10%. Thus, the range of strain application by surface machining is restricted to between 0.2 and 10%.
  • the residual compression stress of the above-­described range is practically applied to the surface of a steel wire by surface machining it such as to impart a strain of between 0.2 and 10% in the following manner.
  • Fig. 1 illustrates a typical method of applying surface residual compression stress by rolling.
  • the steel wire 2 is unwound from a unwinding machine 6, is passed through a pinch roller 7, and is wound on a winding machine 8.
  • the pinch roller 7 is adapted to supply a tension to the steel wire 2.
  • the steel wire 2 is surface machined by a rolling machine 3 located between the pinch roller and the wind machine 8.
  • Fig. 2 shows the rolling jig 3 in detail. Strain is applied to the surface of the steel wire 2 by passing it between a plurality of spherical rollers 1 which are rotated by being rubbed against the passing steel wire. The amount of strain to be applied may be controlled by adjusting the rolling reduction of the rollers 1.
  • rollers of a disk-shaped configuration as shown in Figs. 3A, 3B and 4A, 4B may also be employed.
  • the rolling machine jig 3 may include more than one pair of rollers. This may be a more effective way of carrying out the present invention than employing just one pair of rollers.
  • the present invention may be carried out more effectively by transmitting the rotation of a motor 5 to the rolling machine 3 through a shaft 4 and rotating the rolling machine 3 about the steel wire 2. At this time, if the rollers employed are of a disk-like shape, the rollers are disposed at a certain angle relative to the steel wire 2.
  • Fig. 5 illustrates a typical method of applying a residual compression stress to the surface by shot peening a steel wire.
  • a shot 9 may be blasted through a pipe 10 by means of compressed air or by rotating the jig 3 about the steel wire so as to surface machine the steel wire.
  • This surface machining may be conducted immedi strictlyately after the steel wire comes out of the dies in the wire drawing process or at any time before completion of the final product. If the steel wire is surface machined after blueing or plating, however, it is preferable for the steel wire to be blued again at a temperature of 250°C or less so as to improve the stress relaxation.
  • the difference in hardness between the core and surface of the steel wire is set at 100 or less in vickers hardness. This is because if it exceeds 100, the steel wire may crack during rolling.
  • a steel wire of the present invention exhibits excellent characteristics in terms of fatigue, corrosion fatigue, delayed fracture, stress corrosion cracking or relaxation properties.
  • the steel wire of the present invention is capable of improving the durability or fatigue characteristics of these products.
  • Table 1 lists the compositions, diameters, tensile strengths of the steel wires employed in the examples, the minimum values (0.05 ⁇ + 23) and the maximum values (0.35 ⁇ + 28) of residual compression stresses which can be applied to the surfaces of steel wires which are determined in accordance with the present invention, the residual stresses existing on the surfaces of the steel wires employed in the examples, the results of tests for twisting, fatigue, corrosion fatigue, delayed fracture, and relaxation on these steel wires, and the results of a fatigue test conducted on products employing these steel wires.
  • the symbol + in the item for residual stress indicates that the residual stress is one of tension, while the symbol - means that the stress is one of compression.
  • Abnormal type fracture frequencies refer to occurrences of the abnormal type of fracture shown in Fig. 7 in the torsion tests conducted.
  • Fatigue limits indicate stresses at the fatigue limits observed in the rotary bending tests conducted.
  • Breakage ratios of cords in tires are those for cords employed in tires subjected to a load of 500 kg while running of 100,000 km.
  • Delayed fracture hours refer to the hours to fracture of steel wires when subjected to a tensile stress of 80 kgf/mm2 in a solution of 0.1N hydrochloric acid.
  • Fatigue limits of plastic plates refer to the bending fatigue limits observed in plastic plates having a thickness of 1 mm and a width of 10 mm reinforced by 100 steel wires per 1 mm2. These are expressed by the ratio of the measured value to that of No. 31 sample.
  • Corrosion fatigue lives represent the number of rotations to fracture of steel wires when subjected to a load of 20 kgf/mm2 in rotary bending fatigue tests conducted in a 3% NaCl solution.
  • Stress corrosion cracking hours represent the hours to fracture of steel wires when subjected to a tensile strength of 70 kgf/mm2 in a solution of 0.5% acetic acid + 5% NaCl.
  • Rope fatigue limits show the bending fatigue limits of ropes which conform to JIS No. 1.
  • the rope made from the steel wire shown in example no. 47 of this inven­tion was compared with one made from the steel wire of comparison example No. 48, and the fatigue limits of these ropes were expressed by the ratio of the measured value to that of No. 31 sample.
  • Tests Nos. 1 and 2 use steel wires having dia­meters of 0.2 mm and the tensile strengths of 332 kgf/mm2 and composed of the same chemical components.
  • the steel wire of No. 1 had a residual compression stress of 112 kgf/mm2 which was imparted by applying a strain of 1.2% by rolling, and showed an abnormal fracture ratio of 0 in the torsion test conducted.
  • the steel wire of test No. 2 had a residual tensile stress of 61 kgf/mm2, and showed an abnormal fracture rate of 100%. This shows that the steel wire of this invention is excellent in ductility.
  • the steel wire of this invention also exhibited excellent characteristics in terms of corrosion fatigue properties as well as durability when employed in a tire.
  • Tests Nos. 3 and 4 employed steel wires respec- tively having diameters of 2.6 mm and 4.5 mm, tensile strengths of 168 kgf/mm2 and 196 kgf/mm2, and residual compression stresses of 50 kgf/mm2 and 83 kgf/mm2. Both showed an abnormal fracture ratio of 0, and were excellent in ductility. For both wires, the residual compression stresses were imparted by applying strains of 0.3% and 0.9%, respectively, by shot peening.
  • Tests Nos. 5, 6, 7 and 8 used steel wires having compositions and residual stresses outside the scope of the present invention. Hence, these showed high rates of abnormal fracture and poor ductility.
  • Nos. 9 and 10 represent the tests employing steel wires having diameters of 0.25 mm, tensile strengths of 286 kgf/mm2, and the same composition.
  • the steel wire of test No. 9 had a residual compression stress of 87 kgf/mm2, and showed an abnormal fracture ratio of 5% in the torsion test conducted, while the steel wire of No. 10 had a residual tensile stress of 45 kgf/mm2, and therefore showed an abnormal fracture ratio of 95%. From these tests, it is clear that the steel wire according to the present invention has excellent ductility.
  • the residual compression stress was imparted to both steel wires by applying a strain of 6.2% by rolling.
  • Test No. 11 employed a steel wire having a dia­meter of 2.5 mm, a tensile strength of 205 kgf/mm2 and a residual compression stress of 60 kgf/mm2.
  • the steel wire showed an abnormal fracture ratio of 0, which shows that the ductility thereof was excellent.
  • the residual compres­sion stress was imparted by applying a strain of 1.0% by shot peening.
  • Tests Nos. 12 and 13 represent examples of steel wires having diameters of 0.6 mm and tensile strengths of 256 kgf/mm2 and which are composed of the same components.
  • the steel wire of No. 12 had a residual compression stress of 65 kgf/mm2, while that of No. 13 was 130 kgf/mm2. The latter was imparted its residual compression stress by applying a rolling strain of 12%.
  • the abnormal fracture ratio of No. 12 represented 5%, while that of No. 13 reached 70%.
  • the steel wire of the present invention thus proved to be excellent in ductility.
  • the residual compres­sion stress was imparted to the steel wire of example No. 12 by applying a strain of 0.3% through rolling.
  • Tests Nos. 14 and 15 employed a steel wire and a galvanized steel wire, respectively, which had diameters of 4.5 mm and 3.2 mm, tensile strengths of 195 kgf/mm2 and 1790 kgf/mm2 and residual compression stresses of 45 kgf/mm2 and 41 kgf/mm2, respectively. Both wires showed abnormal fracture ratio of 0, and proved to be excellent in ductility.
  • the residual compression stresses were imparted to the steel wires of Nos. 14 and 15 by applying a strain of 2.0% through rolling and a strain of 0.5% through shot peening, respectively.
  • Tests Nos. 16 to 18 concern the steel wires having diameters of 8 mm and tensile strengths of 152 kgf/mm2 which were composed of the same components.
  • the steel wire of No. 16 had a residual compression stress of 41 kgf/mm2, and showed an abnormal fracture ratio of 5%.
  • Nos. 17 and 18 had a residual tensile stress of 25 kg/mm2 and a residual compression stress of 18 kgf/mm2, respectively, and their abnormal fracture ratios respec­tively represented 60% and 45%.
  • the steel wires of the present invention thus proved to have excellent ductility.
  • the residual compression stresses were imparted to the steel wires of Nos. 16 and 18 by applying strains of 0.3% through shot peening and 0.8% through rolling, respectively.
  • the steel wire of the present invention also exhibited excellent characteristics in relaxation and delayed fracture properties.
  • Tests Nos. 19 and 20 employed steel wires respectively having diameters of 1.2 mm and 3.6 mm, tensile strengths of 220 kgf/mm2 and 184 kgf/mm2 and residual compression stresses of 78 kgf/mm2 and 50 kgf/mm2. Both exhibited abnormal fracture ratios of 5% and 0%, respec­tively, and proved to be excellent in ductility.
  • the residual compression stresses were imparted to both wires by applying strains of 0.5% and 3.2%, respectively, through rolling.
  • Nos. 21 to 27 represent comparison examples employing steel wires whose compositions and residual stresses are outside the scope of the present invention. Hence, both showed high abnormal fracture ratios and poor ductility.
  • Tests Nos. 28 and 29 used steel wires respectively having diameters of 2.0 mm and 0.8 mm, tensile strengths of 196 kgf/mm2 and 258 kgf/mm2, and residual compression stresses of 60 kgf/mm2 and 72 kgf/mm2. Abnormal fracture ratios for both wires showed 0 and 5%, respectively, and their ductilities proved to be excellent.
  • Tests Nos. 30 and 31 employed steel wires having diameters of 0.06 mm and tensile strengths of 408 kgf/mm2 which were composed of the same components.
  • the steel wire of No. 30 had a residual compression stress of 76 kgf/mm2, and showed an abnormal fracture ratio of 5%, while the steel wire of No. 31 had a residual tensile strength of 50 kgf/mm2 and the abnormal fracture ratio thereof therefore represented 100%.
  • Ductility of the steel wire in accordance with the present invention thus proved to be excellent. It also proved that the plastic plate reinforced by the steel wire according to the present invention had excellent fatigue property.
  • the residual compression stress was imparted by applying a strain of 0.2% through rolling.
  • Test No. 32 concerns a steel wire having a dia­meter of 5.5 mm, a tensile strength of 185 kgf/mm2 and a residual compression stress of 65 kgf/mm2.
  • the employed wire showed an abnormal fracture ratios of 0, and proved to be excellent in ductility.
  • Tests Nos. 33 and 34 represent examples employing steel wires having diameters of 3.2 mm and tensile strengths of 146 kgf/mm2 which were composed of the same ingredients.
  • the steel wrie of No. 33 had a residual compression stress of 45 kgf/mm2, and showed an abnormal fracture ratio of 0.
  • the steel wire of No. 34 had a residual compression stress as high as 93 kgf/mm2 which was imparted thereto by apply­ing a rolling strain of 15%, and hence showed an abnormal fracture ratio of 35%. This shows that the steel wire of the present invention was excellent in ductility.
  • Tests Nos. 35 and 36 used steel wires respec­tively having diameters of 3.2 mm and 0.3 mm, tensile strengths of 170 kgf/mm2 and 238 kgf/mm2 and residual compression stresses of 50 kgf/mm2 and 69 kgf/mm2. Abnormal fracture ratios for both steel wires represented 0 and 5%, respectively, and both proved to have excellent ductility. Residual compression stresses were imparted to the steel wires of Nos. 32, 33, 35 and 36 by applying strains of 0.8%, 0.2%, 2.0% and 1.2% through shot peening, respectively.
  • Tests Nos. 37 to 42 represent comparison examples employing steel wires having compositions and residual stresses outside the scope of the present invention.
  • the abnormal fracture ratios of these steel wires were therefore high, and their ductilities were poor.
  • An exces­sively high residual compression stress was imparted to the steel wire of No. 40 by applying a strain as high as 10.8% through rolling.
  • Tests Nos. 43 to 46 employed steel wires respec­tively having diameters of 2.0 mm, 3.6 mm, 1.2 mm and 0.35 mm, tensile strengths of 195 kgf/mm2, 185 kgf/mm2, 221 kgf/mm2 and 260 kgf/mm2, and residual compression stresses of 75 kgf/mm2, 50 kgf/mm2, 40 kgf/mm2 and 80 kgf/mm2. In all cases, the abnormal fracutre ratios represented 0, and the ductilities proved to be excellent.
  • Tests Nos. 47 and 48 used steel wires having diameters of 3.6 mm tensile strengths of 228 kgf/mm2 and the same compositions.
  • the steel wire of No. 47 had a residual compression stress of 63 kgf/mm2, showed an abnormal fracture ratio of 0 and proved to be excellent in ductility.
  • the steel wire of No. 48 had a residual tensile stress of 30 kgf/mm2, and the abnormal fracture ratio thereof represented 75%. This shows that its ductility was poor.
  • the steel wire of No. 47 proved also to be excellent in stress corrosion cracking property.
  • the rope made of this steel wire showed excellent characteristics in fatigue properties.
  • the residual compression stresses were imparted to the steel wires of Nos. 43, 44, 45, 46 and 47 by applying rolling strains of 3.0%, 0.6%, 7.8%, 1.0% and 1.5%, respectively.
  • Tests Nos. 49 and 50 employed steel wires having diameters of 0.6 mm, tensile strengths of 290 kgf/mm2 and the smae compositions.
  • the steel wire of No. 49 had a residual compression stress of 86 kgf/mm2, and showed an abnormal fracture ratio of 0, which represents excellent ductility.
  • a residual tensile stress as high as 43 kgf/mm2 was imparted to the steel wire of No. 50, and the abnormal fracture ratio thereof rose as high as 90%. It is clear that the steel wire of No. 50 had poor ductility.
  • the steel wire of No. 49 also exhibited excellent characteristics in fatigue properties.
  • the residual compression stress was imparted to the wire of No. 49 by applying a strain of 0.7% through shot peening.
  • Tests Nos. 51 to 55 represent comparison examples employing steel wires having compositions and residual stresses outside the scope of the present invention.
  • the abnormal fracture ratios of these steel wires were there­fore high with poor ductility.
  • the steel wire of No. 54 was subjected to a strain as high as 11.6% by rolling, and had a large residual compression stress.
  • the difference in the hardnesses of the core and the surface of each steel wire according to the present invention represented a Vickers hardness of less than 100.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Heat Treatment Of Steel (AREA)
EP86113353A 1985-09-30 1986-09-29 Fil d'acier tréfilé à haute résistance à la rupture et à ductilité modifiée Expired - Lifetime EP0218167B1 (fr)

Applications Claiming Priority (6)

Application Number Priority Date Filing Date Title
JP214977/85 1985-09-30
JP21497785A JPH0248605B2 (ja) 1985-09-30 1985-09-30 Kokyodo*koenseikosennoseizoho
JP214770/85 1985-09-30
JP60214770A JPS6277441A (ja) 1985-09-30 1985-09-30 延性にすぐれた高張力鋼線
JP214771/85 1985-09-30
JP21477185A JPS6277442A (ja) 1985-09-30 1985-09-30 延性にすぐれた高張力鋼線

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Publication Number Publication Date
EP0218167A1 true EP0218167A1 (fr) 1987-04-15
EP0218167B1 EP0218167B1 (fr) 1990-11-28

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EP (1) EP0218167B1 (fr)
KR (1) KR910003978B1 (fr)
DE (1) DE3675874D1 (fr)

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DE4302635A1 (fr) * 1992-02-25 1993-08-26 Finkl & Sons Co
EP0611669A1 (fr) * 1993-02-16 1994-08-24 N.V. Bekaert S.A. Tringle de talon de pneumatique haute résistance
EP1063313A1 (fr) * 1997-08-28 2000-12-27 Sumitomo Electric Industries, Ltd. Fil d'acier et procede de production de ce fil
DE10017069B4 (de) * 1999-04-06 2005-09-01 Kabushiki Kaisha Kobe Seiko Sho, Kobe Unlegierter Stahldraht mit ausgezeichneter Beständigkeit gegen Rißbildung in Längsrichtung, ein Stahlprodukt für denselben und Verfahren zur Herstellung desselben
WO2009089970A1 (fr) * 2008-01-18 2009-07-23 Nv Bekaert Sa Filet pour aquaculture comportant des fils d'acier à haute résistance à la traction
US10072317B2 (en) 2014-02-06 2018-09-11 Nippon Steel & Sumitomo Metal Corporation Filament
US10081846B2 (en) 2014-02-06 2018-09-25 Nippon Steel & Sumitomo Metal Corporation Steel wire
CN110055392A (zh) * 2019-05-27 2019-07-26 武汉钢铁有限公司 一种抗拉强度≥2500Mpa高韧性桥索钢及其制备方法
CN110157988A (zh) * 2019-06-27 2019-08-23 锦州金科高新技术发展有限责任公司 一种高纯、均质稀土冷轧辊用钢合金材料及制备方法
CN110184537A (zh) * 2019-05-24 2019-08-30 武汉钢铁有限公司 一种低碳含钴高强度桥索钢及生产方法

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US5240520A (en) * 1990-11-19 1993-08-31 Nippon Steel Corporation High strength, ultra fine steel wire having excellent workability in stranding and process and apparatus for producing the same
JP3859331B2 (ja) * 1997-11-06 2006-12-20 住友電工スチールワイヤー株式会社 高疲労強度鋼線およびばねとそれらの製造方法
KR100985357B1 (ko) * 2007-06-19 2010-10-04 주식회사 포스코 피로수명이 우수한 고강도, 고인성 스프링, 상기 스프링용강선재와 강선 및 상기 강선과 스프링의 제조방법
KR101455453B1 (ko) * 2012-05-30 2014-10-27 현대제철 주식회사 강재 및 이를 이용한 강 제품 제조 방법

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GB531017A (en) * 1939-07-08 1940-12-27 Richard Johnson & Nephew Ltd Improvements relating to the manufacture of wire
DE747761C (de) * 1941-07-12 1944-10-13 Otto Foeppl Verfahren zur Herstellung von dauerfesten Schraubenfedern
GB712125A (en) * 1950-10-13 1954-07-21 Johannes Schwarz Process for increasing the strength of unalloyed or alloyed steel bars and tubes

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DE4302635A1 (fr) * 1992-02-25 1993-08-26 Finkl & Sons Co
DE4302635C2 (de) * 1992-02-25 1999-05-06 Finkl & Sons Co Verwendung eines niedrig legierten Stahls
EP0611669A1 (fr) * 1993-02-16 1994-08-24 N.V. Bekaert S.A. Tringle de talon de pneumatique haute résistance
US7255758B2 (en) 1997-08-28 2007-08-14 Sumitomo Electric Industries, Ltd. Steel wire and method of manufacturing the same
EP1063313A4 (fr) * 1997-08-28 2004-04-07 Sumitomo Electric Industries Fil d'acier et procede de production de ce fil
EP1063313A1 (fr) * 1997-08-28 2000-12-27 Sumitomo Electric Industries, Ltd. Fil d'acier et procede de production de ce fil
DE10017069B4 (de) * 1999-04-06 2005-09-01 Kabushiki Kaisha Kobe Seiko Sho, Kobe Unlegierter Stahldraht mit ausgezeichneter Beständigkeit gegen Rißbildung in Längsrichtung, ein Stahlprodukt für denselben und Verfahren zur Herstellung desselben
WO2009089970A1 (fr) * 2008-01-18 2009-07-23 Nv Bekaert Sa Filet pour aquaculture comportant des fils d'acier à haute résistance à la traction
US10072317B2 (en) 2014-02-06 2018-09-11 Nippon Steel & Sumitomo Metal Corporation Filament
US10081846B2 (en) 2014-02-06 2018-09-25 Nippon Steel & Sumitomo Metal Corporation Steel wire
CN110184537A (zh) * 2019-05-24 2019-08-30 武汉钢铁有限公司 一种低碳含钴高强度桥索钢及生产方法
CN110184537B (zh) * 2019-05-24 2020-10-30 武汉钢铁有限公司 一种低碳含钴高强度桥索钢及生产方法
CN110055392A (zh) * 2019-05-27 2019-07-26 武汉钢铁有限公司 一种抗拉强度≥2500Mpa高韧性桥索钢及其制备方法
CN110157988A (zh) * 2019-06-27 2019-08-23 锦州金科高新技术发展有限责任公司 一种高纯、均质稀土冷轧辊用钢合金材料及制备方法

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KR910003978B1 (ko) 1991-06-17
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EP0218167B1 (fr) 1990-11-28

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