EP0218167B1 - High tensile strength drawn steel wire with improved ductility - Google Patents

High tensile strength drawn steel wire with improved ductility Download PDF

Info

Publication number
EP0218167B1
EP0218167B1 EP86113353A EP86113353A EP0218167B1 EP 0218167 B1 EP0218167 B1 EP 0218167B1 EP 86113353 A EP86113353 A EP 86113353A EP 86113353 A EP86113353 A EP 86113353A EP 0218167 B1 EP0218167 B1 EP 0218167B1
Authority
EP
European Patent Office
Prior art keywords
weight
steel wire
kgf
steel
wire
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
Application number
EP86113353A
Other languages
German (de)
English (en)
French (fr)
Other versions
EP0218167A1 (en
Inventor
Toshihiko Dainigijutsukenkyusho Takahashi
Yoshiuki Dainigijutsukenkyusho Asano
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Original Assignee
Nippon Steel Corp
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority claimed from JP21497785A external-priority patent/JPH0248605B2/ja
Priority claimed from JP21477185A external-priority patent/JPS6277442A/ja
Priority claimed from JP60214770A external-priority patent/JPS6277441A/ja
Application filed by Nippon Steel Corp filed Critical Nippon Steel Corp
Publication of EP0218167A1 publication Critical patent/EP0218167A1/en
Application granted granted Critical
Publication of EP0218167B1 publication Critical patent/EP0218167B1/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Images

Classifications

    • 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 drawn steel wire having excellent ductility, and to a method of producing such a steel wire.
  • hard drawn steel wires which are used as steel wire for ropes, as tire reinforcing steel wire, as optical fiber cable reinforcing steel wire or as steel wire for suspension bridges, it is increasingly needed to strengthen the wires.
  • JP-A 57 210 916 discloses a high strength steel wire for a spring which is said to have superior bending and twisting characteristics. According to JP-A 57 210 916 compressive residual stress is produced in the surface layer of the wire by a liquid honing or shot peening effect and further compressive residual stress is applied to the surface layer of the wire by means of a wire brushing device after a cold drawing stage.
  • DE-C 747 761 describes a method of improving the durability of wire springs in which the wire surface is compressed before coiling the wire into spring. It may be assumed that the compression is done by rolling.
  • GB-A 531 017 discloses a method of increasing the strength of a steel or steel alloy wire and its resistance to fatigue by subjecting the wire, as a final operation in its manufacture, to a continuous bombardment with round metal shot or metal globules.
  • GB-A 531 017 it is also mentioned that it is already known to surface harden steel articles by subjecting them to bombardment by a stream of metal shot.
  • a steel wire of the present invention contains the following chemical components in amounts 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% Si is contained in a steel wire.
  • Mn is contained to assure hadenability 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% N thereof a deterioration in the ductility is apparent.
  • the thus-composed steel wire of the present invention optionally 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 AI, 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 AI, 0.001 to 0.1% of Ti, '0.001
  • Cr, Mo, W, Cu, Ni and Co are incorporated for the purpose of increasing the strength 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 to of at least 130 kgf/mm 2 , since, if the strength is less than 130 kgf/mm 2 , 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 a + 23) and (0.35 ⁇ + 28) kgf/mm 2 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 observed 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 fracture 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 cuck- ing 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 circumferential 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/mm 2 , respectively.
  • the lower limit of the residual compression stress to be applied to the surface of steel wire was set at (0.05 a + 23) kgf/mm 2 . This value of course changes as the strength of the wire 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 thereby occur 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 deformation 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 appear 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 deformation 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 deforming its surface such as to impart a strain of between 0.2 and 10% in the following manner.
  • 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 deform the surface of the steel wire.
  • This surface deformation may be conducted immediately 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 surface of the steel wire is deformed 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 a + 23) and the maximum values (0.35 a + 28) of residual compression stresses which can be applied to the surfaces of the 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 100,000 km.
  • Delayed fracture hours refer to the hours to fracture of steel wires when subjected to a tensile stress of 80 kgf/mm 2 in a solution of 0.1 N 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 mm 2 . 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/mm 2 in rotary bending fatigue tests conducted in a 3% NaCI 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% NaCi.
  • 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/mm 2 and composed of the same chemical components.
  • the steel wire of No. 1 had a residual compression stress of 112 kgf/mm 2 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/mm 2 , 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 respectively having diameters of 2.6 mm and 4.5 mm, tensile strengths of 168 kgf/mm 2 and 196 kgf/mm 2 , and residual compression stresses of 50 kgf/mm 2 and 83 kgf/mm 2 . 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/mm 2 , and the same composition.
  • the steel wire of test No. 9 had a residual compression stress of 87 kgf/mm 2 , 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/mm 2 , 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/mm 2 and a residual compression stress of 60 kgf/mm 2.
  • 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/mm 2 and which are composed of the same components.
  • the steel wire of No. 12 had a residual compression stress of 65 kgf/mm 2 , while that of No. 13 was 130 kgf/mm 2.
  • 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/mm 2 and 179 kgf/mm 2 and residual compression stresses of 45 kgf/mm 2 and 41 kgf/mm 2 , 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/mm 2 which were composed of the same components.
  • the steel wire of No. 16 had a residual compression stress of 41 kgf/mm 2 , and showed an abnormal fracture ratio of 5%.
  • Nos. 17 and 18 had a residual tensile stress of 25 kgf/mm z 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/mm 2 and 184 kgf/mm 2 and residual compression stresses of 78 kgf/mm 2 and 50 kgf/mm 2 . 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/mm 2 and 258 kgf/mm 2 , and residual compression stresses of 60 kgf/mm 2 and 72 kgf/mm 2 . 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/mm 2 , and showed an abnormal fracture ratio of 5%, while the steel wire of No. 31 had a residual tensile strength of 50 kgf/mm 2 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/mm 2 and a residual compression stress of 65 kgf/mm 2.
  • 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/mm 2 , which were composed of the same ingredients.
  • the steel wire 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/mm 2 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/mm 2 and 238 kgf/mm 2 and residual compression stresses of 50 kgf/mm 2 and 69 kgf/mm 2 .
  • 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/mm 2 ,185 kgf/mm 2 , 221 kgf/mm 2 and 260 kgf/mm 2 , and residual compression stresses of 75 kgf/mm2, 50 kgf/mm2, 40 kgf/mm 2 and 80 kgf/mm 2 . In all cases, the abnormal fracture 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/mm 2 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/mm 2 , 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 same compositions.
  • the steel wire of No. 49 had a residual compression stress of 86 kgf/mm 2 , and showed an abnormal fracture ratio of 0, which represents excellent ductility.
  • a residual tensile stress as high as 43 kgf/mm 2 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.

Landscapes

  • 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 High tensile strength drawn steel wire with improved ductility Expired - Lifetime EP0218167B1 (en)

Applications Claiming Priority (6)

Application Number Priority Date Filing Date Title
JP21497785A JPH0248605B2 (ja) 1985-09-30 1985-09-30 Kokyodo*koenseikosennoseizoho
JP214977/85 1985-09-30
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
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

Publications (2)

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

Family

ID=27329662

Family Applications (1)

Application Number Title Priority Date Filing Date
EP86113353A Expired - Lifetime EP0218167B1 (en) 1985-09-30 1986-09-29 High tensile strength drawn steel wire with improved ductility

Country Status (3)

Country Link
EP (1) EP0218167B1 (ko)
KR (1) KR910003978B1 (ko)
DE (1) DE3675874D1 (ko)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0516857A1 (en) * 1990-11-19 1992-12-09 Nippon Steel Corporation High-strength ultrafine steel wire with excellent workability in stranding, and process and apparatus for producing the same
EP1036851A1 (en) * 1997-11-06 2000-09-20 Sumitomo Electric Industries, Ltd. High fatigue-strength steel wire and spring, and processes for producing these
CN101909435A (zh) * 2008-01-18 2010-12-08 贝卡尔特股份有限公司 具有高抗拉强度钢丝的水产养殖网

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5244626A (en) * 1991-04-21 1993-09-14 A. Finkl & Sons Co. Hot work die block
EP0611669A1 (en) * 1993-02-16 1994-08-24 N.V. Bekaert S.A. High-strength bead wire
EP1063313B1 (en) * 1997-08-28 2008-04-09 Sumitomo Electric Industries, Ltd. Steel wire and method of manufacturing the same
JP3435112B2 (ja) * 1999-04-06 2003-08-11 株式会社神戸製鋼所 耐縦割れ性に優れた高炭素鋼線、高炭素鋼線用鋼材およびその製造方法
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
KR101860246B1 (ko) 2014-02-06 2018-05-21 신닛테츠스미킨 카부시키카이샤 강선
KR101861456B1 (ko) 2014-02-06 2018-05-28 신닛테츠스미킨 카부시키카이샤 필라멘트
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
CN110055392B (zh) * 2019-05-27 2020-08-07 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
CN110157988B (zh) * 2019-06-27 2020-10-27 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

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR678070A (fr) * 1928-07-09 1930-03-18 Procédé et dispositif pour augmenter la résistance d'éléments de construction métalliques aux efforts engendrés par les vibrations
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

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
Herstellung von Stahldraht , Teil 1 ,pages 187,225,257-260, Verein Deutscher Eisenhüttenleute , 1969 *

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0516857A1 (en) * 1990-11-19 1992-12-09 Nippon Steel Corporation High-strength ultrafine steel wire with excellent workability in stranding, and process and apparatus for producing the same
EP0516857A4 (en) * 1990-11-19 1993-05-26 Nippon Steel Corporation High-strength ultrafine steel wire with excellent workability in stranding, and process and apparatus for producing the same
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
EP1036851A1 (en) * 1997-11-06 2000-09-20 Sumitomo Electric Industries, Ltd. High fatigue-strength steel wire and spring, and processes for producing these
EP1036851A4 (en) * 1997-11-06 2001-01-17 Sumitomo Electric Industries STEEL WIRE AND HIGH FATIGUE RESISTANCE SPRING AND METHODS OF MANUFACTURE
CN101909435A (zh) * 2008-01-18 2010-12-08 贝卡尔特股份有限公司 具有高抗拉强度钢丝的水产养殖网
CN101909435B (zh) * 2008-01-18 2012-12-19 贝卡尔特股份有限公司 具有高抗拉强度钢丝的水产养殖网
US8534227B2 (en) 2008-01-18 2013-09-17 Nv Bekaert Sa Aquaculture net with high-tensile steel wires

Also Published As

Publication number Publication date
EP0218167A1 (en) 1987-04-15
KR870003227A (ko) 1987-04-16
DE3675874D1 (de) 1991-01-10
KR910003978B1 (ko) 1991-06-17

Similar Documents

Publication Publication Date Title
EP0218167B1 (en) High tensile strength drawn steel wire with improved ductility
EP0144811A2 (en) Improved steel wire with high tensile strength
EP0201997A2 (en) High strength and toughness steel bar, rod and wire and the process of producing the same
JP2609387B2 (ja) 高強度高靭性極細鋼線用線材、高強度高靭性極細鋼線、および該極細鋼線を用いた撚り製品、並びに該極細鋼線の製造方法
JP3246210B2 (ja) 高強度高靭性溶融めっき鋼線およびその製造方法
JP2682645B2 (ja) オイルテンパー硬引鋼線ばね及びその製造方法
WO1999011836A1 (fr) Fil d'acier et procede de production de ce fil
CA1309323C (en) Oil quench hardening and tempering and hard drawn steel wire of shaped section and process for producing the same
JP3445674B2 (ja) 耐捻回割れ性に優れた高強度鋼線
JP3725576B2 (ja) 高強度亜鉛めっき鋼線の製造方法
JP3267833B2 (ja) 疲労特性の優れた高強度極細鋼線およびその製造方法
JPS6152348A (ja) 高性能炭素鋼線
JPH0248605B2 (ja) Kokyodo*koenseikosennoseizoho
JP2001220649A (ja) 延性及び疲労特性の優れた高強度極細鋼線
JP3299857B2 (ja) 疲労特性の優れた高強度極細鋼線およびその製造方法
JP2593207B2 (ja) ゴム製品補強用高強力鋼線およびスチールコード
JP3061918B2 (ja) 疲労特性の優れたスチールコードの製造方法
JP3036393B2 (ja) 高強度高靭性溶融めっき鋼線、及びその製造方法
JP2862206B2 (ja) 高強度ｐｃ鋼より線およびその製造方法
JP3479724B2 (ja) ゴム製品補強用金属線
JP3169454B2 (ja) 高強度鋼線とその製造法
JP3539866B2 (ja) 疲労性に優れた鋼線およびその製造方法
JP3539865B2 (ja) 疲労性に優れた鋼線およびその製造方法
JPS63179018A (ja) 延性の優れた超高張力鋼線の製造方法
JPH0366386B2 (ko)

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): BE DE FR

17P Request for examination filed

Effective date: 19870831

17Q First examination report despatched

Effective date: 19880803

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): BE DE FR

REF Corresponds to:

Ref document number: 3675874

Country of ref document: DE

Date of ref document: 19910110

ET Fr: translation filed
K2C2 Correction of patent specification (partial reprint) published

Effective date: 19901128

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed
PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: FR

Payment date: 19990909

Year of fee payment: 14

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 19991001

Year of fee payment: 14

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: BE

Payment date: 19991119

Year of fee payment: 14

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20000930

BERE Be: lapsed

Owner name: NIPPON STEEL CORP.

Effective date: 20000930

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20010531

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20010601

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST