EP3056580A1 - Walzdraht, hypereutektoider bainitstahl draht und verfahren zur herstellung davon - Google Patents

Walzdraht, hypereutektoider bainitstahl draht und verfahren zur herstellung davon Download PDF

Info

Publication number
EP3056580A1
EP3056580A1 EP14851484.7A EP14851484A EP3056580A1 EP 3056580 A1 EP3056580 A1 EP 3056580A1 EP 14851484 A EP14851484 A EP 14851484A EP 3056580 A1 EP3056580 A1 EP 3056580A1
Authority
EP
European Patent Office
Prior art keywords
wire rod
bath
wire
molten salt
salt bath
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.)
Withdrawn
Application number
EP14851484.7A
Other languages
English (en)
French (fr)
Other versions
EP3056580A4 (de
Inventor
Tatsusei TADA
Yukihiro Takahashi
Yoshitaka Nishikawa
Daisuke Hirakami
Toshiyuki Manabe
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 and Sumitomo Metal 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
Application filed by Nippon Steel and Sumitomo Metal Corp filed Critical Nippon Steel and Sumitomo Metal Corp
Publication of EP3056580A1 publication Critical patent/EP3056580A1/de
Publication of EP3056580A4 publication Critical patent/EP3056580A4/de
Withdrawn legal-status Critical Current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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • C21D1/44—Methods of heating in heat-treatment baths
    • C21D1/46—Salt baths
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/34—Methods of heating
    • C21D1/44—Methods of heating in heat-treatment baths
    • C21D1/48—Metal baths
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/607—Molten salts
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/54—Furnaces for treating strips or wire
    • C21D9/56—Continuous furnaces for strip or wire
    • C21D9/58—Continuous furnaces for strip or wire with heating by baths
    • 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • 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
    • 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
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite

Definitions

  • the present invention relates to a wire rod for a hypereutectoid bainite steel wire having excellent drawing properties and delayed fracture resistance, a hypereutectoid bainite steel wire which is manufactured from the wire rod, and a method for manufacturing thereof.
  • Wire rods are used as the material to make various machined parts, such as steel wire.
  • various mechanical parts hereinafter referred as final products
  • the wire rods are usually subjected to wire drawing and annealing.
  • the tensile strength of the final product is mainly affected by the chemical composition of the wire rod, in particular, by the C content of the wire rod.
  • the metal structure of the wire is transformed during annealing. Therefore, when the final product is manufactured by the process including annealing, the metal structure of the wire rod does not affect the tensile strength of the final product.
  • it is essential that the chemical composition of the wire rod correspond to the tensile strength which is required of the final product.
  • the tensile strength of the wire rod be minimized.
  • the machinability and drawing properties thereof are decreased.
  • a wire rod having high tensile strength has a high sensitivity to delayed fracture (fracture by the hydrogen embrittlement), breakages easily occur during manufacture, storage and transportation.
  • the C content of the wire rod is 0.8 mass% or more (that is, in a case where the wire rod is hypereutectoid steel, since the C content of the wire rod is higher than the eutectoid point)
  • the sensitivity to delayed fracture (the hydrogen embrittlement) of the wire rod increases.
  • the bundling conditions are relaxed, for example, such as reducing the power to bind the wire rod.
  • the bundling conditions are relaxed, the storage stability of the coil, the transportability of the coil, and safety and the like at the time of handling the coil are impaired.
  • Issues related to the delayed fracture and machinability can be solved by adjusting the chemical composition of the wire rod, for example, by decreasing the tensile strength of the wire rod by decreasing the C content.
  • the chemical composition of the wire rod correspond to the tensile strength which is required of the final product. Therefore, the adjustment of the chemical composition of the wire rod cannot be adopted as a means for preventing the delayed fracture.
  • the tensile strength of the wire rod can be decreased by changing the heat treatment conditions during manufacture the wire rod.
  • the metal structure of general hypereutectoid wire rod (the wire rod in which the C content is higher than the eutectoid point) mainly includes pearlite.
  • the method for manufacturing hypereutectoid wire rod according to the prior art includes a process of rolling the steel to obtain the wire rod and a process of cooling the wire rod. During cooling process, the metal structure of the wire rod becomes pearlite. In this manufacturing method, when the wire rod after rolling is heated to an austenite temperature region at first and then the wire rod is cooled at a relatively slow cooling rate, the tensile strength of the wire rod can be decreased.
  • the present inventors studied that an adjustment of the metal structure of the wire rod was adopted as a means of decreasing the tensile strength.
  • the metal structure of the wire rod does not affect the tensile strength of the final product.
  • General wire rods according to the prior art mainly includes the pearlite structure, and these wire rods are referred as the pearlite wire rods.
  • the wire rod including bainite as a main metal structure (bainite wire rod) has excellent drawing properties compared with the pearlite wire rod (for example, see the patent documents 1 to 7).
  • the tensile strength of the hypereutectoid bainite wire rod in which the C content is higher than the eutectoid point is lower than the tensile strength of the pearlite wire rod which includes the same C content with the bainite wire rod.
  • the present inventors found that the average tensile strength of the bainite wire rod in which the C content is 1.1% is lower 200MPa to 300MPa than the average tensile strength of the pearlite wire rod in which the C content is 1.1%.
  • the tensile strength of the wire rod can decrease, regardless of the tensile strength required of the final product after annealing (that is, regardless of the C content required for steel wire). Therefore, an improvement in both drawing properties and suppression of delayed fracture can be achieved.
  • the bainite wire rod has a problem that the tensile strength is easy to vary.
  • the state where the tensile strength of the wire rod is varied means the state where these measurements are varied, when the tensile strength is measured at a plurality of locations in a one wire rod.
  • the sensitivity to the delayed fracture hydrogen embrittlement
  • the tensile strength of the wire rod varies, since the workability of the wire rod varies, machining of the wire rod becomes difficult.
  • the patent documents 1 to 7 disclose the method for manufacturing the bainite wire rod.
  • the present inventors found that the tensile strength of the wire rod is greatly varied, when the bainite wire rod is manufactured based on the manufacturing methods specifically disclosed in these patent documents. Firstly, the present inventors cut the wire rod obtained by the above-described manufacturing method to a length of 3200 mm. Next, the present inventors made the eight test pieces having a length of 400 mm by dividing the wire rod into eight equal parts, and the tensile strength test was subjected to these test pieces. The difference between the maximum value and minimum value within the tensile strengths of these test pieces (hereinafter, referred as the variation in the tensile strength) was more than 100 N/mm 2 . On the other hand, as a result of studying by the present inventors, it was found that the wire rod in which the variation in the tensile strength is more than 50 N/mm 2 is difficult to use industrially.
  • the pearlite wire rod according to the prior art has high tensile strength, there is a problem that the delayed fracture easily occurs.
  • the amount of the proeutectoid cementite is increased. Therefore, it is not preferable.
  • An increase in the amount of the proeutectoid cementite deteriorates the machinability of the wire rod.
  • the bainite wire rod according to the prior art particularly, the hypereutectoid bainite wire rod in which the C content is higher than the eutectoid point has a problem that the tensile strength is easy to vary. The variation in the tensile strength increases the occurrence frequency of the delayed fracture and deteriorates the machinability.
  • the problem of the present invention is to decrease the tensile strength of the wire rod and increase the ductility of the wire rod in which the C content is higher than the eutectoid point in order to enhance the drawing properties and delayed fracture resistance of the wire rod by being the main metal structure of bainite. Furthermore, the problem of the present invention is to suppress variation in the tensile strength of the wire rod. Accordingly, the aim of the present invention is to provide a wire rod for solving these problems, the hypereutectoid bainite steel wire manufactured by using the wire rod, and the method for stably manufacturing them.
  • the present inventors found that the above-described problem can be solved by manufacturing the wire rods based on the manufacturing conditions that the bainite structure, which can achieve both the suppression of the proeutectoid cementite and the low strength of the wire rod, can be generated.
  • the wire rod which has the lower tensile strength and higher ductility compared with traditional pearlite wire rod and in which the variation in the tensile strength is small compared with the traditional bainite wire rod can be obtained.
  • the wire rod according to the present invention is bundled, or in the state where the wire rod according to the present invention is bundled, the generation of the breakage is suppressed.
  • the workability of the wire rod according to the present invention and the workability of the steel wire according to the present invention obtained by wire drawing the wire rod are favorable.
  • the wire rod having excellent drawing properties and delayed fracture resistance for the hypereutectoid bainite steel wire, the hypereutectoid bainite steel wire manufactured by using the wire rod, and the method for stably manufacturing them can be provided.
  • wire rod for hypereutectoid bainite steel wire having excellent drawing properties and delayed fracture resistance will be described.
  • this wire rod is simply referred to as "wire rod according to the present embodiment".
  • a wire rod according to the present embodiment includes, as a chemical composition, by mass%: C: more than 0.80% to 1.20%, Si: 0.10% to 1.50%, Mn: 0% to 1.00%, P: 0% to 0.02%, S: 0% to 0.02%, Cr: 0% to 1.00%, Ni: 0% to 1.00%, Cu: 0% to 1.00%, Mo: 0% to 0.50%, Ti: 0% to 0.20%, Nb: 0% to 0.20%, V: 0% to 0.20%, B: 0% to 0.0050%, Al: 0% to 0.10%, Ca: 0% to 0.05%; and a remainder including Fe and impurities; in which when eight test pieces having a length of 400 mm, which are obtained by dividing a wire rod having a length of 3200 mm into eight components having a same length, are manufactured, an average tensile strength TS of each test pieces satisfies a following equation 1, by N/mm 2 , a difference between the maximum value
  • [C] means C content in the wire rod by mass%
  • [TS] means the average tensile strength TS by N/mm 2 .
  • C is an element to enhance the hardenability and tensile strength of a wire rod. Enhancing the hardenability of the wire rod causes the main structure thereof to become bainite.
  • the C content is more than 0.80%, the required hardenability and tensile strength can be obtained.
  • the C content is more than 1.20%, proeutectoid cementite is generated and breaking easily occurs during wire drawing of the wire rod. Therefore, in order to suppress generation of proeutectoid cementite, the upper limit of the C content is set to 1.20%.
  • the lower limit of the C content may be set to 0.85%, 0.90% or 0.95%.
  • the lower limit of the C content may be set to 1.15%, 1.10% or 1.05%.
  • Si is an element which enhances the tensile strength of a wire rod.
  • Si is an element which functions as a deoxidizer.
  • the lower limit of the Si content is set to 0.10%.
  • Si promotes precipitation of proeutectoid ferrite in hypereutectoid steel.
  • the proeutectoid ferrite causes breaking during wire drawing of the wire rod.
  • Si deteriorates the working limit of wire drawing in hypereutectoid steel. Therefore, the upper limit of the Si content is set to 1.50%.
  • the lower limit of the Si content may be set to 0.15%, 0.20% or 0.25%.
  • the upper limit of the Si content may be set to 1.45%, 1.40% or 1.35%.
  • the lower limit of Mn content in the wire rod according to the present embodiment is 0%.
  • Mn has an effect for enhance the strength of the wire rod by enhancing hardenability of the wire rod.
  • Mn is an element acting as a deoxidizer as well as Si. Therefore, Mn may be contained in the wire rod if necessary.
  • the Mn content is more than 1.00%, the hardenability is improved in a place where Mn is segregated and the time until the transformation is completed becomes longer. That is, in this case, the hardenability is not uniform in the wire rod and martensite is generated in a place where the hardenability is high. Then, this martensite causes breaking during wire drawing.
  • the upper limit of the Mn content is required to be 1.00%.
  • the upper limit of the Mn content may be set to 0.90% or 0.80%.
  • the lower limit of Mn content is 0%, in order to obtain the above-described effect, the lower limit of the Mn content is preferably 0.20%, and more preferably 0.40%.
  • P and S are impurity elements.
  • the upper limits of the P content and S content are both 0.02%.
  • the upper limits of the P content and S content are both 0.01 %, and more preferably, the upper limits of the P content and S content are both 0.005%. Since the P content and S content are preferably as small as possible, the lower limits of the P content and S content are 0%. However, if the amounts of these elements are reduced to 0.001 % or less, the manufacturing cost of the wire rod increases. Therefore, it is usual for the lower limits of the P content and S content to be 0.001% in practical steel.
  • the wire rod according to the present embodiment may contain Cr, Ni, Cu, Mo, Ti, Nb, V, B, Al and Ca as appropriate within a range that does not inhibit the properties of the wire rod according to the present embodiment. However, it is not essential to contain these elements and the lower limits of the amounts of these elements are 0%.
  • Cr is an element to promote bainite transformation by improving the hardenability of wire rod.
  • time required for transformation from start to finish becomes longer and the heat treatment time to complete the bainite transformation is increased, thereby undesirable.
  • the upper limit of the Cr content is set to 1.00%.
  • the Cr content is preferably 0.50% or less, and more preferably 0.30% or less.
  • the lower limit of the Cr content is 0%, in order to obtain the above-described effect, the amount of Cr contained is preferably 0.01% or more, and more preferably 0.05% or more.
  • Ni is an element to promote bainite transformation by improving the hardenability of wire rod as well as Cr.
  • the upper limit of the Ni content is set to 1.00%.
  • the Ni content is preferably 0.70% or less, and more preferably 0.50% or less.
  • the lower limit of the Ni content is 0%, in order to obtain the above-described effect, the amount of Ni contained is preferably 0.05% or more, and more preferably 0.10% or more.
  • Cu is an element to improve corrosion fatigue properties of wire rod.
  • the upper limit of the Cu content is set to 1.00%.
  • the Cu content is preferably 0.70% or less, and more preferably 0.50% or less.
  • the lower limit of the Cu content is 0%, in order to obtain the above-described effect, the amount of Cu contained is preferably 0.05% or more, and more preferably 0.10% or more.
  • Mo is an element to improve hardenability of wire rod.
  • the Mo content is more than 0.50%, hardenability of wire rod is excessively increased and there is a concern that micro-martensite precipitates at a place where Mo is segregated. The micro-martensite may deteriorate the ductility of the wire rod. Therefore, the upper limit of the Mo content is set to 0.50%.
  • the Mo content is preferably 0.30% or less, and more preferably 0.10% or less.
  • the lower limit of the Mo content is 0%, in order to obtain the above-described effect, the amount of Mo contained is preferably 0.01% or more, and more preferably 0.03% or more.
  • V 0% to 0.20%
  • Ti, Nb and V refine the diameter of y grain of the heated wire rod. In this case, structure formed during cooling the wire rod is refined and toughness of the wire rod is improved.
  • the upper limits of each amount of Ti, Nb and V are set to 0.20%.
  • Each amount of Ti, Nb and V is preferably 0.15% or less, and more preferably 0.10% or less.
  • the lower limits of each amount of Ti, Nb and V may be set to 0.01% preferably, 0.02% and more preferably.
  • the B improves the hardenability of a wire rod.
  • the upper limit of the B content is set to 0.0050%.
  • the B content is preferably 0.0040% of less, and more preferably 0.0030% or less.
  • the lower limit of the B content is 0%, in order to obtain the above-described effect, the amount of B contained is preferably 0.0005% or more, and more preferably 0.0010% or more.
  • Al is an element functioning as a deoxidizer.
  • the upper limit of the Al content is set to 0.10%.
  • the Al content is preferably 0.07% or less, and more preferably 0.05% or less.
  • the lower limit of the Al content is 0%, in order to obtain the above-described effect, the amount of Al of contained is preferably 0.01% or more, and more preferably 0.02% or more.
  • Ca improves delayed fracture resistance of wire rod by controlling form of MnS which is an inclusion in the wire rod.
  • the upper limit of the Ca content is set to 0.05%.
  • the Ca content is preferably 0.04% or less, and more preferably 0.03% or less.
  • the lower limit of the Ca content is 0%, in order to obtain the above-described effect, the amount of Ca contained is preferably 0.001% or more, and more preferably 0.005% or more.
  • the impurity is a component which is incorporated from raw materials such as mineral or scrap or by various factors in a manufacturing process when the steel is industrially manufactured, and is accepted within a range that does not adversely affect the property of the wire rod according to the present embodiment.
  • Bainite 90 area% to 100 area%
  • the metal structure of the wire rod according to the present embodiment includes 90 area% to 100 area% of bainite.
  • the drawing properties of the wire rod in which the metal structure includes bainite of 90 area% to 100 area% are excellent compared with the wire rod in which the metal structure mainly includes pearlite (pearlite wire rod).
  • cementite included in bainite is finer than cementite included in pearlite.
  • the bainite wire rod is compared with the pearlite wire rod having the same chemical composition as the bainite wire rod, the tensile strength of the bainite wire rod is lower than the tensile strength of the pearlite wire rod.
  • the lower limit of the amount of bainite may be set to 95 area%, or 98 area%.
  • micro-martensite (MA), proeutectoid cementite and the like may be included in the metal structure of the wire rod. Inclusion of these structures is acceptable as long as the amount of bainite is 90 area% or more.
  • the amount of bainite can be obtained by observing a cross section of the wire rod perpendicular to a drawing direction.
  • An example of the method for measuring the amount of bainite is as follows. Firstly, metal structure image is obtained at multiple locations on a cross section of the wire rod perpendicular to a drawing direction. Next, the average area ratio of bainite in each metal structure image is obtained.
  • a photographing region to obtain the metal structure image is not particularly limited. For example, as shown in Fig. 6 , each of a center portion 11 of the cross section 1 of the wire rod perpendicular to a drawing direction, a surface layer portion 12, and intermediate portion 13 where is a region of 1/4 depth of the wire diameter preferably includes four photographing region 2 in which they are spaced apart from each other as possible.
  • Means for obtaining the metal structure image is not particularly limited.
  • Means for discriminating bainite in the metal structure image is not particularly limited.
  • the wire rod according to the present embodiment does not include a structure other than pearlite, martensite (including micro-martensite), proeutectoid cementite and bainite. Therefore, in the metal structure image of the wire rod according to the present embodiment, a structure other than pearlite, martensite and proeutectoid cementite may be regarded as bainite.
  • Average tensile strength TS of wire rod 810 ⁇ [C]+475 N/mm 2 or less
  • the mechanical properties of wire rod according to the present embodiment is evaluated by measuring the properties of the eight test pieces having a length of 400 mm, which can be obtained by dividing a wire rod having a length of 3200 mm into eight components having the same length.
  • the average of tensile strength of the above-described eight test pieces is defined as the average tensile strength TS of the wire rod.
  • the average tensile strength TS of the wire rod according to the present embodiment satisfies the following equation 1. TS ⁇ 810 ⁇ C + 475
  • [C] means C content in the wire rod by mass%
  • [TS] means the average tensile strength TS by N/mm 2 .
  • Main factors for increasing tensile strength of wire rod are C content of the wire rod and heat treatment condition during manufacturing the wire rod.
  • An increase in tensile strength due to an increase in the C content of the wire rod does not disperse the tensile strength of the wire rod. The reason is that increase in the tensile strength which is caused by increasing C content occurs uniformly across the entire wire rod.
  • the tensile strength is increased by changing the heat treatment conditions during manufacture of the wire rod, there is a concern that the tensile strength of the wire rod may vary. Particularly, when a wire diameter is small, the heat capacity per unit length of the wire rod is small and temperature distribution in the longitudinal direction of the wire rod varies.
  • the average tensile strength of the wire rod according to the present embodiment it is necessary to be below the upper limit that is only defined by C content.
  • the present inventors limit the upper limit of the average tensile strength TS by the above equation 1.
  • Coefficients of "810" and "475" in the above equation 1 are coefficients that the present inventors have experimentally determined for the wire rod, in which the C content is more than 0.80%, that is, the C content is more than eutectoid point.
  • the average tensile strength TS of the wire rod is more than the upper limit defined by equation 1, (that is, when the average tensile strength is too high for the C content)
  • an influence which the heat treatment brings to the tensile strength increases to inappropriate level and the variation in tensile strength of the wire rod is increased. Therefore, the present inventors found that the stability of the machining is impaired and the breakage is easy to occur. In this case, since the heat treatment condition during manufacturing the wire rod is not appropriate, therefore, it is considered that the tensile strength of the wire rod is increased unevenly.
  • the lower limit of the tensile strength of the wire rod is not particularly limited. However, it is usual for the wire rod which is industrially used that a certain tensile strength is required. In addition, when the average tensile strength of the wire rod is too low for the C content, it is difficult to industrially use the wire rod. Therefore, the average tensile strength of the wire rod according to the present embodiment may be defined by the following equation 1', equation 1" or equation 1"'. 810 ⁇ C + 425 ⁇ TS ⁇ 810 ⁇ C + 475 810 ⁇ C + 435 ⁇ TS ⁇ 810 ⁇ C + 475 810 ⁇ C + 445 ⁇ TS ⁇ 810 ⁇ C + 475
  • Average reduction of area of wire rod -0.083 ⁇ TS+154 or more
  • the mechanical properties of wire rod according to the present embodiment is evaluated by measuring the properties of the eight test pieces having a length of 400 mm, which can be obtained by dividing a wire rod having a length of 3200 mm into eight components having the same length.
  • the average reduction of area of the above-described eight test pieces is defined as the average reduction of area RA of the wire rod.
  • the average reduction of area RA of the wire rod according to the present embodiment satisfies the following equation 2.
  • [TS] means the average tensile strength TS by N/mm 2 .
  • the lower limit of the average reduction of area RA is limited by the lower limit calculated from the average tensile strength TS.
  • Coefficients of "-0.083” and "154" in the above equation 2 are coefficients that the present inventors have experimentally determined for the wire rod by investigating the average tensile strength and average reduction of area in various wire rods, in which C content is within a hypereutectoid region.
  • reduction of area of the wire rod obtained by the method for manufacturing according to the present embodiment had the average reduction of area of "-0.083 ⁇ [TS]+154" or more at least. This average reduction of area is higher than the average reduction of area of the conventional pearlite wire rod.
  • the average reduction of area of the wire rod in which the metal structure does not have 90 area% to 100 area% of bainite was lower than the above-described lower limit.
  • Variation range in tensile strength of wire rod difference between maximum value and minimum value in each tensile strength of eight test pieces is 50 N/mm 2 or less
  • the mechanical properties of wire rod according to the present embodiment is evaluated by measuring the properties of the eight test pieces having a length of 400 mm, which can be obtained by dividing a wire rod having a length of 3200 mm into eight components having the same length.
  • the difference between maximum value and minimum value in each tensile strength of the above-described each test pieces is defined as the variation range in the tensile strength of the wire rod.
  • the variation range in the tensile strength of the wire rod according to the present embodiment is 50 N/mm 2 or less.
  • the variation range in the tensile strength of the wire rod may be 45 N/mm 2 or less, 40 N/mm 2 or less, 35 N/mm 2 or less or 30 N/mm 2 or less.
  • a wire diameter according to the present embodiment is not particularly limited.
  • the wire diameter may be set to 3.5 mm to 16.0 mm.
  • the heat capacity per unit length of the wire rod is small and the temperature distribution in the longitudinal direction of the wire rod varies. Therefore, it is difficult to perform the heat treatment uniformly across the entire wire rod and it is easy to spread the variation in the tensile strength.
  • the wire diameter is more than 16.0 mm, it is difficult to uniformly cool the center portion and surface layer portion of the wire rod and there is a concern that it is difficult to set the metal structure of the center portion of the wire rod to the predetermined structure.
  • a method for manufacturing a wire rod and steel wire according to the present embodiment (hereinafter, may be referred to as "a manufacturing method according to the present embodiment") will described.
  • a method for manufacturing a wire rod according to the present embodiment includes:
  • molten salt bath or molten lead bath is simply referred as “bath” in Figs. 4 and 5 .
  • bath the matter that the wire rod is immersed into the second molten salt bath or the second molten lead bath at the time from t s seconds before to t s seconds after the bainite transformation of the wire rod starts may be referred as "immersing the wire rod into the second molten salt bath or the second molten lead bath at substantially the same time as the start of the bainite transformation of the wire rod”.
  • FIG. 1 A heat treatment of a manufacturing method according to the present embodiment is showed in Fig. 1 .
  • the arrow labeled with symbol (b) in figure represents the wire rod of 850°C to 1050°C being immersed into the first molten salt bath or the first molten lead bath having a temperature T 1 within a range of 350°C to 450°C and subsequently the wire rod is taken out, that is, represents the above-described (b).
  • the wire rod is hold at temperature T 1 , taken out and subsequently transferred to the second molten salt bath or the second molten lead bath.
  • t 1 in figure represents the sum of a time for immersing the wire rod into the first molten salt bath or the first molten lead bath and a time of transferring the wire rod from the first molten salt bath or the first molten lead bath to the second molten salt bath or the second molten lead bath (that is, represents a time from the wire rod is immersed into the first molten salt bath or the first molten lead bath to the wire rod is immersed into the second molten salt bath or the second molten lead bath).
  • the arrow labeled with symbol (c) in figure represents the wire rod being immersed into the second molten salt bath or the second molten lead bath having a temperature (T 1 + ⁇ T) within a range of 530°C to 600°C at substantially the same time as the start of the bainite transformation, that is, represents the above-described (c).
  • the arrow labeled with symbol (d) in the figure represents the wire rod being held in the the second molten salt bath or the second molten lead bath until the bainite transformation is completely finished, that is, represents the above-described (d).
  • the wire rod In the method for manufacturing the wire rod according to the present embodiment, firstly, a billet having the above-described chemical composition of the wire rod according to the present embodiment is rolled to obtain the wire rod. Next, the wire rod is immersed into the first molten salt bath or the first molten lead bath. The wire rod may be cooled once between the rolling and immersing, and reheated, or the wire rod may not be cooled and reheated between the rolling and immersing. In addition, the wire drawing may be performed to the wire rod between the rolling and immersing. In any case, the temperature of the wire rod immersed into the first molten salt bath or the first molten lead bath is set to 850°C to 1050°C.
  • the upper limit of the temperature of the wire rod or steel wire which is immersed becomes substantially 1050°C.
  • the upper limit of the temperature of the wire rod or steel wire which is immersed may be set to 1050°C. The reason is that there is no advantage to heat the wire rod or steel wire to 1050°C or more.
  • the temperature of the wire rod or steel wire which is immersed into the first molten salt bath or the first molten lead bath is less than 850°C, hardening is not performed well to the wire rod or steel wire. Therefore, the lower limit of the temperature of the wire rod or steel wire which is immersed into the first molten salt bath or the first molten lead bath is set to 850°C.
  • the mention of the "wire rod” in the description of the process can be suitably replaced with "steel wire”.
  • the wire rod having a temperature of 850°C to 1050°C is rapidly cooled by immersing into the first molten salt bath or the first molten lead bath ((b) in Fig. 1 ).
  • the temperature T 1 of the first molten salt bath or the first molten lead bath is 350°C to 450°C.
  • the metal structure of the wire rod becomes austenite being cooled to a supercooled state by rapid cooling. When the wire is isothermally held in this state, the bainite transformation of austenite being the supercooled state starts.
  • the temperature T 1 of the first molten salt bath or the first molten lead bath is more than 450°C, the cooling rate of the wire rod decreases and the metal structure of the wire rod is transformed to bainite before austenite is formed in s supercooled state.
  • the tensile strength of the wire rod is deteriorated, proeutectoid cementite precipitates in the wire rod.
  • the proeutectoid cementite deteriorates the drawing properties of the wire rod. Therefore, in order to rapidly cool the wire rod, the temperature T 1 of the first molten salt bath or the first molten lead bath is required to be 450°C or less.
  • the temperature T 1 of the first molten salt bath or the first molten lead bath is less than 350°C, there is a concern that the first molten salt bath or the first molten lead bath will solidify.
  • the length of time for the wire rod being immersed into the first molten salt bath or the first molten lead bath needs to be adjusted so that the wire rod can be immersed into the second molten salt bath or a second molten lead bath as desired.
  • the wire rod is immersed into the second molten salt bath or the second molten lead bath having the temperature T 2 at the time within 5 seconds from when the wire rod is taken out from the first molten salt bath or the first molten lead bath having the temperature T 1 and at the time from t s seconds before to t s seconds after the bainite transformation of the wire rod starts.
  • the present inventors manufactured the wire rod under the various manufacturing conditions in which t 1 that is from the time immersing the wire rod into the first molten salt bath or the first molten lead bath to the time immersing the wire rod into the second molten salt bath or the second molten lead bath (that is, total length of time of time for immersing the wire rod into the first molten salt bath or the first molten lead bath and time for transferring the wire rod from the first molten salt bath or the first molten lead bath to the second molten salt bath or the second molten lead bath) and the temperature T 1 of the first molten salt bath or the first molten lead bath are changed, and measured the variation range in the tensile strength of the wire rod.
  • the present inventors investigated the relationship between the temperature T 1 , time t 1 , and the variation range in the tensile strength. As a result, results shown in Fig. 3 were obtained.
  • Curve attached with symbol "S” in Fig. 3 is the curve showing the temperature and the time when the bainite transformation starts (hereinafter, referred as S curve). This curve varies according to the chemical composition of the wire rod. Data points described in Fig. 3 represents the temperature T 1 and time t 1 when the wire rod according to data point is manufactured.
  • the wire rod according to data point on the left side than the curve is the wire rod immersed into the second molten salt bath or the second molten lead bath before the bainite transformation starts, and the wire rod according to data point on the right side than the curve is the wire rod immersed into the second molten salt bath or the second molten lead bath after the bainite transformation starts.
  • S curve the curve showing the temperature and the time when the bainite transformation starts
  • the dotted line described with respect to each data point represents the thermal history of the wire rod according to each data point.
  • the variation range in the tensile strength of the wire rod in which type of data point is "BAD” is more than 50 N/mm 2
  • the variation range in the tensile strength of the wire rod in which type of data point is "GOOD” is more than 40 N/mm 2 to 50 N/mm 2 or less
  • the variation range in the tensile strength of the wire rod in which type of data point is "VERY GOOD” is 40 N/mm 2 or less.
  • the time t 1 is appropriately set so that the wire rod is immersed into the second molten salt bath or the second molten lead bath at the time from t s seconds before to t s seconds after the bainite transformation of the wire rod starts.
  • the t s is the value obtained by the following equation 3.
  • t s 0.05 ⁇ t complete t complete represents a time from the start to the finish of the bainite transformation of the wire rod in seconds, when continuing an immersion of the wire rod into the first molten salt bath or the first molten lead bath.
  • the time from when the wire rod is immersed into the first molten salt bath or the first molten lead bath to when the bainite transformation of the wire rod starts and the t s are determined dependent on S curve corresponding to the chemical composition of the wire rod and the temperature of the first molten salt bath or the first molten lead bath. Therefore, the time t 1 can be obtained by the simulation based on the chemical composition and the temperature of the first molten salt bath or the first molten lead bath the wire, and/or by the preliminary experiment. In addition, as described later, because the reheat of the wire rod is detected, the time from when the wire rod is immersed into the first molten salt bath or the first molten lead bath to when the bainite transformation of the wire rod starts can be obtained. Therefore, before manufacturing the wire rod, a preliminary investigation may be carried out to determine the time t 1 using the above-described means.
  • the temperature of the wire rod is increased during immersion into the first molten salt bath or the first molten lead bath or during transfer to the second molten salt bath or the second molten lead bath due to reheating (transformation heat).
  • reheating transformation heat
  • the wire rod in the state having the coil shape is immersed into the molten salt bath or molten lead bath and subsequently taken out.
  • the wire rod has a coil shape during heat treatment, the rising of the temperature due to reheating is increased in portions where the wire rods overlap, compared with other portions. The reason is that the cooling effect by the first molten salt bath or the first molten lead bath is difficult to reach to the portion where the wire rod is overlapped with each other. Therefore, since the above-described time t 1 becomes longer, when the start of the heating of the wire rod is delayed, variation in tensile strength of the wire rod occurs due to non-uniform rise in the temperature of the wire rod.
  • the wire rod it is essential that the wire rod have a coil shape during heat treatment in order to enhance the production efficiency thereof.
  • the wire rod in a state where the wire rods do not overlap with each other is not immersed into the molten salt bath or molten lead bath.
  • the start of the transformation accelerates. Therefore, the transformation start temperature is increased. In this case, the strength of the wire rod increases and the ductility of the wire rod decreases.
  • the present inventors found from the experimental facts that the variation in tensile strength of the wire rod is sufficiently suppressed in a wire rod in which the bainite transformation proceeds rapidly and the temperature rise due to reheating is relatively large, when the time between the immersion of the wire rod and the start of the transformation of the wire rod is 5 seconds or less.
  • the present inventors found from the experimental facts that the variation is suppressed in the wire rod in which the bainite transformation proceeds slowly and the temperature rise due to reheating is relatively low, even when the time between the immersion of the wire rod and the start of the transformation of the wire rod is more than 5 seconds.
  • the time between the immersion of the wire rod and the start of the transformation of the wire rod is defined by the value t s which is determined in accordance with the progression rate of the bainite transformation.
  • the upper limit of the t s may be set to 5 seconds.
  • the elapsed time t 1 between the time when the wire rod is immersed into the first molten salt bath or the first molten lead bath and the time when the wire rod is immersed into the second molten salt bath or the second molten lead bath is preferably 10 seconds to 40 seconds.
  • the time t 1 is less than 10 seconds or more than 40 seconds, it is difficult to properly perform the following immersing the wire rod into the second molten salt bath or the second molten lead bath.
  • the wire rod is immersed into the second molten salt bath or the second molten lead bath within 5 seconds from being taken out of the first molten salt bath or the first molten lead bath.
  • the time from the take-out of the wire rod to the immersion of the wire that is, when the transferring time of the wire rod, is more than 5 seconds, there is a concern that the temperature of the wire rod varies during transfer thereof. Therefore, it is extremely difficult to immerse the wire rod into the second molten salt bath or the second molten lead bath at substantially the same time the bainite transformation of the wire rod starts.
  • the start of the bainite transformation in the wire rod in the first molten salt bath or the first molten lead bath may be determined by detecting the reheat of the wire rod (transformation heat).
  • the reheat in the present embodiment represents the phenomenon in which the temperature of the wire rod is increased by starting of the bainite transformation therein.
  • the reheat can be detected, for example, by comparing the temperature of the wire rod, which is immersed into and taken out from the first molten salt bath or the first molten lead bath, with the temperature of the first molten salt bath or the first molten lead bath. When the temperature of the wire rod is higher than the temperature of the first molten salt bath or the first molten lead bath, it can be judged that the reheat is generated in the wire rod.
  • the shortest immersion time t min that the reheat can be generated in the wire rod can be obtained by examining the presence or absence of reheat.
  • the time passed for t min from when the wire rod is immersed into the first molten salt bath or the first molten lead bath can be regarded as the time when the bainite transformation starts in the wire rod. In this way, the time when the bainite transformation starts in the wire rod is obtained in advance by using the reheat, and it is more preferable to manufacture the wire rod based on the obtained time.
  • the time immersed into the first molten salt bath or the first molten lead bath is less than 5 seconds, even if the temperature of the wire rod is higher than the first molten salt bath or the first molten lead bath, it cannot be judged whether the reheat is generated in the wire rod , or not. The reason is that there is a case where the temperature of the wire rod is increased due to insufficient immersion time, and not by reheating.
  • the wire rod is immersed into the second molten salt bath or the second molten lead bath having a temperature T 2 at substantially the same time as the start of the bainite transformation of the wire rod.
  • the temperature T 2 is 530°C to 600°C.
  • the wire rod is rapidly heated to the temperature of 530°C to 600°C ((c) in Fig. 1 ), and the wire rod can be held at that temperature until the bainite transformation is completely finished.
  • cementite spacing in the bainite is widened.
  • the strength of the wire rod is decreased compared with a case in which the rapidly heating is not performed.
  • the temperature of the second molten salt bath or the second molten lead bath is less than 530°C or more than 600°C, it takes a long time until the end of the bainite transformation. Therefore, the temperature of the second molten salt bath or the second molten lead bath is set to 530°C to 600°C in order to certainly complete the bainite transformation in a short time.
  • the heating rate during heating the wire rod to the above temperature range is not particularly limited. However, in order to reduce the time for completing the bainite transformation, the heating rate is preferably faster, specifically, the heating rate is preferably 10 °C/second to 50 °C/second.
  • a hypereutectoid bainite steel wire having excellent delayed fracture resistance according to the present embodiment (hereinafter may be referred as "steel wire according to the present embodiment") is obtained by wire drawing the wire rod having excellent drawing properties according to the present embodiment.
  • Wire drawing may be a conventional wire drawing, and area reduction rate is not particularly limited. Since the steel wire according to the present embodiment has excellent delayed fracture resistance, applications of steel wire are greatly expanding.
  • Hypereutectoid billets having chemical compositions as shown in Table 1 were rolled to obtain wire rods having wire diameters as shown in Table 2, and the bainite transformation was completed under the temperature conditions as shown in Table 2.
  • the average tensile strength of the wire rods (N/mm 2 ), the average reduction of area of the wire rods (%), and variation range in the tensile strength of the wire rods (N/mm 2 ) after the bainite transformation was completed were measured.
  • the average tensile strength of the wire rod is obtained by averaging the tensile strength of each of the eight test pieces having a length of 400 mm, which can be obtained by dividing a wire rod having a length of 3200 mm into eight components having the same length.
  • the average reduction of area of the wire rod is obtained by averaging the reduction of the area each of the eight test pieces having a length of 400 mm, which can be obtained by dividing a wire rod having a length of 3200 mm into eight components having the same length.
  • the variation range in the tensile strength of the wire rod is the difference between the maximum value and minimum value within the tensile strengths of each of the eight test pieces having a length of 400 mm, which can be obtained by dividing a wire rod having a length of 3200 mm into eight components having the same length.
  • the measurement results are also shown in Table 2.
  • the heating rate during immersing the wire rod into the second molten salt bath or the second molten lead bath was 10 °C/second to 50 °C/second.
  • T 0 represents the temperatures of the wire rods immersed into the first molten salt bath or the first molten lead bath
  • T 1 represents the temperatures of the first molten salt bath or the first molten lead bath
  • t 1 represents the time from when the wire rods are immersed into the first molten salt bath or the first molten lead bath to when the wire rods are immersed into the second molten salt bath or the second molten lead bath
  • ⁇ T represents the temperatures that were increased by immersing the wire rods into the second molten salt bath or the second molten lead bath
  • T 2 represents the temperatures of the second molten salt bath or the second molten lead bath
  • the upper limit of TS represents the upper limit of the average tensile strengths calculated by the C contents and equation 1
  • TS average represents the average tensile strengths (N/mm 2 )
  • maximum of TS represents the maximum value of the tensile strengths (N/mm 2 )
  • minimum of TS represents the minimum value of the ten
  • Immersion time t of the wire rods immersed into the first molten salt bath or the first molten lead bath during manufacturing the Nos. 1 to 7 examples were appropriately selected so that the wire rods were immersed into the second molten salt bath or the second molten lead bath at substantially the same time as the start of the bainite transformation.
  • the wire rod was not immersed into the second molten salt bath or the second molten lead bath.
  • the wire rods were immersed into the the second molten salt bath or the second molten lead bath after a long time passed since the bainite transformation started.
  • the wire rods were immersed into the second molten salt bath or the second molten lead bath within 5 seconds when the wire rods were taken out from the first molten salt bath or the first molten lead bath.
  • TS average satisfied equation 1 and RA average satisfied equation 2
  • TS variation range was 50 N/mm 2 or less. From these results, in the examples Nos. 1 to 7, it can be found that the delayed fracture resistance was improved and the breakages were not generated during bundling the wire rods and in the state where the wire rods were bundled.
  • the wire rod has lower strength and higher ductility compared with pearlite steel and the wire rod, in which the breakage is suppressed during bundling operation of the wire rod or in the state where the wire rod is bundled, has excellent drawing properties and delayed fracture resistance, the hypereutectoid bainite steel wire manufactured by using the wire rod, and the method for stably manufacturing them can be provided. Therefore, the present invention has high availability in the steel industry.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
EP14851484.7A 2013-10-08 2014-10-08 Walzdraht, hypereutektoider bainitstahl draht und verfahren zur herstellung davon Withdrawn EP3056580A4 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2013211365 2013-10-08
PCT/JP2014/076938 WO2015053311A1 (ja) 2013-10-08 2014-10-08 線材、過共析ベイナイト鋼線、及びそれらの製造方法

Publications (2)

Publication Number Publication Date
EP3056580A1 true EP3056580A1 (de) 2016-08-17
EP3056580A4 EP3056580A4 (de) 2017-07-26

Family

ID=52813126

Family Applications (1)

Application Number Title Priority Date Filing Date
EP14851484.7A Withdrawn EP3056580A4 (de) 2013-10-08 2014-10-08 Walzdraht, hypereutektoider bainitstahl draht und verfahren zur herstellung davon

Country Status (7)

Country Link
US (1) US20160244858A1 (de)
EP (1) EP3056580A4 (de)
JP (1) JP6079894B2 (de)
KR (1) KR101789949B1 (de)
CN (1) CN105612269B (de)
TW (1) TWI516611B (de)
WO (1) WO2015053311A1 (de)

Families Citing this family (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6416709B2 (ja) * 2015-07-21 2018-10-31 新日鐵住金株式会社 高強度ｐｃ鋼線
JP6416708B2 (ja) * 2015-07-21 2018-10-31 新日鐵住金株式会社 高強度ｐｃ鋼線
CN105220786A (zh) * 2015-10-17 2016-01-06 张磊 一种建筑物保温隔音层
CN105178455A (zh) * 2015-10-17 2015-12-23 张磊 建筑物外墙防火保温层
CN108138285B (zh) * 2015-10-23 2020-02-21 日本制铁株式会社 拉丝加工用钢丝材
TWI643959B (zh) * 2016-07-05 2018-12-11 新日鐵住金股份有限公司 Wire, steel wire and components
KR102021199B1 (ko) * 2017-11-27 2019-09-11 현대제철 주식회사 강재 및 그 제조방법
KR102362665B1 (ko) * 2019-12-20 2022-02-11 주식회사 포스코 선재, 고강도 강선 및 이들의 제조방법
JP7469643B2 (ja) 2020-05-21 2024-04-17 日本製鉄株式会社 鋼線、非調質機械部品用線材、及び非調質機械部品

Family Cites Families (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2742967B2 (ja) * 1991-10-24 1998-04-22 新日本製鐵株式会社 ベイナイト線材の製造法
JP2984886B2 (ja) 1992-04-09 1999-11-29 新日本製鐵株式会社 伸線加工用ベイナイト線材または鋼線およびその製造方法
JP2984885B2 (ja) 1992-04-09 1999-11-29 新日本製鐵株式会社 伸線加工用ベイナイト線材または鋼線およびその製造方法
JP2984887B2 (ja) 1992-04-09 1999-11-29 新日本製鐵株式会社 伸線加工用ベイナイト線材または鋼線およびその製造方法
JP2984889B2 (ja) 1992-07-08 1999-11-29 新日本製鐵株式会社 伸線加工性に優れた高炭素鋼線材または鋼線およびその製造方法
JP3400071B2 (ja) * 1993-04-06 2003-04-28 新日本製鐵株式会社 疲労特性の優れた高強度鋼線材および高強度鋼線
US5662747A (en) * 1993-04-06 1997-09-02 Nippon Steel Corporation Bainite wire rod and wire for drawing and methods of producing the same
DE69424783T2 (de) * 1993-04-06 2000-11-23 Nippon Steel Corp., Tokio/Tokyo Bainitstange oder stahldraht zum drahtziehen und verfahren zu deren herstellung
JP3018268B2 (ja) * 1993-05-25 2000-03-13 新日本製鐵株式会社 伸線加工性に優れた高炭素鋼線材または鋼線およびその製造方法
US5658402A (en) * 1993-05-25 1997-08-19 Nippon Steel Corporation High-carbon steel wire rod and wire excellent in drawability and methods of producing the same
JP3388418B2 (ja) 1994-06-21 2003-03-24 新日本製鐵株式会社 伸線加工性に優れた高炭素鋼線材または鋼線の製造方法
JPH083649A (ja) * 1994-06-21 1996-01-09 Nippon Steel Corp 伸線加工性に優れた高炭素鋼線材または鋼線の製造方法
JP3448459B2 (ja) * 1997-06-10 2003-09-22 新日本製鐵株式会社 鋼線用線材
JP3548419B2 (ja) * 1998-04-15 2004-07-28 新日本製鐵株式会社 高強度鋼線
JP2001220650A (ja) * 1999-11-30 2001-08-14 Sumitomo Electric Ind Ltd 鋼線、ばね及びそれらの製造方法
JP2002241899A (ja) * 2001-02-09 2002-08-28 Kobe Steel Ltd 耐遅れ破壊性と鍛造性に優れた高強度鋼線およびその製造方法
CN102301024B (zh) * 2010-02-01 2014-03-05 新日铁住金株式会社 线材、钢丝以及它们的制造方法

Also Published As

Publication number Publication date
TWI516611B (zh) 2016-01-11
CN105612269B (zh) 2017-11-14
KR101789949B1 (ko) 2017-10-25
TW201516162A (zh) 2015-05-01
US20160244858A1 (en) 2016-08-25
CN105612269A (zh) 2016-05-25
EP3056580A4 (de) 2017-07-26
JP6079894B2 (ja) 2017-02-15
WO2015053311A1 (ja) 2015-04-16
JPWO2015053311A1 (ja) 2017-03-09
KR20160048991A (ko) 2016-05-04

Similar Documents

Publication Publication Date Title
EP3056580A1 (de) Walzdraht, hypereutektoider bainitstahl draht und verfahren zur herstellung davon
JP5114684B2 (ja) 延性に優れた線材及び高強度鋼線並びにそれらの製造方法
US8168011B2 (en) High-strength steel wire excellent in ductility and method of manufacturing the same
EP3640357A1 (de) Walzdraht für federstahl
JP5257082B2 (ja) 低温焼鈍後の冷間鍛造性に優れた鋼線材及びその製造方法並びに冷間鍛造性に優れた鋼線材の製造方法
EP1900837A1 (de) Hochfester walzdraht mit hervorragender drahtziehleistungsfähigkeit und herstellungsverfahren dafür
KR20130034045A (ko) 특수강 강선 및 특수강 선재
WO2017122830A1 (ja) 非調質機械部品用鋼線及び非調質機械部品
EP3342892A1 (de) Stahl für mechanische strukturen zur kaltbearbeitung und herstellungsverfahren dafür
EP3282027B1 (de) Hoch-kohlenstoffhaltiges stahldrahtmaterial mit hervorragender drahtziehfähigkeit und stahldraht
CN108315637B (zh) 高碳热轧钢板及其制造方法
EP3088551A1 (de) Gewalztes stahlmaterial für hochfeste feder und draht für hochfeste feder damit
EP2816130B1 (de) Federstahl
JP6065121B2 (ja) 高炭素熱延鋼板およびその製造方法
JPWO2015163409A1 (ja) 高強度スチールコード用フィラメント
EP3115478B1 (de) Draht aus kohlenstoffreichem stahl mit hervorragenden drahtzieheigenschaften und verfahren zur herstellung davon
CN112969808B (zh) 螺栓用钢及其制造方法
CN108368583B (zh) 非调质机械部件用钢丝及非调质机械部件
JP2010229469A (ja) 冷間加工特性に優れる高強度線材及びその製造方法
JP5945196B2 (ja) 高強度鋼線用線材
KR102456737B1 (ko) 코일드 튜빙용 열연 강판 및 그 제조 방법
CN108699650B (zh) 轧制线材
EP3214189B1 (de) Verfahren zur herstellung von vergüteten nahtlosen rohren für eine hochfeste hohlfeder
CN108350544B (zh) 钢线
JP4765680B2 (ja) 焼戻し効率性および焼戻し安定性に優れるマルテンサイト系ステンレス鋼

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

17P Request for examination filed

Effective date: 20160505

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

DAX Request for extension of the european patent (deleted)
A4 Supplementary search report drawn up and despatched

Effective date: 20170622

RIC1 Information provided on ipc code assigned before grant

Ipc: C21D 6/00 20060101ALI20170616BHEP

Ipc: C21D 1/20 20060101ALI20170616BHEP

Ipc: C21D 9/58 20060101ALI20170616BHEP

Ipc: C22C 38/44 20060101ALI20170616BHEP

Ipc: C21D 8/06 20060101ALI20170616BHEP

Ipc: C22C 38/04 20060101ALI20170616BHEP

Ipc: C22C 38/50 20060101ALI20170616BHEP

Ipc: C22C 38/42 20060101ALI20170616BHEP

Ipc: C22C 38/48 20060101ALI20170616BHEP

Ipc: C22C 38/02 20060101ALI20170616BHEP

Ipc: C21D 1/48 20060101ALI20170616BHEP

Ipc: C21D 1/46 20060101ALI20170616BHEP

Ipc: C22C 38/18 20060101AFI20170616BHEP

Ipc: C21D 9/52 20060101ALI20170616BHEP

Ipc: C21D 1/607 20060101ALI20170616BHEP

Ipc: C22C 38/06 20060101ALI20170616BHEP

Ipc: C22C 38/46 20060101ALI20170616BHEP

Ipc: C22C 38/00 20060101ALI20170616BHEP

Ipc: C22C 38/54 20060101ALI20170616BHEP

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

Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN

18D Application deemed to be withdrawn

Effective date: 20180123