WO2012144630A1 - Fil-machine d'acier à haute teneur en carbone et procédé de fabrication d'un fil-machine d'acier à haute teneur en carbone - Google Patents

Fil-machine d'acier à haute teneur en carbone et procédé de fabrication d'un fil-machine d'acier à haute teneur en carbone Download PDF

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Publication number
WO2012144630A1
WO2012144630A1 PCT/JP2012/060783 JP2012060783W WO2012144630A1 WO 2012144630 A1 WO2012144630 A1 WO 2012144630A1 JP 2012060783 W JP2012060783 W JP 2012060783W WO 2012144630 A1 WO2012144630 A1 WO 2012144630A1
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less
high carbon
steel wire
carbon steel
upper limit
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Ceased
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PCT/JP2012/060783
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English (en)
Japanese (ja)
Inventor
▲琢▼哉 高知
土田　武広
智一 増田
染川　雅実
悠士 中河原
千葉　政道
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Kobe Steel Ltd
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Kobe Steel Ltd
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Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties of ferrous metals or ferrous alloys 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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

Definitions

  • the present invention relates to a high carbon steel wire used as a bearing material in automobiles and various industrial machines and a method for producing the high carbon steel wire.
  • a magnetic field is applied in the temperature range of 800 to 500 ° C. during cooling after hot rolling, and the cooling rate in the temperature range is set to 10 ° C./s or less to suppress the precipitation of proeutectoid cementite.
  • a method has been proposed in which the time required for the spheroidizing annealing in the next step can be shortened by shortening the lamella spacing in the pearlite.
  • special equipment for applying a magnetic field is required, resulting in an increase in production cost and offsetting the cost reduction effect by shortening the spheroidizing time. End up.
  • Patent Document 2 a high carbon chromium bearing steel having a predetermined component composition is rolled while being controlled so that the temperature in the entire cross section is between the A1 point and the Acm point from extraction to finish rolling.
  • a method that can omit or shorten the next spheroidizing annealing has been proposed.
  • special equipment called a rapid rolling mill is required.
  • This proposal like the previous proposal, causes an increase in production costs and shortens the spheroidizing time. The cost reduction effect is offset.
  • a material to be rolled having a predetermined component composition is heated to a temperature range of Ae 1 point to Aem point, and then rolled at a relatively low temperature of 680 ° C. to (Aem point ⁇ 30 °) 2 Rolling is performed by the above-described rolling process and an all-continuous hot rolling method including one or more intermediate cooling processes between the rolling processes. Further, after rolling, the temperature range up to 400 ° C is 5 ° C / s. A method of final cooling under the following conditions has been proposed. Although the spheroidizing annealing can be simplified by implementing this proposal, it is considered that the hardness of the material after the spheroidizing treatment is not sufficiently reduced.
  • the present invention has been made as a solution to the above-described conventional problems.
  • the high carbon steel wire material capable of sufficiently reducing hardness and the high carbon
  • An object of the present invention is to provide a method for producing a steel wire rod.
  • the present invention provides the following high carbon steel wire and method for producing the high carbon steel wire.
  • C 0.95 to 1.10%, Si: 0.15 to 0.70%, Mn: 1.15% or less (excluding 0%), Cr: 0.90 to 1.60%, P: 0.050% or less (not including 0%), S: 0.050% or less (not including 0%), Al: 0.100% or less (not including 0%), Ti: 0.015% or less (not including 0%), N: 0.025% or less (not including 0%), O: 0.0025% or less (not including 0%), the balance being Consisting of iron and inevitable impurities,
  • the ferrite crystal grain size is 20.0 ⁇ m or less,
  • carbonized_material is 6.0% or more by mass%,
  • the high carbon steel wire characterized by the above-mentioned.
  • Nb 0.5% or less (excluding 0%)
  • V 0.5% or less (excluding 0%)
  • B 0.005% or less (0%)
  • the production method of the high carbon steel wire and the high carbon steel wire of the present invention from the viewpoint of cost and environmental load, it is possible to shorten the spheroidizing treatment time during production, and at the same time, the die during cold forging The life can be improved, and the hardness can be sufficiently reduced from the viewpoint of power saving during production.
  • carbon steel and alloy steel have been widely used as materials for machine parts used in automobiles and various industrial machines.
  • a high carbon chromium bearing steel (SUJ material) defined by “JIS G 4805” is often used as a bearing material.
  • SUJ material high carbon chromium bearing steel
  • the bearing steel is hot-rolled into a rolled wire rod, then spheroidized, cut, and cold forged into a predetermined shape. It is manufactured by quenching and tempering, and finally finishing.
  • the material In general hot rolling of bearing steel, the material is heated to the austenite single-phase region and rolled in the austenite state. After rolling, the material is cooled relatively slowly (slow cooling). The metal structure becomes pearlite.
  • Spheroidizing annealing is a treatment for softening a carbide (cementite) in steel by making it spherical and coarsening.
  • cementite carbide
  • the structure before the spheroidizing annealing is pearlite, it takes a long time for the fine lamellar cementite in the pearlite to be divided and coarsely spheroidized.
  • the inventors of the present invention have made extensive studies in order to find a method capable of shortening the spheroidizing time during production and obtaining a high carbon steel wire material having sufficiently reduced hardness. As a result, during the spheroidization heating, when the matrix structure is reverse transformed from ferrite to austenite, the spheroidization of the carbides easily proceeds. I found out that I can do it.
  • the ferrite crystal grain size (average crystal grain size of ferrite) before reverse transformation may be 20.0 ⁇ m or less.
  • the ferrite crystal grain size before reverse transformation is preferably 15.0 ⁇ m or less, more preferably 10.0 ⁇ m or less, and even more preferably 7.5 ⁇ m or less.
  • the ferrite crystal grain size before reverse transformation is preferably as small as possible.
  • the lower limit value is not particularly specified, but the actual lower limit value is considered to be about 1.0 ⁇ m.
  • the ferrite crystal grain size can be obtained by the following method. For the cross section perpendicular to the longitudinal direction of the rolled wire rod, mirror polishing, etching with nital, and observation of the structure with an optical microscope, the structure size of the D / 4 position (D: diameter) of a total of 10 cross sections A total of 400 to 1000 times of photographs are taken, and the results for a total of 30 fields are averaged.
  • the present inventors have intensively studied to deal with these contradictory problems. As a result, the inventors have found a method capable of shortening the spheroidizing time while maintaining the spheroidized structure by making the carbides difficult to dissolve.
  • the dissolution of carbide is greatly affected by the composition of the carbide, and particularly in the case of bearing steel, it is greatly affected by the Cr concentration in the carbide.
  • the more concentrated Cr is in the carbide the more difficult it is to melt during heating, and the spheroidizing time can be shortened while maintaining low hardness by suppressing the formation of pearlite.
  • the Cr solid solution strengthening of ferrite falls with the increase in the Cr concentration of cementite, and a low hardness can be obtained in a stable state.
  • the Cr concentration in the carbide needs to be 6.0% by mass or more. It is preferably 6.5% by mass or more, more preferably 7.0% by mass or more.
  • the upper limit value is not particularly defined, but the actual upper limit value is considered to be about 10.0% by mass.
  • the high carbon steel wire rod of the present invention has a component range including all high carbon chromium bearing steel materials (SUJ materials 2 to 5) defined in “JIS G 4805 (2008)”. Specifically, in terms of mass%, C: 0.95 to 1.10%, Si: 0.15 to 0.70%, Mn: 1.15% or less (not including 0%), Cr: 0.00. It shall contain 90 to 1.60%. In addition, although all units are described as%, all the mass% is included unless otherwise specified, including descriptions in other specifications.
  • the SUJ2 materials are C: 0.95 to 1.10%, Si: 0.15 to 0.35%, Mn: 0.50% or less, Cr: 1.30 to 1.
  • Containing 60% SUJ3 material is C: 0.95 to 1.10%, Si: 0.40 to 0.70%, Mn: 0.90 to 1.15%, Cr: 0.90 to 1 20%
  • SUJ4 material is C: 0.95 to 1.10%, Si: 0.15 to 0.35%, Mn: 0.50% or less, Cr: 1.30 to 1.60
  • the SUJ5 material contains C: 0.95 to 1.10%, Si: 0.40 to 0.70%, Mn: 0.90 to 1.15%, Cr: 0.90 to 1.%. Contains 20%.
  • C 0.95 to 1.10%
  • C is an essential element for increasing the quenching hardness and maintaining the strength at room temperature and high temperature to impart wear resistance. Therefore, it is necessary to contain 0.95% or more. However, if the C content is excessively large, giant carbides are likely to be generated and adversely affect the rolling fatigue characteristics. Therefore, the C content must be suppressed to 1.10% or less.
  • the minimum with preferable content of C is 0.98%, and a preferable upper limit is 1.05%.
  • ⁇ Cr 0.90 to 1.60% Cr is an element that combines with C to form fine carbides, imparts wear resistance, and contributes to improved hardenability. Further, when Cr is concentrated in the carbide, it becomes difficult to dissolve during heating, which contributes to the promotion of spheroidization. In order to exert such an effect, it is necessary to contain 0.90% or more of Cr. However, when the Cr content is excessive, coarse carbides are generated and the rolling fatigue life is reduced. Therefore, the Cr content is 1.60% or less. The preferable lower limit of the Cr content is 1.00%, and the preferable upper limit is 1.55%.
  • Si 0.15 to 0.70%
  • Mn 1.15% or less (excluding 0%)
  • Si is an element useful for improving the solid solution strengthening and hardenability of the matrix.
  • it is necessary to contain Si by 0.15% or more, preferably 0.20% or more (more preferably 0.25% or more).
  • the Si content is 0.70% or less, preferably 0.65% or less (more preferably 0.60% or less).
  • Mn is an element useful for improving the solid solution strengthening and hardenability of the matrix.
  • the Mn content is excessively increased, the workability and machinability are remarkably lowered, so the Mn content is 1.15.
  • % Or less preferably 1.10% or less (more preferably 1.05% or less).
  • the lower limit is not particularly defined, it is necessary to contain 0.1% or more, preferably 0.15% or more (more preferably 0.2% or more) in order to obtain the effects of solid solution strengthening and hardenability improvement. It is desirable to contain.
  • the content of various elements is usually limited in bearing steel from the viewpoint of rolling fatigue properties and machinability.
  • various elements shown below are defined as follows from their respective roles. If content of various elements is in the following range, the effect of the present invention will not be hindered.
  • ⁇ P 0.050% or less (not including 0%)
  • S 0.050% or less (not including 0%)
  • P deteriorates the toughness and workability at the segregation part
  • S forms inclusions and deteriorates the rolling fatigue characteristics.
  • JIS G 4805 (2008) defines the upper limits of P and S, and it is preferable that both be 0.025% or less. A more preferred upper limit is 0.020%, and a still more preferred upper limit is 0.015%.
  • Al 0.100% or less (excluding 0%)
  • Al has the action of forming nitrides, refining the structure, and improving rolling fatigue characteristics.
  • the upper limit of the Al content is 0.100%.
  • a preferable upper limit is 0.050%, a more preferable upper limit is 0.030%, and a further preferable upper limit is 0.010%.
  • Ti 0.015% or less (excluding 0%) Ti forms nitrides like Al.
  • the upper limit of the Ti content is 0.015%.
  • a preferable upper limit is 0.010%, a more preferable upper limit is 0.005%, and a further preferable upper limit is 0.002%.
  • N 0.025% or less (excluding 0%) N is an element effective for solid solution strengthening, and contributes to the improvement of rolling fatigue characteristics as described above. However, if the content is excessive, problems such as deterioration of workability due to strain aging are caused. Therefore, even when it is actively contained, the content is made 0.025% or less.
  • a preferable upper limit is 0.020%, a more preferable upper limit is 0.010%, and a further preferable upper limit is 0.0050%.
  • O 0.0025% or less (excluding 0%) It is known that rolling fatigue breaks starting from inclusions mainly composed of oxide, and O is preferably reduced as much as possible.
  • the upper limit of the O content is 0.0025%.
  • a preferable upper limit is 0.0020%, a more preferable upper limit is 0.0015%, and a further preferable upper limit is 0.0010%.
  • the steel material of the present invention there is an embodiment in which the above components are included and the balance is iron and inevitable impurities.
  • the essential components contained in the steel are as described above, the following elements may be contained within a predetermined range as necessary.
  • the steel material of the present invention includes the following elements, with the balance being iron and inevitable impurities.
  • Cu 0.25% or less (not including 0%), Ni: 0.25% or less (not including 0%), Mo: 0.25% or less (not including 0%) Cu, Ni, and Mo all have the effect of improving the hardenability and contribute to the improvement of rolling fatigue characteristics as described above.
  • the content is excessive, problems such as deterioration of workability are caused, so Cu: 0.25% or less, Ni: 0.25% or less, and Mo: 0.25% or less.
  • the preferable upper limit is 0.20%, the more preferable upper limit is 0.15%, and the more preferable upper limit is 0.10%.
  • Mo is an essential element of the SUJ4 material and the SUJ5 material, and both are contained in an amount of 0.10 to 0.25%.
  • Nb 0.5% or less (not including 0%), V: 0.5% or less (not including 0%), B: 0.005% or less (not including 0%) Nb, V, and B all have the effect of improving the hardenability and contribute to the improvement of the rolling fatigue characteristics as described above, so are contained as necessary. However, if the content is excessive, characteristic deterioration is caused. Therefore, Nb: 0.5% or less, V: 0.5% or less, and B: 0.005% or less.
  • the upper limit with preferable content of Nb and V is 0.25%, a more preferable upper limit is 0.10%, and a still more preferable upper limit is 0.05%.
  • the upper limit with preferable content of B is 0.004%, a more preferable upper limit is 0.003%, and a still more preferable upper limit is 0.002%.
  • Ca, REM (Ce, Y, La, Nd), Mg, Li, and Zr all have the effect of refining oxide and sulfide inclusions, and contribute to the improvement of rolling fatigue characteristics. It is contained as necessary. However, if the content is excessive, deterioration of characteristics is caused. Therefore, Ca: 0.05% or less, REM: 0.05% or less, Mg: 0.02% or less, Li: 0.02% or less, Zr : 0.2% or less.
  • the upper limit with preferable content of Ca and REM is 0.02%, A more preferable upper limit is 0.01%, Furthermore, a preferable upper limit is 0.005%. Moreover, the upper limit with preferable content of Mg and Li is 0.01%, A more preferable upper limit is 0.005%, Furthermore, a preferable upper limit is 0.001%.
  • the preferable upper limit of the Zr content is 0.1%, the more preferable upper limit is 0.05%, and the more preferable upper limit is 0.01%.
  • REM represents one or more of Ce, Y, La and Nd, and when contained alone, the single amount only needs to satisfy the above range, and when two or more are used in combination, The total amount only needs to satisfy the above range.
  • Pb 0.5% or less (not including 0%), Bi: 0.5% or less (not including 0%), Te: 0.1% or less (not including 0%)
  • Pb, Bi, and Te all have an effect of improving machinability and are contained as necessary.
  • Pb 0.5% or less
  • Bi 0.5% or less
  • Te 0.1%
  • a preferable upper limit of the content of Pb and Bi is 0.2%, a more preferable upper limit is 0.1%, and a further preferable upper limit is 0.05%.
  • the upper limit with preferable content of Te is 0.05%, a more preferable upper limit is 0.02%, and a still more preferable upper limit is 0.01%.
  • the upper limit of the preferable content is 0.01%, the more preferable upper limit is 0.005%, and the more preferable upper limit is 0.002%.
  • the bearing is rolled into a rolled wire rod by hot rolling the bearing steel, then spheroidizing annealing, cutting, cold forging into a predetermined shape, quenching and tempering, and finally finishing. Can be manufactured.
  • the finish rolling temperature in the hot rolling process In order to make the ferrite crystal grain size 20 ⁇ m or less as defined in the present invention, it is necessary to control the finish rolling temperature in the hot rolling process and the cooling rate after finish rolling. Conventionally, from the viewpoint of softening the material, cooling after finish rolling has been generally performed by slow cooling. However, if annealing is performed after finish rolling, the austenite coarsens during the slow cooling, and as a result, the ferrite after transformation also tends to coarsen.
  • the coarsening of ferrite reduces the hardness as it is rolled, but it does not necessarily lead to a decrease in hardness after spheroidizing treatment.
  • the inventors have suppressed the austenite coarsening by setting the final rolling temperature to 850 ° C. or lower and the average cooling rate to 740 ° C. after finishing rolling to 10 ° C./s or higher. It was found that the ferrite crystal grain size could be 20.0 ⁇ m or less.
  • the Cr concentration in the carbide is greatly affected by the heating temperature and the rolling temperature.
  • cementite In order to increase the Cr concentration in the carbide, it is necessary that the cementite remains at a high temperature. The higher the temperature, the more the diffusion is promoted and the Cr concentration proceeds.
  • the temperature when the temperature is too high, the cementite dissolves and the volume fraction of the Cr-concentrated cementite decreases. Since cementite precipitated during cooling does not have a high Cr concentration, when the cementite fraction during cooling increases, the proportion of carbides with a high Cr concentration decreases. In particular, the Cr concentration in cementite that precipitates during cooling decreases as it precipitates at low temperatures.
  • the present inventors have studied, and as a result, the temperature from heating to finish rolling is set to a temperature range of 750 to 870 ° C., and the average cooling rate from 740 ° C. to 500 ° C. is 5 ° C. / It was confirmed that the Cr concentration in the carbide could be 6.0% by mass or more by setting it to s or less.
  • slabs were manufactured by continuous casting using steels having respective component compositions shown in Table 1, and the slabs were disassembled and rolled into 155 mm square steel slabs. Using this steel slab, rolled wire rods were obtained under the production conditions shown in Tables 2 and 3. Various measurements and tests shown below were carried out using this rolled wire. In each component composition shown in Table 1, the balance is iron and inevitable impurities.
  • the ferrite crystal grain size was determined by performing mirror polishing on the cross section perpendicular to the longitudinal direction of the rolled wire rod, etching with nital, and observing the structure with an optical microscope. ), 400-1000 times photographs were taken according to the tissue size, and the results for a total of 30 fields were averaged.
  • the high carbon steel wire of the present invention may have a mixed structure of ferrite and pearlite or a structure mainly composed of pearlite.
  • the pearlite nodule (block) size corresponding to the crystal grain size of ferrite is measured. did.
  • “JIS G 0551” describes a particle size measurement method for only the ferrite portion excluding the pearlite portion.
  • the crystal unit is determined by the contrast after etching. did.
  • the ferrite particle size and pearlite nodule size were collectively measured.
  • the Cr concentration in the carbide was determined by measuring the Cr concentration in the electrolytically extracted residue. First, the rolled wire was cut to a length of 20 mm, and then the portion from the outer surface to D / 4 (D: diameter) was removed by grinding to obtain a sample for electrolysis. Next, in order to remove the processed layer, preliminary electrolysis was performed by a constant current electrolysis method using a 10% AA-based electrolytic solution (% is a mass ratio). Thereafter, electrolysis by a constant current electrolysis method using a 10% AA-based electrolyte as main electrolysis was performed, and the residue was collected by filtering the electrolyte solution by a suction filtration method. For filtration, a polycarbonate mesh having a pore size of 0.1 ⁇ m was used. The obtained residue was treated for analysis, and then the Cr concentration was measured by ICP issuance analysis.
  • Vickers hardness Vickers hardness was measured using each rolled wire after spheroidizing annealing. About the cross section perpendicular
  • test results are shown in Tables 2-3. In this test, even when spheroidizing annealing is carried out under shortening conditions, a test with a Vickers hardness of 190 Hv or less is accepted.
  • No. 8, 9, 11 to 14, 17 to 19, 21, 22, 24 to 37 are examples of the invention that satisfy the requirements of the present invention. Even when the spheroidizing annealing is performed under a shortened condition, it is the same as the normal condition. The Vickers hardness was 190 Hv or less. From this result, no. Nos. 8, 9, 11 to 14, 17 to 19, 21, 22, 24 to 37 are high carbon steels capable of shortening the spheroidizing time during production and sufficiently reducing the hardness after spheronizing. It can be said that it is a wire.
  • the production method of the high carbon steel wire and the high carbon steel wire of the present invention from the viewpoint of cost and environmental load, it is possible to shorten the spheroidizing treatment time during production, and at the same time, the die during cold forging The life can be improved, and the hardness can be sufficiently reduced from the viewpoint of power saving during production.

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Abstract

L'invention concerne un fil-machine d'acier à haute teneur en carbone dont la dureté est suffisamment réduite et qui est apte à diminuer le temps de sphéroïdisation pendant sa fabrication ; et un procédé de fabrication d'un fil-machine d'acier à haute teneur en carbone. La présente invention concerne un fil-machine d'acier à haute teneur en carbone qui contient, en % en masse, 0,95-1,10 % de C, 0,15-0,70 % de Si, 1,15 % ou moins de Mn (à l'exclusion de 0 %), 0,90-1,60 % de Cr, 0,050 % ou moins de P, 0,050 % ou moins de S, 0,100 % ou moins d'Al, 0,015 % ou moins de Ti, 0,025 % ou moins de N et 0,0025 % ou moins d'O, le reste étant constitué de fer et des impuretés inévitables. Ce fil-machine d'acier à haute teneur en carbone présente une dimension cristalline de grain de ferrite de 20,0 μm ou moins et une concentration en Cr dans les carbures de 6,0 % en masse ou plus.
PCT/JP2012/060783 2011-04-20 2012-04-20 Fil-machine d'acier à haute teneur en carbone et procédé de fabrication d'un fil-machine d'acier à haute teneur en carbone Ceased WO2012144630A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2011-094098 2011-04-20
JP2011094098 2011-04-20

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WO2012144630A1 true WO2012144630A1 (fr) 2012-10-26

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KR20160147041A (ko) 2014-06-02 2016-12-21 신닛테츠스미킨 카부시키카이샤 강 선재
CN117327973A (zh) * 2023-08-23 2024-01-02 江阴兴澄合金材料有限公司 一种含硫高碳铬轴承钢盘条及其制造方法
CN119121052A (zh) * 2024-08-27 2024-12-13 鞍钢股份有限公司 一种1200MPa级索道绳用盘条及其制备方法

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JP6082342B2 (ja) * 2013-12-20 2017-02-15 株式会社神戸製鋼所 高炭素鋼線材の製造方法
EP3211106B1 (fr) * 2014-10-20 2020-05-06 Nippon Steel Corporation Fil machine en acier pour palier présentant d'excellentes aptitude à l'étirage et aptitude à la formation de bobine après étirage
JP6193842B2 (ja) * 2014-12-11 2017-09-06 株式会社神戸製鋼所 軸受用鋼線材
KR102047403B1 (ko) 2017-12-26 2019-11-22 주식회사 포스코 냉간압조용 선재, 이를 이용한 가공품 및 이들의 제조방법
KR102421642B1 (ko) * 2019-12-20 2022-07-18 주식회사 포스코 베어링용 선재 및 이의 제조방법
JP7587106B2 (ja) * 2020-07-09 2024-11-20 日本製鉄株式会社 鋼線及び金網

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JP2000119808A (ja) * 1998-10-13 2000-04-25 Kobe Steel Ltd 迅速球状化可能で冷間鍛造性の優れた鋼線材およびその製造方法
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Publication number Priority date Publication date Assignee Title
CN105164293A (zh) * 2013-03-28 2015-12-16 株式会社神户制钢所 生拉性优异的高强度钢丝用线材和高强度钢丝
KR20160147041A (ko) 2014-06-02 2016-12-21 신닛테츠스미킨 카부시키카이샤 강 선재
CN117327973A (zh) * 2023-08-23 2024-01-02 江阴兴澄合金材料有限公司 一种含硫高碳铬轴承钢盘条及其制造方法
CN119121052A (zh) * 2024-08-27 2024-12-13 鞍钢股份有限公司 一种1200MPa级索道绳用盘条及其制备方法

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