WO2016088803A1 - 伸線加工性に優れる高炭素鋼線材 - Google Patents

伸線加工性に優れる高炭素鋼線材 Download PDF

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WO2016088803A1
WO2016088803A1 PCT/JP2015/083879 JP2015083879W WO2016088803A1 WO 2016088803 A1 WO2016088803 A1 WO 2016088803A1 JP 2015083879 W JP2015083879 W JP 2015083879W WO 2016088803 A1 WO2016088803 A1 WO 2016088803A1
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pearlite
wire
steel wire
wire drawing
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PCT/JP2015/083879
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English (en)
French (fr)
Japanese (ja)
Inventor
俊彦 手島
大藤　善弘
敏之 真鍋
大輔 平上
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新日鐵住金株式会社
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Priority to EP15865720.5A priority Critical patent/EP3228721A4/de
Priority to KR1020177018113A priority patent/KR101952527B1/ko
Priority to JP2016562658A priority patent/JP6394708B2/ja
Priority to MX2017006990A priority patent/MX2017006990A/es
Priority to CN201580075308.5A priority patent/CN107208208B/zh
Publication of WO2016088803A1 publication Critical patent/WO2016088803A1/ja

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
    • 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
    • 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
    • C22C38/22—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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/28—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
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a high carbon steel wire used for various wire ropes such as a power transmission cable and a suspension bridge cable after drawing.
  • High carbon steel wire used for cables for transmission lines, cables for suspension bridges, various wire ropes, etc. has good drawing workability from the viewpoint of productivity in addition to high strength and high ductility after drawing. Desired. Due to such demands, various high-quality high-carbon wires have been developed so far.
  • Patent Document 1 proposes a technique for obtaining a good wire drawing workability by reducing individual N by adding Ti and reducing strain aging by individual Ti.
  • Patent Document 2 proposes a technique for obtaining low strength and good wire drawing workability by controlling the cementite form to be spherical.
  • patent document 3 while specifying each content of C, Si, Mn, P, S, N, Al, and O in steel materials, by controlling a 2nd phase ferrite area rate and a pearlite lamella space
  • Patent Document 4 C: 0.6 to 1.1% high carbon steel wire, 95% or more of pearlite structure, and pearlite pearlite block measured by EBSP device at the center of hot rolled wire
  • High ductility high carbon steel wires having a maximum particle size of 45 ⁇ m or less and an average value of 10 to 25 ⁇ m have been proposed.
  • This invention is made
  • the present invention is a high carbon steel wire used as a material for a high strength steel wire, the summary of which is as follows.
  • High carbon steel wire after hot rolling, steel component is mass%, C: 0.60 to 1.10%, Si: 0.02 to 2.0%, Mn: 0.1 to 2.0%, Cr: 0.3-1.6%, Al: 0.001-0.05%, N: 0.008% or less, P: 0.020% or less, S: 0.0.
  • the structure is limited to 020% or less, the balance is made of Fe and inevitable impurities, and the area ratio in the cross section perpendicular to the longitudinal direction of the wire rod is pearlite of 95% or more, and the average lamellar spacing of the pearlite is 50 to 100 nm.
  • the high carbon whose average pearlite block diameter is 5 ⁇ m ⁇ pearlite block diameter ⁇ 15 ⁇ m at the center of the cross section perpendicular to the longitudinal direction of the wire from the center of the diameter D to the diameter D of the wire.
  • Steel wire rod The high carbon whose average pearlite block diameter is 5 ⁇ m ⁇ pearlite block diameter ⁇ 15 ⁇ m at the center of the cross section perpendicular to the longitudinal direction of the wire from the center of the diameter D to the diameter D of the wire.
  • the industrial contribution is extremely remarkable, such as being able to provide a high ductility high carbon steel wire while having a tensile strength of 1300 MPa or more.
  • FIG. 1 shows a central part A and an outer peripheral part B in a cross section perpendicular to the longitudinal direction of the wire.
  • a region within a circle having a diameter of 1 / 2D from the center is defined as a central portion A with respect to a wire having a diameter of Dmm, and a region within 500 ⁇ m from the surface layer is an outer peripheral portion. B is defined.
  • the pearlite block diameter can be measured by an electron backscatter (EBSD) method using the central portion A in FIG. 1 as a measurement location.
  • EBSD electron backscatter
  • a cross section perpendicular to the longitudinal direction of the wire is mirror-polished with colloidal silica particles, and measurement is performed by the EBSD method in the vicinity of the center in the radial direction to create a map of the ferrite crystal orientation.
  • the mapping area is a rectangular area with each side of 500 ⁇ m or more, the pixel shape is a regular hexagonal element arrangement, and the measurement interval is 0.5 ⁇ m.
  • the degree of integration of the ferrite crystal orientation ⁇ 110> in the longitudinal direction of the wire can be measured by plotting the crystal orientation of each pixel on a ⁇ 110 ⁇ pole figure with the outer peripheral portion B of FIG. More specifically, the degree of integration of the ferrite crystal orientation ⁇ 110> is measured by generating a ⁇ 110 ⁇ pole figure using the measurement result of the EBSD method and analyzing the obtained pole figure by texture analysis. Is possible.
  • the degree of integration is expressed as an intensity ratio, where 1 is the case where the crystal orientation is random.
  • the ferrite crystal orientation is identified by the EBSD method, information on the crystal orientation of the ferrite is given to each hexagonal pixel, and as a result, information on the angle difference of the crystal orientation is present at the boundary between adjacent pixels. Defined. If there is a continuous difference in the tilt angle of 9 ° or more, such as a 9 ° or more ferrite crystal orientation tilt difference at the boundary between two pixels, and the adjacent pixel boundary is also 9 ° or more, connect them. And defined as pearlite block grain boundaries.
  • the pearlite block grain boundary branches.
  • this pixel boundary is not regarded as a pearlite block grain boundary and is ignored.
  • a pixel boundary having a ferrite misorientation of 9 ° or more is defined over the entire rectangular area, and if the pixel boundary surrounds one closed area, this area is defined as one perlite block. Is defined as a pearlite block grain boundary.
  • the pearlite block grain boundaries are shown on the ferrite crystal orientation map, and the pearlite block diameter is measured.
  • one grain of the defined perlite block is composed of 25 pixels or less, it is treated as noise and ignored.
  • the pearlite block and the pearlite nodule are synonymous.
  • the perlite is a lamellar perlite.
  • the lamellar spacing corrodes the cross section perpendicular to the longitudinal direction of the wire with nital, and draws a line perpendicular to the 5 lamellar spacing at the place where the lamellar spacing is the smallest in the field of view taken at a magnification of 10,000 using an SEM. It can be obtained by dividing the length of 5 intervals by 5.
  • photography with SEM is performed in 10 or more visual fields, and it is set as an average value by dividing the lamellar space calculated
  • the wire drawing workability is evaluated by immersing a test material having a length of 10 m in hydrochloric acid to remove the scale, washing with water, performing a bond treatment, and performing a dry wire drawing.
  • the wire drawing can be performed using a WC-Co cemented carbide die having a die approach (total) angle of 20 ° and a bearing length of about 0.3 times the diameter.
  • the wire drawing speed is 50 m / min, and a dry wire drawing lubricant mainly composed of sodium stearate and calcium stearate can be used.
  • the die diameter is reduced so that the cross-section reduction rate is 20%, and wire drawing is performed until disconnection occurs.
  • FIG. 2 is a test result of a wire coil that is a reference for determining that wire drawing workability is good.
  • the degree of wire drawing is 1.7
  • the number of breaks is 1, and the cumulative break rate on the vertical axis is 0.05 (1/20).
  • the number of breaks is 5 and the breaking rate is 0.25.
  • cumulative breaking rate 0.05 before that (drawing degree 1.7) is added, cumulative breaking The rate is 0.3.
  • a cumulative breaking rate will be set to 1.0.
  • the degree of wire drawing at which the cumulative breaking rate is 0.5 is obtained from the graph and defined as wire drawing workability.
  • the wire drawing workability of the wire coil that is a criterion for determining that the wire drawing workability is good is 2.23.
  • the wire drawing rate at which the cumulative breaking rate is 0.9 is 3.0
  • the wire drawing rate at which the cumulative breaking rate is 1.0 is 3.12. Therefore, in the present invention, the wire drawing workability is evaluated as good when it is 2.23 or more, more preferably, the wire drawing workability is 2.53 or more, and more preferably, the wire drawing workability is evaluated as 2.95 or more. To do.
  • C C is an element whose structure is pearlite and improves strength.
  • the amount of C is less than 0.60%, a non-pearlite structure such as grain boundary ferrite is generated, the wire drawing workability is impaired, and the tensile strength of the ultra fine steel wire is also reduced.
  • the C content exceeds 1.10%, a non-pearlite structure such as pro-eutectoid cementite is generated, and the wire drawing workability is deteriorated. Therefore, the C content is limited to a range of 0.60 to 1.10%. Preferably, the C content is 0.65% or more.
  • Si Si is an element used for deoxidation of steel and contributes to solid solution strengthening. In order to obtain the effect, 0.02% or more of Si is added. Preferably, the Si amount is 0.05% or more. On the other hand, if the Si content exceeds 2.0%, surface decarburization is likely to occur in the hot rolling process, so the upper limit is made 2.0%. Preferably, the Si amount is 1.0% or less, more preferably 0.5% or less.
  • Mn Mn is an element used for deoxidation and desulfurization, and 0.1% or more is added. On the other hand, if the amount of Mn exceeds 2.0%, the pearlite transformation is remarkably delayed and the patenting process takes a long time, so the amount of Mn is set to 2.0% or less.
  • the amount of Mn is preferably 1.0% or less.
  • Cr Cr is an element that refines the old ⁇ grain size and refines the pearlite structure, and contributes to increasing the strength. In order to obtain the effect, 0.3% or more of Cr is added. On the other hand, if the Cr content exceeds 1.6%, pro-eutectoid cementite precipitates and the wire drawing workability is lowered, so the upper limit is made 1.6%. Preferably it is 1.3% or less. More preferably, the content is 1.0% or less.
  • Al Al is an element having a deoxidizing action and is necessary for reducing the amount of oxygen in the steel. However, this effect is difficult to obtain when the Al content is less than 0.001%. On the other hand, Al tends to form hard oxide inclusions, and particularly when the Al content exceeds 0.05%, the formation of coarse oxide inclusions becomes remarkable, so that the wire drawing processability is lowered. Becomes prominent. Therefore, the Al content is set to 0.001 to 0.05%. A more preferable lower limit is 0.01% or more, and a more preferable upper limit is 0.04% or less.
  • N N is an element that adheres to dislocations during cold wire drawing to improve the strength of the steel wire, but reduces wire drawing workability.
  • the N content exceeds 0.008%, the wire drawing workability is significantly lowered. Therefore, the N content is limited to 0.008% or less. More preferably, it is 0.005% or less.
  • P P is easily segregated in steel, and when segregated, the eutectoid transformation is remarkably delayed, so that the eutectoid transformation is not completed and hard martensite is easily formed. In order to prevent this, the P content is limited to 0.02% or less.
  • MnS is formed in a large amount and the ductility of the steel is lowered, so it is limited to not more than 0.020%. More preferably, it is 0.01% or less.
  • Mo is optional. If added, it has the effect of increasing the tensile strength of the steel wire. In order to obtain this effect, it is desirable to add 0.02% or more of Mo. However, if the Mo content exceeds 0.20%, a martensite structure is easily generated, and the wire drawing workability is lowered. Therefore, the Mo content is preferably 0.02 to 0.20%. More preferably, it is 0.08% or less.
  • V The addition of V is optional. If added, carbonitride is formed in the steel wire rod, the pearlite block diameter is reduced, and the wire drawing workability is improved. In order to obtain this effect, it is desirable to add 0.02% or more of V. However, if the V content exceeds 0.20%, coarse carbonitrides are likely to be produced, and the wire drawing workability may be reduced. Therefore, the V content is preferably 0.02 to 0.20%. More preferably, it is 0.08% or less.
  • Nb Addition of Nb is optional. If added, carbonitride is formed in the steel wire rod, the pearlite block diameter is reduced, and the wire drawing workability is improved. In order to obtain this effect, it is desirable to add Nb 0.002% or more. However, if the Nb content exceeds 0.05%, coarse carbonitrides are likely to be generated, and the wire drawing workability may be reduced. Therefore, the Nb content is preferably 0.002 to 0.05%. More preferably, it is 0.02% or less.
  • Ti The addition of Ti is optional. If added, carbide or nitride is formed in the steel wire rod, the pearlite block diameter is reduced, and the wire drawing workability is improved. In order to obtain this effect, it is desirable to add 0.002% or more of Ti. However, if the Ti content exceeds 0.05%, coarse carbides or nitrides are likely to be formed, and the wire drawing workability may begin to deteriorate. Therefore, the Ti content is preferably 0.02 to 0.05%. More preferably, it is 0.03% or less.
  • B The addition of B is optional. If added, the solid solution N in the steel wire is formed as BN, and the individual solution N in the steel is reduced to improve the wire drawing workability. In order to acquire this effect, it is desirable to add B 0.0003% or more. However, if the B content exceeds 0.003%, coarse nitrides are likely to be generated, and the wire drawing workability may be reduced. Therefore, the B content is preferably 0.0003 to 0.003%. More preferably, it is 0.002% or less.
  • Non-pearlite structures such as pro-eutectoid ferrite and pro-eutectoid cementite cause cracks in the final wire drawing.
  • the area ratio of pearlite is 95% or more in order to improve the wire drawing workability.
  • the balance is a non-pearlite structure such as pro-eutectoid ferrite or pro-eutectoid cementite.
  • said metal structure can be specified by observing with a scanning electron microscope, after cut out the cross section cut
  • the area ratio of each metal structure can be calculated
  • the observation magnification is preferably 1000 times or more, and the observation area is preferably 1000 ⁇ m 2 or more, for example.
  • the area ratio is specified by, for example, a point counting method, it is preferable that the number of measurement points is 200 or more.
  • the pearlite block diameter (hereinafter also referred to as pearlite block diameter) is 15 ⁇ m or less because wire drawing workability deteriorates when it exceeds 15 ⁇ m. More preferably, it is 12 ⁇ m or less. Further, if the pearlite block diameter is 5 ⁇ m or less, the non-pearlite structure increases, so 5 ⁇ m is set as the lower limit.
  • the degree of integration of the ferrite crystal orientation ⁇ 110> is set to 1.3 or more. Preferably it is 1.5 or more, More preferably, it is 1.7 or more.
  • the degree of integration of the pearlite block diameter and the ferrite crystal orientation ⁇ 110> can be specified by the EBSD method as described above.
  • the metal structure in the present invention is mainly pearlite, and the steel wire rod has a target tensile strength of 1300 MPa or more, preferably 1350 MPa or more, more preferably 1400 MPa or more.
  • the average lamellar spacing of pearlite shown in the examples described later needs to be 100 nm or less.
  • the target strength cannot be obtained, and the wire drawing work hardening rate decreases, so the lower limit was set to 50 nm.
  • the steel wire rod of the present invention is manufactured by melting and casting steel having the above-described components by a conventional method, and subjecting the obtained steel piece to hot rolling.
  • Hot rolling is performed by heating the steel slab to about 1150 ° C.
  • the finishing temperature of hot rolling is 740 to 880 ° C.
  • it is cooled (primary cooling) at 25 ° C./sec to 40 ° C./sec until reaching 550 ° C. to 650 ° C. by means of blast cooling, mist cooling, water cooling, etc. After holding for 30 seconds to 180 seconds in the range, it is cooled (secondary cooling) to 300 ° C.
  • the diameter of a wire is not specifically limited as long as the work hardening required when it is set as a steel wire can be ensured.
  • the holding temperature exceeds 650 ° C.
  • the old ⁇ grain size becomes coarse and the strength decreases, so the upper limit was set to 650 ° C.
  • the temperature is lower than 550 ° C.
  • the non-pearlite structure increases, so the lower limit was set to 550 ° C.
  • the upper limit is set to 180 seconds.
  • the steel wire material and the method for manufacturing the steel wire material according to the embodiment of the present invention will be specifically described with reference to examples.
  • the Example shown below is an example to the last of the manufacturing method of the steel wire which concerns on embodiment of this invention, and a steel wire, Comprising:
  • the manufacturing method of the steel wire and steel wire which concerns on this invention is limited to the following example. It is not something.
  • the pearlite structure is commonly obtained by changing the hot rolling conditions shown in Table 2, but the pearlite block diameter in the center and the ferrite crystal orientation in the surface layer.
  • Wire rods having different degrees of integration and tensile strength were produced. These wires were evaluated by the wire drawing limit strain. The results are shown in Table 3.
  • the wire rod was immediately cooled to a temperature range of 550 ° C. to 650 ° C. by spraying cooling water with a nozzle in a cooling zone provided in a rolling line shape. At this time, the reached temperature was controlled by changing the amount of water and the cooling time. Further, the wire was subsequently cooled to a range of 650 ° C. to 550 ° C. at a cooling rate of 5 ° C./sec to 25 ° C./sec by blast cooling. Thereafter, the pearlite transformation was completed by maintaining the temperature in these temperature ranges for about 60 seconds, and the mixture was cooled to room temperature by air cooling.
  • the pearlite area ratio (%), pearlite block diameter, lamellar spacing, ferrite crystal orientation, and tensile strength of these steel wires were measured.
  • the pearlite area ratio was obtained by etching a sample obtained by cutting a wire and mirror-polishing the cross section with a mixed solution of nitric acid and ethanol, and observing the central portion between the surface and the center of the wire at a magnification of 2000 times.
  • the pearlite block diameter and lamellar spacing were measured in a region of 62500 ⁇ m 2 in the range of 5 mm center of the steel wire rod.
  • the ferrite orientation ⁇ 110> integration degree was measured in an area of 62500 ⁇ m 2 within a range of 500 ⁇ m from the surface layer using an EBSD measuring apparatus manufactured by TSL.
  • the tensile test was performed in accordance with JIS Z 2241.
  • wire drawing workability as described above, dry wire drawing is performed, the total number of wire breaks is 20 times, the relationship between wire drawing true strain and cumulative breaking rate is plotted, and the drawing rate at which the cumulative breaking rate is 50% is plotted. Evaluated by line true strain.
  • the results are shown in Table 3.
  • PBS is the average pearlite block diameter.
  • No. 10 has a high holding temperature, the lamellar spacing is large and the tensile strength is insufficient.
  • No. No. 11 has a low Cr content, and the pearlite block diameter is not sufficiently refined, so that the wire drawing limit strain is small.
  • No. No. 12 has a large amount of Mn, the pearlite transformation is not completed, and the pearlite area ratio is very small, so that the wire drawing limit strain is small.
  • No. No. 13 has a high C content, and since proeutectoid cementite is generated, the pearlite area ratio is small, and the wire drawing limit strain is small.
  • No. 18 has a high finish rolling temperature and a coarse old ⁇ grain size, so that the pearlite block diameter is large and the wire drawing limit strain is small.
  • No. No. 19 has a low secondary cooling rate, the shape of the lamellar pearlite is broken, and the tensile strength is reduced.
PCT/JP2015/083879 2014-12-05 2015-12-02 伸線加工性に優れる高炭素鋼線材 WO2016088803A1 (ja)

Priority Applications (5)

Application Number Priority Date Filing Date Title
EP15865720.5A EP3228721A4 (de) 2014-12-05 2015-12-02 Stahldrahtstange mit hohem kohlenstoffanteil und hervorragender drahtziehbarkeitseigenschaften
KR1020177018113A KR101952527B1 (ko) 2014-12-05 2015-12-02 신선 가공성이 우수한 고탄소강 선재
JP2016562658A JP6394708B2 (ja) 2014-12-05 2015-12-02 伸線加工性に優れる高炭素鋼線材
MX2017006990A MX2017006990A (es) 2014-12-05 2015-12-02 Barra de alambre de acero con alto contenido de carbono que tiene excelentes propiedades de estiramiento de alambre.
CN201580075308.5A CN107208208B (zh) 2014-12-05 2015-12-02 拉丝加工性优异的高碳钢线材

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JP2014247258 2014-12-05
JP2014-247258 2014-12-05

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