WO2015190422A1 - Tige de fil métallique en acier inoxydable duplex à haute résistance, fil métallique en acier inoxydable duplex à haute résistance et procédé de fabrication s'y rapportant ainsi qu'élément ressort - Google Patents

Tige de fil métallique en acier inoxydable duplex à haute résistance, fil métallique en acier inoxydable duplex à haute résistance et procédé de fabrication s'y rapportant ainsi qu'élément ressort Download PDF

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Publication number
WO2015190422A1
WO2015190422A1 PCT/JP2015/066436 JP2015066436W WO2015190422A1 WO 2015190422 A1 WO2015190422 A1 WO 2015190422A1 JP 2015066436 W JP2015066436 W JP 2015066436W WO 2015190422 A1 WO2015190422 A1 WO 2015190422A1
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stainless steel
steel wire
amount
duplex stainless
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Japanese (ja)
Inventor
祥太 山先
光司 高野
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Nippon Steel Stainless Steel Corp
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Nippon Steel and Sumikin Stainless Steel Corp
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Priority to JP2016527787A priority Critical patent/JP6286540B2/ja
Priority to KR1020157019800A priority patent/KR101600251B1/ko
Publication of WO2015190422A1 publication Critical patent/WO2015190422A1/fr
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    • 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
    • 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
    • C22C38/18—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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
    • F16F—SPRINGS; SHOCK-ABSORBERS; MEANS FOR DAMPING VIBRATION
    • F16F1/00—Springs
    • F16F1/02—Springs made of steel or other material having low internal friction; Wound, torsion, leaf, cup, ring or the like springs, the material of the spring not being relevant
    • F16F1/04—Wound springs
    • F16F1/06—Wound springs with turns lying in cylindrical surfaces

Definitions

  • the present invention relates to a high-strength duplex stainless steel wire, a high-strength duplex stainless steel wire and a method for producing the same, and a spring component.
  • the high-strength duplex phase suitable for a spring component and excellent in rigidity and twist workability.
  • the present invention relates to a stainless steel wire and a wire used therefor.
  • the stainless steel obtained by the above technique contains a large amount of rare metal expensive Ni, which is not desirable from the viewpoint of manufacturing cost. Therefore, in recent years, there is an increasing demand for cost reduction by reducing Ni (reducing Ni content) for such stainless steel.
  • High-Mn stainless steel has been proposed as a measure for reducing Ni. And as a means for improving the strength of the high Mn-based stainless steel, there is a multiphase organization of the metal structure (making the metal structure a multiphase structure) (for example, Patent Document 3).
  • the technique described in Patent Document 3 controls the amount of austenite ( ⁇ ) in the multiphase structure to increase the strength.
  • the technique described in Patent Document 3 does not meet the recent required strength for further enhancement of strength, and the rigidity is not sufficient.
  • Patent Document 3 is a technique suitable for a steel sheet used for a structural member that requires high strength, and has a multiphase structure (steel wire material having a multiphase structure). The technology using) has not been studied yet.
  • An object of the present invention is to provide a high-strength duplex stainless steel material excellent in rigidity and twist workability, a high-strength duplex stainless steel wire, a manufacturing method thereof, and a spring component.
  • a high-Mn, low-Ni-based inexpensive raw material that defines the Md30 value in the austenite phase ( ⁇ ) and the SFE that is a generation index of stacking fault energy
  • wire drawing process control drawing area reduction (50 to 90%)
  • BA heat treatment strand annealing temperature (950 to 1150 ° C.)
  • the deformation texture of the ferrite phase ( ⁇ ) is oriented to RD // ⁇ 100 ⁇ ( ⁇ 100 ⁇ plane parallel to the RD direction) by the work-induced martensite phase (work-induced ⁇ ′).
  • the deformed texture of ⁇ is also oriented to RD // ⁇ 100 ⁇ due to low SFE (small SFE value). Thereby, the rigidity and twist workability of the obtained steel wire are improved. Further, since the phase ratio of the steel wire according to one embodiment of the present invention is a high ( ⁇ + working induced ⁇ ′) amount (the total amount of the ferrite phase and the working induced martensite phase is large), the austenite system having an FCC structure. It is possible to show higher rigidity than stainless steel wire.
  • the summary of one aspect of the present invention is as follows.
  • the metal structure includes a ferrite phase and an austenite phase, and the amount of the ferrite phase is 20 to 70 vol. % Md30 in the austenite phase represented by the following formula (a) is ⁇ 15 to 45,
  • the F value represented by the following formula (b) is ⁇ 6.12 or less,
  • a high-strength duplex stainless steel wire characterized by SFE in the austenite phase represented by the following formula (c) being -20 to 35.
  • Md30 551-462 (C + N) -9.2Si-8.1Mn-29 (Ni + Cu) -13.7Cr-18.5Mo
  • F value Ni + 30C + 0.12Mn + 18N ⁇ (0.78Cr + 1.17Si + 1.09Mo)
  • SFE ⁇ 53 + 6.2Ni + 0.7Cr + 3.2Mn + 9.3Mo
  • the element symbol in a formula means content (mass%) in the steel of the element.
  • the metal structure has a multiphase structure composed of a ferrite phase, an austenite phase and a work-induced martensite phase, and the amount of the ferrite phase is 20 to 70 vol. %, And the amount of the processing-induced martensite phase is 5 to 50 vol. %, And the total amount of the ferrite phase and the work-induced martensite phase is 30 vol.
  • Md30 in the austenite phase represented by the following formula (a) is ⁇ 15 to 45
  • the F value represented by the following formula (b) is ⁇ 6.12 or less
  • a high-strength duplex stainless steel wire characterized by SFE in the austenite phase represented by the following formula (c) being -20 to 35.
  • Md30 551-462 (C + N) -9.2Si-8.1Mn-29 (Ni + Cu) -13.7Cr-18.5Mo
  • F value Ni + 30C + 0.12Mn + 18N ⁇ (0.78Cr + 1.17Si + 1.09Mo)
  • SFE ⁇ 53 + 6.2Ni + 0.7Cr + 3.2Mn + 9.3Mo
  • the element symbol in a formula means content (mass%) in the steel of the element.
  • the high-strength duplex stainless steel according to any one of (6) to (10) above which uses the high-strength duplex stainless steel wire according to any one of (1) to (5) above.
  • a method of manufacturing a steel wire A primary wire drawing step of drawing the high-strength duplex stainless steel wire with a reduction in area of 50 to 90%, and then the high-strength duplex stainless steel wire at 950 to 1150 ° C. for 5 min or less.
  • a spring component comprising the high-strength duplex stainless steel wire according to any one of (6) to (10) above.
  • the present invention it is possible to provide a high-strength duplex stainless steel material excellent in rigidity and twist workability, a high-strength duplex stainless steel wire, a manufacturing method thereof, and a spring component.
  • the high-strength duplex stainless steel wire and stainless steel wire according to one aspect of the present invention are inexpensive and excellent in strength and rigidity, the rigidity and twist can be obtained by applying the steel wire to a spring component or the like. Parts such as a spring excellent in workability can be provided at low cost.
  • Sectional drawing cross-sectional view along the central axis of a through-hole of a wire drawing die is shown.
  • the high-strength double-phase stainless steel material according to the present embodiment (hereinafter also simply referred to as high-strength double-phase stainless steel material, stainless steel wire, or wire) is mass%, C: 0.01 to 0.21% or less, Si : 0.05 to 3.2%, Mn: 0.1 to 15%, Ni: 0.5% or more and less than 5%, Cr: 10 to 25%, and N: 0.01 to 0.35% And the balance is composed of Fe and inevitable impurities, the metal structure includes a ferrite phase and an austenite phase, and the amount of the ferrite phase is 20 to 70 vol.
  • Md30 in the austenite phase represented by the following formula (a) is ⁇ 15 to 45
  • the F value represented by the following formula (b) is ⁇ 6.12 or less
  • the SFE in the austenite phase shown is -20 to 35.
  • C is added in an amount of 0.01% or more in order to obtain high strength after wire drawing.
  • the C content is 0.21% or less, preferably 0.14% or less.
  • the rigidity may be insufficient. From the above, the C content is 0.01% or more and 0.21% or less.
  • Si is deoxidized and added in an amount of 0.05% or more in order to reduce deoxidation products and ensure strength characteristics.
  • the Si amount is 0.2% or more.
  • Si is added in excess of 3.2%, not only the effect is saturated, but also the wire drawing and twisting workability deteriorates, and the rigidity of the steel wire is deteriorated. Set the upper limit to 3.2%.
  • the amount of Si is preferably 1.5% or less.
  • Mn is an effective element as an alternative element to expensive Ni and is an element that increases SFE, which will be described later. For this reason, after wire drawing, the deformation texture of austenite ( ⁇ ) can be sufficiently oriented to the ⁇ 100 ⁇ plane (RD // ⁇ 100 ⁇ ) parallel to the RD direction, and Mn is the rigidity and twist. Has the effect of improving workability. In order to enjoy these effects, the amount of Mn is made 0.1% or more. The amount of Mn is preferably more than 1%. However, if Mn is added in an amount exceeding 15%, the rigidity of the material and the twisting workability are deteriorated, so the upper limit of the amount of Mn is limited to 15%.
  • Ni is added in an amount of 0.5% or more in order to ensure rigidity and twist workability.
  • the Ni content is 1.0% or more.
  • the upper limit of the Ni amount is less than 5%.
  • the amount of Ni is preferably 4.5% or less.
  • Cr is added in an amount of 10.0% or more to ensure corrosion resistance.
  • the Cr content is 13.0% or more.
  • the upper limit of the Cr content is made 25.0%.
  • the amount of Cr is preferably 24.0% or less.
  • N is added in an amount of 0.01% or more to ensure the rigidity.
  • the N content is 0.04% or less.
  • the upper limit of the N amount is set to 0.35%.
  • the amount of N is preferably 0.30% or less.
  • the stainless steel wire and steel wire of this embodiment are composed of Fe and inevitable impurities other than the elements described above.
  • Typical inevitable impurities include O, S, P and the like, and usually mixed in an amount in the range of 0.0001 to 0.1% as inevitable impurities in the steel manufacturing process.
  • representative optional elements other than the elements described above have been described in the above [2] to [5], and details will be described below. In addition, even if it is an element which is not described in this specification, it can be contained in the range which does not impair the effect of this embodiment.
  • Mo has the effect of improving corrosion resistance, it is preferable to contain 0.05% or more. However, if Mo is contained in an amount exceeding 3.0%, the effect is not only saturated, but conversely, the rigidity and twist workability may be deteriorated. Therefore, it is preferable to contain Mo in an amount in the range of 3.0% or less as necessary. The amount of Mo is more preferably 2.5% or less.
  • Cu can contribute to strength and rigidity as fine Cu precipitates, it is preferable to contain Cu by 0.05% or more. However, if Cu is contained in excess of 3.0%, the rigidity may decrease. Therefore, it is preferable to contain Cu in an amount in the range of 3.0% or less as necessary. The amount of Cu is more preferably 2.5% or less.
  • Co has an effect of improving the rigidity of the wire rod and the steel wire, it is preferably contained at 0.05% or more, more preferably 0.1% or more. However, if Co is contained in excess of 2.5%, not only the effect is saturated, but also the rigidity of the steel wire may be deteriorated. Therefore, it is preferable to contain Co in an amount in the range of 2.5% or less as necessary. The amount of Co is more preferably 1.0% or less, and still more preferably 0.8% or less.
  • B is an element effective in improving the grain boundary strength and improving the strength of the wire rod and steel wire. Therefore, it is preferable to contain 0.0004% or more of B, and more preferably 0.001% or more. However, if B is contained in an amount exceeding 0.012%, the strength may be deteriorated due to the formation of coarse boride. Therefore, it is preferable to contain B in an amount in the range of 0.012% or less as necessary. The amount of B is more preferably 0.010% or less, and still more preferably 0.005% or less.
  • Al is an element effective for promoting deoxidation to improve the cleanliness level of inclusions and improving the strength of wire rods and steel wires. Therefore, Al is preferably contained in an amount of 0.001% or more.
  • the amount of Al is more preferably 0.003% or more, and further preferably 0.005% or more. However, if Al is contained in excess of 2.0%, the effect is saturated and the strength of the material itself is deteriorated. Therefore, it is preferable to contain Al in an amount in the range of 2.0% or less as necessary.
  • the amount of Al is more preferably 1.0% or less, and still more preferably 0.1% or less.
  • W is an element effective for improving the corrosion resistance, so 0.05% or more is preferably contained.
  • the amount of W is more preferably 0.1% or more.
  • W it is preferable to contain W in an amount in the range of 2.5% or less as necessary.
  • the amount of W is more preferably 2.0% or less, and still more preferably 1.5% or less.
  • Sn is an element effective for improving the corrosion resistance, it is preferable to contain 0.01% or more.
  • the amount of Sn is more preferably 0.05% or more.
  • Sn is contained in excess of 2.5%, not only the effect is saturated, but also the rigidity may be deteriorated. Therefore, it is preferable to contain Sn in an amount of 2.5% or less as necessary.
  • the amount of Sn is more preferably 1.0% or less, and still more preferably 0.2% or less.
  • Ti, V, Nb, and Ta form carbonitride to refine the crystal grain size and improve the rigidity of the wire rod and steel wire. Therefore, if necessary, Ti: 1.0% or less, V : One or more selected from 2.5% or less, Nb: 2.5% or less, and Ta: 2.5% or less may be contained. However, if these elements are contained in excess of their prescribed upper limits, coarse inclusions are generated, and the rigidity of the wire rod and steel wire may be reduced.
  • preferable ranges of the amount of each element are Ti: 0.03-0.7%, V: 0.04-1.5%, Nb: 0.04-1.5%, Ta: 0 0.04 to 1.5%, more preferably, Ti: 0.05 to 0.5%, V: 0.08 to 0.9%, Nb: 0.08 to 0.9%, Ta: 0 0.08 to 0.9%.
  • Ca, Mg, Zr, and REM are for deoxidation, and as required, Ca: 0.012% or less, Mg: 0.012% or less, Zr: 0.012% or less, and REM: 0.05% You may contain 1 or more types selected from the following. However, if each of these elements is contained exceeding the specified upper limit, coarse inclusions may be generated and the rigidity of the steel wire may be reduced.
  • preferable ranges of the amount of each element are: Ca: 0.0004 to 0.010%, Mg: 0.0004 to 0.010%, Zr: 0.0004 to 0.010%, REM: 0 .0004 to 0.05%, more preferably Ca: 0.001 to 0.005%, Mg: 0.001 to 0.005%, Zr: 0.001 to 0.005%, REM: 0.00. 001 to 0.05%.
  • the elements can be contained within a range not impairing the effects of the present embodiment. Although other components are not particularly defined in the present embodiment, it is preferable to reduce general impurity elements such as P, S, Zn, Bi, Pb, Se, Sb, H, and Ga as much as possible. .
  • the content (ratio) of these elements is controlled to the extent that solves the problem of the present embodiment, and P ⁇ 400 ppm, S ⁇ 100 ppm, Zn ⁇ 100 ppm, Bi ⁇ 100 ppm, Pb ⁇ 100 ppm as necessary. , Se ⁇ 100 ppm, Sb ⁇ 500 ppm, H ⁇ 100 ppm, Ga ⁇ 500 ppm.
  • the amount ( ⁇ amount) of the ferrite phase is limited to 20 to 70% by volume. If the ⁇ amount of the wire is less than 20%, the rigidity is deteriorated, so the lower limit is made 20%.
  • the amount of ⁇ is preferably 27% or more.
  • the upper limit of the ⁇ amount is limited to 70%.
  • the ⁇ amount is preferably 60% or less.
  • the balance of the metal structure other than the ferrite phase is an austenite phase and an inevitable precipitation phase (a precipitation phase inevitably included).
  • a precipitation phase inevitably included.
  • the Md30 value in the austenite phase is limited to ⁇ 15 to 45.
  • the Md30 value is an index obtained by investigating the relationship between the amount of work-induced martensite after drawing and the component, and it is necessary to control the strength in order to stably secure the fatigue strength of the steel wire. .
  • the Md30 value is a value obtained from the following formula (a).
  • this value in the austenite phase is less than ⁇ 15, it is difficult to form a processing-induced ⁇ ′ phase, and the rigidity is inferior.
  • the Md30 value exceeds 45 the austenite phase becomes unstable, and the work-induced martensite phase is generated in an amount exceeding 50% by volume in the wire drawing process, and the twist workability deteriorates. Therefore, the Md30 value is limited to ⁇ 15 to 45.
  • the Md30 value is ⁇ 10 or more and 40 or less.
  • SFE indicates a generation index of stacking fault energy, and is a value obtained by the following formula (c).
  • SFE value in the austenite phase ( ⁇ ) is less than ⁇ 20, the dislocation structure is planarized, resulting in poor twist workability.
  • the SFE value in ⁇ exceeds 35, the amount of orientation of the deformed texture of austenite to the RD // ⁇ ⁇ 100 ⁇ plane decreases during wire drawing, so that the rigidity is deteriorated. Therefore, the upper limit of the SFE value is limited to 35.
  • SFE is ⁇ 15 or more and 30 or less.
  • F value is a value calculated
  • this value is larger than ⁇ 6.12, the amount of machining-induced ⁇ ′ increases and the twistability is inferior. In addition, the amount of ⁇ decreases, so the rigidity becomes inferior. Therefore, the upper limit of the F value is limited to ⁇ 6.12.
  • the F value is -15 or more and -6.1 or less.
  • F value Ni + 30C + 0.12Mn + 18N ⁇ (0.78Cr + 1.17Si + 1.09Mo) (b)
  • the element symbols in the above formulas (a) to (c) mean the content (mass%) of the element in steel, and when the element content in the formula is 0%, the symbol A value is calculated by substituting “0” in the place.
  • the chemical composition of the steel wire is the same as the chemical composition of the steel wire described above, and satisfies the Md30 value, the F value, and the SFE value.
  • the metal structure of the steel wire has a multiphase structure composed of a ferrite phase, an austenite phase and a work-induced martensite phase, and the amount of the ferrite phase is 20 to 70 vol. %, And the amount of processing-induced martensite phase is 5 to 50 vol. %, And the total amount of ferrite phase and work-induced martensite phase is 30 vol. % Or more.
  • the amount of ⁇ of the steel wire is 20 to 70% by volume as in the case of the wire. If the ⁇ amount of the steel wire is less than 20%, the rigidity is deteriorated, so the lower limit of the ⁇ amount is 20%. The amount of ⁇ is preferably 27% or more. On the other hand, if the amount of ⁇ exceeds 70%, strength characteristics may be deteriorated, so the upper limit is limited to 70%. The ⁇ amount is preferably 60% or less.
  • Steel wire processing induced ⁇ 'amount is 5 vol. If it is less than%, the deformation texture of ⁇ is not sufficiently oriented to RD // ⁇ 100 ⁇ at the time of wire drawing, so that a high rigidity cannot be obtained. Therefore, the lower limit of the processing-induced ⁇ ′ amount of the steel wire is set to 5 vol. %. On the other hand, the processing-induced ⁇ ′ amount is 50 vol. %, Twist workability becomes inferior, so the upper limit is 50 vol. %.
  • the processing-induced ⁇ ′ amount is preferably 40 vol. % Or less, and more preferably 15 vol. % Or less.
  • the total amount of the ferrite phase and the work-induced martensite phase ( ⁇ + work-induced ⁇ ′) (BCC amount) of the steel wire is less than 30%, high rigidity cannot be obtained, so the lower limit is set to 30 vol. Limited to%.
  • the total amount ( ⁇ + processing induced ⁇ ′) is preferably 35 vol. % Or more, more preferably 70 vol. % Or more.
  • the upper limit of the total amount ( ⁇ + working induction ⁇ ′) is not particularly limited, but is preferably 98 vol% or less from the viewpoint of securing a ferrite phase and an austenite phase.
  • the orientation amount of ⁇ 100 ⁇ plane (RD // ⁇ 100 ⁇ ) parallel to the RD direction in ⁇ and ⁇ of the steel wire will be described.
  • the rigidity has a property depending on the texture, and RD // ⁇ 100 ⁇ has the highest rigidity.
  • the orientation amount of RD // ⁇ 100 ⁇ in ⁇ and ⁇ is 5 vol. % Is less than 5 vol., Since high rigidity and twist workability cannot be obtained. Limited to%.
  • the upper limit of the orientation amount of RD // ⁇ 100 ⁇ in ⁇ and ⁇ is not particularly limited, but from the viewpoint of twist workability, 40 vol. % Or less, more preferably 5 to 20 vol. %.
  • the conditions for setting RD // ⁇ 100 ⁇ to 5 to 20% are SFE ⁇ 0 and the amount of BCC ( ⁇ + working induction ⁇ ′)> 70%.
  • the amount of RD // ⁇ 100 ⁇ of the steel wire can be measured by, for example, FE-SEM / EBSD analysis. Specifically, for example, the analysis location is the center (D / 2; D is the diameter of the steel wire), and 5 fields of 60 ⁇ 60 ⁇ m are measured. Then, the drawing axis direction is set to RD, the crystal plane is analyzed in the RD direction, main orientation components of ⁇ 001>, ⁇ 101>, and ⁇ 111> are displayed only within a clearance of 15 °, and RD // ⁇ 100 ⁇ Measure the quantity. The rigidity depends greatly on RD // ⁇ 100 ⁇ and the amount of BCC.
  • the rigidity becomes RD // ⁇ 100 ⁇ > 5%. 65 GPa or more.
  • the rigidity is 75 GPa or more.
  • the twist value greatly depends on RD // ⁇ 100 ⁇ and the processing induced ⁇ ′ amount, and when the alloy element and the manufacturing conditions satisfy the requirements of the present embodiment, the processing induced ⁇ ′ amount is 50% or less. As a result, the twist value becomes 10 times or more.
  • the twist value is 30 times or more.
  • austenite phase is transformed into a work-induced martensite phase by cold working. This is because the work to increase the strength while maintaining the toughness at a high level and the shock absorbing ability can be expected.
  • the balance of the metal structure other than the ferrite phase and the work-induced martensite phase is an austenite phase and an inevitable precipitation phase (a precipitation phase inevitably included). This is because, depending on the combination of additive elements, precipitates such as carbides, sulfides and nitrides may be deposited in the stainless steel wire, or oxides generated during deoxidation may inevitably remain. Because there is.
  • the ferrite phase and the processing-induced martensite phase are ferromagnetic.
  • the austenite phase is paramagnetic. Therefore, the phase ratio can be measured by using an electromagnetic measurement method, and the ferrite phase and the work-induced martensite phase can be obtained in volume%. Since the amount of the inevitable precipitate phase is negligible, the amount of the austenite phase is a value obtained by subtracting the total amount (volume%) of the ferrite phase and the work-induced martensite phase from 100 volume%.
  • the billet having the above chemical components is heated at a heating temperature in the range of 1000 to 1300 ° C.
  • maintains a billet in a furnace) at the time of heating can be made into 200 minutes or less from a viewpoint of preventing deterioration of a fatigue characteristic, for example.
  • hot wire rolling is performed on the billet after heating, and hot working is performed at a reduction in area of 99.0% or more.
  • in-line heat treatment at a heat treatment temperature of less than 950 ° C. tends to deteriorate the fatigue characteristics of the steel wire.
  • the heat treatment conditions are 950 to 1150 ° C. and 600 s or less.
  • the manufacturing method of the steel wire using the wire which concerns on this embodiment is demonstrated.
  • the production conditions of the steel wire should be controlled in order to increase the amount of ⁇ and ⁇ RD // ⁇ 100 ⁇ orientation. is important.
  • the steel wire according to the present embodiment can be obtained by cold-drawing the above-described wire, and specifically, the reduction in surface area is 50 to 90% with respect to the high-strength duplex stainless steel wire.
  • Wire is drawn at a rate (primary wire drawing).
  • heat treatment strand annealing, hereinafter also referred to as BA heat treatment
  • BA heat treatment strand annealing, hereinafter also referred to as BA heat treatment
  • the high strength duplex stainless steel wire is drawn with a reduction in area of 50 to 90% (secondary drawing).
  • the RD // ⁇ 100 ⁇ orientation amount of ⁇ and ⁇ cannot be secured (RD // ⁇ 100 ⁇ ⁇ 5%), so the lower limit of the area reduction ratio Is 50%. Further, from the viewpoint of twist workability, the upper limit of the area reduction rate is 90%. A preferable range of the area reduction rate is 85% or less.
  • BA temperature 950 degreeC or more
  • BA temperature shall be 1000 degreeC or more.
  • the BA temperature exceeds 1150 ° C., crystal grains develop, coarse crystal grains remain, and in addition to deteriorating the strength of the steel wire, the orientation amount of RD // ⁇ 100 ⁇ of ⁇ and ⁇ is Cannot be secured (RD // ⁇ 100 ⁇ ⁇ 5%).
  • BA temperature shall be 1150 degrees C or less, Preferably it shall be 1100 degrees C or less.
  • BA time when the time of BA heat treatment (BA time) is longer than 5 minutes, in addition to creep deformation, the amount of ⁇ and ⁇ RD // ⁇ 100 ⁇ orientation cannot be secured (RD // ⁇ 100 ⁇ ⁇ 5% ).
  • the upper limit of the BA time is 5 minutes.
  • the lower limit of the BA time is not particularly limited, but is preferably 0.6 minutes.
  • a preferable BA time range is 1 minute or more and 3.5 minutes or less. More preferably, it is 3 minutes or less.
  • ⁇ and ⁇ that are not oriented in RD // ⁇ 100 ⁇ are controlled by the area reduction rate of the secondary wire drawing.
  • the area reduction ratio of the secondary wire drawing of the steel wire is less than 50%, the amount of ⁇ 100 ⁇ in the RD direction of ⁇ and ⁇ cannot be secured (RD // ⁇ 100 ⁇ ⁇ 5%), Twist workability is inferior.
  • the lower limit of the area reduction rate is set to 50%.
  • the upper limit of the area reduction rate of the secondary wire drawing is not particularly limited, but is preferably 90% from the viewpoint of twist workability.
  • in the present embodiment as “indirect cooling”, for example, a method of cooling in a pipe that is installed in water and the inside of which is a cavity (air), etc. can be cited. In this embodiment, it is a method of cooling indirectly rather than directly contacting a coolant (cooling water or the like) with a steel wire).
  • FIG. 1 shows a cross-sectional view of a wire drawing die (a cross-sectional view along the central axis of a through hole).
  • the wire drawing die 1 includes a case 2 having a through hole and a chip 3 accommodated in the through hole of the case 2.
  • the tip 3 has a tapered through hole 31 having a large diameter on the inlet side and a small diameter on the outlet side. By drawing the wire through the through-hole 31 of the chip 3, the wire is thinned to increase the length.
  • the chip 3 has an inlet side introduction portion 32 and a wire drawing portion 33.
  • the wire drawing portion 33 includes a reduction portion 34 that is in contact with the introduction portion 32, and a bearing portion 35 that is in contact with the reduction portion 34 and located on the outlet side of the reduction portion 34.
  • the diameter of the through hole 31 in the reduction portion 34 decreases at a constant rate from the entrance side to the exit side.
  • the diameter of the through hole 31 in the bearing portion 35 is constant.
  • the wire drawing temperature affects the amount of processing-induced ⁇ ′ produced, and the RD // ⁇ 100 ⁇ amount changes accordingly. Therefore, the wire drawing temperature is set to 20 to 100 ° C., preferably 20 to 70 ° C.
  • the die half angle also affects the amount of machining-induced ⁇ ′ and the amount of RD // ⁇ 100 ⁇ . Therefore, the die half angle is 6 to 11 °, preferably 6 to 9 °.
  • Tables 1 to 4 show the chemical compositions (steel types A to BV), ferrite amount ( ⁇ amount), Md30 value in austenite ( ⁇ ), F value, and SFE in ⁇ .
  • surface show what has remove
  • an aging treatment was performed in the atmosphere at 400 ° C. for 30 minutes to obtain a high-strength stainless steel wire product.
  • processing-induced martensite ratio (processing-induced ⁇ ′ amount (fraction)) of the steel wire product, the sum of the ferrite phase and the processing-induced martensite phase ( ⁇ + processing-induced ⁇ ′) (BCC amount), the ferrite phase
  • the orientation amount (RD // ⁇ 100 ⁇ amount), rigidity, and twist value of the ⁇ 100 ⁇ plane in the RD direction in the austenite phase were evaluated.
  • the evaluation results are shown in Tables 5 and 6.
  • the processing-induced ⁇ ′ amount is simply abbreviated as the ⁇ ′ amount.
  • a slab of ⁇ 180 mm of steel A, D, F, K, P, Q, or I having the composition shown in Table 1 is heated at 1100 ° C. for 200 minutes and then hot-rolled to ⁇ 5.5 mm (reduced surface area) Rate: 99.9%) and hot rolling was completed at 1050 ° C. Immediately after that, it was cooled with water, or continuously from the end of hot rolling, followed by in-line heat treatment at 1050 ° C. for 3 minutes as a solution treatment to cool with water. Next, pickling was performed to obtain a wire. The wire was subjected to primary wire drawing at each wire drawing area reduction rate (primary wire drawing rate) shown in Table 7.
  • the steel wire (wire material) was heated at the BA temperature and holding time (BA time) shown in Table 7 (BA heat treatment).
  • secondary wire drawing was performed on the steel wire (wire material) at each wire drawing area reduction rate (secondary wire drawing rate) shown in Table 7.
  • the wire drawing temperature and the die angle during the secondary wire drawing were 70 ° C. and 8 °, respectively.
  • an aging treatment was performed in the atmosphere at 400 ° C. for 30 minutes to obtain a high-strength stainless steel wire product.
  • the processing-induced martensite ratio (processing-induced ⁇ ′ amount (fraction)), ⁇ + processing-induced ⁇ ′ amount (BCC amount), and RD // ⁇ 100 ⁇ of the obtained steel wire were measured.
  • the evaluation results are shown in Table 7.
  • the rigidity and twist value of the steel wire were evaluated by a twist test. Regarding the conditions of the twist test, the distance L between chucks was 200 mm, and the rotation speed was 1 rpm.
  • the rigidity G was calculated as follows.
  • the twist value Tn was calculated as follows.
  • the total rotation angle ⁇ a was measured and calculated from the following equation (B).
  • T torque (Nmm)
  • ⁇ twist angle (rad)
  • L distance between chucks (mm)
  • ⁇ a total rotation angle (degree).
  • Tables 5 to 8 show the results of rigidity and twist values.
  • the rigidity was 75 GPa or more or 65 to 75 GPa.
  • the twist value was 30 times or more or 10 to 30 times.
  • the ⁇ amount of the wire, the processing induced ⁇ ′ amount of the steel wire, the ⁇ amount, and the ⁇ + processing induced ⁇ ′ amount (BCC amount) were determined by the following methods. With respect to “product (wire material or steel wire)” and “material obtained by heat-treating the product at 1050 ° C. ⁇ 3 minutes”, the saturation magnetization value when a magnetic field of 10000 Oe was applied by a DC magnetometer was measured. Then, each value was obtained by the following equations (C) to (G). For measurement of the saturation magnetization value, a DC magnetization characteristic test apparatus (manufactured by Metron Giken Co., Ltd.) was used.
  • the amount of RD // ⁇ 100 ⁇ of the steel wire was measured by an FE-SEM / EBSD (JSM-700F / manufactured by JEOL Ltd.) analyzer.
  • the analysis location was the center (D / 2), and 5 fields of 60 ⁇ 60 ⁇ m were measured.
  • the axial direction of the wire drawing is RD, the crystal plane is analyzed in the RD direction, and the main orientation components ⁇ 001>, ⁇ 101>, and ⁇ 111> are displayed only within a clearance of 15 °, and RD // ⁇ 100 ⁇ amount was measured.
  • Tables 5 to 8 in the steel wire products of the examples of the present invention, the amount of RD // ⁇ 100 ⁇ was 5% or more.
  • an inexpensive low Ni / high Mn-based high-strength stainless steel wire rod and steel wire which are excellent in rigidity and twist workability, can be manufactured at low cost.
  • the high-strength stainless steel wire of the present invention can be formed with high accuracy without cracking into a spring having a complicated shape, can provide an accurate spring product having excellent rigidity and high strength and a complicated shape at low cost. For this reason, this invention is very useful industrially.

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  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • General Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
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Abstract

La présente invention concerne une tige en acier inoxydable duplex à haute résistance contenant, en % en masse, 0,01 à 0,21 % de C, 0,05 à 3,2 % de Si, 0,1 à 15 % de Mn, 0,5 % à moins de 5 % de Ni, 10,0 à 25,0 % de Cr et 0,01 à 0,35 % de N, le reste étant obtenu à partir de Fe et d'impuretés inévitables. La structure métallique est une structure à plusieurs phases constituée d'une phase α, d'une phase γ et d'une phase α' induite par contrainte, la phase α représentant 20 à 70 % en volume, la phase α' induite par contrainte représentant 5 à 50 % en volume et la phase α + la phase α' induite par contrainte représentant au moins 30 % en volume. L'importance de l'orientation du plan [100] dans la direction de laminage RD dans la phase α et la phase γ est d'au moins 5 %. La température Md30 dans la phase γ est de -15 à 45 °C. La valeur de F est inférieure ou égale à -6,12 et la valeur de l'énergie de défaut d'empilement SFE dans la phase γ est de -20 à 35.
PCT/JP2015/066436 2014-06-11 2015-06-08 Tige de fil métallique en acier inoxydable duplex à haute résistance, fil métallique en acier inoxydable duplex à haute résistance et procédé de fabrication s'y rapportant ainsi qu'élément ressort Ceased WO2015190422A1 (fr)

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KR1020157019800A KR101600251B1 (ko) 2014-06-11 2015-06-08 고강도 복상 스테인리스 강선재, 고강도 복상 스테인리스 강선과 그 제조 방법 및 스프링 부품

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