EP3091098B1 - Heissgewalztes stahlblech mit hohem kohlenstoffgehalt und verfahren zur herstellung davon - Google Patents

Heissgewalztes stahlblech mit hohem kohlenstoffgehalt und verfahren zur herstellung davon Download PDF

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Publication number
EP3091098B1
EP3091098B1 EP15770102.0A EP15770102A EP3091098B1 EP 3091098 B1 EP3091098 B1 EP 3091098B1 EP 15770102 A EP15770102 A EP 15770102A EP 3091098 B1 EP3091098 B1 EP 3091098B1
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steel sheet
content
cementite
temperature
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EP15770102.0A
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English (en)
French (fr)
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EP3091098A4 (de
EP3091098A1 (de
Inventor
Yuka Miyamoto
Takashi Kobayashi
Kaneharu Okuda
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JFE Steel Corp
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JFE Steel Corp
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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C22C38/001—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
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/32—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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
    • 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
    • C21D2211/003—Cementite
    • 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
    • C21D2211/005—Ferrite
    • 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 hot-rolled steel sheet and a method for manufacturing the steel sheet, and, in particular, to a high-carbon hot-rolled steel sheet excellent in terms of workability and hardenability to which B is added and which is highly effective for inhibiting nitrogen ingress in a surface layer thereof and a method for manufacturing the steel sheet.
  • automotive parts such as gears, transmission parts, and seat recliner parts are manufactured by forming a hot-rolled steel sheet, which is carbon steel material for machine structural use prescribed in JIS G 4051, into desired shapes by using a cold forming method and by performing a quenching treatment on the formed steel sheet in order to achieve a desired hardness. Therefore, a hot-rolled steel sheet, which is a raw material for the parts, is required to have excellent cold workability and hardenability, and various steel sheets have been proposed to date.
  • Patent Literature 1 discloses a medium-carbon steel sheet to be subjected to cold forming, the medium-carbon steel sheet having a hardness of 500 HV or more and 900 HV or less in the case where the steel sheet is subjected to an induction hardening treatment in which the steel sheet is heated at an average heating rate of 100°C/s, then held at a temperature of 1000°C for 10 seconds, and then rapidly cooled to room temperature at an average cooling rate of 200°C/s, having a chemical composition containing, by mass%, C: 0.30% to 0.60%, Si: 0.06% to 0.30%, Mn: 0.3% to 2.0%, P: 0.030% or less, S: 0.0075% or less, Al: 0.005% to 0.10%, N: 0.001% to 0.01%, Cr: 0.001% to 0.10%, and, optionally, one or more of Ni: 0.01% to 0.5%, Cu: 0.05% to 0.5%, Mo: 0.01% to 0.5%, Nb: 0.01% to 0.5%
  • Patent Literature 1 discloses a method for manufacturing such a medium-carbon steel sheet to be subjected to cold forming in which steel having the chemical composition mentioned above is held at a temperature of 1050°C to 1300°C, then subjected to hot rolling in which rolling is finished at a temperature of 750°C to 1000°C, then cooled to a temperature of 500°C to 700°C at a cooling rate of 20°C/s to 50°C/s, then cooled to a specified temperature at a cooling rate of 5°C/s to 30°C/s, then coiled, then held under specified conditions, and then annealed at a temperature of 600°C or higher and equal to or lower than the Ac 1 -10°C.
  • Patent Literature 2 discloses a boron-added steel sheet having a chemical composition containing, by mass%, C: 0.20% or more and 0.45% or less, Si: 0.05% or more and 0.8% or less, Mn: 0.5% or more and 2.0% or less, P: 0.001% or more and 0.04% or less, S: 0.0001% or more and 0.006% or less, Al: 0.005% or more and 0.1% or less, Ti: 0.005% or more and 0.2% or less, B: 0.001% or more and 0.01% or less, N: 0.0001% or more and 0.01% or less, and, optionally, one, two, or more of Cr: 0.05% or more and 0.35% or less, Ni: 0.01% or more and 1.0% or less, Cu: 0.05% or more and 0.5% or less, Mo: 0.01% or more and 1.0% or less, Nb: 0.01% or more and 0.5% or less, V: 0.01% or more and 0.5% or less, Ta: 0.01% or more and 0.5% or less,
  • Patent Literature 2 discloses that, in the case where annealing is performed in an atmosphere mainly containing nitrogen, since a phenomenon called nitrogen absorption occurs, B, which is an important chemical element from the viewpoint of hardenability, combines with N in steel to form BN in an annealing process, which results in the effect of increasing hardenability through the use of B not being realized due to a decrease in the amount of a solid solution B.
  • Patent Literature 2 discloses that, in order to achieve satisfactory hardenability, it is necessary to control the concentration of a solid solution B in a region from the surface to a depth of 100 ⁇ m to be 10 ppm or more, and that, therefore, it is important to suppress the influence of the atmosphere of a heating process and an annealing process included in a manufacturing process.
  • Patent Literature 2 discloses a method for manufacturing such a boron-added steel sheet in which steel having the chemical composition mentioned above is heated to a temperature of 1200°C or lower, then subjected to hot rolling with a finishing delivery temperature of 800°C to 940°C, then cooled to a temperature of 650°C or lower at a cooling rate of 20°C/s or more, then cooled at a cooling rate of 20°C/s or less, then coiled at a temperature of 400°C to 650°C, then pickled, and then annealed at a temperature of 660°C or higher and equal to or lower than the Ac 1 in an atmosphere in which hydrogen concentration is 95% or more, the dew point in a temperature range lower than 400°C is -20°C or lower, and the dew point in a temperature range of 400°C or higher is -40°C or lower.
  • Patent Literature 2 discloses, for example, a method in which the above-mentioned pickled steel sheet is further subjected to cold rolling and a method in which the above-mentioned annealed steel sheet is subjected to cold rolling, then further subjected to annealing in a temperature range from the Ac 1 to the Ac 1 +50°C, and then subjected to slow cooling to a temperature of the JP 54 586 49B discloses a hot rolled steel sheet having a small ferrite grain size and in which the cementite has a high spheroidizing ratio.
  • a high-carbon hot-rolled steel sheet is required to have a comparatively low hardness and a high elongation.
  • the automotive parts which have been manufactured by performing plural processes such as hot forging, machining, and welding, are integrally molded by performing cold press forming, the automotive parts are required to have properties such as a hardness of 73 or less in terms of Rockwell hardness HRB and a total elongation (El) of 39% or more.
  • a high-carbon hot-rolled steel sheet having a comparatively low hardness and a high elongation in order to achieve good workability as described above is required to have excellent hardenability such that, for example, the steel sheet has a Vickers hardness of HV440 or more after water quenching has been performed.
  • B is known as chemical element that increases hardenability when added in minute amounts, however, as described in Patent Literature 2, in the case where annealing is performed in an atmosphere containing mainly nitrogen, which is generally used as an atmospheric gas, there is a problem in that it is not possible to realize the effect of increasing hardenability caused by adding B due to a decrease in the amount of a solid solution B.
  • Patent Literature 2 such a problem is solved by performing annealing in an atmosphere containing 95% or more of hydrogen or in an atmosphere in which an inert gas such as Ar is used instead of hydrogen, there is an increase in cost in the case of a heat treatment in which such a gas is used.
  • An object of the present invention is, in order to solve the problems described above, to provide a high-carbon hot-rolled steel sheet whose raw material is B-added steel having a lower Mn content than conventional steel, with which it is possible to stably achieve excellent hardenability even if annealing is performed in a nitrogen atmosphere, and which has excellent workability corresponding to a hardness of 73 or less in terms of HRB and to a total elongation of 39% or more before a quenching treatment is performed and a method for manufacturing the steel sheet.
  • the present inventors diligently conducted investigations regarding the relationship between manufacturing conditions and workability and hardenability, in the case of a B-added high-carbon hot-rolled steel sheet having lower Mn content than conventional steel, that is, a Mn content of 0.50% or less, and, as a result, obtained the following knowledge.
  • the present invention it is possible to manufacture a high-carbon hot-rolled steel sheet excellent in terms of hardenability and workability.
  • the high-carbon hot-rolled steel sheet according to the present invention can preferably be used for automotive parts such as gears, transmission parts, and seat recliner parts whose raw material steel sheet is required to have satisfactory cold workability.
  • C is a chemical element which is important for achieving strength after quenching has been performed.
  • the C content is less than 0.20%, it is not possible to achieve the desired hardness by performing a heat treatment after a part has been formed, or, specifically, it is not possible to achieve a hardness of HV440 or more after water quenching has been performed. Therefore, it is necessary that the C content be 0.20% or more.
  • the C content is set to be 0.40% or less. It is preferable that the C content be 0.26% or more in order to achieve a high quenched hardness. It is more preferable that the C content be 0.32% or more, because it is possible to stably achieve a hardness of HV440 or more after water quenching has been performed.
  • Si is a chemical element which increases strength through solid solution strengthening. Since hardness increases with increasing Si content, there is a decrease in cold workability. Therefore, the Si content is set to be 0.10% or less, preferably 0.05% or less, or more preferably 0.03% or less. Although it is preferable that the Si content be as small as possible because Si decreases cold workability, since there is an increase in refining costs in the case where the Si content is excessively decreased, it is preferable that the Si content be 0.005% or more.
  • Mn is a chemical element which increases hardenability
  • Mn is also a chemical element which increases strength through solid solution strengthening.
  • the Mn content is set to be 0.50% or less, preferably 0.45% or less, or more preferably 0.40% or less.
  • the Mn content be 0.20% or more in order to achieve the specified quenched hardness by allowing all the C in a steel sheet to form a solid solution in a heating process for a quenching treatment as a result of inhibiting the precipitation of graphite.
  • the P content is a chemical element which increases strength through solid solution strengthening.
  • the P content is set to be 0.03% or less. It is preferable that the P content be 0.02% or less in order to achieve excellent toughness after quenching has been performed.
  • the P content be as small as possible because P decreases cold workability and toughness after quenching has been performed, since there is an increase in refining costs in the case where the P content is decreased more than necessary, it is preferable that the P content be 0.005% or more.
  • S Since S forms sulfides and decreases the cold workability of a high-carbon hot-rolled steel sheet and toughness after quenching has been performed, S is a chemical element whose content should be decreased. In the case where the S content is more than 0.010%, there is a significant decrease in the cold workability of a high-carbon hot-rolled steel sheet and toughness after quenching has been performed. Therefore, the S content is set to be 0.010% or less. It is preferable that the S content be 0.005% or less in order to achieve excellent cold workability and excellent toughness after quenching has been performed.
  • the S content be as small as possible because S decreases cold workability and toughness after quenching has been performed, since there is an increase in refining costs in the case where the S content is decreased more than necessary, it is preferable that the S content be 0.0005% or more.
  • sol.Al 0.10% or less
  • the sol.Al content is set to be 0.10% or less, or preferably 0.06% or less.
  • Al is effective for deoxidation, and it is preferable that the sol.Al content be 0.005% or more in order to sufficiently perform deoxidation.
  • the N content is set to be 0.0050% or less, or preferably 0.0045% or less.
  • N forms BN and AlN as described above.
  • the N content be 0.0005% or more.
  • B is an important chemical element which increases hardenability.
  • the B content is less than 0.0005%, since there is an insufficient amount of a solid solution B, which delays ferrite transformation, it is not possible to realize sufficient effect of increasing hardenability. Therefore, it is necessary that the B content be 0.0005% or more, or preferably 0.0010% or more.
  • the B content is more than 0.0050%, the recrystallization of austenite after finish rolling has been performed is delayed.
  • the B content be 0.0050% or less. It is preferable that the B content be 0.0035% or less from the viewpoint of increasing hardenability and of decreasing anisotropy. Therefore, the B content is set to be 0.0005% or more and 0.0050% or less, or preferably 0.0010% or more and 0.0035% or less.
  • the proportion of the content of a solid solution B to the content of B 70% or more
  • the control of the amount of a solid solution B which contributes to an increase in hardenability, is important.
  • the proportion of the amount of B present in a solid solution state to the amount of B contained in a steel sheet is 70% or more, that is, in the case where the proportion of the content of a solid solution B to the total content of B (B content) in a steel sheet is 70% or more, it is possible to achieve excellent hardenability targeted in the present invention. Therefore, the proportion of the content of a solid solution B to the content of B is set to be 70% or more, or preferably 75% or more.
  • the proportion of the content of a solid solution B to the content of B refers to ⁇ (content of a solid solution B (mass%))/(total B content (mass%)) ⁇ 100 (%).
  • One or more of Sb, Sn, Bi, Ge, Te, and Se 0.002% or more and 0.030% or less in total
  • Sb, Sn, Bi, Ge, Te, and Se are all chemical elements which are effective for inhibiting nitrogen ingress through the surface of a steel sheet, and it is necessary that one or more of Sb, Sn, Bi, Ge, Te, and Se be added in the present invention.
  • one or more of Sb, Sn, Bi, Ge, Te, and Se is added in an amount of 0.002% or more in total, or preferably 0.005% or more in total.
  • the total content of these chemical elements is more than 0.030%, the effect of inhibiting nitrogen ingress becomes saturated.
  • one or more of Sb, Sn, Bi, Ge, Te, and Se is added in an amount of 0.030% or less in total, or preferably 0.020% or less.
  • the N content is 0.0050% or less, and by adding one or more of Sb, Sn, Bi, Ge, Te, and Se in an amount of 0.002% or more and 0.030% or less in total, since it is possible to inhibit an increase in nitrogen concentration in the surface layer of a steel sheet by inhibiting nitrogen ingress through the surface of the steel sheet even in the case where annealing is performed in a nitrogen atmosphere, it is possible to control the difference between an average nitrogen concentration in a region from the surface to a depth of 150 ⁇ m in the thickness direction of the steel sheet and an average nitrogen concentration in the whole steel sheet to be 30 mass ppm or less.
  • the difference between an average nitrogen concentration in a region from the surface to a depth of 150 ⁇ m in the thickness direction of the steel sheet and an average nitrogen concentration in the whole steel sheet is more than 30 mass ppm, there is an increase in the difference between the amounts of BN and AlN formed in the surface layer of the steel sheet and the amounts of BN and AlN formed in the vicinity of the central portion in the thickness direction of the steel sheet. In this case, there is a problem such as one in that it is not possible to achieve uniform hardness distribution after a quenching treatment has been performed. Therefore, it is necessary to suppress the difference between an average nitrogen concentration in a region from the surface to a depth of 150 ⁇ m in the thickness direction of the steel sheet and an average nitrogen concentration in the whole steel sheet to be 30 mass ppm or less.
  • Ni, Cr, and Mo may be added in order to further increase hardenability. In order to realize such an effect, it is preferable that one or more of Ni, Cr, and Mo be added and that the total content of these chemical elements be 0.01% or more. On the other hand, since these chemical elements are expensive, in the case where one or more of Ni, Cr, and Mo are added, it is necessary that the total content of these chemical elements be 0.50% or less, or preferably 0.20% or less.
  • a microstructure including ferrite and cementite be formed by performing annealing (spheroidizing annealing), in which spheroidal cementite is formed, after hot rolling has been performed.
  • annealing spheroidizing annealing
  • spheroidal refers to a case where the proportion of the amount of cementite having an aspect ratio (the length of major axis/the length of minor axis) of 3 or less to the total amount of cementite is 90% or more in terms of volume fraction.
  • the density of cementite in ferrite grains be 0.08 pieces/ ⁇ m 2 or less.
  • the density of cementite is also referred to as "the number density of cementite grains”.
  • the steel sheet according to the present invention has a microstructure including ferrite and cementite.
  • the number density of cementite grains in ferrite grains is high, there is an increase in hardness due to dispersion strengthening and there is a decrease in elongation.
  • the number density of cementite grains in ferrite grains be 0.08 pieces/ ⁇ m 2 or less, preferably 0.07 pieces/ ⁇ m 2 or less, or more preferably 0.06 pieces/ ⁇ m 2 or less.
  • the length of the major axis of cementite grains in ferrite grains is about 0.15 ⁇ m to 1.8 ⁇ m, the sizes of cementite grains slightly contributes to precipitation strengthening of a steel sheet. Therefore, it is possible to decrease strength by decreasing the number density of cementite grains in ferrite grains. Since cementite grains existing at ferrite grain boundaries scarcely contribute to dispersion strengthening, the number density of cementite grains in ferrite grains is set to be 0.08 pieces/ ⁇ m 2 or less.
  • remaining microstructures such as pearlite other than ferrite and cementite described above be inevitably formed in the case where the total volume fraction of the remaining microstructures be about 5% or less, because the effects of the present invention are not decreased.
  • Average grain diameter of all the cementite 0.60 ⁇ m or more and 1.00 ⁇ m or less and average grain diameter of cementite in ferrite grains: 0.40 ⁇ m or more
  • the average grain diameter of cementite in ferrite grains is less than 0.40 ⁇ m
  • the average grain diameter of cementite in ferrite grains be 0.40 ⁇ m or more, or more preferably 0.45 ⁇ m or more.
  • the average grain diameter of all the cementite be 0.60 ⁇ m or more, or preferably 0.65 ⁇ m or more, in order to control the average grain diameter of cementite in ferrite grains to be 0.40 ⁇ m or more.
  • the average grain diameter of all the cementite is more than 1.00 ⁇ m, since cementite is not completely dissolved in a short-time heating such as heating for an induction hardening treatment, there is a case where it is not possible to control hardness to be equal to or less than the desired value.
  • the average grain diameter of all the cementite be 1.00 ⁇ m or less, or more preferably 0.95 ⁇ m or less.
  • the average grain diameter of cementite described above it is possible to determine the average grain diameter of all the cementite and the average grain diameter of cementite in ferrite grains by observing the microstructure by using a SEM and by determining the lengths of the major axis and minor axis of cementite grains.
  • the average grain diameter of ferrite be 12 ⁇ m or less, or more preferably 9 ⁇ m or less, in the microstructure including ferrite and cementite described above.
  • the average grain diameter of ferrite is less than 6 ⁇ m, there is a case where there is an increase in the hardness of a steel sheet. Therefore, it is preferable that the average grain diameter of ferrite be 6 ⁇ m or more. It is possible to determine the grain diameter of ferrite described above by observing the microstructure by using a SEM.
  • the steel sheet according to the present invention since automotive parts such as gears, transmission parts, and seat recliner parts are formed by performing cold press forming, excellent workability is required. In addition, it is necessary to provide abrasion resistance to the parts by increasing hardness by performing a quenching treatment. Therefore, in addition to increasing hardenability, it is necessary that the hardness of a steel sheet is decreased to 73 or less in terms of HRB and total elongation (El) of a steel sheet is increased to 39% or more. Although it is preferable that the hardness of a steel sheet be as low as possible from the viewpoint of workability, since some parts are partially subjected quenching, the strength of a raw material steel sheet may influence fatigue characteristics.
  • the hardness of a steel sheet be more than 60 in terms of HRB.
  • HRB Rockwell hardness meter
  • B scale Rockwell hardness meter
  • the high-carbon hot-rolled steel sheet according to the present invention is manufactured by using raw material steel having the chemical composition described above, by performing hot rolling including performing hot rough rolling and then performing hot finish rolling with a finishing delivery temperature equal to or higher than the Ar 3 transformation temperature and 870°C or lower in order to obtain a desired thickness, by then cooling the hot-rolled steel sheet to a temperature of 700°C at an average cooling rate of 25°C/s or more and 150°C/s or less, by then coiling the cooled steel sheet at a coiling temperature of 500°C or higher and 700°C or lower in order to obtain a steel sheet having a microstructure including pearlite and, in terms of volume fraction, 5% or more of pro-eutectoid ferrite, and by then performing spheroidizing annealing on the steel sheet at a temperature equal to or lower than the Ac 1 transformation temperature.
  • the rolling reduction of finish rolling be 85% or more.
  • Finishing delivery temperature equal to or higher than the Ar 3 transformation temperature and 870°C or lower
  • the finishing delivery temperature is set to be 870°C or lower. In order to sufficiently increase the proportion of pro-eutectoid ferrite, it is preferable that the finishing delivery temperature be 850°C or lower.
  • the finishing delivery temperature is set to be equal to or higher than the Ar 3 transformation temperature, or preferably 820°C or higher.
  • finishing delivery temperature refers to the surface temperature of a steel sheet.
  • the cooling rate from the finishing delivery temperature to 700°C is an important factor in order to control a pro-eutectoid ferrite phase fraction in a steel sheet after hot rolling has been performed to be 5% or more in terms of volume fraction.
  • the average cooling rate in a temperature range from the finishing delivery temperature to 700°C is less than 25°C/s, since ferrite transformation is less likely to progress in a short time, which results in an increase in pearlite phase fraction more than necessary, it is not possible to form, in terms of volume fraction, 5% or more of pro-eutectoid ferrite.
  • the average cooling rate in a temperature range down to a temperature of 700°C after finish rolling has been performed is set to be 25°C/s or more.
  • the pro-eutectoid ferrite phase fraction be 10% or more in terms of volume fraction in order to control the number density of cementite grains in ferrite grains to be 0.07 pieces/ ⁇ m 2 or less after spheroidizing annealing has been performed, it is preferable that the average cooling rate be 30°C/s or more, or more preferably 40°C/s or more, in this case. On the other hand, in the case where the average cooling rate is more than 150°C/s, it is difficult to form pro-eutectoid ferrite.
  • the average cooling rate down to a temperature of 700°C after finish rolling has been performed is set to be 150°C/s or less, preferably 120°C/s or less, or more preferably 100°C/s or less.
  • this "temperature” refers to the surface temperature of a steel sheet.
  • Coiling temperature 500°C or higher and 700°C or lower
  • the steel sheet which has been subjected to finish rolling is wound in a coil shape at a coiling temperature of 500°C or higher and 700°C or lower after cooling has been performed as described above. It is not preferable that the coiling temperature be higher than 700°C, because it is not possible to form the desired steel sheet microstructure after annealing has been performed due to an increase in the grain diameter of the microstructure of a hot-rolled steel sheet, and because, from the viewpoint of operational efficiency, there is a case where coil deforms under its own weight due to an excessive decrease in the strength of a steel sheet when the steel sheet is wound in a coil shape. Therefore, the coiling temperature is set to be 700°C or lower, or preferably 650°C or lower.
  • the coiling temperature is set to be 500°C or higher, or preferably 550°C or higher.
  • “coiling temperature” refers to the surface temperature of a steel sheet.
  • Steel sheet microstructure after hot rolling has been performed including pearlite and, in terms of volume fraction, 5% or more of pro-eutectoid ferrite
  • a steel sheet having a microstructure which includes ferrite and cementite and in which the number density of cementite grains in the ferrite grains is 0.08 pieces/ ⁇ m 2 or less is obtained.
  • the microstructure after spheroidizing annealing has been performed is strongly influenced by the steel sheet microstructure after hot rolling has been performed.
  • the microstructure of a steel sheet (hot-rolled steel sheet) obtained by performing hot rolling, cooling, and coiling under the conditions described above is a microstructure including pearlite and, in terms of volume fraction, 5% or more of pro-eutectoid ferrite, or preferably, pearlite and, in terms of volume fraction, 10% or more of pro-eutectoid ferrite.
  • the pro-eutectoid ferrite phase fraction be 50% or less in terms of volume fraction.
  • Annealing temperature equal to or lower than the Ac 1 transformation temperature
  • the hot-rolled steel sheet obtained as described above is subjected to annealing (spheroidizing annealing).
  • annealing temperature is set to be equal to or lower than the Ac 1 transformation temperature.
  • the annealing temperature be 600°C or higher, or more preferably 700°C or higher, in order to control the number density of cementite grains in ferrite grains to be the desired value.
  • the annealing time be 0.5 hours or more and 40 hours or less.
  • the annealing time be 0.5 hours or more, or more preferably 8 hours or more.
  • the annealing time in the case where the annealing time is more than 40 hours, there is a decrease in productivity, and there is tendency for manufacturing costs to excessively increase. Therefore, it is preferable that the annealing time be 40 hours or less.
  • annealing temperature refers to the surface temperature of a steel sheet.
  • annealing time refers to a period of time during which the specified temperature is maintained.
  • any of a converter and an electric furnace may be used.
  • the molten material of the high-carbon steel prepared as described above is made into a slab by using an ingot casting-slabbing method or a continuous casting method.
  • the slab is usually heated and then subjected to hot rolling.
  • hot direct rolling which is performed on the slab in the cast state or after heat retention has been performed in order to inhibit a fall in temperature, may be performed.
  • the slab heating temperature be 1280°C or lower in order to inhibit a deterioration in surface quality due to scale.
  • the material to be rolled may be heated by using a heating means such as a sheet bar heater in a hot rolling process.
  • hot rolled steel sheets were obtained.
  • the cooling rates given in Table 2 were the average cooling rates down to a temperature of 700°C after finish rolling has been performed.
  • annealing sinizing annealing
  • nitrogen atmosphere atmospheric gas: nitrogen
  • the microstructure of the hot-rolled steel sheet before annealing was performed (the microstructure of the hot-rolled steel sheet) by using a SEM, the kinds of the microstructures were identified, and a pro-eutectoid ferrite phase fraction was derived.
  • the volume fraction of pro-eutectoid ferrite was determined as the obtained area fraction thereof.
  • microstructure of the hot-rolled steel sheet after annealing had been performed was observed by using microstructure photographs which were captured by using a scanning electron microscope at a magnification of 3000 times at five positions located at a depth of 1/4 in the thickness direction of a sample which had been prepared by taking the sample from the central portion in the width direction of the steel sheet, by performing cutting and polishing, and by performing nital etching.
  • the density of cementite in ferrite grains (the number density of cementite grains in ferrite grains) was derived.
  • the average grain diameter of all the cementite and the average grain diameter of cementite in grains were derived.
  • Ferrite grain diameter was derived by determining grain size by using the microstructure photograph described above, and then average ferrite grain diameter was calculated.
  • average N content within 150 ⁇ m of the surface layer and the average N content of the steel sheet were determined, and then the difference between the average N content within 150 ⁇ m of the surface layer and the average N content of the steel sheet was derived.
  • average N content within 150 ⁇ m of the surface layer refers to average N content in a region from the surface of the steel sheet to a depth of 150 ⁇ m in the thickness direction.
  • the average N content within 150 ⁇ m of the surface layer was derived by using the following method.
  • the produced cutting chips were collected as samples.
  • the average N content within 150 ⁇ m of the surface layer was defined as the N content of the samples.
  • the average N content within 150 ⁇ m of the surface layer and the average N content of the steel sheet were determined by using an inert gas fusion-thermal conductivity method.
  • a sample was taken from the central portion in the width direction of the steel sheet after annealing had been performed.
  • the proportion of the content of a solid solution B to the total content of B (B content) in steel was calculated to be equal to ⁇ (content of a solid solution B (mass%))/(total B content (mass%)) ⁇ 100 (%).
  • this proportion was 70 (%) or more may be judged as a case where a decrease in the content of a solid solution B was inhibited.
  • a quenching treatment was performed on the flat-sheet-type test piece by using a method in which cooling (water cooling) was performed with water immediately after the test piece had been held at a temperature of 870°C for 30 seconds or a method in which cooling (120°C-oil cooling) was performed with oil having a temperature of 120°C immediately after the test piece had been held at a temperature of 870°C for 30 seconds.
  • quenched hardness was defined as the average hardness.
  • a quenching treatment was also performed by using an induction hardening method (heating the test piece to a temperature of 1000°C at a heating rate of 200°C/s and then cooling the test piece with water).
  • an induction hardening method heatating the test piece to a temperature of 1000°C at a heating rate of 200°C/s and then cooling the test piece with water.
  • the hot-rolled steel sheets of the examples of the present invention had a microstructure which included ferrite and cementite and in which the number density of cementite grains in the ferrite grains was 0.08 pieces/ ⁇ m 2 or less, a hardness of 73 or less in terms of HRB, and a total elongation of 39% or more, which means these hot-rolled steel sheets were excellent in terms of cold workability and hardenability.
  • HV Hardness of Sample Water-cooled after Holding at 870°C for 30 s
  • HV Hardness of Sample 120°C-oil-cooled after Holding at 870°C for 30 s
  • HV Hardness of Sample Water-cooled in Induction Hardening 0.20 or more and less than 0.35 ⁇ 440 ⁇ 360 ⁇ 435 0.35 or more and less than 0.38 ⁇ 600 ⁇ 530 ⁇ 595 0.38 or more and less than 0.40 ⁇ 610 ⁇ 540 ⁇ 605 0.40 ⁇ 620 ⁇ 550 ⁇ 615

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Claims (5)

  1. Warmgewalztes Stahlblech mit hohem Kohlenstoffgehalt mit einer chemischen Zusammensetzung, die in Masseprozent C: 0,20% oder mehr und 0,40% oder weniger, Si: 0,10% oder weniger, Mn: 0,50% oder weniger, P: 0,03% oder weniger, S: 0,010% oder weniger, sol. Al: 0,10% oder weniger, N: 0,0050% oder weniger, B: 0,0005% oder mehr und 0,0050% oder weniger, ein oder mehrere aus Sb, Sn, Bi, Ge, Te und Se in einer Menge von insgesamt 0,002% oder mehr und 0,030% oder weniger, optional ein oder mehrere aus Ni, Cr und Mo in einer Menge von insgesamt 0,50% oder weniger enthält und der Rest Fe und unvermeidbare Verunreinigungen ist, wobei der Anteil des Gehalts einer festen Lösung B zu dem Gehalt von B 70% oder mehr beträgt, einer Mikrostruktur einschließlich Ferrit und Zementit, wobei die Dichte von Zementit in den Ferritkörnern 0,08 Teile/µm2 oder weniger beträgt, einer Härte von 73 oder weniger, ausgedrückt als HRB, und einer Gesamtdehnung von 39% oder mehr.
  2. Warmgewalztes Stahlblech mit hohem Kohlenstoffgehalt nach Anspruch 1, wobei das Stahlblech die chemische Zusammensetzung aufweist, die in Masseprozent eins oder mehrere von Ni, Cr und Mo in einer Menge von insgesamt 0,01% oder mehr und 0,50% oder weniger enthält.
  3. Warmgewalztes Stahlblech mit hohem Kohlenstoffgehalt nach Anspruch 1 oder 2, wobei das Stahlblech eine Mikrostruktur mit Ferrit und Zementit aufweist, wobei der durchschnittliche Korndurchmesser des gesamten Zementits 0,60 µm oder mehr und 1,00 µm oder weniger beträgt und wobei der durchschnittliche Korndurchmesser von Zementit in Ferritkörnern 0,40 µm oder mehr beträgt.
  4. Verfahren zur Herstellung eines warmgewalzten Stahlblechs mit hohem Kohlenstoffgehalt, wobei das Verfahren aufweist Durchführen von Warmgrobwalzen auf dem Stahl mit einer chemischen Zusammensetzung, die in Masseprozent C: 0,20% oder mehr und 0,40% oder weniger Si: 0,10% oder mehr weniger, Mn: 0,50% oder weniger, P: 0,03% oder weniger, S: 0,010% oder weniger, sol. Al: 0,10% oder weniger, N: 0,0050% oder weniger, B: 0,0005% oder mehr und 0,0050% oder weniger, ein oder mehrere aus Sb, Sn, Bi, Ge, Te und Se in einer Menge von insgesamt 0,002% oder mehr und 0,030% oder weniger, optional ein oder mehrere aus Ni, Cr und Mo in einer Menge von insgesamt 0,50% oder weniger enthält und der Rest Fe und unvermeidbare Verunreinigungen ist, dann Durchführen von Fertigwalzen mit einer Endausgangstemperatur gleich oder höher als die Ar3-Umwandlungstemperatur und 870°C oder niedriger, dann Kühlen des warmgewalzten Stahlblechs auf eine Temperatur von 700°C mit einer durchschnittlichen Kühlrate von 25°C/s oder mehr und 150°C/s oder weniger, dann Wickeln des gekühlten Stahlblechs auf eine Wickeltemperatur von 500°C oder höher und 700°C oder mehr niedriger, um ein Stahlblech mit einer Mikrostruktur zu erhalten, die Perlit und bezogen auf den Volumenanteil 5% oder mehr pro-eutektoidisches Ferrit enthält, und dann Wärmebehandeln des Stahlblechs bei einer Temperatur gleich oder niedriger als die Ac1-Umwandlungstemperatur.
  5. Verfahren zur Herstellung eines warmgewalzten Stahlblechs mit hohem Kohlenstoffgehalt nach Anspruch 4, wobei der Stahl, die chemische Zusammensetzung aufweist, die in Masseprozent eins oder mehrere von Ni, Cr und Mo in einer Menge von insgesamt 0,01% oder mehr und 0,50% oder weniger enthält.
EP15770102.0A 2014-03-28 2015-03-26 Heissgewalztes stahlblech mit hohem kohlenstoffgehalt und verfahren zur herstellung davon Not-in-force EP3091098B1 (de)

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CN113366137B (zh) * 2019-01-30 2022-10-28 杰富意钢铁株式会社 高碳热轧钢板及其制造方法
JP7067578B2 (ja) * 2019-02-28 2022-05-16 Ｊｆｅスチール株式会社 鋼板、及び鋼板と部材の製造方法
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JPS5317661B2 (de) 1973-08-31 1978-06-09
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US20050199322A1 (en) * 2004-03-10 2005-09-15 Jfe Steel Corporation High carbon hot-rolled steel sheet and method for manufacturing the same
JP5292698B2 (ja) * 2006-03-28 2013-09-18 Ｊｆｅスチール株式会社 極軟質高炭素熱延鋼板およびその製造方法
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JP5358914B2 (ja) * 2007-09-14 2013-12-04 Ｊｆｅスチール株式会社 極軟質高炭素熱延鋼板
TWI404808B (zh) * 2009-03-16 2013-08-11 Nippon Steel & Sumitomo Metal Corp 淬火性優異之硼添加鋼板及製造方法
JP5458649B2 (ja) * 2009-04-28 2014-04-02 Ｊｆｅスチール株式会社 高炭素熱延鋼板およびその製造方法
JP5056876B2 (ja) * 2010-03-19 2012-10-24 Ｊｆｅスチール株式会社 冷間加工性と焼入れ性に優れた熱延鋼板およびその製造方法
JP5594226B2 (ja) * 2011-05-18 2014-09-24 Ｊｆｅスチール株式会社 高炭素薄鋼板およびその製造方法
IN2014KN01254A (de) * 2012-01-05 2015-10-16 Jfe Steel Corp
JP5590254B2 (ja) * 2012-01-05 2014-09-17 Ｊｆｅスチール株式会社 高炭素熱延鋼板およびその製造方法
JP5812048B2 (ja) * 2013-07-09 2015-11-11 Ｊｆｅスチール株式会社 焼入れ性および加工性に優れる高炭素熱延鋼板およびその製造方法
EP3020839B1 (de) * 2013-07-09 2019-09-11 JFE Steel Corporation Kohlenstoffreiches warmgewalztes stahlblech und herstellungsverfahren dafür

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

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KR101892524B1 (ko) 2018-08-28
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EP3091098A1 (de) 2016-11-09
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TWI557239B (zh) 2016-11-11
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KR20160138230A (ko) 2016-12-02
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