WO2015146173A1 - Tôle d'acier laminée à chaud à haute teneur en carbone et son procédé de production - Google Patents

Tôle d'acier laminée à chaud à haute teneur en carbone et son procédé de production Download PDF

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WO2015146173A1
WO2015146173A1 PCT/JP2015/001712 JP2015001712W WO2015146173A1 WO 2015146173 A1 WO2015146173 A1 WO 2015146173A1 JP 2015001712 W JP2015001712 W JP 2015001712W WO 2015146173 A1 WO2015146173 A1 WO 2015146173A1
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steel sheet
content
cementite
ferrite
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PCT/JP2015/001712
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English (en)
Japanese (ja)
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友佳 宮本
崇 小林
金晴 奥田
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Ｊｆｅスチール株式会社
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Priority to US15/129,520 priority Critical patent/US20170121787A1/en
Priority to CN201580016876.8A priority patent/CN106133170B/zh
Priority to JP2015537042A priority patent/JP6065120B2/ja
Priority to EP15770102.0A priority patent/EP3091098B1/fr
Priority to KR1020167029879A priority patent/KR101892524B1/ko
Publication of WO2015146173A1 publication Critical patent/WO2015146173A1/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 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
    • 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
    • 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
    • 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 producing the same.
  • the present invention relates to a high-carbon hot-rolled steel sheet to which B is added, which has a high effect of suppressing nitriding in the surface layer, is excellent in workability and hardenability, and a method for producing the same.
  • automotive parts such as gears, transmission parts, seat recliner parts, etc. are manufactured by processing hot-rolled steel sheets, which are carbon steel materials for machine structures specified in JIS G 4051, into desired shapes by cold working. In many cases, it is manufactured by quenching in order to ensure the desired hardness. For this reason, the hot-rolled steel sheet used as a raw material is required to have excellent cold workability and hardenability, and various steel sheets have been proposed so far.
  • Patent Document 1 discloses that hardness is increased when induction hardening is performed by heating at an average heating rate of 100 ° C./second, holding at 1000 ° C. for 10 seconds, and rapidly cooling to room temperature at an average cooling rate of 200 ° C./second.
  • Patent Document 1 discloses, as a method for producing such a cold-working medium carbon steel sheet, a hot steel in which the steel having the above-described chemical composition is kept at 1050 to 1300 ° C. and then rolled at 750 to 1000 ° C. Rolled, then cooled to 500 to 700 ° C. at a cooling rate of 20 to 50 ° C./s, cooled to a predetermined temperature at a cooling rate of 5 to 30 ° C./s, wound up, and held under predetermined conditions Thereafter, annealing at a temperature of 600 ° C. or higher and Ac 1 ⁇ 10 ° C. or lower is disclosed.
  • Patent Document 2 by mass, C: 0.20% to 0.45%, Si: 0.05% to 0.8%, Mn: 0.5% to 2.0% P: 0.001% to 0.04%, S: 0.0001% to 0.006%, Al: 0.005% to 0.1%, Ti: 0.005% to 0.2 %: B: 0.001% or more and 0.01% or less and N: 0.0001% or more and 0.01% or less, or Cr: 0.05% or more and 0.35% or less, Ni: 0.01% to 1.0%, Cu: 0.05% to 0.5%, Mo: 0.01% to 1.0%, Nb: 0.01% to 0.5%
  • V 0.01% to 0.5%
  • Ta 0.01% to 0.5%
  • W 0.01% to 0.5%
  • Sn 0.00%.
  • Patent Document 2 in order to ensure hardenability, the solid solution B in the region from the surface layer to a depth of 100 ⁇ m needs to be 10 ppm or more, and for that purpose, heating and annealing processes in the manufacturing process are required. It is disclosed that it is important to suppress the influence of the atmosphere.
  • Patent Document 2 discloses, as a method for producing such a boron-added steel sheet, a steel having the above component composition is heated at 1200 ° C. or less, hot-rolled at a finish rolling temperature of 800 to 940 ° C., and then cooled. After cooling at 20 ° C./s to 650 ° C.
  • Patent Document 2 further describes cold rolling after the pickling, or cold rolling after the annealing, and further annealing at a temperature of Ac 1 to Ac 1 + 50 ° C. to Ac 1 -30 ° C. Slow cooling and the like are disclosed.
  • the high carbon hot rolled steel sheet is required to have relatively low hardness and high elongation.
  • the hardness is 73 or less in Rockwell hardness HRB, The characteristic that the total elongation (El) is 39% or more is required.
  • excellent hardenability is desired for such a high carbon hot-rolled steel sheet having relatively low hardness and high elongation and good workability, for example, Vickers hardness of HV440 or higher after water quenching. Is desired.
  • the average diameter of the carbide is set to 0.6 ⁇ m or less in order to ensure quench hardening ability in induction hardening at an average heating rate of 100 ° C./second, but the C content is 0.3 to 0.00.
  • the average particle size of carbides is made as fine as 0.6 ⁇ m or less, so the density of carbides tends to increase, the strength tends to increase, and workability may be reduced.
  • the manufacturing method includes two-stage cooling, such as cooling to 500 to 700 ° C. at a cooling rate of 20 to 50 ° C./s after hot rolling and then cooling to a cooling rate of 5 to 30 ° C./s. There is a problem that it is difficult to manage the cooling control because of the control.
  • B is known as an element that improves hardenability by adding a small amount.
  • annealing is performed in an atmosphere mainly composed of nitrogen, which is generally used as an atmospheric gas. Then, there was a problem that the solid solution B decreased and the effect of improving the hardenability by B could not be obtained.
  • Patent Document 2 such a problem is solved by annealing in an atmosphere containing 95% or more of hydrogen or an atmosphere in which the hydrogen is replaced with an inert gas such as Ar. The cost of heat treatment using is increased. Moreover, it is unclear whether this technique alone can suppress nitrogen absorption by annealing in a nitrogen atmosphere.
  • the present invention uses a steel with a Mn content lower than that of conventional steel and added with B, and even if annealing is performed in a nitrogen atmosphere, excellent quenching can be achieved. It is an object of the present invention to provide a high carbon hot-rolled steel sheet having excellent workability such that the hardness is 73 or less in HRB and the total elongation is 39% or more before quenching, and a method for producing the same. .
  • the inventors of the present invention made an intensive study on the relationship between the manufacturing conditions, workability, and hardenability of high carbon hot-rolled steel sheets containing B, with a Mn content of 0.50% or less and a lower Mn content than conventional steel. As a result, the following knowledge was obtained. i) The hardness and total elongation (hereinafter also simply referred to as elongation) of the high carbon hot-rolled steel sheet before quenching are greatly affected by the cementite density in the ferrite grains, with a hardness of 73 or less in HRB and 39% or more. In order to obtain the total elongation (El), the cementite density in the ferrite grains needs to be 0.08 pieces / ⁇ m 2 or less.
  • the cementite density in the ferrite grains is greatly affected by the finish rolling temperature in the hot rolling finish rolling and the cooling rate from 700 to 700 ° C. after the finish rolling. If the finish rolling temperature is too high or the cooling rate is too low, in the steel sheet after hot rolling, a steel sheet having a structure with pearlite and a predetermined proeutectoid ferrite volume fraction cannot be obtained, and spheroidizing annealing is performed. It becomes difficult to reduce the cementite density later.
  • the present invention has been made on the basis of such knowledge, and the gist thereof is as follows.
  • 700 Is cooled at an average cooling rate of 25 ° C./s or more and 150 ° C./s or less, and coiled at a winding temperature of 500 ° C. or more and 700 ° C. or less, so that pearlite and pro-eutectoid ferrite with a volume ratio of 5% or more can be obtained.
  • a high carbon hot rolled steel sheet having excellent hardenability and workability can be produced.
  • the high carbon hot-rolled steel sheet of the present invention is suitable for automotive parts such as gears, transmission parts, and seat recliner parts, which require cold workability for the raw steel sheet.
  • % which is a unit of component content, means “% by mass” unless otherwise specified.
  • Composition C 0.20 to 0.40% C is an important element for obtaining strength after quenching.
  • C content is less than 0.20%, HV440 or more cannot be obtained with the desired hardness, specifically the hardness after water quenching, by heat treatment after forming into a part. For this reason, C content needs to be 0.20% or more.
  • the C content is set to 0.40% or less.
  • the C content is preferably 0.26% or more.
  • Si 0.10% or less
  • Si is an element that increases the strength by solid solution strengthening. As the Si content increases, it hardens and the cold workability deteriorates, so the Si content is made 0.10% or less.
  • the Si content is 0.05% or less, more preferably 0.03% or less. Since Si lowers the cold workability, the lower the Si content, the better. However, since excessively reducing Si increases the refining cost, the Si content is preferably 0.005% or more.
  • Mn 0.50% or less
  • Mn content is 0.50% or less.
  • the Mn content is 0.45% or less, more preferably 0.40% or less.
  • the lower limit is not specified, in order to suppress the precipitation of graphite and obtain a predetermined quenching hardness by solid solution of all C in the steel sheet during quenching heating, the Mn content is 0.20% or more. It is preferable that
  • P 0.03% or less
  • P is an element that increases the strength by solid solution strengthening. If the P content exceeds 0.03%, the steel sheet becomes too hard and cold workability is reduced. Moreover, since the strength of the grain boundary is lowered, the toughness after quenching deteriorates. Therefore, the P content is 0.03% or less. In order to obtain excellent toughness after quenching, the P content is preferably 0.02% or less. P decreases the cold workability and toughness after quenching, so the lower the P content, the better. However, if P is reduced more than necessary, the refining cost increases, so the P content is 0.005% or more. preferable.
  • S 0.010% or less
  • S is an element that has to be reduced in order to form sulfides and to reduce the cold workability of the high carbon hot-rolled steel sheet and the toughness after quenching. If the S content exceeds 0.010%, the cold workability and the toughness after quenching of the high carbon hot-rolled steel sheet are significantly deteriorated. Therefore, the S content is set to 0.010% or less. In order to obtain excellent cold workability and toughness after quenching, the S content is preferably 0.005% or less. Since S decreases cold workability and toughness after quenching, the S content is preferably as low as possible. However, if S is reduced more than necessary, the refining cost increases, so the S content is 0.0005% or more. preferable.
  • sol. Al 0.10% or less sol.
  • sol. Al content shall be 0.10% or less.
  • sol. Al content is 0.06% or less.
  • Al has a deoxidizing effect, and in order to sufficiently deoxidize, sol.
  • the Al content is preferably 0.005% or more.
  • N 0.0050% or less
  • the N content exceeds 0.0050%, BN is formed more than necessary, so that the amount of dissolved B decreases.
  • the formation of BN and AlN more than necessary causes the austenite grains to become too fine during heating in the quenching process, and the formation of a ferrite phase is promoted during cooling, so the hardness after quenching decreases. Therefore, the N content is 0.0050% or less.
  • the N content is 0.0045% or less.
  • the lower limit is not particularly defined, but N forms BN and AlN as described above. If appropriate amounts of BN and AlN are formed, these nitrides moderately suppress austenite grain coarsening during heating in the quenching process and improve toughness after quenching, so the N content is 0.0005% or more. Is preferred.
  • B 0.0005 to 0.0050% B is an important element that enhances hardenability.
  • the B content needs to be 0.0005% or more, and is preferably 0.0010% or more.
  • the B content exceeds 0.0050%, the recrystallization of austenite after finish rolling is delayed. As a result, the rolling texture of the hot-rolled steel sheet develops and the in-plane anisotropy of the mechanical property value of the steel sheet after annealing increases.
  • the B content is preferably 0.0035% or less. Therefore, the B content is set to 0.0005 to 0.0050%. More preferably, the B content is 0.0010 to 0.0035%.
  • the ratio of the solid solution B amount in the B content is set to 70% or more.
  • the ratio of the solid solution B content to the B content is 75% or more.
  • the ratio of the solid solution B amount in the B content means ⁇ (solid solution B amount (mass%)) / (total B content (mass%)) ⁇ ⁇ 100 (%).
  • Sb, Sn, Bi, Ge, Te, Se are all elements that have an effect of suppressing nitriding from the steel sheet surface.
  • one of Sb, Sn, Bi, Ge, Te, Se is used. It is necessary to contain the above. Further, when the total content of these elements is less than 0.002%, a sufficient nitriding suppression effect is not recognized. For this reason, one or more of Sb, Sn, Bi, Ge, Te and Se are contained in a total amount of 0.002% or more.
  • the total content of Sb, Sn, Bi, Ge, Te, Se is 0.005% or more.
  • Sb, Sn, Bi, Ge, Te, and Se are contained in a total amount of 0.030% or less.
  • the contents of Sb, Sn, Bi, Ge, Te and Se are preferably 0.020% or less in total.
  • the N content is 0.0050% or less, and at least one of Sb, Sn, Bi, Ge, Te, and Se is contained by 0.002 to 0.030% in total.
  • the nitriding from the steel sheet surface is suppressed, the increase in the nitrogen concentration in the steel sheet surface layer is suppressed, and the average amount of nitrogen contained in the range of 150 ⁇ m depth from the steel sheet surface in the sheet thickness direction, The difference from the average amount of nitrogen contained in the entire steel sheet can be 30 ppm by mass or less.
  • the ratio of the solid solution B content in the B content in the steel sheet after annealing can be 70% or more. .
  • the remainder other than the above is Fe and inevitable impurities, but in order to further improve the hardenability, one or more of Ni, Cr, and Mo may be contained. In order to obtain such an effect, it is preferable that at least one of Ni, Cr, and Mo is contained and the total content is 0.01% or more. On the other hand, since these elements are expensive, when one or more of Ni, Cr, and Mo are contained, the total content needs to be 0.50% or less. Preferably, the content of these elements is 0.20% or less in total.
  • spheroidization refers to a state in which cementite having an aspect ratio (major axis / minor axis) ⁇ 3 occupies 90% or more by volume with respect to the total cementite.
  • the cementite density in the ferrite grains needs to be 0.08 pieces / ⁇ m 2 or less.
  • the cementite density is also referred to as the number density of cementite grains.
  • the steel sheet of the present invention comprises ferrite and cementite. If the number density of cementite grains in the ferrite grains is high, it becomes hard due to dispersion strengthening and the elongation decreases. In order to set the hardness to a predetermined value or less and the elongation to a predetermined value or more, the number density of cementite grains in the ferrite grains needs to be set to 0.08 particles / ⁇ m 2 or less.
  • the number density of cementite grains in the ferrite grains is preferably 0.07 / ⁇ m 2 or less, and more preferably 0.06 / ⁇ m 2 or less.
  • the cementite diameter present in the ferrite grains is about 0.15 to 1.8 ⁇ m in the major axis, and is a size that has a slight effect on the precipitation strengthening of the steel sheet. Therefore, by reducing the number density of the cementite grains in the ferrite grains The strength can be reduced. Since cementite at the ferrite grain boundary hardly contributes to dispersion strengthening, the number density of cementite grains in the ferrite grain is defined as 0.08 / ⁇ m 2 or less. In addition to the above ferrite and cementite, even if the remaining structure such as pearlite is inevitably generated, the effect of the present invention is not impaired as long as the total volume ratio of the remaining structure is about 5% or less. , It may be contained.
  • Average diameter of all cementite 0.60 ⁇ m or more and 1.00 ⁇ m or less and average diameter of cementite in ferrite grains: 0.40 ⁇ m or more
  • Steel sheets whose average diameter of cementite in ferrite grains is less than 0.40 ⁇ m are cementite in ferrite grains Since the number density of grains increases, the hardness of the steel sheet after annealing may increase.
  • the average diameter of cementite in the ferrite grains is preferably 0.40 ⁇ m or more. More preferably, the average diameter of cementite in the ferrite grains is 0.45 ⁇ m or more.
  • the cementite at the ferrite grain boundary tends to be coarser than the cementite in the ferrite grain, and in order to make the average diameter of the cementite in the ferrite grain 0.40 ⁇ m or more, the average diameter of the entire cementite is 0.60 ⁇ m or more. There is a need.
  • the average diameter of all cementite is 0.65 ⁇ m or more.
  • the cementite may not be melted during heating in a short time such as induction hardening, and the hardness may not be less than the desired value.
  • the average diameter of all cementite is preferably 1.00 ⁇ m or less.
  • the average diameter of all cementite is 0.95 ⁇ m or less.
  • the average diameter of the cementite can be determined by observing the microstructure by SEM, measuring the long diameter and short diameter of the cementite grains, and measuring the average diameter of all cementite and the average diameter of cementite in the ferrite grains.
  • the average grain size of ferrite in the structure composed of ferrite and cementite should be 12 ⁇ m or less. Is preferable, and 9 ⁇ m or less is more preferable.
  • the average particle diameter of ferrite is less than 6 ⁇ m, the steel sheet may be hardened, so the average particle diameter of ferrite is preferably 6 ⁇ m or more. The particle size of the ferrite can be measured by observing the microstructure with an SEM.
  • the steel sheet of the present invention requires excellent workability in order to form automotive parts such as gears, transmission parts, and sheet recliner parts by cold pressing. In addition, it is necessary to increase the hardness by quenching to impart wear resistance to the parts. For that purpose, in addition to improving hardenability, it is necessary to reduce the hardness of the steel sheet to HRB 73 or less and increase the elongation to make the total elongation (El) 39% or more. The lower the hardness of the steel sheet, the better from the viewpoint of workability, but there are parts that are partially quenched, and the strength of the original sheet may affect the fatigue characteristics. For this reason, as for the hardness of a steel plate, HRB60 excess is preferable.
  • said HRB can be measured using a Rockwell hardness meter (B scale).
  • the total elongation is 10 mm / min with a tensile tester of Shimadzu AG10TB AG / XR using a JIS No. 5 tensile test piece cut in a direction of 0 ° (L direction) with respect to the rolling direction. It can be done by measuring the broken sample.
  • the high carbon hot-rolled steel sheet of the present invention is made of steel having the above composition, and is desired by hot rolling after hot rough rolling and finish rolling at a finish rolling temperature of Ar 3 transformation point or higher and 870 ° C. or lower. After finishing rolling, the steel sheet is cooled to 700 ° C. at an average cooling rate of 25 ° C./s to 150 ° C./s, and the winding temperature is 500 ° C. to 700 ° C. A steel sheet having 5% or more pro-eutectoid ferrite is produced, and then subjected to spheroidizing annealing at an Ac 1 transformation point or less. In addition, it is preferable that the rolling reduction in finish rolling shall be 85% or more.
  • Final rolling temperature Ar 3 transformation point or more and 870 ° C. or less
  • pearlite and pro-eutectoid ferrite with a volume ratio of 5% or more are used. It is necessary to spheroidize the hot-rolled steel sheet having a microstructure.
  • finish rolling temperature when the finish rolling temperature is higher than 870 ° C., the proportion of pro-eutectoid ferrite decreases, and the number density of predetermined cementite grains cannot be obtained after spheroidizing annealing. .
  • finish rolling temperature shall be 870 degrees C or less.
  • the finish rolling temperature is preferably 850 ° C. or lower.
  • the finish rolling temperature is 820 ° C or higher.
  • the finish rolling temperature is the surface temperature of the steel sheet.
  • Average cooling rate from the finish rolling temperature to 700 ° C . 25 ° C./s or more and 150 ° C./s or less
  • the cooling rate from the finish rolling temperature to 700 ° C. is an important factor. If the average cooling rate in the temperature range from finish rolling to 700 ° C. is less than 25 ° C./s, the ferrite transformation hardly progresses in a short time, and the paride fraction becomes higher than necessary. The fraction of precipitated ferrite cannot be obtained. In addition, the formation of coarse pearlite makes it difficult to obtain a desired steel sheet structure after spheroidizing annealing. Therefore, the average cooling rate in the temperature range from finish rolling to 700 ° C. is set to 25 ° C./s or more.
  • the pro-eutectoid ferrite fraction is preferably 10% or more by volume.
  • the average cooling rate is preferably 30 ° C./s or more. More preferably, the average cooling rate is 40 ° C./s or more.
  • the average cooling rate exceeds 150 ° C./s, it is difficult to obtain pro-eutectoid ferrite. Therefore, the average cooling rate from 700 ° C. after finish rolling is set to 150 ° C./s or less.
  • the average cooling rate is 120 ° C./s or less. More preferably, the average cooling rate is 100 ° C./s or less.
  • the temperature is the surface temperature of the steel sheet.
  • Winding temperature 500 ° C. or higher and 700 ° C. or lower
  • the steel sheet after finish rolling is wound into a coil shape at a winding temperature of 500 ° C. or higher and 700 ° C. or lower after cooling as described above.
  • the coiling temperature exceeds 700 ° C., the structure of the hot-rolled steel sheet becomes coarse and a desired steel sheet structure cannot be obtained after annealing, and the strength of the steel sheet becomes too low to be coiled into a coil shape. It may be deformed by its own weight, which is not preferable for operation. Therefore, the coiling temperature is 700 ° C. or less. Preferably, the coiling temperature is 650 ° C. or lower.
  • the coiling temperature is 500 ° C. or higher.
  • the winding temperature is 550 ° C. or higher.
  • the winding temperature is the surface temperature of the steel plate.
  • Microstructure of steel sheet after hot rolling Structure having pearlite and pro-eutectoid ferrite of 5% or more in volume ratio
  • it consists of ferrite and cementite, and the cementite grains in the ferrite grains
  • a steel sheet having a microstructure with a number density of 0.08 pieces / ⁇ m 2 or less is obtained.
  • the microstructure after spheroidizing annealing is greatly affected by the microstructure of the steel sheet after hot rolling.
  • the microstructure of the steel sheet after hot rolling into a structure having pearlite and 5% or more pro-eutectoid ferrite in volume ratio it can be made a desired structure after spheroidizing annealing, Become.
  • a predetermined number density of cementite grains can be obtained after spheroidizing annealing below the Ac 1 transformation point. Therefore, the steel sheet strength is increased.
  • the microstructure of the steel sheet (hot-rolled steel sheet) obtained by hot rolling, cooling and winding under the above-described conditions is a structure having pearlite and a pro-eutectoid ferrite of 5% or more by volume ratio.
  • the structure is composed of pearlite and pro-eutectoid ferrite with a volume ratio of 10% or more.
  • the fraction of pro-eutectoid ferrite is preferably 50% or less by volume.
  • Annealing temperature Ac 1 transformation point or less Annealing (spheroidizing annealing) is performed on the hot-rolled steel sheet obtained as described above.
  • the annealing temperature exceeds the Ac 1 transformation point, austenite precipitates, and a coarse pearlite structure is formed in the cooling process after annealing, resulting in a non-uniform structure. Therefore, the annealing temperature is less Ac 1 transformation point.
  • the annealing temperature is preferably 600 ° C. or higher, more preferably 700 ° C. or higher, in order to obtain the desired number density of cementite grains in the ferrite grains.
  • the atmospheric gas any of nitrogen, hydrogen, and a mixed gas of nitrogen and hydrogen can be used, and these gases are preferably used, but Ar may be used and is not particularly limited.
  • the annealing time is preferably 0.5 to 40 hours. By setting the annealing time to 0.5 hours or more, the target structure can be stably obtained, the hardness of the steel sheet can be set to a predetermined value or less, and the elongation can be set to a predetermined value or more.
  • the annealing time is preferably 0.5 hours or longer. More preferably, it is 8 hours or more. Further, if the annealing time exceeds 40 hours, the productivity is lowered and the manufacturing cost is likely to be excessive. Therefore, the annealing time is preferably 40 hours or less.
  • the annealing temperature is the surface temperature of the steel sheet.
  • the annealing time is a time during which a predetermined temperature is maintained.
  • both a converter and an electric furnace can be used. Further, the high carbon steel thus melted is made into a slab by ingot-bundling rolling or continuous casting.
  • the slab is usually heated and then hot rolled.
  • slab heating temperature 1280 degrees C or less it is preferable to make slab heating temperature 1280 degrees C or less in order to avoid the deterioration of the surface state by a scale.
  • the material to be rolled may be heated by a heating means such as a sheet bar heater during hot rolling.
  • Hot rolled annealed sheet hardness A sample was taken from the center of the plate width of the steel sheet after annealing, and measured at five points using a Rockwell hardness meter (B scale) to obtain an average value.
  • Total elongation of hot-rolled annealed sheet (El) Using a JIS No. 5 tensile test piece cut from the annealed steel sheet in a direction of 0 ° (L direction) with respect to the rolling direction, a tensile test was performed at 10 mm / min with a Shimadzu AG10TB AG / XR tensile tester. The fractured samples were butted together to determine the elongation (total elongation).
  • microstructure of the hot-rolled steel sheet before annealing was observed by SEM, and the type of the structure and the fraction of proeutectoid ferrite were determined.
  • the fraction of pro-eutectoid ferrite was divided into locations other than the ferrite region and the ferrite region, and the area ratio was determined by determining the proportion of the ferrite region, and this value was defined as the volume fraction of the pro-eutectoid ferrite.
  • the hot-rolled steel sheet before annealing shown in Table 2 the presence of pearlite is confirmed by the above SEM observation.
  • the microstructure of the steel sheet after annealing (the microstructure of the hot-rolled annealed sheet) is obtained by cutting and polishing a sample taken from the center part of the sheet width, applying nital corrosion, and using a scanning electron microscope, 1/4 of the sheet thickness. Using structure photographs taken at a magnification of 3000 at five locations, the type of the structure was observed, and the number of cementites that were not on the grain boundaries and whose major axis was 0.15 ⁇ m or more was measured. Dividing by the area of the field of view of the photograph, the cementite density in the ferrite grains (number density of cementite grains) was determined.
  • the cementite diameter was determined by measuring the long diameter and short diameter of each cementite grain using the above structure photograph, and determining the average diameter of all cementite and cementite within the grain. For the ferrite grain size, the average grain size was calculated by obtaining the grain size using the above structure photograph.
  • the difference between the average N amount of the surface layer 150 ⁇ m and the average N amount in the steel sheet Using a sample taken from the center of the sheet width of the steel sheet after annealing, the average N amount of the surface layer 150 ⁇ m and the average N amount in the steel sheet were measured, and the surface layer 150 ⁇ m The difference between the average N amount and the average N amount in the steel sheet was determined.
  • the average N amount of the surface layer of 150 ⁇ m is the average N amount contained in the range from the steel plate surface to the depth of 150 ⁇ m in the plate thickness direction.
  • the average amount of N in the surface layer of 150 ⁇ m was determined as follows.
  • the cutting was started from the surface of the collected steel sheet, the steel sheet was cut to a depth of 150 ⁇ m from the surface, and the cut piece generated at this time was collected as a sample.
  • the amount of N in this sample was measured and used as the average amount of N on the surface layer of 150 ⁇ m.
  • the average N amount of the surface layer of 150 ⁇ m and the average N amount in the steel sheet were determined by measurement by an inert gas melting-thermal conductivity method.
  • the difference between the average N content of the surface layer 150 ⁇ m obtained in this way (the N content in the range of 150 ⁇ m depth from the surface to the surface) and the average N content in the steel sheet (N content in the steel) is 30 ppm by mass or less. If it is, it can be evaluated that the nitrification can be suppressed.
  • the ratio of the amount of solute B in the B content A sample was taken from the center of the plate width of the steel plate after annealing. BN in the steel was extracted with 10% by volume Br methanol, and the B content precipitated as BN was subtracted from the total B content in the steel to obtain the solid solution B amount.
  • the ratio of the solute B amount to the total B content (B content) contained in the steel is ⁇ (solid solution B amount (mass%)) / (total B content (mass%)) ⁇ ⁇ It calculated
  • a flat plate test piece (width 15 mm ⁇ length 40 mm ⁇ plate thickness 4 mm) is taken from the center of the plate width of the steel plate (original plate) after annealing, and is immediately cooled with water by holding the plate test piece at 870 ° C. for 30 s. Quenching was performed by a method (water cooling), a method of holding at 870 ° C. for 30 s and immediately cooling with 120 ° C. oil (120 ° C. oil cooling). For the quenching characteristics, the hardness of the cut surface of the test piece after the quenching treatment was measured with a Vickers hardness tester under the condition of a load of 1 kgf to obtain an average hardness, which was defined as the quenching hardness.
  • a disk test piece (55 mm ⁇ ⁇ plate thickness 4 mm) is taken from the center of the width of the steel plate (original plate) after annealing, and induction-quenched (heated at a heating rate of 200 ° C./s, water-cooled after reaching 1000 ° C.) Also quenching treatment was performed.
  • the hardness of the cut surface of the test piece at the outermost peripheral portion of the test piece was measured at two points with a Vickers hardness tester under a load of 0.2 kgf to obtain the average hardness, and this was set as quenching hardness.
  • the quenching hardness which was kept at 870 ° C. for 30 s and was water-cooled and 120 ° C.
  • Table 3 represents the quenching hardness according to the C content that can be evaluated as having sufficient quenchability from experience.
  • the hot-rolled steel sheet of the present invention example has a microstructure composed of ferrite and cementite, and the cementite density in the ferrite grains is 0.08 pieces / ⁇ m 2 or less, and the hardness is 73 or less in HRB. It can be seen that since the total elongation is 39% or more, the cold workability is excellent and the hardenability is also excellent.

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  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

La présente invention concerne une tôle d'acier laminée à chaud à haute teneur en carbone dans laquelle un acier auquel B est ajouté est utilisé en tant que matière première, ladite tôle d'acier présentant régulièrement une excellente trempabilité même lorsque le recuit est effectué dans une atmosphère d'azote, et présentant une excellente aptitude au façonnage ayant, avant un traitement de trempe, une dureté de HRB 73 ou moins et un allongement total de 39 % ou plus. L'invention concerne une tôle d'acier laminée à chaud à haute teneur en carbone qui : a une composition contenant, en % en masse, C : 0,20 à 0,40 %, Si : 0,10 % ou moins, Mn : 0,50 % ou moins, P : 0,03 % ou moins, S : 0,010 % ou moins, Al sol. : 0,10 % ou moins, N : 0,0050 % ou moins, et B : 0,0005 à 0,0050 %, et contenant en outre 0, 002 à 0,030 %, au total, d'un ou de plusieurs des éléments suivants : Sb, Sn, Bi, Ge, Te et Se, la proportion de la teneur en B absorbée par la solution solide B est de 70 % ou plus ; possède une microstructure comprenant de la ferrite et de la cémentite, la densité de cémentite à l'intérieur des grains de ferrite est de 0,08/µm2 ou moins ; et a une dureté de HRB 73 ou moins et un allongement total de 39 % ou plus.
PCT/JP2015/001712 2014-03-28 2015-03-26 Tôle d'acier laminée à chaud à haute teneur en carbone et son procédé de production WO2015146173A1 (fr)

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JP2015537042A JP6065120B2 (ja) 2014-03-28 2015-03-26 高炭素熱延鋼板およびその製造方法
EP15770102.0A EP3091098B1 (fr) 2014-03-28 2015-03-26 Tôle d'acier laminée à chaud à haute teneur en carbone et son procédé de production
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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2019151048A1 (fr) 2018-01-30 2019-08-08 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute teneur en carbone et son procédé de fabrication
WO2020158356A1 (fr) 2019-01-30 2020-08-06 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute teneur en carbone et son procédé de production
WO2020158357A1 (fr) 2019-01-30 2020-08-06 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute teneur en carbone et son procédé de fabrication
JP2020143367A (ja) * 2019-02-28 2020-09-10 Ｊｆｅスチール株式会社 鋼板、部材及びそれらの製造方法

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR102288156B1 (ko) 2017-02-21 2021-08-11 제이에프이 스틸 가부시키가이샤 고탄소 열연 강판 및 그 제조 방법
WO2020175665A1 (fr) * 2019-02-28 2020-09-03 Ｊｆｅスチール株式会社 Tôle en acier, élément, et procédé de fabrication de ceux-ci

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007291495A (ja) * 2006-03-28 2007-11-08 Jfe Steel Kk 極軟質高炭素熱延鋼板およびその製造方法
JP2008156712A (ja) * 2006-12-25 2008-07-10 Jfe Steel Kk 高炭素熱延鋼板およびその製造方法
JP2009068081A (ja) * 2007-09-14 2009-04-02 Jfe Steel Kk 極軟質高炭素熱延鋼板
WO2010106748A1 (fr) * 2009-03-16 2010-09-23 新日本製鐵株式会社 Tôle d'acier contenant du bore et présentant une excellente trempabilité et procédé de fabrication associé
WO2013102982A1 (fr) * 2012-01-05 2013-07-11 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute teneur en carbone avec une excellente trempabilité et une anisotropie minimale dans le plan et son procédé de production
WO2013102986A1 (fr) * 2012-01-05 2013-07-11 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à forte teneur en carbone et son procédé de production
WO2015004902A1 (fr) * 2013-07-09 2015-01-15 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à teneur élevée en carbone et procédé de production de cette dernière
WO2015004906A1 (fr) * 2013-07-09 2015-01-15 Ｊｆｅスチール株式会社 Tôle d'acier à haute teneur en carbone, laminée à chaud, et son procédé de production

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5317661B2 (fr) 1973-08-31 1978-06-09
KR100673422B1 (ko) * 2003-08-28 2007-01-24 제이에프이 스틸 가부시키가이샤 고탄소열연강판, 냉연강판 및 그 제조방법
US20050199322A1 (en) * 2004-03-10 2005-09-15 Jfe Steel Corporation High carbon hot-rolled steel sheet and method for manufacturing the same
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

Patent Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2007291495A (ja) * 2006-03-28 2007-11-08 Jfe Steel Kk 極軟質高炭素熱延鋼板およびその製造方法
JP2008156712A (ja) * 2006-12-25 2008-07-10 Jfe Steel Kk 高炭素熱延鋼板およびその製造方法
JP2009068081A (ja) * 2007-09-14 2009-04-02 Jfe Steel Kk 極軟質高炭素熱延鋼板
WO2010106748A1 (fr) * 2009-03-16 2010-09-23 新日本製鐵株式会社 Tôle d'acier contenant du bore et présentant une excellente trempabilité et procédé de fabrication associé
WO2013102982A1 (fr) * 2012-01-05 2013-07-11 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute teneur en carbone avec une excellente trempabilité et une anisotropie minimale dans le plan et son procédé de production
WO2013102986A1 (fr) * 2012-01-05 2013-07-11 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à forte teneur en carbone et son procédé de production
WO2015004902A1 (fr) * 2013-07-09 2015-01-15 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à teneur élevée en carbone et procédé de production de cette dernière
WO2015004906A1 (fr) * 2013-07-09 2015-01-15 Ｊｆｅスチール株式会社 Tôle d'acier à haute teneur en carbone, laminée à chaud, et son procédé de production

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20200097806A (ko) 2018-01-30 2020-08-19 제이에프이 스틸 가부시키가이샤 고탄소 열연 강판 및 그의 제조 방법
JP6569845B1 (ja) * 2018-01-30 2019-09-04 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
US11434542B2 (en) 2018-01-30 2022-09-06 Jfe Steel Corporation High-carbon hot-rolled steel sheet and method for producing the same
WO2019151048A1 (fr) 2018-01-30 2019-08-08 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute teneur en carbone et son procédé de fabrication
JPWO2020158357A1 (ja) * 2019-01-30 2021-02-18 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
WO2020158357A1 (fr) 2019-01-30 2020-08-06 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute teneur en carbone et son procédé de fabrication
JPWO2020158356A1 (ja) * 2019-01-30 2021-02-18 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
KR20210105417A (ko) 2019-01-30 2021-08-26 제이에프이 스틸 가부시키가이샤 고탄소 열연 강판 및 그 제조 방법
KR20210107106A (ko) 2019-01-30 2021-08-31 제이에프이 스틸 가부시키가이샤 고탄소 열연 강판 및 그 제조 방법
CN113366136A (zh) * 2019-01-30 2021-09-07 杰富意钢铁株式会社 高碳热轧钢板和其制造方法
WO2020158356A1 (fr) 2019-01-30 2020-08-06 Ｊｆｅスチール株式会社 Tôle d'acier laminée à chaud à haute teneur en carbone et son procédé de production
CN113366136B (zh) * 2019-01-30 2023-10-31 杰富意钢铁株式会社 高碳热轧钢板和其制造方法
JP2020143367A (ja) * 2019-02-28 2020-09-10 Ｊｆｅスチール株式会社 鋼板、部材及びそれらの製造方法
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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US20170121787A1 (en) 2017-05-04
TW201538744A (zh) 2015-10-16
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