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WO2021039021A1 - Tôle d'acier mince résistante à l'abrasion, et procédé de fabrication de celle-ci - Google Patents

Tôle d'acier mince résistante à l'abrasion, et procédé de fabrication de celle-ci Download PDF

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Publication number
WO2021039021A1
WO2021039021A1 PCT/JP2020/022744 JP2020022744W WO2021039021A1 WO 2021039021 A1 WO2021039021 A1 WO 2021039021A1 JP 2020022744 W JP2020022744 W JP 2020022744W WO 2021039021 A1 WO2021039021 A1 WO 2021039021A1
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steel sheet
thin steel
wear
amount
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English (en)
Japanese (ja)
Inventor
貴之 遠藤
室田　康宏
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JFE Steel Corp
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JFE Steel Corp
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Priority to CN202080052281.9A priority Critical patent/CN114127322B/zh
Priority to KR1020227005096A priority patent/KR102674055B1/ko
Priority to JP2020552421A priority patent/JP6874916B1/ja
Publication of WO2021039021A1 publication Critical patent/WO2021039021A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C47/00—Winding-up, coiling or winding-off metal wire, metal band or other flexible metal material characterised by features relevant to metal processing only
    • B21C47/02—Winding-up or coiling
    • 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
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a thin wear-resistant steel having a plate thickness of less than 6.0 mm, that is, a high-hardness wear-resistant thin steel plate and a method for manufacturing the same.
  • Industrial machinery, parts, and transportation equipment eg, power shovels, bulldozers, hoppers, bucket conveyors, rock crushers
  • fields such as construction, civil engineering, and mining
  • Exposed to wear such as wear and impact wear. Therefore, steel used for such industrial machines, parts, and transportation equipment is required to have excellent wear resistance in order to improve the life.
  • Patent Document 1 describes hot steel containing 0.10 to 0.19% of C, further containing appropriate amounts of Si and Mn, and having an equivalent carbon content of Ceq of 0.35 to 0.44.
  • the hot-rolled steel sheet is rolled to obtain a hot-rolled steel sheet, which is directly or reheated to 900 to 950 ° C., then quenched, and then tempered at 300 to 500 ° C. to increase the surface hardness to 300 Hv (Vickers hardness).
  • the method for manufacturing the wear-resistant thick steel sheet described above is described.
  • Patent Document 2 contains 0.10 to 0.20% of C, further contains appropriate amounts of Si, Mn, P, S, N, Al, and O, and optionally Cu, Ni, Cr, and Mo.
  • B A steel material containing one or more of B is hot-rolled to obtain a hot-rolled steel sheet, and the hot-rolled steel sheet is directly or allowed to cool and reheated and then quenched to increase the surface hardness to 340 HB (.
  • a method for manufacturing a wear-resistant thick steel sheet having a Brinell hardness) or higher is described.
  • Patent Document 3 contains 0.07 to 0.17% of C, further contains appropriate amounts of Si, Mn, V, B, and Al, and optionally one of Cu, Ni, Cr, and Mo.
  • the steel material containing the above is hot-rolled to obtain a hot-rolled steel sheet, and the hot-rolled steel sheet is directly or once air-cooled, reheated, and then quenched to obtain a surface hardness of 321 HB or more.
  • the manufacturing method of is described.
  • Patent Document 4 contains 0.10 to 0.45% of C, 0.10 to 1.0% of Ti, and further contains appropriate amounts of Si, Mn, P, S, N, and Al, and further.
  • molten steel containing at least one of Cu, Ni, Cr, Mo, and B is continuously cast to deposit 400 or more TiC-based precipitates having a size of 0.5 ⁇ m or more per 1 mm 2.
  • Abrasion resistant steel has been proposed.
  • coarse precipitates mainly composed of TiC having high hardness are generated during solidification of continuous casting, and the abrasion resistance is improved by the precipitates.
  • Japanese Unexamined Patent Publication No. 62-142726 Japanese Unexamined Patent Publication No. 63-169359 Japanese Unexamined Patent Publication No. 1-142023 Japanese Unexamined Patent Publication No. 6-256896
  • Patent Documents 1 to 4 also describe that a wear-resistant thick steel sheet is manufactured by a method for manufacturing a wear-resistant steel sheet by a thick plate process.
  • the limit is industrially to produce a thick steel plate having a plate thickness of about 6 mm, and the thick plate process has a plate thickness of less than 6.0 mm. It could not be applied to the production of thin steel sheets. That is, when a thin steel sheet having a plate thickness of less than 6.0 mm is to be manufactured by the thick plate process, there is a problem that the flatness specification cannot be satisfied due to the cooling strain due to the characteristics of the thick plate process.
  • an object of the present invention is to provide a wear-resistant thin steel sheet having high flatness and an advantageous manufacturing method thereof.
  • the present inventors have come up with the idea of manufacturing a wear-resistant thin steel sheet by a hot rolling process for manufacturing a general thin steel sheet. That is, the slab was hot-rolled into a thin steel sheet using a hot-rolling machine including a rough-rolling machine and a finishing-rolling machine used in the hot-rolling process. Then, by cooling the thin steel sheet under the condition that the average cooling rate between 900 and 300 ° C. was 30 ° C./s or more, a martensite-based structure could be obtained. Then, by winding the thin steel sheet under the condition that the winding temperature was 200 ° C. or lower, it was possible to obtain a wear-resistant thin steel sheet having a high hardness due to the structure mainly composed of martensite. Then, by the hot rolling process, it was possible to produce a wear-resistant thin steel sheet having high flatness.
  • the abstract structure of the present invention completed based on the above findings is as follows. (1) By mass% C: 0.10 to 0.30%, Si: 0.01-1.0%, Mn: 0.30 to 2.00%, P: 0.03% or less, S: 0.03% or less, Cr: 0.01-2.00%, Al: 0.001 to 0.100%, Ti: 0.001 to 0.050%, B: 0.0001 to 0.0100% and N: 0.01% or less, and the balance has a component composition consisting of Fe and unavoidable impurities. It has a structure in which the volume fraction of martensite is 90% or more in the total plate thickness. A wear-resistant thin steel sheet having a hardness at a depth of 0.5 mm from the surface of Brinell hardness of 360 to 490 HBW5 / 750.
  • the composition of the components is mass%. Cu: 2.00% or less, Ni: 5.00% or less, Mo: 3.00% or less, V: 1.000% or less, W: 1.50% or less, Ca: 0.0200% or less,
  • the slab is subjected to hot rolling including finish rolling performed under the condition that the finish rolling temperature is 900 ° C. or higher to obtain a thin steel sheet.
  • the thin steel sheet is wound under the condition that the winding temperature is 200 ° C. or less.
  • a method for manufacturing a wear-resistant thin steel sheet which comprises.
  • C 0.10 to 0.30% C is an essential element for increasing the hardness of the martensite matrix.
  • the amount of C is 0.10% or more, preferably 0.14% or more.
  • the amount of C is set to 0.30% or less, preferably 0.25% or less.
  • Si 0.01-1.0% Si is an element effective for deoxidation and also contributes to increasing the hardness of steel by solid solution strengthening. From the viewpoint of obtaining these effects, the amount of Si is 0.01% or more, preferably 0.10% or more. On the other hand, when the amount of Si is excessive, it adheres to the surface of the thin steel sheet as scale and deteriorates the surface roughness. From this viewpoint, the amount of Si is 1.0% or less, preferably 0.40% or less.
  • Mn 0.30 to 2.00%
  • Mn is an element effective for improving the hardenability of steel. By adding Mn, the hardness of the hardened steel is increased, and as a result, the wear resistance is improved. From the viewpoint of obtaining this effect, the amount of Mn is set to 0.30% or more, preferably 0.50% or more, and more preferably 0.60% or more. On the other hand, when the amount of Mn is excessive, the weldability and toughness are significantly deteriorated. From this viewpoint, the amount of Mn is set to 2.00% or less, preferably 1.50% or less.
  • P 0.03% or less
  • P is an element that has the effect of increasing the strength of steel, but is an element that reduces toughness, especially the toughness of welds. Therefore, the amount of P is 0.03% or less, preferably 0.02% or less, and more preferably 0.01% or less.
  • the smaller the amount of P the more preferable, so the lower limit is not particularly limited and may be 0%.
  • the amount of P may be industrially more than 0%. From the viewpoint of steelmaking cost, the amount of P is preferably 0.001% or more.
  • S 0.03% or less S exists as sulfide-based inclusions such as MnS in steel and deteriorates toughness. Therefore, the amount of S is 0.03% or less, preferably 0.02% or less, and more preferably 0.015% or less. On the other hand, the smaller the amount of S, the more preferable, so the lower limit is not particularly limited and may be 0%. However, since S is unavoidably contained in steel as an impurity, the amount of S may be industrially more than 0%. From the viewpoint of steelmaking cost, the amount of S is preferably 0.0001% or more.
  • Cr 0.01-2.00% Cr is an element effective for improving the hardenability of steel.
  • the amount of Cr is 0.01% or more, preferably 0.05% or more, and more preferably 0.10% or more.
  • the amount of Cr is set to 2.00% or less, preferably 1.80% or less, and more preferably 1.00% or less.
  • Al 0.001 to 0.100%
  • Al is an element that is effective as an antacid and has the effect of forming a nitride to reduce the austenite particle size. From the viewpoint of obtaining this effect, the amount of Al is 0.001% or more, preferably 0.010% or more. On the other hand, if the amount of Al is excessive, the toughness deteriorates. Therefore, the amount of Al is 0.100% or less, preferably 0.050% or less.
  • Ti 0.001 to 0.050%
  • Ti is an element having a strong affinity for N, and has the effect of precipitating as TiN during solidification, reducing the solid solution N in steel, and reducing the deterioration of toughness due to strain aging of N after cold working. Ti also contributes to improving the toughness of the welded portion. From the viewpoint of obtaining these effects, the Ti amount is 0.001% or more, preferably 0.005% or more, and more preferably 0.007% or more. On the other hand, when the amount of Ti is excessive, the TiN particles become coarse and the above effect cannot be sufficiently obtained. Therefore, from this viewpoint, the amount of Ti is set to 0.050% or less, preferably 0.045% or less.
  • B 0.0001 to 0.0100% B is an element having the effect of improving hardenability by adding a very small amount, thereby improving the strength of the steel sheet. From the viewpoint of obtaining this effect, the amount of B is 0.0001% or more, preferably 0.0003% or more, and more preferably 0.0010% or more. On the other hand, when the amount of B is excessive, the toughness, particularly the toughness of the welded portion, decreases. Therefore, the amount of B is 0.0100% or less, preferably 0.0040% or less.
  • N 0.01% or less Since N is an element that reduces ductility and toughness, the amount of N is 0.01% or less. On the other hand, the smaller the amount of N is, the more preferable it is. Therefore, the lower limit is not particularly limited and may be 0%. However, since N is usually unavoidably contained in steel as an impurity, the amount of N may be industrially more than 0%. From the viewpoint of steelmaking cost, the amount of N is preferably 0.0005% or more.
  • Cu 2.00% or less, Ni: 5.00% or less, Mo: 3.00% or less, V: 1 for the purpose of improving hardenability and weldability.
  • W 1.50% or less, Ca: 0.0200% or less, Mg: 0.0200% or less, and REM: 0.0500% or less.
  • Cu 2.00% or less
  • Cu is an element that can improve hardenability without significantly deteriorating toughness.
  • the amount of Cu is preferably 0.01% or more, and more preferably 0.05% or more.
  • the amount of Cu is 2.00% or less, preferably 1.50% or less.
  • Ni 5.00% or less
  • Ni is an element that has the effect of improving hardenability and toughness.
  • the amount of Ni is preferably 0.01% or more, and more preferably 0.05% or more.
  • the amount of Ni is 5.00% or less, preferably 4.50% or less.
  • Mo 3.00% or less Mo is an element that improves the hardenability of steel.
  • the amount of Mo is preferably 0.01% or more, and more preferably 0.05% or more.
  • the amount of Mo is 3.00% or less, preferably 2.00% or less.
  • V 1.000% or less
  • V is an element that improves the hardenability of steel.
  • the amount of V is preferably 0.001% or more.
  • the amount of V is excessive, the weldability is lowered. Therefore, when V is added, the amount of V is 1.000% or less.
  • W 1.50% or less W is an element that improves the hardenability of steel.
  • the amount of W is preferably 0.01% or more.
  • the amount of W is excessive, the weldability is lowered. Therefore, when W is added, the amount of W is 1.50% or less.
  • Ca 0.0200% or less
  • Ca is an element that improves weldability by forming an acid sulfide having high stability at high temperatures.
  • the amount of Ca is preferably 0.0001% or more.
  • the amount of Ca is excessive, the cleanliness is lowered and the toughness of the steel is impaired. Therefore, when Ca is added, the amount of Ca is 0.0200% or less.
  • Mg 0.0200% or less
  • Mg is an element that improves weldability by forming an acid sulfide with high stability at high temperatures.
  • the amount of Mg is preferably 0.0001% or more.
  • the amount of Mg is 0.0200% or less.
  • REM 0.0500% or less REM (rare earth metal) is an element that improves weldability by forming an acid sulfide with high stability at high temperatures.
  • the REM amount is preferably 0.0005% or more.
  • the amount of REM is set to 0.0500% or less.
  • the rest of the component composition other than the above consists of Fe and unavoidable impurities.
  • Sb, Sn, Co, As, Pb, and Zn may each be contained in an amount of 1.0% or less.
  • the wear-resistant thin steel sheet of the present invention has a structure in which the volume fraction of martensite is 90% or more in the total thickness including from the front surface to the back surface.
  • volume fraction of martensite 90% or more
  • the volume fraction of martensite is 90% or more, preferably 95% or more.
  • the residual structure other than martensite is not particularly limited, but may be one or more selected from the group consisting of ferrite, pearlite, austenite, and bainite.
  • the upper limit of the volume fraction is not particularly limited and may be 100%.
  • the volume fraction of the martensite is a value at the total thickness including the front surface to the back surface of the wear-resistant thin steel sheet. The volume fraction of martensite can be measured by the method described in Examples.
  • Brinell hardness 360-490HBW5 / 750
  • the wear resistance of the thin steel sheet can be improved by increasing the hardness of the surface layer portion of the thin steel sheet.
  • Brinell hardness is used as an index for evaluating the wear resistance characteristics. If the Brinell hardness of the surface layer of the thin steel sheet is less than 360 HBW, sufficient wear resistance cannot be obtained. On the other hand, when the Brinell hardness of the surface layer portion of the thin steel sheet exceeds 490 HBW, the bending workability deteriorates. Therefore, in the present invention, the hardness of the surface layer portion of the thin steel sheet is 360 to 490 HBW in terms of Brinell hardness.
  • the "hardness in the surface layer portion” is defined as the hardness at a depth of 0.5 mm from the surface of the wear-resistant thin steel sheet. This is because the decarburized layer on the surface layer of the thin steel sheet is largely removed to reduce the variation in the measured values.
  • the "Brinell hardness” is a value (unit: HBW5 / 750) measured with a load of 750 kgf using a tungsten steel ball having a diameter of 5 mm. This Brinell hardness can be measured by the method described in the examples.
  • the thickness of the wear-resistant thin steel sheet of the present invention is less than 6.0 mm, preferably 4.5 mm or less, and more preferably 4.0 mm or less. Further, the lower limit of the plate thickness is not particularly limited, but is generally 2.0 mm or more due to the limitation in the hot rolling process.
  • the wear-resistant thin steel sheet of the present invention can have a surface roughness Ra of 40 ⁇ m or less.
  • the lower the surface roughness the more beautiful the surface of the thin steel sheet and the better the paintability. Therefore, the present invention is also suitable when the wear-resistant thin steel sheet is coated and used.
  • the surface roughness is small, when the wear-resistant thin steel plate of the present invention is used in a portion that comes into contact with a rotating body such as a cover of a shaft center for wind power generation, it does not become a resistance to rotation. ..
  • the lower limit of the surface roughness Ra is not particularly limited, but is generally 10 ⁇ m or more due to the limitation in the hot rolling process.
  • the wear-resistant thin steel sheet of the present invention is manufactured by a hot rolling process.
  • the hot-rolled coil is rewound on the skin pass line, front-back tension is applied to extend the thin steel sheet, and a leveler is applied on it. Therefore, the range that can be straightened is wide and the straightening effect is high. Therefore, the wear-resistant thin steel sheet of the present invention can obtain a high flatness.
  • the maximum value of the gap can be 10 mm or less, more preferably 5 mm or less. The smaller the maximum value of the gap is, the more preferable it is, and it can be 0 mm or more.
  • the method for producing a wear-resistant thin steel sheet of the present invention includes a step of continuously casting molten steel having the above-mentioned composition to obtain a slab, a step of heating the slab to a predetermined temperature, and then subjecting the slab to a predetermined condition under predetermined conditions. It has a step of obtaining a thin steel sheet by hot rolling in, a step of cooling the thin steel sheet under a predetermined condition, and then a step of winding the thin steel sheet under a predetermined condition.
  • the wear-resistant thin steel sheet of the present invention can be obtained by rewinding the hot-rolled coil thus obtained and performing arbitrary temper rolling for the purpose of shape correction.
  • each step will be described in detail.
  • Continuous casting Steel having the above-mentioned composition is melted by a conventional method in a melting facility such as a converter or an electric furnace, and continuously cast to obtain a slab.
  • the conditions for continuous casting are not particularly limited and may be carried out by a conventional method.
  • the heating temperature is 1000 ° C. or higher, preferably 1100 ° C. or higher, and more preferably 1200 ° C. or higher.
  • the heating temperature is set to 1300 ° C. or lower.
  • the heating temperature of the slab is the temperature of the surface of the slab.
  • the slab is hot-rolled to obtain a thin steel plate.
  • This process uses a hot rolling mill including a rough rolling mill and a finishing rolling mill used in the hot rolling process for manufacturing thin steel sheets, not a hot rolling mill (thick plate mill) used in the thick plate process. Do.
  • the thickness of the thin steel sheet obtained by this step is as described above as the thickness of the wear-resistant thin steel sheet of the present invention.
  • Finish-rolling temperature 900 ° C. or higher If the finish-rolling temperature is too low, the hardenability becomes insufficient and the hardness of the surface layer of the thin steel sheet decreases, so that the wear resistance deteriorates. From this point of view, the finish rolling temperature is 900 ° C. or higher. The upper limit of the finish rolling temperature is not particularly limited, but if the finish rolling temperature is too high, the rolling efficiency deteriorates. From this point of view, the finish rolling temperature is preferably 1000 ° C. or lower. In the present invention, the "finish rolling temperature" is the temperature of the surface of the thin steel sheet, but in the case of the thin steel sheet, the temperature at the center of the plate thickness is also substantially the same as the surface temperature.
  • the upper limit of the average cooling rate is not particularly limited, but the average cooling rate is approximately 150 ° C./s or less due to restrictions on the cooling equipment.
  • the "average cooling rate" is determined based on the decrease in the surface temperature of the thin steel sheet.
  • the cooling means for the thin steel sheet is not particularly limited, but water cooling is preferable from the viewpoint of obtaining the average cooling rate.
  • Winding temperature 200 ° C. or lower Subsequently, the thin steel sheet is wound to obtain a hot-rolled coil.
  • the winding temperature exceeds 200 ° C., the volume fraction of martensite becomes less than 90%, the hardness of the surface layer portion cannot be ensured, and the wear resistance deteriorates. Therefore, the winding temperature is set to 200 ° C. or lower, preferably 150 ° C. or lower.
  • the lower limit of the take-up temperature is not particularly limited, but the take-up temperature is preferably 50 ° C. or higher because the steel sheet is taken up and conveyed.
  • the "winding temperature" is the temperature of the surface of the thin steel sheet.
  • the thin steel sheet may be cooled after finish rolling and then wound as it is, and reheating (tempering) is not required.
  • the time from finish rolling to winding is preferably 30 to 90 seconds.
  • temper rolling It is preferable to rewind the hot-rolled coil obtained in the winding step and perform temper rolling for the purpose of shape correction on the thin steel sheet.
  • shape correction is performed by stretching a steel sheet by about 0.1 to 1.0%.
  • temper rolling it is preferable to use a tension leveler.
  • a slab was obtained by casting molten steel having the component composition shown in Table 1.
  • Table 2 a "hot rolling process” or a “thick plate process” was applied to each slab to manufacture a steel plate.
  • slab heating temperature "finish rolling temperature”
  • average cooling rate are shown in Table 2.
  • Table 2 shows the “winding temperature” as a parameter related only to the “hot rolling process”. No reheating was performed after cooling at any level.
  • the plate thickness at each level is also shown in Table 2.
  • the average cooling rate between 900 and 300 ° C is used. Shown, when the finish rolling temperature is less than 900 ° C and the winding temperature is 300 ° C or less, the average cooling rate between the finish rolling temperature and 300 ° C is shown, and the finish rolling temperature is less than 900 ° C and winding. When the take-up temperature exceeded 300 ° C., the average cooling rate between the finish rolling temperature and the take-up temperature was shown.
  • the average cooling rate when the finish rolling temperature is 900 ° C or higher, the average cooling rate is between 900 and 300 ° C, and the finish rolling temperature is less than 900 ° C.
  • the average cooling rate between the finish rolling temperature and 300 ° C. is shown.
  • temper rolling was performed.
  • level of the thick plate process the thick steel plate after cooling (quenching) was shape-corrected by a leveler.

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  • Mechanical Engineering (AREA)
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  • Organic Chemistry (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention fournit un procédé de fabrication avantageux de tôle d'acier mince résistante à l'abrasion et de planéité élevée. Plus précisément, l'invention concerne un procédé de fabrication de tôle d'acier mince qui est caractéristique en ce qu'il présente : une étape au cours de laquelle un acier en fusion qui possède une composition de composants contenant en quantités prédéfinies Ｃ, Ｓｉ, Ｍｎ, Ｐ, Ｓ, Ｃｒ, Ａｌ, Ｔｉ, Ｂ et Ｎ, le reste étant constitué de Fe et des impuretés inévitables, est coulé en continu, et une ébauche est ainsi obtenue ; une étape au cours de laquelle ladite ébauche est chauffée entre １０００ et １３００℃ ; puis, une étape au cours de laquelle un laminage à chaud incluant un laminage de finition effectué sous des conditions de température de laminage de finition supérieure ou égale à 900°C, est exécuté sur ladite ébauche, et une tôle d'acier mince est ainsi obtenue ; une étape au cours de laquelle ladite tôle d'acier mince est refroidie dans des conditions de vitesse moyenne de refroidissement entre 900 et 300°C supérieure ou égale à 30°C/s ; et enfin, une étape au cours de laquelle ladite tôle d'acier mince est enroulée dans des conditions de température d'enroulement inférieure ou égale à 200°C.
PCT/JP2020/022744 2019-08-26 2020-06-09 Tôle d'acier mince résistante à l'abrasion, et procédé de fabrication de celle-ci Ceased WO2021039021A1 (fr)

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CN117947344A (zh) * 2024-03-05 2024-04-30 鞍钢股份有限公司 一种免调质布氏硬度400hbw低屈强比高强热轧钢板及制造方法

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TW202108780A (zh) 2021-03-01
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