WO2020110660A1 - Matériau de couche externe de rouleau devant être laminé à chaud, et rouleau composite devant être laminé à chaud - Google Patents

Matériau de couche externe de rouleau devant être laminé à chaud, et rouleau composite devant être laminé à chaud Download PDF

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WO2020110660A1
WO2020110660A1 PCT/JP2019/043844 JP2019043844W WO2020110660A1 WO 2020110660 A1 WO2020110660 A1 WO 2020110660A1 JP 2019043844 W JP2019043844 W JP 2019043844W WO 2020110660 A1 WO2020110660 A1 WO 2020110660A1
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roll
outer layer
hot rolling
layer material
hot
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PCT/JP2019/043844
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English (en)
Japanese (ja)
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直道 岩田
鈴木　健史
智久 升光
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Ｊｆｅスチール株式会社
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Priority to BR112021009847-0A priority Critical patent/BR112021009847B1/pt
Priority to KR1020217015973A priority patent/KR102551616B1/ko
Priority to EP19889262.2A priority patent/EP3859025B1/fr
Priority to JP2020509132A priority patent/JP6866958B2/ja
Priority to CN201980077813.1A priority patent/CN113166864B/zh
Publication of WO2020110660A1 publication Critical patent/WO2020110660A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D13/00—Centrifugal casting; Casting by using centrifugal force
    • B22D13/10—Accessories for centrifugal casting apparatus, e.g. moulds, linings therefor, means for feeding molten metal, cleansing moulds, removing castings
    • B22D13/101—Moulds
    • B22D13/102—Linings for moulds
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B27/00—Rolls, roll alloys or roll fabrication; Lubricating, cooling or heating rolls while in use
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D13/00—Centrifugal casting; Casting by using centrifugal force
    • B22D13/02—Centrifugal casting; Casting by using centrifugal force of elongated solid or hollow bodies, e.g. pipes, in moulds rotating around their longitudinal axis
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D19/00—Casting in, on, or around objects which form part of the product
    • B22D19/16—Casting in, on, or around objects which form part of the product for making compound objects cast of two or more different metals, e.g. for making rolls for rolling mills
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D5/00—Heat treatments of cast-iron
    • 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
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C21D9/14—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes wear-resistant or pressure-resistant pipes
    • 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
    • C21D9/38—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for roll bodies
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/06—Cast-iron alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C37/00—Cast-iron alloys
    • C22C37/10—Cast-iron alloys containing aluminium or 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
    • C22C38/001—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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2251/00—Treating composite or clad material
    • C21D2251/02—Clad material
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation

Definitions

  • the present invention relates to a hot-rolling composite roll, and more particularly to a hot-rolling roll outer layer material and a hot-rolling composite roll suitable for a hot-rolling finishing mill for steel sheets.
  • an outer layer material of such a work roll for rolling for example, in Patent Document 1, C: 1.5 to 3.5%, Si: 1.5% or less, Mn: 1.2% or less, Ni: 5 0.5% or less, Cr: 5.5 to 12.0%, Mo: 2.0 to 8.0%, V: 3.0 to 10.0%, Nb: 0.5 to 7.0%
  • a rolling roll outer layer material containing Nb and V so that the contents of Nb, V and C satisfy a specific relationship and the ratio of Nb and V is within a specific range is proposed. There is. As a result, even if the centrifugal casting method is applied, the segregation of hard carbide in the outer layer material is suppressed, and the outer layer material for rolling is excellent in wear resistance and crack resistance.
  • Patent Document 2 C: 1.5 to 3.5%, Si: 1.5% or less, Mn: 1.2% or less, Cr: 5.5 to 12.0%, Mo: 2. 0 to 8.0%, V: 3.0 to 10.0%, Nb: 0.5 to 7.0%, and Nb and V are related to each other in a specific content of Nb, V and C.
  • a rolling roll outer layer material containing Nb and V so that the ratio of Nb and V is within a specific range. It is said that even if the centrifugal casting method is applied, segregation of hard carbides in the outer layer material is suppressed, wear resistance and crack resistance are improved, and it greatly contributes to the improvement in productivity of hot rolling.
  • Patent Document 3 C: 1.5 to 3.5%, Si: 0.1 to 2.0%, Mn: 0.1 to 2.0%, Cr: 5 to 25%, Mo: 2 to 12%, V: 3 to 10%, Nb: 0.5 to 5%, and contained so that the ratio of Mo and Cr is within a specific range, and further up to 30 mm from the surface in the radial direction of the roll.
  • a rolling roll outer layer material having a carbide amount distribution in which the difference between the maximum value and the minimum value adjacent to each other is 20% or less of the average value has been proposed.
  • the occurrence of segregation patterns is suppressed due to the reduction of lamination segregation, and the roll outer layer material for rolling has excellent surface quality.
  • the present invention has been made in view of the above circumstances, has wear resistance and fatigue resistance equal to or higher than conventional, and reduced porosity and dents, a hot rolling outer layer material and
  • An object is to provide a composite roll for hot rolling.
  • having abrasion resistance equal to or higher than conventional as described above means that the abrasion ratio measured by the following method is 0.97 or more.
  • Abrasion test piece 5 (outer diameter 60 mm ⁇ , wall thickness 10 mm, chamfered) taken from the outer layer material of the roll and the mating material were subjected to a two-disc sliding rolling method (see FIG. 3) to cool the abrasion test piece 5 with cooling water. Rotate at 700 rpm while cooling with water.
  • having the fatigue resistance equal to or higher than the conventional one as described above means a case where the hot rolling fatigue life measured by the following method exceeds 350 thousand times (350,000 times).
  • a notch depth t: 1.2 mm, circumferential length L: 0.8 mm was formed on the outer peripheral surface of a hot-rolled fatigue test piece (outer diameter 60 mm ⁇ , wall thickness 10 mm) collected from the roll outer layer material. It is introduced into two places by an electric discharge machining (wire cutting) method using a wire of 0.2 mm ⁇ (see FIG. 6).
  • a chamfer of 1.2 C is applied to the end of the rolling surface of the hot rolling fatigue test piece 5.
  • the hot rolling fatigue test piece 5 is rotated at 700 rpm while being water-cooled with the cooling water 6 by a two-disk rolling slide method of the hot rolling fatigue test piece 5 having a notch and the heated counterpart material 8.
  • Sliding ratio 9 while pressing a counter piece (material: S45C, outer diameter: 190 mm ⁇ , width: 15 mm) 8 heated to 800° C. by the high frequency induction heating coil 7 to the rotating test piece 5 with a load of 980 N.
  • Rolling is performed until the two notches 9 introduced into the hot rolling fatigue test piece 5 are broken, the rolling rotational speeds until the respective notches 9 are broken are obtained, and the average value thereof is measured to determine the hot rolling fatigue. Life expectancy.
  • the reduction of porosity and zigzag as described above means that the surface of the outer layer material of the roll has irregularities and scales (oxide layers) removed by grinding, and then the maximum tube voltage of 225 kV and tube voltage X-ray CT measurement was performed at 150 kV and a tube current of 80 ⁇ A, and indicates the case where the diameter of the circle circumscribing the imaged porosity or the burrow is 0.50 mm or less.
  • the present inventors have investigated in detail the relationship between the chemical composition and the porosity inside the hot-rolling roll and the dents.
  • porosity and dents exist near the eutectic carbides (mainly M 2 C-based, M 6 C-based, M 7 C 3 -based and M 23 C 6- based carbides), and the occurrence of porosity and dents is N.
  • eutectic carbides mainly M 2 C-based, M 6 C-based, M 7 C 3 -based and M 23 C 6- based carbides
  • the occurrence of porosity and dents is N.
  • O, O, Al and eutectic carbide there is a relation with the amounts of O, O, Al and eutectic carbide. That is, by adjusting the amount of N, O, Al, and eutectic carbide of the roll outer layer material within a specific range, it is possible to obtain a roll outer layer material for hot rolling which does not have porosity or dents.
  • the casting temperature was set to 1500° C., and the centrifugal force was set so that the outer peripheral portion of the ring-shaped roll material was a gravity multiple of 150 G.
  • quenching treatment and tempering treatment were performed.
  • the quenching treatment was performed by heating to a heating temperature of 1030° C. and air cooling.
  • the tempering treatment was carried out at a temperature of 500° C. two or three times depending on the components so that the residual austenite amount was less than 10% by volume.
  • three X-ray CT measurement test pieces (20 ⁇ 20 ⁇ 50 mm) were collected and subjected to X-ray CT measurement. Conducted to investigate the presence or absence of porosity and Zaku nest. As shown in FIG. 1, three X-ray CT measurement test pieces 2 were sampled from the center of the width of the ring-shaped test material 1 at 120° intervals. FIG. 2 shows an example of the burrow 3 in the test piece confirmed by the X-ray CT measurement.
  • the relationship between the diameter of the circle circumscribing the porosity or the burrow and the total content of N and O (N+O) is shown in FIG. 4, and the relationship between the Al content and the wear resistance is shown in FIG.
  • N+O 400 mass ppm or less
  • the diameter of the circumscribed circle is 0.50 mm or less, which is a size that does not pose a problem in quality.
  • Porosity is generated as gas during the process of cooling N and O contained in the molten metal from solidification to room temperature. By reducing the amount of N and O, the size of porosity can be reduced. Is.
  • the N content and the O content do not include N and O existing as inclusions (nitrides and oxides) in steel, but are N and O that are solid-solved in the matrix.
  • Zaku nests are shrinkage nests, and it is possible to reduce the size of Zaku nests by setting the amount of eutectic carbides in an appropriate range. Further, it can be seen from FIG. 5 that particularly excellent wear resistance is exhibited when the amount of Al is within the range of the present invention. The presence of coarse porosity or burrows causes the surroundings to fall off during rolling, resulting in reduced wear resistance.
  • N and O are contained in the raw material in advance or are mixed in contact with the atmosphere during melting of the raw material, the surface of the raw material to be used and inert gas (Ar, etc.) should be used to prevent contact with the atmosphere during melting. It is possible to adjust N+O by covering, but N and O combine with Al to easily form a nitride or an oxide, and it is also possible to adjust by the Al content. Further, the amount of eutectic carbide can be adjusted by the contents of Mo, Cr, and C constituting the eutectic carbide.
  • the present invention has been completed based on the above findings, and its gist is as follows. [1]% by mass, C: 1.6 to 2.5%, Si: 0.2 to 1.5%, Mn: 0.2 to 1.6%, Cr: 4.5 to 7.0% , Mo: 1.0 to 5.0%, V: 4.0 to 6.0%, Nb: 0.5 to 2.5%, and the total amount of N and O is 100 to 400 mass ppm. And a roll outer layer material for hot rolling having a composition of balance Fe and inevitable impurities. [2] The roll outer layer material for hot rolling according to the above [1], further containing Al: 0.01 to 0.30% by mass.
  • a composite roll for hot rolling having a three-layer structure of an outer layer, an intermediate layer and an inner layer or a two-layer structure of an outer layer and an inner layer, wherein the outer layer is the hot roll according to any one of the above [1] to [4].
  • a composite roll for hot rolling which comprises an outer layer material for a rolling roll.
  • the present invention it is possible to reduce the occurrence of porosity and dents, and to manufacture the outer layer material for hot rolling and the composite roll for hot rolling which are excellent in wear resistance and fatigue resistance. As a result, the surface quality of the material to be rolled and the roll life can be improved.
  • FIG. 1 is an explanatory view schematically showing a (test piece for X-ray CT) of a test piece used in X-ray CT measurement.
  • FIG. 2 is an example of a zigzag in a test piece confirmed in a transmission image obtained by X-ray CT measurement.
  • FIG. 3 is an explanatory view schematically showing a configuration of a tester used in the hot rolling wear test and a test piece for hot rolling wear test (wear test piece).
  • FIG. 4 is a diagram showing the relationship between N+O and the diameter of the circumscribed circle of porosity or burrow.
  • FIG. 5 is a diagram showing the relationship between the amount of Al and wear resistance.
  • FIG. 6 shows the configuration of the test machine used in the hot rolling fatigue test, the test piece for hot rolling fatigue test (fatigue test piece), and the outer circumference of the test piece for hot rolling fatigue test (fatigue test piece). It is explanatory drawing which shows typically the shape and dimension of the notch introduced into the surface.
  • FIG. 7 is a diagram showing a relationship between wear resistance and fatigue resistance according to the present invention.
  • the roll outer layer material of the present invention is produced by a known casting method such as a centrifugal casting method or a continuous casting overlay method, and can be directly used as a ring roll or a sleeve roll, but is suitable for hot finish rolling. It is applied as an outer layer material of a composite roll for hot rolling.
  • the composite roll for hot rolling of the present invention comprises an outer layer and an inner layer welded and integrated with the outer layer.
  • An intermediate layer may be arranged between the outer layer and the inner layer. That is, instead of the inner layer weld-integrated with the outer layer, an intermediate layer weld-integrated with the outer layer and an inner layer weld-integrated with the intermediate layer may be used.
  • the roll outer layer material for hot rolling of the present invention is, in mass %, C: 1.6 to 2.5%, Si: 0.2 to 1.5%, Mn: 0.2 to 1.6%, Cr. : 4.5 to 7.0%, Mo: 1.0 to 5.0%, V: 4.0 to 6.0%, Nb: 0.5 to 2.5%, and
  • the total amount of O is 100 to 400 mass ppm, and the balance is Fe and inevitable impurities.
  • C 1.6 to 2.5%
  • C has a function of forming a solid solution to increase the matrix hardness and to combine with a carbide forming element to form a hard carbide to improve the wear resistance of the roll outer layer material. If the C content is less than 1.6%, the amount of carbide is insufficient, and the wear resistance is reduced. In addition, the amount of eutectic solidification is reduced, and zigzag is generated. On the other hand, if the content of C exceeds 2.5%, the coarsening of carbides and the amount of eutectic carbides excessively increase, the outer layer material of the roll is hardened and embrittled, the generation and growth of fatigue cracks are promoted, and Reduces fatigue. Therefore, the C content is limited to the range of 1.6 to 2.5%. The C content is preferably 1.7% or more. Also, the C content is preferably 2.4% or less.
  • Si 0.2-1.5%
  • Si is an element that acts as a deoxidizer and improves the castability of the molten metal. Further, Si has a function of forming a solid solution in the matrix to strengthen the matrix. In order to obtain such an effect, it is necessary to contain 0.2% or more of Si. If the Si content is less than 0.2%, the strengthening effect of the matrix is small and the wear resistance is reduced. On the other hand, even if Si is contained in excess of 1.5%, the effect is saturated and the effect commensurate with the content cannot be expected, which is economically disadvantageous, and further, the matrix structure becomes brittle and fatigue resistance is reduced. In some cases. Therefore, the Si content is limited to 0.2 to 1.5%. The Si content is preferably 0.3% or more. Further, the Si content is preferably 1.3% or less.
  • Mn 0.2-1.6%
  • Mn is an element that has the effect of fixing S as MnS and making S harmless, and partly forming a solid solution with the matrix structure to improve the hardenability. Further, Mn has a function of forming a solid solution in the matrix to strengthen the matrix (solid solution strengthening). In order to obtain such an effect, it is necessary to contain 0.2% or more of Mn. If the Mn content is less than 0.2%, the strengthening effect of the matrix is small and the wear resistance is reduced. On the other hand, even if Mn is contained in excess of 1.6%, the effect is saturated, the effect commensurate with the content cannot be expected, and further, the material becomes brittle and the fatigue resistance may decrease. Therefore, the Mn content is limited to 0.2 to 1.6%. The Mn content is preferably 0.3% or more. Further, preferably, the Mn content is 1.4% or less.
  • Cr 4.5-7.0% Cr combines with C to mainly form a eutectic carbide to improve wear resistance, reduce the frictional force with the steel sheet during rolling, reduce surface damage of the roll, and stabilize rolling. Is an element having. In order to obtain such an effect, it is necessary to contain 4.5% or more of Cr. Further, when the content of Cr is less than 4.5%, the amount of eutectic carbide is small and the wear resistance is reduced. On the other hand, when the content of Cr exceeds 7.0%, coarse eutectic carbides increase, so that the fatigue resistance decreases. Therefore, when the Cr content is in the range of 4.5 to 7.0%, a rolling roll outer layer material having excellent fatigue resistance can be obtained.
  • the Cr content is preferably 4.7% or more. Further, the Cr content is preferably 6.5% or less.
  • Mo 1.0-5.0%
  • Mo is an element that combines with C to form hard carbides and improves wear resistance. Further, Mo dissolves in a hard MC-type carbide in which V, Nb and C are bonded to strengthen the carbide, and also dissolves in the eutectic carbide to increase the fracture resistance of these carbides. Through such an action, Mo improves the wear resistance and fatigue resistance of the roll outer layer material. In order to obtain such an effect, it is necessary to contain 1.0% or more of Mo. On the other hand, when Mo is contained in excess of 5.0%, hard and brittle carbides containing Mo as a main component are generated, and the rolling fatigue resistance during heat resistance is lowered, and the fatigue resistance is lowered. Therefore, the Mo content is limited to the range of 1.0 to 5.0%. The Mo content is preferably 1.2% or more. Further, the Mo content is preferably 4.9% or less.
  • V 4.0 to 6.0%
  • V is an important element in the present invention in order to combine wear resistance and fatigue resistance as a roll.
  • V forms extremely hard carbides (MC-type carbides), improves wear resistance, and effectively acts to divide and disperse eutectic carbides to improve heat resistance rolling fatigue resistance.
  • V content exceeds 6.0%, MC type carbides are coarsened, and thus various characteristics of the rolling roll are made unstable. Therefore, the V content is limited to the range of 4.0 to 6.0%.
  • the V content is preferably 4.3% or more. Further, the V content is preferably 5.9% or less.
  • Nb 0.5-2.5%
  • Nb improves wear resistance, particularly fatigue resistance, through the action of solid-dissolving in MC type carbide to strengthen MC type carbide and increase fracture resistance of MC type carbide.
  • Both Nb and Mo are solid-solved in the carbide, so that the wear resistance and the fatigue resistance are significantly improved.
  • Nb is an element that promotes the division of the eutectic carbide and suppresses the destruction of the eutectic carbide, and improves the fatigue resistance of the roll outer layer material.
  • Nb also has an action of suppressing segregation of MC type carbide during centrifugal casting. Such an effect becomes remarkable when the content of Nb is 0.5% or more.
  • the Nb content exceeds 2.5%, the growth of MC type carbides in the molten metal is promoted, and the rolling fatigue resistance during heat resistance is deteriorated. Therefore, the Nb content is limited to the range of 0.5 to 2.5%.
  • the Nb content is preferably 0.8% or more. Further, the Nb content is preferably 2.0% or less.
  • N+O 100-400 mass ppm N and O are mixed in the molten metal by absorbing nitrogen and oxygen in the raw material and nitrogen and oxygen existing in the atmosphere. Therefore, reduce the amount of nitrogen and oxygen in the raw material, cut off from the atmosphere during melting of the raw material (cover the surface of the molten metal with an inert gas such as argon gas, and cut off from the air), use the centrifugal casting method or It is possible to adjust the amounts of N and O in the molten metal by, for example, reducing the entrainment of air when casting by a casting method such as a continuous casting overlay method. Porosity can be reduced by setting the total content of N and O (N+O) to 400 mass ppm or less.
  • N+O is limited to the range of 100 to 400 mass ppm.
  • N+O is preferably 120 mass ppm or more, and more preferably 150 mass ppm or more.
  • N+O is preferably 370 mass ppm or less, more preferably 350 mass ppm or less.
  • Remainder Fe and Inevitable Impurities the balance other than the composition described above is Fe and inevitable impurities.
  • unavoidable impurities include S, Ni, Cu, Ca, Sb, Ti, Zr, and B. These are mixed in from raw materials and refractory materials during melting. These unavoidable impurities are S: 0.05% or less, Ni: 0.15% or less, Cu: 0.20% or less, Ca: 0.01% or less, Sb: 0.01% or less, Ti:0.
  • the total amount should be 0.5% or less. In addition, more preferably, the total amount is 0.4% or less.
  • Al and P may be mixed as unavoidable impurities. These contents are Al: less than 0.01% and P: less than 0.010%.
  • Al 0.01 to 0.30% and/or P: 0.010 to 0.040% may be contained.
  • Al 0.01 to 0.30%
  • Al is an element that combines with nitrogen and oxygen in the molten metal to form oxides and nitrides, and is an element that suppresses the formation of porosity and zigzags.
  • Al content is 0.01 to 0.30%.
  • the Al content is 0.02% or more.
  • the Al content is 0.25% or less.
  • P 0.010 to 0.040% It has been thought that P inevitably mixes from raw materials and the like in the manufacturing process and causes deterioration of mechanical properties. However, as a result of diligent studies by the inventors, the inclusion of a small amount of P results in hardness, tensile strength and compression. It was clarified that it has the effect of improving strength.
  • the high-strength (high hardness) action of P is considered to be solid solution strengthening by solid solution of P in the matrix structure. If the P content is 0.010 to 0.040%, the effect of improving the wear resistance can be obtained by increasing the strength of the matrix structure. However, if the P content exceeds 0.040%, the mechanical properties deteriorate. May be invited. Therefore, when P is contained, the P content is preferably in the range of 0.010 to 0.040%. In addition, more preferably, the P content is 0.012% or more. Further, the P content is preferably 0.035% or less.
  • the contents of C, V, Nb, and Mo satisfy the following formulas (1) and (2). 1.60 ⁇ (%V+%Nb)/%Mo ⁇ 3.5...(1) Formula 9.00 ⁇ %V+0.5 ⁇ %Nb+2.1 ⁇ %C ⁇ 11.0...(2) Formula
  • %C, %V, %Nb, and %Mo are contents (mass %) of each element.
  • Mo is solid-solved in the MC type carbide to be solid solution strengthened and wear resistance is improved.
  • carbide segregation is suppressed, and wear resistance and fatigue resistance are improved.
  • the wear resistance and fatigue resistance are improved because the content of V, Nb and C satisfies the range of the formula (2), and the structure forming process when the molten metal is solidified is changed. Conceivable.
  • the roll outer layer material is preferably produced by a known casting method such as a centrifugal casting method or a continuous casting overlay method. Needless to say, the present invention is not limited to these methods.
  • a molten metal having the above-described roll outer layer material composition is applied to a rotating mold whose inner surface is coated with a refractory material mainly containing zircon in a thickness of 1 to 5 mm. It is poured to a predetermined thickness and centrifugally cast.
  • the number of rotations of the mold is preferably set such that the gravity multiple applied to the outer surface of the roll is in the range of 100 to 200G.
  • the rotation of the mold is stopped and the mold is erected, and then the inner layer material is statically cast to form a composite roll.
  • the inner surface side of the roll outer layer material is redissolved to form a composite roll in which the outer layer and the inner layer, or the outer layer and the intermediate layer, and the intermediate layer and the inner layer are welded and integrated.
  • the composition of the inner layer and the intermediate layer is not particularly limited, but the inner layer to be statically cast is spheroidal graphite cast iron (ductile cast iron) excellent in castability and mechanical properties, worm-like graphite cast iron (CV cast iron) , Or forged steel is preferably used. Since the outer layer and the inner layer are integrally welded to each other in the centrifugal casting roll, about 1 to 8% of the components of the outer layer material are mixed in the inner layer. When carbide forming elements such as Cr and V contained in the outer layer material are mixed into the inner layer, the inner layer is weakened. Therefore, it is preferable that the mixing ratio of the components of the outer layer to the inner layer is suppressed to less than 6%.
  • the intermediate layer When forming the intermediate layer, it is preferable to use graphite steel, C: 1.5 to 3.0 mass% high carbon steel, hypoeutectic cast iron, etc. as the intermediate layer material. Similarly, the intermediate layer and the outer layer are integrally welded, and the components of the outer layer are mixed in the intermediate layer in the range of 10 to 95%. From the viewpoint of suppressing the mixing amount of the outer layer component to the inner layer, it is important to reduce the mixing amount of the outer layer component to the intermediate layer as much as possible.
  • the composite roll for hot rolling of the present invention is preferably heat-treated after casting. It is preferable that the heat treatment is performed twice or more by heating to 950 to 1100° C. and air-cooling or air-blast cooling, and further heating and holding at 480 to 570° C. and then cooling.
  • the preferable hardness of the hot rolling composite roll of the present invention is 79 to 88 HS (Shore hardness), and the more preferable hardness is 80 to 86 HS. If the hardness is lower than 79HS, the wear resistance deteriorates, and conversely, if the hardness exceeds 88HS, it becomes difficult to remove the cracks formed on the surface of the hot rolling roll during grinding by grinding. Such hardness can be obtained by adjusting the heat treatment temperature.
  • a molten metal having the composition of the roll outer layer material shown in Table 1 was melted in a high frequency induction furnace, and was made into a ring-shaped test material (ring roll; outer diameter: 250 mm ⁇ , width: 65 mm, wall thickness: 55 mm) by a centrifugal casting method.
  • the casting temperature was set to 1500° C.
  • the centrifugal force was set so that the outer peripheral portion of the ring-shaped roll material was a gravity multiple of 150 G.
  • the quenching process of heating to 1030° C. and air cooling, and the tempering process were performed at a temperature of 500° C. two or three times depending on the components so that the residual austenite amount was less than 10% by volume. Cooling from the tempering temperature was furnace cooling.
  • a wear test piece and an X-ray CT measurement test piece were sampled from the obtained ring-shaped test material, and a wear test and an X-ray CT measurement were performed.
  • three X-ray CT measurement test pieces (20 ⁇ 20 ⁇ 50 mm) were collected and subjected to X-ray CT measurement. Conducted to investigate the presence or absence of porosity and Zaku nest. As shown in FIG. 1, three X-ray CT measurement test pieces 2 were sampled at 120° intervals from the width center of the ring-shaped test material 1. An X-ray CT apparatus having a maximum tube voltage of 225 kV was used, and a transmission image of the entire test piece was taken at a tube voltage of 150 kV and a tube current of 80 ⁇ A.
  • the wear test method was as follows. A wear test piece (outer diameter 60 mm ⁇ , wall thickness 10 mm, chamfered) was taken from the obtained ring-shaped test material. As shown in FIG. 3, the abrasion test was performed by a two-disc sliding rolling method between the test piece and the mating material. The test piece 5 was rotated at 700 rpm while being cooled with cooling water 6, and the rotating test piece 5 was heated to 800° C.
  • the high frequency induction heating coil 7 material: S45C, outer diameter: 190 mm ⁇ , width: 15 mm.
  • C1 chamfer 8 was contacted with a load of 980 N, and was rolled at a slip ratio of 9%.
  • the abrasion test was carried out for 300 minutes, the mating piece was replaced with a new one every 50 minutes, and the test was carried out.
  • a hot rolling fatigue test piece (outer diameter 60 mm ⁇ , wall thickness 10 mm) was taken from the obtained ring-shaped roll material, and the fatigue resistance of the work roll for hot rolling in the actual machine was reproduced in JP 2010-101752.
  • a hot rolling fatigue test was carried out showing that it can be evaluated well.
  • a notch depth t: 1.2 mm, circumferential length L: 0.8 mm
  • FIG. 6 was used at two locations on the outer peripheral surface with a wire of 0.2 mm ⁇ . It was introduced by the electric discharge machining (wire cutting) method.
  • chamfering of 1.2 C was performed on the end of the rolling surface of the fatigue test piece. As shown in FIG.
  • the hot rolling fatigue test was performed by a two-disk rolling slide method of a notched test piece (hot rolling fatigue test piece) 5 and a heated counterpart material 8. That is, as shown in FIG. 6, a test piece (hot rolling fatigue test piece) 5 was rotated at 700 rpm while being water-cooled with cooling water 6, and the rotating test piece 5 was heated to 800° C. by a high frequency induction heating coil 7. The mating piece (material: S45C, outer diameter: 190 mm ⁇ , width: 15 mm) 8 was pressed with a load of 980 N and rolled at a slip ratio of 9%.
  • the two notches 9 introduced into the hot rolling fatigue test piece 5 were rolled until they were broken, and the rolling speeds until the respective notches were broken were obtained, and the average value thereof was taken as the hot rolling fatigue life. Then, when the hot rolling fatigue life exceeded 350 thousand times, it was evaluated that the hot rolling fatigue life was remarkably excellent.
  • the example of the present invention has wear resistance equal to or higher than that of the conventional example, and the porosity and the dents are remarkably reduced.
  • the wear ratio is large and the wear resistance is excellent. This is because if porosity or a dent exists, the periphery of the dent drops off during the wear test, and the weight of the test piece is greatly reduced.
  • the Al content in a preferable range, This is because the size is greatly reduced and the change in mass of the test piece during the wear test is reduced.
  • FIG. 7 when C, V, Nb, and Mo satisfy the formulas (1) and (2) (Nos. 11 to 13), while suppressing the formation of porosity and zigzag nests. It can be seen that it has excellent wear resistance and fatigue resistance as compared with the conventional example and the example of the present invention which does not satisfy the expressions (1) and (2).
  • the occurrence of porosity and burrows is reduced, and it is possible to manufacture the hot rolling roll outer layer material and the hot rolling composite roll that are excellent in wear resistance and fatigue resistance. . As a result, the surface quality of the material to be rolled and the roll life can be improved.
  • Ring-shaped test material 2 Test piece (Test piece for X-ray CT measurement) 3 Porosity or Zaku nest 4 Circumscribing circle 5 Specimen (wear specimen, hot rolling fatigue specimen) 6 Cooling water 7 High-frequency induction heating coil 8 Opposite piece 9 Notch

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Abstract

L'invention concerne un matériau de couche externe de rouleau devant être laminé à chaud et un rouleau composite devant être laminé à chaud, dont chacun a une résistance à l'abrasion/résistance à la fatigue équivalente à ou meilleure que celle des matériaux et rouleaux classiques et a une porosité et des cavités de retrait poreuses réduites.　À cet effet, l'invention porte sur un matériau de couche externe de rouleau devant être laminé à chaud, lequel matériau a une composition contenant, en % en masse, de 1,6 à 2,5% de C, de 0,2 à 1,5% de Si, de 0,2 à 1,6% de Mn, de 4,5 à 7,0 % de Cr, de 1,0 à 5,0% de Mo, de 4,0 à 6,0% de V et de 0,5 à 2,5% de Nb, et lequel contient également de N et de O dans une quantité totale de 100 à 400 ppm en masse, le reste étant constitué par du Fe et des impuretés inévitables.
PCT/JP2019/043844 2018-11-28 2019-11-08 Matériau de couche externe de rouleau devant être laminé à chaud, et rouleau composite devant être laminé à chaud WO2020110660A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
BR112021009847-0A BR112021009847B1 (pt) 2018-11-28 2019-11-08 Material de camada externa de rolo para ser laminado a quente, e rolo compósito para ser laminado a quente
KR1020217015973A KR102551616B1 (ko) 2018-11-28 2019-11-08 열간 압연용 롤 외층재 및 열간 압연용 복합 롤
EP19889262.2A EP3859025B1 (fr) 2018-11-28 2019-11-08 Matériau de couche extérieure pour rouleau à chaud et rouleau à chaud composite
JP2020509132A JP6866958B2 (ja) 2018-11-28 2019-11-08 熱間圧延用ロール外層材および熱間圧延用複合ロール
CN201980077813.1A CN113166864B (zh) 2018-11-28 2019-11-08 热轧用辊外层材料和热轧用复合辊

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JP2018-221998 2018-11-28
JP2018221998 2018-11-28

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JPH051350A (ja) 1990-11-21 1993-01-08 Kawasaki Steel Corp 圧延用ロール外層材
JP2000239779A (ja) 1999-02-19 2000-09-05 Kawasaki Steel Corp 遠心鋳造製圧延ロール用外層材、圧延ロールおよびその製造方法
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JPH051350A (ja) 1990-11-21 1993-01-08 Kawasaki Steel Corp 圧延用ロール外層材
JP2000239779A (ja) 1999-02-19 2000-09-05 Kawasaki Steel Corp 遠心鋳造製圧延ロール用外層材、圧延ロールおよびその製造方法
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JP2009221573A (ja) * 2008-03-18 2009-10-01 Jfe Steel Corp 熱間圧延用遠心鋳造製複合ロール
JP2010101752A (ja) 2008-10-23 2010-05-06 Jfe Steel Corp 熱間圧延用ロールの評価方法
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EP3859025B1 (fr) 2023-05-03
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TWI735082B (zh) 2021-08-01
KR102551616B1 (ko) 2023-07-04
JP6866958B2 (ja) 2021-04-28
BR112021009847B1 (pt) 2023-12-12
KR20210082226A (ko) 2021-07-02
CN113166864A (zh) 2021-07-23
JPWO2020110660A1 (ja) 2021-02-15
EP3859025A1 (fr) 2021-08-04
BR112021009847A2 (pt) 2021-08-17

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