WO2016031519A1 - 圧延用複合ロールの外層材及び圧延用複合ロール - Google Patents

圧延用複合ロールの外層材及び圧延用複合ロール Download PDF

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Publication number
WO2016031519A1
WO2016031519A1 PCT/JP2015/072375 JP2015072375W WO2016031519A1 WO 2016031519 A1 WO2016031519 A1 WO 2016031519A1 JP 2015072375 W JP2015072375 W JP 2015072375W WO 2016031519 A1 WO2016031519 A1 WO 2016031519A1
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Prior art keywords
outer layer
rolling
less
layer material
composite roll
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Ceased
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PCT/JP2015/072375
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English (en)
French (fr)
Japanese (ja)
Inventor
豊 辻本
剛 大段
木村　広之
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Kubota Corp
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Kubota Corp
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First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=55399418&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=WO2016031519(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Kubota Corp filed Critical Kubota Corp
Priority to US15/500,283 priority Critical patent/US10376937B2/en
Priority to EP15835002.5A priority patent/EP3187606B1/en
Priority to KR1020177005050A priority patent/KR102361917B1/ko
Priority to BR112017002383-0A priority patent/BR112017002383B1/pt
Priority to CN201580045767.9A priority patent/CN106574332B/zh
Publication of WO2016031519A1 publication Critical patent/WO2016031519A1/ja
Anticipated expiration legal-status Critical
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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
    • B22D13/02—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
    • 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
    • B21B27/005—Rolls with a roughened or textured surface; Methods for making same
    • 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
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • 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
    • 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
    • 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
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/613—Gases; Liquefied or solidified normally gaseous 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/62—Quenching devices
    • 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
    • C22C37/06—Cast-iron alloys containing chromium
    • C22C37/08—Cast-iron alloys containing chromium with nickel
    • 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
    • C22C38/02—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
    • C22C38/18—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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
    • C22C38/56—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.7% by weight of carbon
    • H—ELECTRICITY
    • H05—ELECTRIC TECHNIQUES NOT OTHERWISE PROVIDED FOR
    • H05B—ELECTRIC HEATING; ELECTRIC LIGHT SOURCES NOT OTHERWISE PROVIDED FOR; CIRCUIT ARRANGEMENTS FOR ELECTRIC LIGHT SOURCES, IN GENERAL
    • H05B6/00—Heating by electric, magnetic or electromagnetic fields
    • H05B6/02—Induction heating
    • H05B6/22—Furnaces without an endless core
    • H05B6/24—Crucible furnaces
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B2001/225—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by hot-rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B2203/00—Auxiliary arrangements, devices or methods in combination with rolling mills or rolling methods
    • B21B2203/18—Rolls or rollers

Definitions

  • the present invention relates to an outer layer material of a composite roll for rolling used for hot rolling and a composite roll for rolling using this as an outer layer.
  • the composite roll for rolling used in hot rolling is required to have excellent wear resistance, rough skin resistance and crack resistance in the outer layer in contact with the steel plate. For this reason, a high-speed cast iron material is used as the outer layer material constituting the roll outer layer (see, for example, Patent Document 1).
  • the rolling pitch has been shortened from the viewpoint of productivity improvement, and the thermal load on the outer surface of the roll has increased.
  • the rolled steel sheet is also thin and hard, and the wear of the outer roll layer is also increasing. Since the roll surface is repeatedly exposed to a high temperature of about 1000 ° C. and a water cooling of about 30 ° C. during rolling, surface heat cracks occur due to thermal shock, and microscopic structural loss occurs. It is said that the rough skin resistance is good when the degree of heat cracking or tissue loss is shallow. Heat cracks and structure loss are likely to occur preferentially in the eutectic carbides at the grain boundaries that will be the final solidified part.
  • the outer layer is exposed to heat by molten metal in the intermediate layer or inner layer or heat by high-temperature heat treatment such as austenite after solidification. It was found that when elevating to a temperature exceeding the melting point of the eutectic carbide at the grain boundary of the outer layer material during this heating, the eutectic carbide partially melted and cavities were formed. Due to the formation of the cavities, the rough skin resistance of the outer layer is lowered, and the roll life may be shortened due to deep damage to the roll surface.
  • MC type carbides In the outer layer made of high-speed cast iron material, Cr, Mo, W, V, Nb, Fe, etc. are combined with C to mainly form MC type carbides.
  • This carbide increases the normal temperature and high temperature hardness and contributes to the improvement of wear resistance. Cracks occur on the outer layer surface due to thermal shock during rolling, but the inventors have partial melting damage in secondary eutectic carbides at grain boundaries that are weaker to thermal shock than MC type carbides. I clarified that.
  • B is an effective component that improves the effect of cleaning the molten metal during casting and improves the hardenability.
  • B is an effective component that improves the effect of cleaning the molten metal during casting and improves the hardenability.
  • the object of the present invention is to increase the strength and melting point of the secondary eutectic carbide and to improve the rough skin resistance by containing a small amount of B in the secondary eutectic carbide. It is providing the composite roll for rolling which uses a material and this as an outer layer.
  • the outer layer material of the composite roll for rolling of the present invention is It is an outer layer material of a composite roll for rolling, In mass%, C: 1.8% to 2.5%, Si: more than 0% to 1.0% or less, Mn: more than 0% to 1.0% or less, Ni: more than 0% 0.5% or less, Cr: more than 3.0% to 8.0% or less, Mo: more than 2.0% to 10.0% or less, W: more than 0% to 10.0% or less, V: more than 0% and not more than 10.0%, B: more than 0% and less than 0.01%, balance Fe and inevitable impurities are contained.
  • the outer layer material preferably further contains Nb: 0.01% or more and 2.0% or less and / or Ti: 0.01% or more and 1.0% or less in mass%.
  • the solidification rate during casting of the outer layer material is desirably 8 mm / min or more.
  • the outer layer material preferably contains secondary eutectic carbide, and the melting temperature of the secondary eutectic carbide is preferably higher than 1100 ° C. Further, B (t2) ⁇ B (t1) ⁇ 0.002 where B (t1) is the mass% of the B concentration on the surface of the outer layer material and B (t2) is the mass% of the B concentration on the inner surface of the outer layer material. It is desirable.
  • the composite roll for rolling of the present invention is
  • the outer layer material is an outer layer, and an inner layer or an intermediate layer and an inner layer are provided inside the outer layer material.
  • the outer layer material of the composite roll for rolling of the present invention can reduce the amount of B contained in the secondary eutectic carbide by adjusting the amount of B as described above. Thereby, since the strength of the secondary eutectic carbide can be improved, the secondary eutectic carbide can be prevented from being melted even when exposed to a high temperature of about 1100 ° C. after solidification.
  • the outer layer of the high-speed roll having secondary eutectic carbide having no melted portion can exhibit excellent skin roughness resistance.
  • the composite roll for rolling using the outer layer material of the present invention as an outer layer has high secondary eutectic carbide strength and excellent skin roughness resistance. Therefore, it is possible to reduce the structural loss of the outer layer surface during rolling, to reduce the grinding frequency of the outer layer surface, and to reduce the consumption of the outer layer.
  • the outer layer material constituting the outer layer of the rolling composite roll of the present invention is a high-speed cast iron material and contains the following components. In the following description, “%” is mass% unless otherwise specified.
  • C 1.8% or more and 2.5% or less
  • C mainly combines with Fe and Cr to form M 7 C 3 type high-hardness composite carbide, and also combines with Mo, V, Nb, W, etc.
  • MC type, M 6 C type, M 2 C type and other high hardness composite carbides are also formed.
  • C% of 1.8% or more is required, and more preferably 1.85% or more.
  • the C content exceeds 2.5%, the amount of carbide increases and becomes brittle, and crack resistance deteriorates. Therefore, it is defined as 2.5% or less, and more preferably 2.25% or less. .
  • Si more than 0% and not more than 1.0% Si is added because it is an element necessary for ensuring hot metal flow and deoxidation. On the other hand, if it exceeds 1.0%, the hardenability decreases and the material becomes brittle, so the Si content exceeds 0% and is 1.0% or less.
  • Mn more than 0% and 1.0% or less Mn has a function of increasing the curing ability. Further, it is an element effective for binding to S to form MnS and preventing embrittlement by S. On the other hand, if the content is too large, the toughness is lowered, so the Mn content is specified to exceed 0% and not more than 1.0%.
  • Ni more than 0% and 0.5% or less Ni lowers the hardness at high temperature, so a small addition amount is desired.
  • a sufficient quenching rate during heat treatment is required.
  • the lower limit of the Ni content is desirably 0.01%.
  • Ni exceeds 0.5% the decrease in high-temperature hardness becomes large, so the upper limit is made 0.5%, preferably 0.3%.
  • Cr 3.0% to 8.0% Cr dissolves in the base and improves hardenability. Also, eutectic carbide is formed together with Mo and W. In order to improve the hardenability, it is necessary to contain Cr of 3.0% or more. Conversely, if it exceeds 8.0%, eutectic carbide increases, and the tensile strength of the material decreases. 3.0% to 8.0%. Desirably, Cr is 3.5% or more and 6.5% or less.
  • Mo 2.0% or more and 10.0% or less Mo combines with Fe, Cr, Nb, W and C to form a composite carbide mainly of M 7 C type, M 6 C type, M 2 C type. , Contribute to improving wear resistance by increasing the normal temperature and high temperature hardness. For this reason, it is contained at least 2.0% or more, preferably 4.0% or more. On the other hand, if the content is too large, the retained austenite is stabilized and it becomes difficult to obtain high hardness. Therefore, the upper limit is defined as 10.0%, preferably 7.0%.
  • W more than 0% and 10.0% or less W also combines with C together with Fe, Cr, Mo, Nb to form a composite carbide to improve normal temperature and high temperature hardness and improve wear resistance Included to contribute.
  • an upper limit is prescribed
  • V More than 0% and 10.0% or less V combines with C together with Fe, Cr, Mo, W, and mainly constitutes MC type carbides at the time of solidification, increasing the normal temperature and high temperature hardness, and wear resistance Contributes to improvement.
  • MC type carbide containing V contributes to improvement of wear resistance by increasing normal temperature and high temperature hardness.
  • This MC-type carbide is formed in a branch shape in the thickness direction and suppresses plastic deformation of the base, contributing to improvement of mechanical properties and further crack resistance.
  • the upper limit of V is defined as 10.0%, preferably 8.0%.
  • B More than 0% and 0.01% or less B is contained because it has an effect of increasing the hardenability by B dissolved in the base.
  • the lower limit of the B content is preferably 0.0002%.
  • the content is too high, the melting point of the secondary eutectic carbide is lowered and the material becomes brittle, so the upper limit of the content in the cast iron material is set to 0.01%.
  • the difference in B concentration can be adjusted by dividing the addition of B to the molten metal.
  • the value of B (t2) ⁇ B (t1) is It is preferable that it is 0.002 or more. More preferably, it is 0.003 or more. If the value of B (t2) ⁇ B (t1) is too large, the B concentration on the inner surface of the outer layer material becomes too high, and is preferably 0.008 or less, and more preferably 0.005 or less.
  • the outer layer can further contain the following components.
  • Nb 0.01% or more and 2.0% or less and / or Ti: 0.01% or more and 1.0 or less
  • Nb combines with Fe, Cr, Mo, W and C to form mainly MC type carbides. In addition, it increases the normal temperature and high temperature hardness and contributes to the improvement of wear resistance. Further, Nb has the effect of finely dispersing MC type carbides and refining the structure, and contributes to improvement of mechanical properties and crack resistance. For this reason, Nb is contained 0.01% or more, desirably 0.1% or more. On the other hand, when it contains too much, a carbide
  • Ti also generates oxides in the molten metal, lowers the oxygen content in the molten metal, improves the soundness of the product, and the generated oxides act as crystal nuclei. There is an effect in making. On the other hand, when it contains too much, there exists an inconvenience which remains as an inclusion. For this reason, even when adding Ti, the content should be 0.01% or more and 1.0% or less.
  • the outer layer material of the present invention contains the above components, and the remainder is formed of Fe and impurities inevitably mixed.
  • P and S may be contained in the balance, and in that case, it is preferable to define the components as follows. If the P content exceeds 0.08% and the S content exceeds 0.06%, the oxidation resistance and toughness deteriorate. Therefore, P and S are 0.08% or less and 0.06% or less, respectively. Is preferred. Desirably, the upper limit of P and S is made 0.05% or less. On the other hand, since P improves machinability, it is preferable to contain it exceeding 0%, and it is desirable to contain 0.015% or more. Further, S is combined with Mn to improve the machinability, so it is preferable to contain more than 0%, and more preferably 0.005% or more.
  • FIG. 1 is a photograph in which a dye penetrant inspection was performed on a test piece of Example 3 which is an invention example.
  • FIG. 2 is a photograph in which a dye penetration test was performed on the test piece of Comparative Example 2.
  • FIG. 3 is a photograph showing an enlarged view of the melted portion of FIG.
  • the composite roll for rolling of the present invention can be composed of an outer layer to be rolled, an intermediate layer and / or an inner layer inside the outer layer, and a shaft material.
  • the inner layer material constituting the inner layer include materials having toughness such as high-grade cast iron, ductile cast iron, and graphite steel, and examples of the intermediate layer material constituting the intermediate layer include an adamite material.
  • the outer layer can be cast by, for example, centrifugal casting or stationary casting, by melting a molten alloy of the outer layer material having the above components.
  • Centrifugal casting may be any of a vertical type (rotary axis is vertical), an inclined type (rotary axis is oblique), and a horizontal type (rotary axis is horizontal).
  • the solidification rate is 8 mm / min or more when casting the outer layer material.
  • the solidification rate can be adjusted by cooling the mold with air or water.
  • an inner layer or an intermediate layer and an inner layer are cast or shrink-fitted to produce a composite roll for rolling.
  • the rolling composite roll is subjected to quenching treatment.
  • B can improve the hardenability.
  • B since B is not concentrated in the secondary eutectic carbide, it is contained in the base in a large amount, so that the hardness of the base is further increased by quenching. Can do.
  • the outer layer according to the present invention can have a Vickers hardness of the secondary eutectic carbide of, for example, 1500 HV to 1900 HV by applying the above components and solidification rate. The reason why the hardness is increased in this way is considered to be because the B amount of the secondary eutectic carbide is reduced.
  • the composite roll for rolling comprised as said outer layer material as an outer layer suppresses the coarsening of secondary eutectic carbide, and has received a thermal shock during heat treatment and rolling due to increased strength and melting point. Can prevent the secondary eutectic carbide from being lost or melted.
  • the area ratio of MC type carbide was 7% to 15%
  • the area ratio of secondary eutectic carbide was 1% to 6%
  • the remaining base By adjusting the content of B and further adjusting the solidification rate, it was possible to suppress the growth of secondary eutectic carbide. This means that the area ratio of the secondary eutectic carbide could be kept low.
  • the amount of B in the outer layer was measured, the amount of B on the outer layer surface was 0.006%, the amount of B on the inner surface of the outer layer was 0.009%, and the mass% of the B concentration on the outer layer material surface was B (t1 )
  • the mass% of the B concentration on the inner surface of the outer layer material is B (t2)
  • the value of B (t2) ⁇ B (t1) is 0.002 or more.
  • the composite roll for rolling using the outer layer material of the present invention as an outer layer has high secondary eutectic carbide strength and excellent skin roughness resistance. Accordingly, it is possible to suppress defects on the outer layer surface during rolling, and it is possible to reduce the frequency of grinding the outer layer surface and reduce the consumption of the outer layer.
  • the composite roll for rolling composed of the outer layer material of the present invention as an outer layer is particularly suitable for application to the pre- and middle-stage stands of hot finish rolling that requires operational stability.
  • the inner layer was cast to produce a composite roll for rolling.
  • the obtained composite roll for rolling was quenched.
  • the quenching was performed by forced air cooling using a large electric fan so that the cooling rate on the roll surface from the austenitizing temperature to 700 ° C. was 900 ° C./h or more.
  • the test piece which has a side of 30 mm or more and each has about 10 mm in thickness is cut out.
  • the test piece was held at a temperature of 1050 ° C. to 1125 ° C. for 30 minutes, and a dye penetrant inspection was performed on each test piece, and the surface state was observed.
  • “ ⁇ ” represents a test piece in which no erosion loss was confirmed in the dye penetration inspection
  • “ ⁇ ” represents a test piece in which erosion was confirmed.
  • FIG. 1 is a photograph of a test piece of Invention Example 3. Referring to FIG. 1, no indication pattern is observed on the surface of the test piece.
  • FIG. 2 is a photograph of the test piece of Comparative Example 2. Referring to FIG. 2, indication patterns in which secondary eutectic carbides are dissolved at a plurality of locations on the surface of the test piece are observed.
  • FIG. 3 is an enlarged photograph of the instruction pattern of FIG. As shown in the figure, it can be seen from the instruction pattern that the organization is missing. This means that the secondary eutectic carbide was melted at a high temperature as a result of B being concentrated and mixed in the secondary eutectic carbide.
  • This invention is useful for the outer-layer material of the composite roll for rolling used for hot rolling, and the composite roll for rolling which uses this as an outer layer.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Electromagnetism (AREA)
  • Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
PCT/JP2015/072375 2014-08-25 2015-08-06 圧延用複合ロールの外層材及び圧延用複合ロール Ceased WO2016031519A1 (ja)

Priority Applications (5)

Application Number Priority Date Filing Date Title
US15/500,283 US10376937B2 (en) 2014-08-25 2015-08-06 Outer layer material for composite roll for rolling and composite roll for rolling
EP15835002.5A EP3187606B1 (en) 2014-08-25 2015-08-06 Outer layer material for composite rolls for rolling, and composite roll for rolling
KR1020177005050A KR102361917B1 (ko) 2014-08-25 2015-08-06 압연용 복합 롤의 외층재 및 압연용 복합 롤
BR112017002383-0A BR112017002383B1 (pt) 2014-08-25 2015-08-06 Material da camada externa para um cilindro composto para laminação, e cilindro composto para laminação
CN201580045767.9A CN106574332B (zh) 2014-08-25 2015-08-06 轧制用复合辊的外层材料及轧制用复合辊

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JP2014-170139 2014-08-25
JP2014170139A JP6028282B2 (ja) 2014-08-25 2014-08-25 圧延用複合ロールの外層材及び圧延用複合ロール

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JP2020022989A (ja) * 2018-08-08 2020-02-13 日立金属株式会社 圧延用遠心鋳造複合ロールの外層材、及び圧延用遠心鋳造複合ロール

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JP6313844B1 (ja) * 2016-12-28 2018-04-18 株式会社クボタ 圧延用複合ロール

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EP3187606A1 (en) 2017-07-05
EP3187606B1 (en) 2019-05-22
JP2016043389A (ja) 2016-04-04
BR112017002383A2 (pt) 2017-11-28
BR112017002383B1 (pt) 2021-06-01
KR20170045226A (ko) 2017-04-26
KR102361917B1 (ko) 2022-02-11
CN106574332A (zh) 2017-04-19
US20170225209A1 (en) 2017-08-10
CN106574332B (zh) 2019-08-06
US10376937B2 (en) 2019-08-13
JP6028282B2 (ja) 2016-11-16

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