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WO2018042929A1 - Matériau de couche externe pour cylindre de laminage, et cylindre composite de laminage - Google Patents

Matériau de couche externe pour cylindre de laminage, et cylindre composite de laminage Download PDF

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Publication number
WO2018042929A1
WO2018042929A1 PCT/JP2017/026246 JP2017026246W WO2018042929A1 WO 2018042929 A1 WO2018042929 A1 WO 2018042929A1 JP 2017026246 W JP2017026246 W JP 2017026246W WO 2018042929 A1 WO2018042929 A1 WO 2018042929A1
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WO
WIPO (PCT)
Prior art keywords
roll
outer layer
rolling
layer material
carbide
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2017/026246
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English (en)
Japanese (ja)
Inventor
市野　健司
鈴木　健史
直道 岩田
哲男 持田
石田　清仁
郁雄 大沼
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Steel Corp
Original Assignee
JFE Steel Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by JFE Steel Corp filed Critical JFE Steel Corp
Priority to EP17846538.1A priority Critical patent/EP3488942A4/fr
Priority to JP2017558592A priority patent/JP6304466B1/ja
Priority to KR1020197006147A priority patent/KR102228851B1/ko
Priority to BR112019004312-8A priority patent/BR112019004312B1/pt
Priority to PCT/JP2017/031081 priority patent/WO2018043534A1/fr
Priority to CN201780053764.9A priority patent/CN109641251B/zh
Priority to TW106129885A priority patent/TWI650430B/zh
Publication of WO2018042929A1 publication Critical patent/WO2018042929A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • 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
    • 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
    • C22C27/00—Alloys based on rhenium or a refractory metal not mentioned in groups C22C14/00 or C22C16/00
    • C22C27/04—Alloys based on tungsten or molybdenum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18—High-melting or refractory metals or alloys based thereon

Definitions

  • the present invention relates to a rolling roll outer layer material suitable for hot rolling or cold rolling and a composite roll for rolling using the same, and particularly relates to improvement of wear resistance.
  • a cold roll work roll is required to have excellent wear resistance and high hardness.
  • the wear resistance is improved by making the roll material highly alloyed.
  • the grindability is deteriorated or the damage caused by a roll accident is increased (decrease in accident resistance). Therefore, it is necessary to use a material that has both grindability and accident resistance.
  • the surface properties of the roll in direct contact with the steel sheet uniform and fine. Specifically, the roll material is highly clean and fine. It is required to make cast iron and cast steel having a fine microstructure.
  • Patent Document 1 describes a hot roll composite roll in which an outer layer is formed around a steel core by a continuous overlaying method.
  • the outer layer material is, by weight, C: 1.0 to 4.0%, Si: 3.0% or less, Mn: 1.5% or less, Cr: 2 to 10%, Mo : 9% or less, W: 20% or less, V: 2 to 15% included, P: 0.08% or less, S: 0.06% or less, B: 0.0500% or less, with the composition composed of the remaining Fe and inevitable impurities It is said that the hardness of the base has a Vickers hardness (Hv) of 550 or more, which is composed of a structure containing 5-30% granular carbide and 6% or more non-particulate carbide.
  • Hv Vickers hardness
  • the outer layer material may further contain Ni: 5.0% or less, Co: 5.0% or less, and Nb: 5.0% or less. Due to this, due to the presence of non-particulate carbides of a predetermined amount or more, even if cracks are generated, it is suppressed from progressing to the deep part of the roll, heat crack resistance is improved, and VC-based hard carbides are included. Therefore, the wear resistance is also good.
  • Such a high-speed roll outer layer material needs to disperse a large amount of hard carbide throughout the base in order to improve wear resistance.
  • hard carbides produced with a high-speed composition generally have a lighter specific gravity than the base, and are likely to cause segregation during casting.
  • the centrifugal casting method which is a typical casting method for roll outer layer material because of its excellent productivity and economy, the phase with light specific gravity tends to accumulate and segregate inside due to centrifugal force. It has been considered difficult to manufacture by a centrifugal casting method.
  • Patent Document 2 discloses, in mass%, C: 1.5- Including 3.5%, Si: 1.5% or less, Mn: 1.2% or less, Ni: 5.5% or less, Cr: 5.5-12.0%, Mo: 2.0-8.0%, V: 3.0-10.0%, Nb: 0.5-7.0%
  • a roll outer layer material containing Nb and V such 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 described.
  • Patent Document 3 by mass, 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 contained so that the contents of Nb, V, and C satisfy a specific relationship, and the ratio of Nb and V falls within a specific range.
  • a roll outer layer material is described. By adopting such a composition, segregation in the roll outer layer material is suppressed even when the centrifugal casting method is applied, and wear resistance and crack resistance are improved, which greatly contributes to improvement in hot rolling productivity. .
  • Patent Document 4 describes a centrifugal cast composite roll.
  • the centrifugally cast composite roll described in Patent Document 4 is composed of an outer layer and an inner layer of cast iron or cast steel, and the outer layer is, by weight, C: 1.0 to 3.0%, Si: 0.1 to 3.0%, Mn: 0.1 to 2.0% , Cr: 2.0-10.0%, Mo: 0.1-10.0%, V: 1.0-10.0%, W: 0.1-10.0%, and Mo + W: 10.0% or less of the alloy components and the balance are from Fe and inevitable impurities It has the composition which becomes.
  • Patent Document 5 describes a centrifugal cast outer layer material for a roll.
  • the centrifugal cast outer layer material for rolling rolls described in Patent Document 5 contains C: 4.5 to 9%, Si: 0.1 to 3.5%, Mn: 0.1 to 3.5%, and V: 18 to 40% by mass. It has a composition, and preferably has a structure in which MC carbides are dispersed in an area ratio of 20 to 60% in a base having a Vickers hardness of HV550 to 900.
  • MC carbide with a small specific gravity is concentrated on the inner surface side, and positively utilizes centrifugal casting segregation. After centrifugal casting, cutting is performed so as to leave only a layer in which MC carbide is concentrated. For example, it is said that an outer layer of a roll containing many MC carbides can be reliably formed at low cost.
  • Cemented carbide has long been known as a material having extremely excellent wear resistance.
  • tungsten carbide WC is generally molded and sintered together with Co as a binder.
  • Patent Document 6 Patent Document 7, Patent Document 8, Patent Document 9, Patent Document 10, and the like are described.
  • Patent Document 6 describes a tungsten carbide-based cemented carbide for hot rolling rolls and hot rolling guide rolls.
  • the weight ratio of chromium to the sum of cobalt and nickel is 1/1 to 1/99
  • the weight ratio of cobalt to nickel is 9/1 to 1/9
  • tungsten carbide is 88 weights. %
  • a tungsten carbide based alloy in which the total of cobalt, nickel and chromium is 12 to 65% by weight.
  • Patent Document 6 describes an example in which such a cemented carbide is applied to a roll for hot rolling of a normal steel material (wire material).
  • Patent Document 7 describes a hot wire roll made of cemented carbide.
  • the cemented carbide used is replaced with WC having an average particle diameter of 1 ⁇ m to 5 ⁇ m, or a part of WC is replaced by 10% by weight or less with one or more of TiC, TaC, and NbC.
  • the cemented carbide has a polarization potential of 0.33 to 0.90 with respect to the sum of Ni and Co, and a polarization potential of 0.3 V or more with respect to cooling general industrial water.
  • Patent Document 8 discloses that an outer layer made of cemented carbide is joined to an outer periphery of an inner layer made of a steel or iron-based material via an intermediate layer, and the intermediate layer has a mean particle size of 3 ⁇ m or less.
  • a rolling composite roll made of cemented carbide formed using powder is described. Further, the content of WC particles in the intermediate layer is preferably set to 70% or less by weight. Thereby, it is said that the roll for cemented carbide rolling excellent in abrasion resistance and highly reliable in strength can be obtained.
  • Patent Document 9 an outer layer is formed of a cemented carbide having excellent wear resistance, and an intermediate layer made of a cemented carbide containing WC and Ni is provided to provide a highly reliable cemented carbide.
  • An alloy rolling roll is disclosed.
  • Patent Document 1 has a problem that productivity is low and cost is high because an outer layer is formed around a steel core by a continuous overlaying method.
  • the contents of Nb, V and C are limited to a specific range, and MC type carbides are uniformly dispersed to improve wear resistance and crack resistance. It is said.
  • M 7 C 3 type carbides and M 6 C type carbides that contain a large amount of Cr and Mo, so that further improvement in properties can be achieved only from the viewpoint of uniformly dispersing MC type carbides. That's not enough.
  • Mo + W is limited to 10.0% or less in order to suppress crystallization of M 6 C-type carbides that are likely to cause aggregation and segregation. Making it possible.
  • limiting the contents of Mo and W has left a problem for the recent demand for further improvement in wear resistance.
  • the amount of carbide forming elements such as Mo, V, and W is increased because the formed carbide is light, so that the formed carbide is accumulated on the inner surface side, There was a concern that it would agglomerate at the boundary of the film and cause a decrease in the bonding strength at the boundary.
  • Patent Document 6 and Patent Document 7 using cemented carbide are intended for small rolls for wire rod rolling, and this technique can be used as a cold rolling roll or a hot rolling roll. It is difficult to apply as it is to the manufacture of a large roll.
  • HIP processing which is an expensive process compared with centrifugal casting products, is required, there is a problem that manufacturing costs are high even for small products.
  • Patent Document 8 Patent Document 9, and Patent Document 10 that use cemented carbide as an outer layer material for a roll for sheet rolling assume that the outer layer material is formed by a sintered-HIP method. Therefore, the problem that the manufacturing cost is extremely high remains.
  • these techniques use soft Co or Ni as a binder, and there is a problem that dents (recesses) are easily generated during rolling, and the practical application has not progressed.
  • the present invention solves such problems of the prior art, and provides a roll outer layer material excellent in wear resistance, which has significantly improved wear resistance compared to the prior art, and a composite roll for rolling using the roll at low cost. Objective.
  • the present inventors have made it possible to manufacture a rolling roll having extremely high wear resistance similar to that of cemented carbide by a centrifugal casting method that is excellent in productivity and economy.
  • the hard carbides can be concentrated and concentrated on the outer surface side of the roll by utilizing the centrifugal force acting on the molten metal and the crystallization phase during centrifugal casting, the wear resistance of the centrifugal casting roll is reduced. I came to think that the sex could be remarkably improved.
  • the alloy used is an Fe-based alloy
  • the formation of W-type eutectic carbide is promoted, and the appearance of M 6 C type carbide as the primary crystal is inhibited.
  • a W—Co-based alloy that increases the carbon activity as the alloy used the formation of W-type eutectic carbide is suppressed, and M 6 C-type carbide enriched with W in the molten metal is the first.
  • the C content is less than 0.6% by mass, the primary crystal M 6 C type carbide does not appear.
  • the C content exceeds 3% by mass, the liquidus temperature increases. It has been found that, since it becomes too high, melting and casting become difficult, and MC-type carbides and M 2 C-type carbides that are very fragile grow and become coarse, which easily causes roll breakage.
  • the gist of the present invention is as follows.
  • W-Co based alloy roll outer layer material for rolling which has a gradient composition in which the W content decreases in the radial direction from the outer peripheral side of the roll toward the inner peripheral side, and corresponds to the maximum diameter during rolling use.
  • the outer layer material surface at the position is mass%, W: 25 to 70%, Co: 5 to 45%, C: 0.6 to 3.5%, Si: 0.05 to 3%, Mn: 0.05 to 3%, Mo: 1 to
  • a roll outer layer material for rolling having a composition containing 15% and the balance of inevitable impurities.
  • a rolling composite roll comprising an outer layer, an intermediate layer welded and integrated with the outer layer, and an inner layer welded and integrated with the intermediate layer, wherein the outer layer is any one of (1) to (3)
  • a composite roll for rolling which is an outer layer material for a roll for rolling described in 1.
  • a roll for rolling excellent in wear resistance particularly suitable for a hot rolling or cold rolling roll, particularly a roll for centrifugal casting, can be manufactured at low cost and easily. There are remarkable effects in the industry.
  • tissue photograph which shows the scanning electron microscope structure
  • (A) is sleeve No. 13 (test material No. 13), and
  • (b) is sleeve No. 5 (test material No. 5). It is explanatory drawing which shows typically the outline
  • the roll outer layer material for rolling of the present invention is made by centrifugal casting.
  • centrifugal rolling roll outer layer material means a rolling roll outer layer material that has been manufactured using a centrifugal casting method that has been conventionally used as a rolling roll manufacturing method. To do.
  • Roll outer layer material for rolling manufactured using the centrifugal casting method (“centrifugal casting” outer layer material for rolling roll) is conventionally referred to as "things" with rolling rolls manufactured by other manufacturing methods. It can be clearly distinguished, and specifying the outer layer material of the roll made of “centrifugal casting” by structure and characteristics is laborious and impractical.
  • the roll outer layer material for rolling according to the present invention is made of a W—Co base alloy, and has a gradient composition in which the W content decreases in the radial direction from the outer peripheral side of the roll toward the inner peripheral side.
  • the surface of the outer layer material at the corresponding position is in mass%, W: 25-70%, Co: 5-45%, C: 0.6-3.5%, Si: 0.05-3%, Mn: 0.05-3% , Mo: 1 to 15%, with the balance being inevitable impurities.
  • the above-described composition has a radial position corresponding to at least 20% of the volume on the outer surface side with respect to the total volume of the outer layer material. It is preferable to satisfy even a position of at least 9 mm in the radial direction from the position corresponding to
  • the surface of the outer layer material at the position corresponding to the maximum diameter during rolling use is a layer formed on the outer surface of the outer layer material as cast (the molten metal is rapidly cooled by contact with the mold and solidified.
  • the surface of the outer layer material at the position corresponding to the maximum diameter of the product roll diameter that is used for rolling for the first time that is, the position corresponding to the maximum diameter that can be used as a product (roll outer layer material).
  • the “outer layer surface at the position corresponding to the maximum diameter during rolling use” means that the layer formed on the outer surface of the outer layer material as cast is ground and removed, and the maximum product roll diameter that is used for rolling for the first time is used.
  • composition analysis of the outer layer material surface can be performed by instrumental analysis such as fluorescent X-ray analysis or emission spectroscopic analysis. Either a block sample having a diameter of less than 10 mm may be collected and subjected to chemical analysis.
  • C 0.6-3.5%
  • C is an element having an action of combining with W and a carbide-forming element such as Mo, Cr, V, and Nb to form a hard carbide and improve wear resistance.
  • a carbide-forming element such as Mo, Cr, V, and Nb
  • the form of carbide, the amount of crystallization, and the crystallization temperature change.
  • M 6 C type carbides are crystallized as primary crystals, and a structure form segregating to the outer surface side during centrifugal casting is obtained, and wear resistance is improved. If the C content is less than 0.6%, the amount of M 6 C-type carbides crystallized as primary crystals is insufficient and wear resistance is reduced.
  • C is limited to the range of 0.6 to 3.5%.
  • C is 1.0 to 3.0%. More preferably, C is 1.2 to 2.8%.
  • Si 0.05-3% Si is an element that acts as a deoxidizer and also has a matrix strengthening action. In order to obtain such an effect, it is necessary to contain 0.05% or more of Si. On the other hand, even if Si is contained over 3%, the effect is saturated and flake graphite appears and the toughness is lowered. For this reason, Si was limited to the range of 0.05 to 3%. Preferably, Si is 0.1 to 2%. More preferably, Si is 0.2 to 1.8%.
  • Mn 0.05-3% Mn is an element having an action of fixing S as MnS and detoxifying S that adversely affects the material. Further, Mn contributes to improving hardenability by dissolving in the base. In order to obtain such an effect, it is necessary to contain 0.05% or more of Mn. On the other hand, even if Mn is contained in an amount exceeding 3%, the above effect is saturated and the material is deteriorated. Therefore, Mn is limited to the range of 0.05 to 3%. Preferably, Mn is 0.1 to 1%. More preferably, Mn is 0.2 to 0.8%.
  • Mo 1-15%
  • Mo is a carbide-forming element that forms a carbide by combining with C.
  • solid carbide dissolves in a hard M 6 C-type carbide that is a primary crystal carbide enriched in W to strengthen the carbide.
  • Mo has the effect of increasing the fracture resistance of the roll outer layer material.
  • Mo also improves the hardenability during heat treatment and contributes to the increase in hardness of the outer layer material of the roll.
  • Mo is an element heavier than Co and has an effect of not inhibiting or promoting the centrifugation of primary carbides to the outer surface side. In order to obtain these effects, it is necessary to contain 1% or more of Mo.
  • Mo is contained in a large amount exceeding 15%, hard and brittle carbides mainly composed of Mo appear and wear resistance decreases. For this reason, Mo is limited to a range of 1 to 15%. Preferably, Mo is 2 to 10%. More preferably, Mo is 4 to 10%.
  • W 25-70% W is the most important element in the present invention, and has an alloy composition of 25% or more. As a result, a large amount of hard M 6 C-type carbide enriched with W can appear as a primary crystal, and a roll outer layer material for rolling with significantly improved wear resistance can be obtained. When the W content is less than 25%, it is difficult to obtain a rolling roll outer layer material excellent in wear resistance, which is an object of the present invention. On the other hand, if the W content exceeds 70%, the M 6 C type carbide becomes coarse and brittle, and the melting point of the molten metal rises, so that melting, casting, etc. become difficult. For this reason, W is limited to a range of 25 to 70%. Preferably, W is 30 to 65%. More preferably, W is 35 to 55%.
  • Co 5-45% Co, together with W, is an important element in the present invention.
  • the activity of C increases, and a large amount of hard carbides (M 6 C type, M 2 C type, MC type, etc.) enriched with W are used as primary crystals. Appearance is promoted and contributes to the improvement of the wear resistance of the outer layer material of the roll for rolling. In order to obtain such an effect, it is necessary to contain 5% or more of Co.
  • Co is limited to a range of 5 to 45%.
  • Co is 10 to 40%. More preferably, Co is 15 to 35%.
  • the above components are basic components, but in addition to the basic composition, Fe: 5 to 40%, Cr: 0.1 to 10%, V: 0.1 to 6%, Nb: 0.1 to 3% were selected. One or more kinds and / or Ni: 0.05 to 3% may be selected and contained as necessary.
  • Fe 5 to 40%, Cr: 0.1 to 10%, V: 0.1 to 6%, Nb: One or more selected from 0.1 to 3% Fe, Cr, V, and Nb are all It is a carbide forming element, is an element having an action of strengthening the carbide by solid solution in the carbide, and can be selected as necessary to contain one or more kinds.
  • Fe dissolves in the carbide and also in the base, contributes to strengthening of the base, and has an effect of preventing formation of dents (recesses) when used as a rolling roll. In order to obtain such an effect, it is preferable to contain 5% or more of Fe.
  • Fe when Fe is contained in excess of 40%, the amount of hard M 6 C type carbides appearing as primary crystals decreases, fragile M 3 C type carbides increase, and wear resistance decreases.
  • Fe is preferably limited to a range of 5 to 40%. More preferably, Fe is 10 to 35%. More preferably, Fe is 12 to 30%.
  • Cr is a strong carbide-forming element and has the effect of mainly forming eutectic carbides and improving the strength of the formed carbides.
  • the eutectic carbides crystallize in the gaps between the primary crystals of the M 6 C type carbide, and as a result, act to strengthen the gaps of the M 6 C type carbides.
  • Cr also has an action of suppressing the appearance of graphite.
  • W-Co based alloys have a high activity coefficient of C, so that graphite is likely to appear, and when graphite appears, toughness decreases. In order to suppress the appearance of graphite and use it stably as a roll for rolling, in the present invention, it is preferable to contain Cr as necessary.
  • Cr is preferably limited to a range of 0.1 to 10%. More preferably, Cr is 1 to 8%. More preferably, Cr is 1.5 to 7%.
  • V is an element that combines with C to form hard VC (MC-type carbide containing Mo, Nb, Cr, W, etc.).
  • the formed MC-type carbide crystallizes as the primary crystal and W is concentrated. It becomes a crystallization nucleus of the converted M 6 C type carbide, promotes the appearance of M 6 C type carbide, and further has a function of dispersing fine M 6 C type carbide at high density. In order to acquire such an effect, it is preferable to contain V 0.1% or more.
  • V is preferably limited to a range of 0.1 to 6%. More preferably, V is 1 to 5%. More preferably, V is 1.5 to 4%.
  • Nb has a very high bonding strength with C and is a strong carbide forming element, and easily forms a composite carbide with V and W.
  • Such a composite carbide of Nb and V or W becomes a crystallization nucleus of M 6 C type carbide enriched with W, which is crystallized as a primary crystal, promotes the appearance of M 6 C type carbide, and further refines. It has the effect of dispersing high density M 6 C type carbide. In order to acquire such an effect, Nb needs to contain 0.1% or more.
  • Nb is preferably limited to a range of 0.1 to 3%. More preferably, Nb is 0.5 to 2%. More preferably, Nb is 0.6 to 1.8%.
  • Ni 0.05-3%
  • Ni is an element that has the effect of improving hardenability, and can be contained as necessary, for example, to solve the shortage of hardenability in large rolls. In order to obtain such an effect, it is preferable to contain 0.05% or more of Ni. In addition, the effect is not recognized if it is less than 0.05% which is an impurity level. On the other hand, when Ni exceeds 3%, the ⁇ phase is stabilized and the desired hardenability cannot be ensured. Therefore, when Ni is contained, Ni is preferably limited to a range of 0.05 to 3%. Preferably, Ni is 0.1 to 2.5%.
  • the remainder other than the above-mentioned components consists of inevitable impurities.
  • inevitable impurities are P, S, N, and B.
  • P is segregated at the grain boundary and has an adverse effect such as embrittlement of the material. Therefore, it is desirable to reduce P as much as possible, but 0.05% or less is acceptable.
  • S is segregated at the grain boundaries and has the effect of embrittlement of the material, so it is desirable to reduce it as an impurity.
  • part of it is Mn. Since they combine to exist as sulfide inclusions and are rendered harmless, they are acceptable.
  • N is mixed in an amount of about 0.01 to 0.1% as an impurity if it is normally dissolved.
  • N is preferably limited to less than 0.07% because gas defects may be generated at the boundary between the outer layer and the intermediate layer or the inner layer of the composite roll.
  • B is mixed from scrap of melting raw material or casting flux and contained as an unavoidable impurity element.
  • B may be dissolved in carbides or bases to change the properties of the carbides, or may be dissolved in bases to affect the hardenability of the bases, thereby fostering quality variations. For this reason, it is preferable to reduce B as much as possible, but if it is 0.1% or less, the effect of the present invention will not be adversely affected.
  • the roll outer layer material for rolling is manufactured using a centrifugal casting method in which a casting mold is rotated. Thereby, the roll outer layer material for rolling excellent in abrasion resistance can be manufactured at low cost.
  • molten metal having the above-mentioned roll outer layer material composition is poured into a rotating mold so as to have a predetermined thickness, and centrifugally cast to obtain a roll outer layer material for rolling.
  • the inner surface is generally covered with a refractory material mainly composed of zircon or the like.
  • the obtained roll outer layer material for rolling may be a single sleeve, and a shaft material may be fitted therein to form a rolling roll.
  • the obtained roll outer layer material for rolling may be formed as a roll for rolling by providing an intermediate layer welded and integrated on the inner side thereof, fitting a shaft member therein as a sleeve having the intermediate layer.
  • the intermediate layer is preferably formed by pouring molten metal having an intermediate layer composition and centrifugal casting while rotating the mold after the outer layer material of the roll is solidified or completely solidified.
  • the intermediate layer material include graphite steel, 1-2% by mass C high carbon steel, hypoeutectic cast iron, and the like.
  • the shaft material of these rolls for rolling is not specifically limited, It is preferable to set it as the forged steel product (shaft) manufactured separately, a cast steel product (shaft), and a cast iron product (shaft).
  • the above-described rolling roll outer layer material is an outer layer
  • a composite roll comprising an inner layer fused and integrated with the outer layer, or the above-described rolling roll outer layer material is an outer layer, and the outer layer is welded integrally. It is good also as a composite roll which consists of the intermediate
  • the outer layer layer material is solidified in the middle or completely, and then the molten metal having the intermediate layer composition is poured and centrifugally cast while rotating the mold.
  • the intermediate layer material it is preferable to use graphite steel, 1-2% by mass C high carbon steel, hypoeutectic cast iron or the like.
  • the intermediate layer and the outer layer are integrally welded, and the outer layer component is mixed in the intermediate layer in a range of about 10 to 90%. From the viewpoint of suppressing the amount of the outer layer component mixed into the inner layer, it is desirable to reduce the amount of the outer layer component mixed into the intermediate layer as much as possible.
  • the inner layer is formed by static casting of the inner layer material after the outer layer or the intermediate layer is completely solidified, and then the rotation of the mold is stopped and the mold is set up.
  • the component of the outer layer material is often mixed into the inner layer by about 1 to 10%.
  • W, Cr, V, and the like contained in the outer layer material are strong carbide forming elements, and when these elements are mixed into the inner layer, the inner layer is weakened. For this reason, in the present invention, the mixing rate of the outer layer component into the inner layer is preferably suppressed to less than 5%.
  • the above-described outer roll material for rolling and the composite roll for rolling are preferably subjected to heat treatment after casting.
  • Heat treatment is performed at 1000 to 1200 ° C and held for 5 to 40 hours, then cooled in the furnace, air cooled or blast air cooled, and further heated and held at 400 to 600 ° C and then cooled once or more It is preferable to perform the treatment.
  • the hardness of the outer roll material for rolling and the composite roll for rolling of the present invention is preferably adjusted within the range of 79 to 100 HS depending on the application. It is recommended to adjust the heat treatment after casting so that such hardness can be secured stably.
  • the molten metal having the composition shown in Table 1 was melted in a high frequency induction furnace, and a sleeve-shaped roll outer layer material (outer diameter: 250 mm ⁇ , radial thickness: 55 mm) was cast as a test material by a centrifugal casting method.
  • the casting temperature was 1450 to 1550 ° C., and the centrifugal force was 140 to 220 G in multiples of gravity.
  • some test materials (melt No. S)
  • significant carbide segregation occurred on the inner surface so 60 G was used for the purpose of reducing this segregation.
  • the hardness at a position of 5 mm in the thickness direction from the outer surface of the test material was adjusted to approximately 85 to 100 HS.
  • composition of a commercially available outer layer made of centrifugal cast used as a roll for hot finish rolling of steel (high-roll composition: 2.2% C-0.4% Si-0.4% Mn-5.3% Cr-5.2% Mo-5.6 % V-1.1% Nb) melted (molten No.V), and a sleeve-shaped roll outer layer material was cast in the same manner and heat-treated after casting to obtain a test material (hardness 85HS). Test material No. 22).
  • Test piece for composition analysis and the test piece for wear test were collected from the test material subjected to the heat treatment.
  • Test material No. 19 was very fragile and it was very difficult to collect the test material.
  • the specimen for composition analysis was ground 5 mm in the radial direction from the outer surface of the test material after the heat treatment described above, 5 mm in the radial direction from the outer surface after the grinding, and 10 mm ⁇ 10 mm in a plane parallel to the outer surface.
  • a specimen of a size was collected.
  • Each component element was analyzed using the obtained test piece.
  • the analysis method was chemical analysis, C was a combustion method, Si and W were gravimetric methods, Mn, Cr and Mo were atomic absorption methods, Co was a volumetric method, Fe was a volumetric method or atomic absorption method.
  • the obtained results are shown in Table 2.
  • the wear test piece (outer diameter 60 mm ⁇ ⁇ width 10 mm) is arranged so that the center position of the wear test piece is 10 mm in the radial direction from the outer surface of the test material after the heat treatment test piece described above. Collected. As shown in FIG. 2, the wear test was performed by a two-disk sliding rolling method of a test piece (wear test piece) and a mating material (material: S45C, outer diameter 190 mm ⁇ ⁇ width 15 mm).
  • the sliding rate is 14.2 while the test piece rotating at 700 rpm (peripheral speed: 2.1 m / s) is pressed against the test piece rotating at 850 ° C with a load of 980 N while the sample is cooled with water. %.
  • the mating material was updated every 21000 times of rolling of the test piece and rolled until the cumulative number of rotations reached 168000.
  • the wear loss of the wear test piece was investigated. With respect to the obtained wear loss, the wear loss of the conventional example (test material No.
  • the wear resistance ratio (wear loss of the conventional example) / (Abrasion loss of the test material)
  • the wear resistance ratio is 2.1 or more, and the wear resistance is remarkably improved as compared with the conventional example (high-speed roll).
  • the comparative example that is out of the scope of the present invention cracking occurs during the test, and the wear resistance ratio is less than 2, so that the wear resistance is less improved than the conventional example.
  • tissue is observed about this invention example (No.13, No.5), and it shows in FIG.
  • a specimen for tissue observation was collected so that the position 5 mm in the radial direction from the outer surface of the test material after heat treatment was the observation surface, and observed with a scanning electron microscope (magnification: 250 times) to obtain a reflected electron image .
  • the white region is primary crystal carbide (M 6 C type carbide in which W is concentrated).
  • primary crystal carbides are dispersed at high density on the outer surface side of the test material (sleeve-shaped roll outer layer material).
  • test material No. 11 (example of the present invention)
  • a specimen for composition analysis having a size of 5 mm in the radial direction from the position and 10 mm ⁇ 10 mm in a plane parallel to the outer surface was collected.
  • the composition in each position was analyzed by chemical analysis. The obtained results are also shown in Table 2.
  • test surface of the wear test piece was 18 mm in the radial direction from the outer surface of the test material after heat treatment (18 mm position) and 38 to 48 mm in the position (38 mm). Wear test specimens were collected so that A wear test was carried out in the same manner as described above to measure wear loss. The obtained results are also shown in Table 3.
  • W is concentrated mainly on the outer surface of the test material (sleeve-shaped roll outer layer material), a position 18 mm away from the outer surface in the radial direction (18 mm position), and 38 mm away from the outer surface in the radial direction.
  • the ratio of W decreases, the ratio of Co, Fe, etc. increases, and it can be seen that the composition is clearly gradient. Therefore, as can be seen from Table 3, the wear resistance is 18 mm in the radial direction from the outer surface (18 mm position) and 38 mm away (38 mm position) compared to the area from the outer surface to 10 mm in the radial direction. It is falling.

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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)
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Abstract

L'invention fournit un matériau de couche externe dont la résistance à l'usure est remarquablement améliorée, et un cylindre composite de laminage. Ce matériau de couche externe possède une composition d'alliage à base de W-Co. Plus précisément, ce matériau de couche externe présente une composition progressive dans laquelle la teneur en W diminue en allant d'un côté périphérique externe vers un côté périphérique interne dans la direction radiale contient, en % en masse Ｗ：25～70％ et Co：5～45％, à sa surface en une position correspondant au diamètre maximal lors de sa mise en œuvre par laminage. En outre, ce matériau de couche externe comprend Ｃ：0,6～3,5％, Si：0,05～3％, Mn：0,05～3％ et Mo：1～15％, le reste étant constitué des impuretés inévitables.
PCT/JP2017/026246 2016-09-02 2017-07-20 Matériau de couche externe pour cylindre de laminage, et cylindre composite de laminage Ceased WO2018042929A1 (fr)

Priority Applications (7)

Application Number Priority Date Filing Date Title
EP17846538.1A EP3488942A4 (fr) 2016-09-02 2017-08-30 Matériau de couche externe pour cylindre de laminage, et cylindre composite de laminage
JP2017558592A JP6304466B1 (ja) 2016-09-02 2017-08-30 圧延用ロール外層材および圧延用複合ロール
KR1020197006147A KR102228851B1 (ko) 2016-09-02 2017-08-30 압연용 롤 외층재 및 압연용 복합 롤
BR112019004312-8A BR112019004312B1 (pt) 2016-09-02 2017-08-30 Material de camada exterior para cilindros de laminação e cilindros de compósitos para laminação
PCT/JP2017/031081 WO2018043534A1 (fr) 2016-09-02 2017-08-30 Matériau de couche externe pour cylindre de laminage, et cylindre composite de laminage
CN201780053764.9A CN109641251B (zh) 2016-09-02 2017-08-30 轧制用辊外层材料和轧制用复合辊
TW106129885A TWI650430B (zh) 2016-09-02 2017-09-01 輥軋用輥子外層材以及輥軋用複合輥子

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JP2016171382 2016-09-02

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CN113756118B (zh) * 2020-06-04 2023-09-15 南通华严磨片有限公司 一种添加半金属的强韧高铬铸铁磨片
CN112846126B (zh) * 2020-12-31 2022-05-17 北京科技大学 多组元径向功能梯度材料设备的熔体流速调节系统及方法

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JP6606977B2 (ja) * 2014-10-31 2019-11-20 日立金属株式会社 熱間圧延用複合ロールの製造方法
KR102228851B1 (ko) * 2016-09-02 2021-03-16 제이에프이 스틸 가부시키가이샤 압연용 롤 외층재 및 압연용 복합 롤

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JP7396256B2 (ja) 2020-11-30 2023-12-12 Ｊｆｅスチール株式会社 圧延用ロール外層材及び圧延用複合ロール

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