WO2018043534A1 - 圧延用ロール外層材および圧延用複合ロール - Google Patents
圧延用ロール外層材および圧延用複合ロール Download PDFInfo
- Publication number
- WO2018043534A1 WO2018043534A1 PCT/JP2017/031081 JP2017031081W WO2018043534A1 WO 2018043534 A1 WO2018043534 A1 WO 2018043534A1 JP 2017031081 W JP2017031081 W JP 2017031081W WO 2018043534 A1 WO2018043534 A1 WO 2018043534A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- roll
- rolling
- outer layer
- layer material
- carbide
- Prior art date
Links
Images
Classifications
-
- 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
-
- 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
- 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
- B22D13/023—Centrifugal casting; Casting by using centrifugal force of elongated solid or hollow bodies, e.g. pipes, in moulds rotating around their longitudinal axis the longitudinal axis being horizontal
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/07—Alloys based on nickel or cobalt based on cobalt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
- C22C29/08—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on tungsten carbide
-
- 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
-
- 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
- B21B27/02—Shape or construction of rolls
- B21B27/03—Sleeved rolls
-
- 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 roll outer layer material suitable for hot rolling or cold rolling as a first embodiment and a composite roll for rolling using the same, and more particularly to improvement of wear resistance.
- the present invention also relates to a roll outer layer material suitable for hot rolling or cold rolling and a composite roll for rolling using the same, as a second embodiment, particularly with improved wear resistance and It relates to reduction of rolling load.
- 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.
- 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 For the demand for improving the wear resistance of the rolling roll, for example, as described in Non-Patent Document 1 and Non-Patent Document 2, the outer layer composition is similar to the high-speed tool steel composition, and hard carbide is used. High-speed rolls that have been dispersed in large quantities and have improved wear resistance have been developed. Further, for example, 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.
- 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 carbide is 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 been known for a long time as a material having extremely excellent wear resistance and high Young's modulus.
- tungsten carbide WC
- 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 rolling 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.
- 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 the problems of the prior art, and has a roll outer layer material excellent in wear resistance and significantly improved in wear resistance as compared with the prior art, and a composite roll for rolling using the same. Is intended to be provided at low cost.
- 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 increase in the amount of carbide forming elements such as Mo, V, and W is because the specific gravity of the generated VC-based hard carbide is lighter than the molten metal forming the base, There was a concern that the generated VC-based hard carbide accumulates on the inner surface side and aggregates at the boundary with the inner layer, leading to a decrease in 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 in the second embodiment, solves the problems of the prior art, has a significantly improved wear resistance and Young's modulus compared with the conventional roll outer layer material excellent in wear resistance and rolling load reduction effect, and It aims at providing the composite roll for rolling using it at low cost.
- the present inventors made a roll for rolling having extremely high wear resistance comparable to that of cemented carbide and centrifugal casting excellent in productivity and economy.
- the conditions for enabling manufacturing by the method were studied earnestly.
- the hard carbide 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.
- 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 which is the surface layer of the position is mass%, W: 25-70%, Co: 5-45%, C: 0.6-3.5%, Si: 0.05-3%, Mn: 0.05-3%, Mo:
- a roll outer layer material for rolling comprising 1 to 15%, the content of W, Co, Mo, and Fe satisfies the following formula [1], and the balance is composed of inevitable impurities.
- a rolling composite roll comprising an outer layer and an inner layer welded and integrated with the outer layer, wherein the outer layer is made of a W—Co-based alloy, and the W content is directed from the outer peripheral side of the roll toward the inner peripheral side.
- the outer layer material which has a gradient composition that decreases in the radial direction and becomes the surface layer at the position corresponding to the maximum diameter when used in rolling, is W: 25 to 70%, Co: 5 to 45%, C: 0.6 to 3.5%, Si: 0.05-3%, Mn: 0.05-3%, Mo: 1-15%, and the contents of W, Co, Mo and Fe satisfy the following formula [1], and the balance A composite roll for rolling having a composition comprising 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 made of a W—Co base alloy and contains W
- the outer layer material which is a gradient composition whose amount decreases in the radial direction from the outer peripheral side of the roll to the inner peripheral side and becomes the surface layer at the position corresponding to the maximum diameter during rolling use, is in 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 15%, Fe: 5 to 40%, and W, Co, Mo
- a roll for rolling that is remarkably excellent in wear resistance, particularly a roll for centrifugal casting, suitable as a roll for hot rolling or cold rolling, is inexpensive. In addition, it can be easily manufactured and has a remarkable industrial effect.
- a rolling roll suitable for hot rolling or cold rolling which is remarkably excellent in wear resistance and rolling load reduction effect, particularly made by centrifugal casting.
- the roll for rolling can be easily manufactured at a low cost, and has a remarkable industrial effect.
- FIG. 2 is a structure photograph showing a scanning electron microscope structure in Example 1.
- FIG. (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 the outline
- FIG. 1 It is a schematic diagram of a cross section of a composite roll for explaining an example of a composite roll for rolling 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 in the present invention.
- 6 is a structure photograph showing a scanning electron microscope structure in Example 2.
- FIG. (A) is sleeve No. 13 and (b) is sleeve No. 5. It is explanatory drawing which shows the outline
- 4 is a schematic diagram of a composite roll for rolling load evaluation in Example 2.
- FIG. 1 It is a schematic diagram of a composite roll for rolling load evaluation in Example 2.
- 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.
- 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 composition is preferably satisfied at 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.
- a sleeve having an outer diameter of 250 mm and an inner diameter of 140 mm it is preferable to satisfy even a position of at least 9 mm in the radial direction from the position corresponding to the maximum diameter during rolling to the inner peripheral side.
- 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 surface of the outer layer material at the position corresponding to the maximum diameter at the time of rolling use” means a product roll that is first used for rolling after grinding and removing the layer formed on the outer surface of the outer layer material as cast.
- composition analysis of the outer layer material surface may be performed by instrumental analysis such as X-ray fluorescence analysis or emission spectroscopic analysis, or it may be a destructive inspection, but from the position including the outer layer material surface, the thickness in the roll radial direction. 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%. More 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 roll outer layer material for rolling may be shrink-fitted to a shaft material (roll shaft) made of carbon steel forged steel to form a composite 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 examples 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 used as an outer layer, and a composite roll (for example, see the schematic diagram of the cross section of the composite roll in FIG. 4) composed of the outer layer and the inner layer integrated with the outer layer, or A composite roll comprising the outer layer material for rolling described above as an outer layer, an intermediate layer welded and integrated with the outer layer, and an inner layer welded and integrated with the intermediate layer (for example, see the schematic diagram of the cross section of the composite roll in FIG. 5) ).
- a composite roll for example, see the schematic diagram of the cross section of the composite roll in FIG. 4
- a composite roll comprising the outer layer material for rolling described above as an outer layer, an intermediate layer welded and integrated with the outer layer, and an inner layer welded and integrated with the intermediate layer (for example, see the schematic diagram of the cross section of the composite roll in FIG. 5) ).
- 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 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 outer layer material that is the surface layer 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%, the content of W, Co, Mo, and Fe satisfies the following formula [1], and the balance is composed of inevitable impurities.
- the above composition is preferably satisfied at 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.
- a sleeve having an outer diameter of 250 mm and an inner diameter of 140 mm it is preferable to satisfy even a position of at least 9 mm in the radial direction from the position corresponding to the maximum diameter during rolling to the inner peripheral side.
- outer layer material that is the surface layer at the position corresponding to the maximum diameter during rolling use refers to 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) This refers to an outer layer material that becomes a surface layer at a position corresponding to the maximum diameter of the product roll diameter to be used for rolling for the first time after grinding and removing a solidified portion. That is, it means an outer layer material having a thickness of at least 9 mm in the radial direction as a surface layer at a position corresponding to the maximum diameter that can be used as a product (roll outer layer material).
- composition analysis of the outer layer material as the surface layer can be performed by instrumental analysis such as X-ray fluorescence analysis or emission spectroscopic analysis, or it can be a destructive inspection, but from the position including the outer layer material as the surface layer, Either a block-shaped sample having a radial thickness 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
- 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
- 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 acquire such an effect, Si needs to contain 0.05% or more. 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 0.05 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 effects, 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%.
- 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 centrifugal separation of primary crystal carbide to the outer surface side. In order to obtain these effects, Mo needs to be contained by 1% or more.
- 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. 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 and the like 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 12 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 contained in an amount of 0.1% or more.
- Cr content exceeds 10%, a large amount of Cr-based eutectic carbide appears and the toughness decreases. Therefore, when contained, 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 when Nb is contained in a large amount exceeding 3%, Nb-based MC type carbides with low specific gravity are formed and coarsened, and during centrifugal casting, the carbides are easily separated to the inner surface side of the roll outer layer material, and the inner surface of the outer layer material The amount of MC carbide on the side increases. Moreover, the MC type carbide that is centrifuged to the inner surface side of the outer layer material, when the amount increases, the quality of the inner surface side decreases, for example, the boundary strength between the inner layer of the roll and the intermediate layer decreases. For this reason, when Nb is contained, 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.
- Ni is preferably contained in an amount of 0.05% or more. Note that the effect of Ni is not recognized when the impurity level is less than 0.05%.
- 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%. More 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 it as an impurity, but it is acceptable if P is 0.05% or less.
- S segregates at the grain boundaries and has the effect of embrittlement of the material, so it is desirable to reduce it as an impurity. However, if S is 0.05% or less, some It is acceptable because it combines with Mn and is made harmless by the presence of sulfide inclusions.
- N is mixed in an amount of about 0.01 to 0.1% as an impurity if it is normally dissolved. However, this content does not affect the effects of the present invention. However, since N may generate gas defects at the boundary between the outer layer and the intermediate layer or the inner layer of the composite roll, N is preferably limited to less than 0.07%.
- 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 B is 0.1% or less, the effect of the present invention will not be adversely affected. Here, it is preferable to adjust the above inevitable impurity elements to less than 1% in total.
- the outer layer material that becomes the surface layer at the position corresponding to the maximum diameter during rolling in the present invention includes the above composition, and the contents of W, Co, Mo, and Fe satisfy the following formula [1]. .
- (% W +% Mo) / (% Co +% Fe) satisfies the above formula [1], so that the sum of the solid solution amounts of W and Mo in the base can be reduced. It has been confirmed that a Young's modulus of 270 GPa or more can be obtained with a value of 3.5% or more. Control of (% W +% Mo) / (% Co +% Fe) may be adjusted by the molten metal composition, the casting temperature during centrifugal casting, and the centrifugal force. In addition, Preferably, (% W +% Mo) / (% Co +% Fe) is 4.8 or more and 7.8 or less.
- the roll outer layer material for rolling according to the present invention exhibits an excellent rolling load reduction effect, so that the Young's modulus of the outer layer material that becomes the surface layer at the position corresponding to the maximum diameter during rolling use is 270 GPa or more and 500 GPa or less. preferable.
- the conventional high-speed tool steel roll has a Young's modulus of about 220 to 235 GPa on the surface layer in contact with the material to be rolled (see, for example, Non-Patent Documents 4 and 5), and a Young's modulus of 270 GPa. If it is above, the rolling load reduction effect by elastic deformation suppression of a roll surface layer is acquired.
- the Young's modulus is preferably 270 GPa or more and 500 GPa or less.
- the Young's modulus is measured by taking a compression test piece or tensile test piece from the outer layer material at the position corresponding to the maximum diameter during rolling and calculating from the gradient during elastic deformation in the compression test or tensile test, or by ultrasonic You may measure by the nondestructive measuring method like the method.
- 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 (see, for example, FIG. 8).
- 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 a 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 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)
- Example 1 all of the examples of the present invention have a wear resistance ratio of 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.
- the molten metal having the composition shown in Table 4 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 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 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.
- the abrasion test was performed by a two-disc sliding rolling method of a test piece (wear test piece) and a counterpart 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 was calculated and the wear resistance was evaluated.
- the symbol ⁇ indicates very good, the symbol ⁇ indicates good, and the symbol ⁇ indicates inferior.
- the Young's modulus measurement specimen ( ⁇ 16 ⁇ 5mm thickness) is 5mm in diameter from the outer surface of the test material after the heat treatment described above, and is 5mm in diameter from the outer surface after grinding and parallel to the outer surface. A test piece having a size of ⁇ 16 mm was collected. Using the obtained specimen, Young's modulus was measured by an ultrasonic method.
- a roll test piece (outer diameter 230 mm ⁇ ⁇ width 40 mm) was collected by grinding the above-mentioned heat-treated test material 10 mm in the radial direction from the outer surface and using the ground surface as the outer surface, as shown in FIG. .
- the composite roll is installed in a 4Hi thin plate cold rolling mill (backup roll: outer diameter 500mm ⁇ x barrel length 40mm) Then, the rolling load was measured when cold rolling was performed with a steel sheet having a tensile strength of 590 MPa (plate width: 20 mm, plate thickness: 1.5 mm ⁇ length: 20 m) at a reduction rate of 20%.
- the rolling load was reduced by 10% or more, the reduction effect of the rolling load was recognized.
- Example 2 all of the examples of the present invention have a wear resistance ratio of 2.1 or higher, which is markedly improved compared to the conventional example (high-speed roll), and the rolling load is 10% or higher compared to the conventional example. Is reduced, showing an excellent rolling load reduction effect.
- the wear resistance ratio was less than 2
- the improvement in wear resistance was less than the conventional example, or the Young's modulus was less than 270 GPa. Therefore, the rolling load reduction effect is small.
- tissue was observed about the example of this invention (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 . It is confirmed that the white region is primary crystal carbide (M 6 C type carbide in which W is concentrated). In the example of the present invention, it can be seen that 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 5.
- 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).
- the wear test piece was collected so as to be at the position), and the wear test was performed in the same manner as described above to measure the weight loss. The obtained results are also shown in Table 6.
- 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 6, the 18mm position (18mm position) in the radial direction from the outer surface and the 38mm position (38mm position) are more wear resistant than the area from the outer surface to 10mm in the radial direction. It is falling.
Landscapes
- 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)
- Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
Abstract
Description
まず、第1の実施形態において、近年、鋼板の圧延技術の進歩は著しく、それに伴い、圧延用ロールの使用環境は一段と苛酷化している。とくに最近では、高強度鋼板や薄肉製品など、圧延負荷が大きく、かつ優れた表面品質が要求される鋼板の生産量が増大している。
〔第2の実施形態〕
また、第2の実施形態において、近年、鋼板の圧延技術の進歩は著しく、それに伴い、圧延用ロールの使用環境は一段と苛酷化している。とくに最近では、高強度鋼板や薄肉製品など、圧延負荷が大きく、かつ優れた表面品質が要求される鋼板の生産量が増大している。
しかしながら、第1の実施形態において、特許文献1に記載された技術では、鋼製の芯材の周りに、連続肉盛法で外層を形成するため、生産性が低く、コストも高いという問題があった。また、特許文献2、3に記載された技術では、主として、Nb、VおよびCの含有量を特定範囲に限定し、MC型炭化物を均一分散させて、耐摩耗性と耐クラック性を向上させるとしている。しかし、実際には、CrやMoを多く含むM7C3型炭化物やM6C型炭化物も相当量存在するため、更なる特性の向上は、MC型炭化物を均一分散させるという観点のみからでは十分であるとはいえない。また、特許文献4に記載された技術では、凝集や偏析を起こしやすいM6C型炭化物の晶出を抑制するため、Mo+W:10.0%以下に限定し、これにより、遠心鋳造法によるロール外層材の製造を可能にしている。しかし、Mo、W含有量を制限することは、最近の更なる耐摩耗性の向上という要望に対しては、問題を残していた。
また、第2の実施形態において、特許文献1に記載された技術では、鋼製の芯材の周りに、連続肉盛法で外層を形成するため、生産性が低く、コストも高いという問題があった。また、特許文献2、3に記載された技術では、主として、Nb、VおよびCの含有量を特定範囲に限定し、MC型炭化物を均一分散させて、耐摩耗性と耐クラック性を向上させるとしている。しかし、実際には、CrやMoを多く含むM7C3型炭化物やM6C型炭化物も相当量存在するため、更なる特性の向上は、MC型炭化物を均一分散させるという観点のみからでは十分であるとはいえない。また、特許文献4に記載された技術では、凝集や偏析を起こしやすいM6C型炭化物の晶出を抑制するため、Mo+W:10.0%以下に限定し、これにより、遠心鋳造法によるロール外層材の製造を可能にしている。しかし、Mo、W含有量を制限することは、最近の更なる耐摩耗性の向上という要望に対しては、問題を残していた。
まず、第1の実施形態において、本発明者らは、上記した課題を達成するため、超硬合金並みの極めて高い耐摩耗性を有する圧延用ロールを、生産性・経済性に優れた遠心鋳造法によって製造可能にする条件について、鋭意検討した。その結果、遠心鋳造時に溶湯、および晶出相に作用する遠心力を利用して、硬質な炭化物をロールの外表面側に密集、濃化させることができれば、遠心鋳造製圧延用ロールの耐摩耗性を顕著に向上させることができることに思い至った。そして更なる検討により、遠心鋳造時に、硬質な炭化物をロールの外表面側に密集、濃化させるためには、遠心力が作用している液相中から、液相よりも比重の大きい炭化物が初晶として晶出し得る条件を見出せば良いことに思い至った。
(1)比重が大きいWを多量に含有するW-Co基合金に、0.6質量%以上のCを含有させた溶湯とすると、Wが濃化したM6C型炭化物が初晶として出現すること、
(2)このようなW-Co基合金溶湯を遠心鋳造すると、初晶として晶出するM6C型炭化物が外層材の外表面側に高濃度に偏析する組織形態が得られること、
を見出した。
(1)W-Co基合金製圧延用ロール外層材であって、W含有量がロール外周側から内周側に向けて径方向に低下する傾斜組成で、圧延使用時の最大径に相当する位置の外層材表面が、質量%で、W:25~70%、Co:5~45%、C:0.6~3.5%、Si:0.05~3%、Mn:0.05~3%、Mo:1~15%を含み、残部が不可避的不純物からなる組成を有する圧延用ロール外層材。
(2)前記組成に加えてさらに、質量%で、Fe:5~40%、Cr:0.1~10%、V:0.1~6%、Nb:0.1~3%のうちから選ばれた1種又は2種以上を含有する(1)に記載の圧延用ロール外層材。
(3)前記組成に加えてさらに、質量%で、Ni:0.05~3%を含有する(1)または(2)に記載の圧延用ロール外層材。
(4)前記圧延用ロール外層材が、遠心鋳造製である(1)ないし(3)のいずれかに記載の圧延用ロール外層材。
(5)外層と、該外層と溶着一体化した内層とからなる圧延用複合ロールであって、前記外層が、(1)ないし(3)のいずれかに記載の圧延用ロール外層材である圧延用複合ロール。
(6)外層と、該外層と溶着一体化した中間層、該中間層と溶着一体化した内層とからなる圧延用複合ロールであって、前記外層が、(1)ないし(3)のいずれかに記載の圧延用ロール外層材である圧延用複合ロール。
(7)前記外層が、遠心鋳造製である(5)または(6)に記載の圧延用複合ロール。
また、第2の実施形態において、本発明者らは、上記した課題を達成するため、超硬合金並みの極めて高い耐摩耗性および高いヤング率を有する圧延用ロールを、生産性・経済性に優れた遠心鋳造法によって製造可能にする条件について、鋭意検討した。その結果、遠心鋳造時に溶湯、および晶出相に作用する遠心力を利用して、硬質な炭化物をロールの外表面側に密集、濃化させることができれば、遠心鋳造製圧延用ロールの耐摩耗性を顕著に向上させることができることに思い至った。そして更なる検討により、遠心鋳造時に、硬質な炭化物をロールの外表面側に密集、濃化させるためには、遠心力が作用している液相中から、液相よりも比重の大きい炭化物が初晶として晶出し得る条件を見出せば良いことに思い至った。また、ヤング率の向上には、硬質な炭化物をロールの外表面側に密集、濃化させることに加えて、基地に固溶するWおよびMoの量を増加させれば良いことを見出した。
(1)比重が大きいWを多量に含有するW-Co基合金に、0.6質量%以上のCを含有させた溶湯とすると、Wが濃化したM6C型炭化物が初晶として出現すること、
(2)このようなW-Co基合金溶湯を遠心鋳造すると、初晶として晶出するM6C型炭化物が外層材の外表面側に高濃度に偏析する組織形態が得られること、
を見出した。
(1)W-Co基合金製圧延用ロール外層材であって、W含有量がロール外周側から内周側に向けて径方向に低下する傾斜組成で、圧延使用時の最大径に相当する位置の表層となる外層材が、質量%で、W:25~70%、Co:5~45%、C:0.6~3.5%、Si:0.05~3%、Mn:0.05~3%、Mo:1~15%を含み、かつW、Co、Mo、Feの含有量が次の[1]式を満足し、残部が不可避的不純物からなる組成を有する圧延用ロール外層材。
ここで、%W、%Mo、%Co、%Feは、各元素の含有量(質量%)である。
(2)(1)において、前記圧延使用時の最大径に相当する位置の表層となる外層材のヤング率が270GPa以上500GPa以下である圧延用ロール外層材。
(3)(1)または(2)において、前記組成に加えてさらに、質量%で、Fe:5~40%、Cr:0.1~10%、V:0.1~6%、Nb:0.1~3%のうちから選ばれた1種又は2種以上を含有する圧延用ロール外層材。
(4)(1)ないし(3)のいずれかにおいて、前記組成に加えてさらに、質量%で、Ni:0.05~3%を含有する圧延用ロール外層材。
(5)(1)ないし(4)のいずれかにおいて、前記圧延用ロール外層材が、遠心鋳造製である圧延用ロール外層材。
(6)外層と、該外層と溶着一体化した内層とからなる圧延用複合ロールであって、前記外層が、W-Co基合金製で、W含有量がロール外周側から内周側に向けて径方向に低下する傾斜組成で、圧延使用時の最大径に相当する位置の表層となる外層材が、質量%で、W:25~70%、Co:5~45%、C:0.6~3.5%、Si:0.05~3%、Mn:0.05~3%、Mo:1~15%を含み、かつW、Co、Mo、Feの含有量が次の[1]式を満足し、残部が不可避的不純物からなる組成を有する圧延用複合ロール。
ここで、%W、%Mo、%Co、%Feは、各元素の含有量(質量%)である。
(7)(6)において、前記圧延使用時の最大径に相当する位置の表層となる外層材のヤング率が270GPa以上500GPa以下である圧延用複合ロール。
(8)(6)または(7)において、前記組成に加えてさらに、質量%で、Fe:5~40%、Cr:0.1~10%、V:0.1~6%、Nb:0.1~3%のうちから選ばれた1種又は2種以上を含有する圧延用複合ロール。
(9)(6)ないし(8)のいずれかにおいて、前記組成に加えてさらに、質量%で、Ni:0.05~3%を含有する圧延用複合ロール。
(10)外層と、該外層と溶着一体化した中間層、該中間層と溶着一体化した内層とからなる圧延用複合ロールであって、前記外層が、W-Co基合金製で、W含有量がロール外周側から内周側に向けて径方向に低下する傾斜組成で、圧延使用時の最大径に相当する位置の表層となる外層材が、質量%で、W:25~70%、Co:5~45%、C:0.6~3.5%、Si:0.05~3%、Mn:0.05~3%、Mo:1~15%、Fe:5~40%を含み、かつW、Co、Mo、Feの含有量が次の[1]式を満足し、残部が不可避的不純物からなる組成を有する圧延用複合ロール。
1.2≦(%W+%Mo)/(%Co+%Fe)≦9.0 [1]
ここで、%W、%Mo、%Co、%Feは、各元素の含有量(質量%)である。
(11)(10)において、前記圧延使用時の最大径に相当する位置の表層となる外層材のヤング率が270GPa以上500GPa以下である圧延用複合ロール。
(12)(10)または(11)において、前記組成に加えてさらに、質量%で、Fe:5~40%、Cr:0.1~10%、V:0.1~6%、Nb:0.1~3%のうちから選ばれた1種又は2種以上を含有する圧延用複合ロール。
(13)(10)ないし(12)のいずれかにおいて、前記組成に加えてさらに、質量%で、Ni:0.05~3%を含有する圧延用複合ロール。
(14)(6)ないし(13)のいずれかにおいて、前記外層が、遠心鋳造製である圧延用複合ロール。
〔第1の実施形態〕
本発明の圧延用ロール外層材は、遠心鋳造製とする。ここでいう「遠心鋳造製圧延用ロール外層材」とは、従来から圧延用ロールの製造方法として用いられてきた遠心鋳造法を用いて製造された状態の圧延用ロール外層材であることを意味する。遠心鋳造法を用いて製造された圧延用ロール外層材(「遠心鋳造製」圧延用ロール外層材)は、従来から、それ以外の製造方法で製造された圧延用ロールとは、「物」として明瞭に区別でき、しかも、その「遠心鋳造製」圧延用ロール外層材を構造や特性で特定することは、多大の労力を必要とし、非実際的である。
Cは、W、およびMo、Cr、V、Nbなどの炭化物形成元素と結合し、硬質炭化物を形成し、耐摩耗性を向上させる作用を有する元素である。C量に応じて、炭化物の形態や晶出量および晶出温度が変化する。Cの含有が0.6%以上では、M6C型炭化物が初晶として晶出し、遠心鋳造時に外表面側に偏析する組織形態が得られ、耐摩耗性が向上する。なお、Cの含有が0.6%未満では、初晶として晶出するM6C型炭化物量が不足し耐摩耗性が低下する。一方、Cが3.5%を超えて多量に含有すると、外層材として製造が困難になるうえ、非常に割れ易いM2C炭化物やMC炭化物が生成し、粗大化するため、圧延時にロール破壊を生じやすくなる。このようなことから、Cは0.6~3.5%の範囲に限定した。なお、好ましくはCは1.0~3.0%である。より好ましくはCは1.2~2.8%である。
Siは、脱酸剤として作用するとともに、基地の強化作用をも有する元素である。そのような効果を得るためには、0.05%以上のSiの含有を必要とする。一方、Siは3%を超えて含有しても、効果が飽和するうえ、片状黒鉛が出現して靭性が低下する。このため、Siは0.05~3%の範囲に限定した。なお、好ましくはSiは0.1~2%である。より好ましくはSiは0.2~1.8%である。
Mnは、MnSとしてSを固定し、材質に悪影響を及ぼすSを無害化する作用を有する元素である。また、Mnは、基地に固溶して焼入れ性向上に寄与する。このような効果を得るためには、0.05%以上のMnを含有させる必要がある。一方、Mnは3%を超えて含有しても上記した効果が飽和するうえ、材質低下を招く。このため、Mnは0.05~3%の範囲に限定した。なお、好ましくはMnは0.1~1%である。より好ましくはMnは0.2~0.8%である。
Moは、Cと結合して炭化物を形成する炭化物形成元素であり、本発明ではとくに、Wが濃化した初晶炭化物である硬質なM6C型炭化物中に固溶して炭化物を強化し、ロール外層材の破壊抵抗を増加する作用を有する。また、Moは熱処理時に焼入れ性を向上させ、ロール外層材の硬さ増加に寄与する。さらに、Moは、Coよりも重い元素であり、初晶炭化物の外表面側への遠心分離を阻害しないか、あるいは促進する効果をも有する。これらの効果を得るには、1%以上のMoの含有を必要とする。一方、Moは15%を超えて多量に含有すると、Mo主体の硬脆な炭化物が出現し、耐摩耗性が低下する。このため、Moは1~15%の範囲に限定した。なお、好ましくはMoは2~10%である。より好ましくはMoは4~10%である。
Wは、本発明で最も重要な元素であり、25%以上と多量に含有させた合金組成とする。これにより、Wが濃化した硬質なM6C型炭化物を初晶として多量に出現させることができ、耐摩耗性が著しく向上した圧延用ロール外層材とすることができる。なお、Wの含有量が25%未満の場合には、本発明の目的とする耐摩耗性に優れた圧延用ロール外層材を得ることが困難となる。一方、70%を超えるWの含有は、M6C型炭化物が粗大化し脆くなるうえ、溶湯の融点が上昇して、溶解、鋳造等が困難となる。このため、Wは25~70%の範囲に限定した。なお、好ましくはWは30~65%である。より好ましくはWは35~55%である。
Coは、Wとともに、本発明で重要な元素である。CoをWと共に、多量に含有することにより、Cの活量が増加して、Wが濃化した硬質な炭化物(M6C型あるいはM2C型やMC型など)を初晶として多量に出現させることが促進され、圧延用ロール外層材の耐摩耗性の向上に寄与する。このような効果を得るためには、Coを5%以上含有させる必要がある。一方、Coは45%を超えて多量に含有すると、γ相が安定化し、基地が軟質となり、圧延用ロールとして使用した場合には、くぼみ疵(凹部)の多発を招き、耐摩耗性が著しく低下する。このため、Coは5~45%の範囲に限定した。なお、好ましくはCoは10~40%である。より好ましくはCoは15~35%である。
Fe、Cr、V、Nbはいずれも、炭化物形成元素であり、炭化物に固溶して炭化物を強化する作用を有する元素であり、必要に応じて選択して1種または2種以上を含有できる。
Niは、焼入れ性を向上させる作用がある元素であり、例えば、大型ロールにおける焼入れ性不足を解消するためなど、必要に応じて含有できる。このような効果を得るためには、Niを0.05%以上含有することが好ましい。なお、不純物レベルである0.05%未満ではその効果が認められない。一方、Niが3%を超える含有は、γ相が安定化し、所望の焼入れ性を確保できなくなる。このため、含有する場合には、Niは0.05~3%の範囲に限定することが好ましい。より好ましくはNiは0.1~2.5%である。
本発明の圧延用ロール外層材は、遠心鋳造製とする。ここでいう「遠心鋳造製圧延用ロール外層材」とは、従来から圧延用ロールの製造方法として用いられてきた遠心鋳造法を用いて製造された状態の圧延用ロール外層材であることを意味する。遠心鋳造法を用いて製造された圧延用ロール外層材(「遠心鋳造製」圧延用ロール外層材)は、従来から、それ以外の製造方法で製造された圧延用ロールとは、「物」として明瞭に区別でき、しかも、その「遠心鋳造製」圧延用ロール外層材を構造や特性で特定することは、多大の労力を必要とし、非実際的である。
ここで、%W、%Mo、%Co、%Feは、各元素の含有量(質量%)であり、含有しない場合は0とする。
Cは、W、およびMo、Cr、V、Nbなどの炭化物形成元素と結合し、硬質炭化物を形成し、耐摩耗性を向上させる作用を有する元素である。C量に応じて、炭化物の形態や晶出量および晶出温度が変化する。Cが0.6%以上では、M6C型炭化物が初晶として晶出し、遠心鋳造時に外表面側に偏析する組織形態が得られ、耐摩耗性が向上する。なお、Cが0.6%未満では、初晶として晶出するM6C型炭化物量が不足し耐摩耗性が低下する。一方、Cは3.5%を超えて多量に含有すると、外層材として製造が困難になるうえ、非常に割れ易いM2C炭化物やMC炭化物が生成し、粗大化するため、圧延時にロール破壊を生じやすくなる。このようなことから、Cは0.6~3.5%の範囲に限定した。なお、好ましくはCは1.0~3.0%である。より好ましくはCは1.2~2.8%である。
Siは、脱酸剤として作用するとともに、基地の強化作用をも有する元素である。そのような効果を得るためには、Siは0.05%以上の含有を必要とする。一方、Siは3%を超えて含有しても、効果が飽和するうえ、片状黒鉛が出現して靭性が低下する。このため、Siは0.05~3%の範囲に限定した。なお、好ましくはSiは0.05~2%である。より好ましくはSiは0.2~1.8%である。
Mnは、MnSとしてSを固定し、材質に悪影響を及ぼすSを無害化する作用を有する元素である。また、Mnは、基地に固溶して焼入れ性向上に寄与する。このような効果を得るためには、Mnは0.05%以上含有させる必要がある。一方、Mnは3%を超えて含有しても上記した効果が飽和するうえ、材質低下を招く。このため、Mnは0.05~3%の範囲に限定した。なお、好ましくはMnは0.1~1%である。より好ましくはMnは0.2~0.8%である。
Moは、Cと結合して炭化物を形成する炭化物形成元素であり、本発明ではとくに、Wが濃化した初晶炭化物である硬質なM6C型炭化物中に固溶して炭化物を強化し、ロール外層材の破壊抵抗を増加する作用を有する。また、Moは熱処理時に焼入れ性を向上させ、ロール外層材の硬さ増加に寄与する。さらにMoは、Coよりも重い元素であり、初晶炭化物の外表面側への遠心分離を阻害しないか、あるいは促進する効果をも有する。これらの効果を得るには、Moは1%以上の含有を必要とする。一方、Moは15%を超えて多量に含有すると、Mo主体の硬脆な炭化物が出現し、耐摩耗性が低下する。このため、Moは1~15%の範囲に限定した。なお、好ましくは、Moは2~10%である。より好ましくは、Moは4~10%である。
Wは、本発明で最も重要な元素であり、25%以上と多量に含有させた合金組成とする。これにより、Wが濃化した硬質なM6C型炭化物を初晶として多量に出現させることができ、耐摩耗性が著しく向上した圧延用ロール外層材とすることができる。一方、Wが70%を超える含有は、M6C型炭化物が粗大化し脆くなるうえ、溶湯の融点が上昇して、溶解、鋳造等が困難となる。このため、Wは25~70%の範囲に限定した。なお、好ましくは、Wは30~65%である。より好ましくは、Wは35~55%である。
Coは、Wとともに、本発明で重要な元素である。CoをWと共に、多量に含有することにより、Cの活量が増加して、Wが濃化した硬質な炭化物(M6C型あるいはM2C型やMC型など)を初晶として多量に出現させることが促進され、圧延用ロール外層材の耐摩耗性の向上に寄与する。このような効果を得るためには、Coを5%以上含有させる必要がある。一方、Coは45%を超えて多量に含有すると、γ相が安定化し、基地が軟質となり、圧延用ロールとして使用した場合には、くぼみ疵(凹部)の多発を招き、耐摩耗性が著しく低下する。このため、Coは5~45%の範囲に限定した。なお、好ましくはCoは10~40%である。より好ましくは、Coは12~35%である。
Fe、Cr、V、Nbはいずれも、炭化物形成元素であり、炭化物に固溶して炭化物を強化する作用を有する元素であり、必要に応じて選択して1種または2種以上を含有できる。
Niは、焼入れ性を向上させる作用がある元素であり、例えば、大型ロールにおける焼入れ性不足を解消するためなど、必要に応じて含有できる。このような効果を得るためには、Niは0.05%以上含有することが好ましい。なお、Niは不純物レベルである0.05%未満ではその効果が認められない。一方、Niは3%を超える含有は、γ相が安定化し、所望の焼入れ性を確保できなくなる。このため、含有する場合には、Niは0.05~3%の範囲に限定することが好ましい。より好ましくはNiは0.1~2.5%である。
ここで、%W、%Mo、%Co、%Feは、各元素の含有量(質量%)であり、含有しない場合は0とする。
まず、上述した第1の実施形態における実施例について説明する。
次に、上述した第2の実施形態における実施例について説明する。
Claims (21)
- W-Co基合金製圧延用ロール外層材であって、
W含有量がロール外周側から内周側に向けて径方向に低下する傾斜組成で、圧延使用時の最大径に相当する位置の外層材表面が、質量%で、
W:25~70%、
Co:5~45%、
C:0.6~3.5%、
Si:0.05~3%、
Mn:0.05~3%、
Mo:1~15%
を含み、残部が不可避的不純物からなる組成を有する圧延用ロール外層材。 - 前記組成に加えてさらに、質量%で、
Fe:5~40%、
Cr:0.1~10%、
V:0.1~6%、
Nb:0.1~3%
のうちから選ばれた1種又は2種以上を含有する請求項1に記載の圧延用ロール外層材。 - 前記組成に加えてさらに、質量%で、
Ni:0.05~3%
を含有する請求項1または2に記載の圧延用ロール外層材。 - 前記圧延用ロール外層材が、遠心鋳造製である請求項1ないし3のいずれかに記載の圧延用ロール外層材。
- 外層と、該外層と溶着一体化した内層とからなる圧延用複合ロールであって、
前記外層が、請求項1ないし3のいずれかに記載の圧延用ロール外層材である圧延用複合ロール。 - 外層と、該外層と溶着一体化した中間層、該中間層と溶着一体化した内層とからなる圧延用複合ロールであって、
前記外層が、請求項1ないし3のいずれかに記載の圧延用ロール外層材である圧延用複合ロール。 - 前記外層が、遠心鋳造製である請求項5または6に記載の圧延用複合ロール。
- W-Co基合金製圧延用ロール外層材であって、W含有量がロール外周側から内周側に向けて径方向に低下する傾斜組成で、圧延使用時の最大径に相当する位置の表層となる外層材が、質量%で、
W:25~70%、
Co:5~45%、
C:0.6~3.5%、
Si:0.05~3%、
Mn:0.05~3%、
Mo:1~15%を含み、
かつW、Co、Mo、Feの含有量が下記の[1]式を満足し、残部が不可避的不純物からなる組成を有する圧延用ロール外層材。
記
1.2≦(%W+%Mo)/(%Co+%Fe)≦9.0 [1]
ここで、%W、%Mo、%Co、%Feは、各元素の含有量(質量%)である。 - 前記圧延使用時の最大径に相当する位置の表層となる外層材のヤング率が270GPa以上500GPa以下である請求項8に記載の圧延用ロール外層材。
- 前記組成に加えてさらに、質量%で、
Fe:5~40%、
Cr:0.1~10%、
V:0.1~6%、
Nb:0.1~3%
のうちから選ばれた1種又は2種以上を含有する請求項8または9に記載の圧延用ロール外層材。 - 前記組成に加えてさらに、質量%で、
Ni:0.05~3%
を含有する請求項8ないし10のいずれかに記載の圧延用ロール外層材。 - 前記圧延用ロール外層材が、遠心鋳造製である請求項8ないし11のいずれかに記載の圧延用ロール外層材。
- 外層と、該外層と溶着一体化した内層とからなる圧延用複合ロールであって、
前記外層が、W-Co基合金製で、W含有量がロール外周側から内周側に向けて径方向に低下する傾斜組成で、圧延使用時の最大径に相当する位置の表層となる外層材が、質量%で、
W:25~70%、
Co:5~45%、
C:0.6~3.5%、
Si:0.05~3%、
Mn:0.05~3%、
Mo:1~15%を含み、
かつW、Co、Mo、Feの含有量が下記の[1]式を満足し、残部が不可避的不純物からなる組成を有する圧延用複合ロール。
記
1.2≦(%W+%Mo)/(%Co+%Fe)≦9.0 [1]
ここで、%W、%Mo、%Co、%Feは、各元素の含有量(質量%)である。 - 前記圧延使用時の最大径に相当する位置の表層となる外層材のヤング率が270GPa以上500GPa以下である請求項13に記載の圧延用複合ロール。
- 前記組成に加えてさらに、質量%で、
Fe:5~40%、
Cr:0.1~10%、
V:0.1~6%、
Nb:0.1~3%
のうちから選ばれた1種又は2種以上を含有する請求項13または14に記載の圧延用複合ロール。 - 前記組成に加えてさらに、質量%で、
Ni:0.05~3%
を含有する請求項13ないし15のいずれかに記載の圧延用複合ロール。 - 外層と、該外層と溶着一体化した中間層、該中間層と溶着一体化した内層とからなる圧延用複合ロールであって、
前記外層が、W-Co基合金製で、W含有量がロール外周側から内周側に向けて径方向に低下する傾斜組成で、圧延使用時の最大径に相当する位置の表層となる外層材が、質量%で、
W:25~70%、
Co:5~45%、
C:0.6~3.5%、
Si:0.05~3%、
Mn:0.05~3%、
Mo:1~15%、
Fe:5~40%を含み、
かつW、Co、Mo、Feの含有量が下記の[1]式を満足し、残部が不可避的不純物からなる組成を有する圧延用複合ロール。
記
1.2≦(%W+%Mo)/(%Co+%Fe)≦9.0 [1]
ここで、%W、%Mo、%Co、%Feは、各元素の含有量(質量%)である。 - 前記圧延使用時の最大径に相当する位置の表層となる外層材のヤング率が270GPa以上500GPa以下である請求項17に記載の圧延用複合ロール。
- 前記組成に加えてさらに、質量%で、
Fe:5~40%、
Cr:0.1~10%、
V:0.1~6%、
Nb:0.1~3%
のうちから選ばれた1種又は2種以上を含有する請求項17または18に記載の圧延用複合ロール。 - 前記組成に加えてさらに、質量%で、
Ni:0.05~3%
を含有する請求項17ないし19のいずれかに記載の圧延用複合ロール。 - 前記外層が、遠心鋳造製である請求項13ないし20のいずれかに記載の圧延用複合ロール。
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP17846538.1A EP3488942A4 (en) | 2016-09-02 | 2017-08-30 | EXTERNAL LAYER MATERIAL OF A ROLLER FOR ROLLING AND ASSEMBLING ROLLING FOR ROLLING |
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 |
BR112019004312-8A BR112019004312B1 (pt) | 2016-09-02 | 2017-08-30 | Material de camada exterior para cilindros de laminação e cilindros de compósitos para laminação |
KR1020197006147A KR102228851B1 (ko) | 2016-09-02 | 2017-08-30 | 압연용 롤 외층재 및 압연용 복합 롤 |
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 |
Applications Claiming Priority (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2016-171382 | 2016-09-02 | ||
JP2016171382 | 2016-09-02 | ||
JP2017134552 | 2017-07-10 | ||
JP2017-134552 | 2017-07-10 | ||
JPPCT/JP2017/026246 | 2017-07-20 | ||
PCT/JP2017/026246 WO2018042929A1 (ja) | 2016-09-02 | 2017-07-20 | 圧延用ロール外層材および圧延用複合ロール |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2018043534A1 true WO2018043534A1 (ja) | 2018-03-08 |
Family
ID=61301082
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2017/031081 WO2018043534A1 (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 |
Country Status (7)
Country | Link |
---|---|
EP (1) | EP3488942A4 (ja) |
JP (1) | JP6304466B1 (ja) |
KR (1) | KR102228851B1 (ja) |
CN (1) | CN109641251B (ja) |
BR (1) | BR112019004312B1 (ja) |
TW (1) | TWI650430B (ja) |
WO (1) | WO2018043534A1 (ja) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2018039047A (ja) * | 2016-09-02 | 2018-03-15 | Jfeスチール株式会社 | 耐摩耗性に優れた圧延用ロール外層材および圧延用複合ロール |
CN108568502A (zh) * | 2018-05-18 | 2018-09-25 | 东北大学 | 一种制备成分梯度铝合金材料的装置及方法 |
CN109465418A (zh) * | 2018-12-12 | 2019-03-15 | 中钢集团邢台机械轧辊有限公司 | 一种辊压机辊套及其制造方法 |
JP2022085966A (ja) * | 2020-11-30 | 2022-06-09 | 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 |
Families Citing this family (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN113522974A (zh) * | 2020-04-21 | 2021-10-22 | 宝山钢铁股份有限公司 | 一种高强度钢板的制造工艺 |
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 |
CN113388758A (zh) * | 2021-05-31 | 2021-09-14 | 芜湖舍达激光科技有限公司 | 一种耐高温腐蚀、长寿命的硬质合金轴套 |
Citations (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS4869719A (ja) * | 1971-12-23 | 1973-09-21 | ||
JPS576502B2 (ja) | 1972-10-30 | 1982-02-05 | ||
JPS5839906B2 (ja) | 1973-07-13 | 1983-09-02 | 住友電気工業株式会社 | 熱間線材用ロ−ル |
JPS60177945A (ja) * | 1984-02-24 | 1985-09-11 | Kubota Ltd | 耐摩耗鋳物の遠心力鋳造法 |
JPS6160858A (ja) * | 1984-08-29 | 1986-03-28 | Kubota Ltd | 耐摩耗鋳物 |
JPS61182862A (ja) * | 1985-02-09 | 1986-08-15 | Kubota Ltd | 耐摩耗複合鋳物の製造方法 |
JPH04141553A (ja) | 1990-10-01 | 1992-05-15 | Hitachi Metals Ltd | 熱間圧延用複合ロール |
JPH04365836A (ja) | 1990-10-01 | 1992-12-17 | Kawasaki Steel Corp | 圧延用ロール外層材 |
JPH051350A (ja) | 1990-11-21 | 1993-01-08 | Kawasaki Steel Corp | 圧延用ロール外層材 |
JPH0860289A (ja) | 1994-08-24 | 1996-03-05 | Nippon Steel Corp | 遠心鋳造複合ロール |
JP2004243341A (ja) | 2003-02-12 | 2004-09-02 | Hitachi Metals Ltd | 超硬合金製圧延用複合ロール |
JP2004268140A (ja) | 2003-02-17 | 2004-09-30 | Hitachi Metals Ltd | 板圧延用超硬合金製複合ロール |
WO2006030795A1 (ja) | 2004-09-13 | 2006-03-23 | Hitachi Metals, Ltd. | 圧延ロール用遠心鋳造外層及びその製造方法 |
JP2006175456A (ja) | 2004-12-21 | 2006-07-06 | Hitachi Metals Ltd | 超硬合金製圧延用複合ロール |
Family Cites Families (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS576502A (en) | 1980-06-11 | 1982-01-13 | Hitachi Ltd | Regeneration control circuit of electric rolling stock |
JPS5839906A (ja) | 1981-09-03 | 1983-03-08 | Matsushita Electric Works Ltd | 木材粗面測定装置 |
JPS6150858A (ja) * | 1984-08-18 | 1986-03-13 | Nippon Air Brake Co Ltd | ブレ−キ作動方法 |
JPS6234610A (ja) * | 1985-08-05 | 1987-02-14 | Kubota Ltd | 圧延用複合ロ−ルの外層材 |
JPH04220106A (ja) * | 1990-08-31 | 1992-08-11 | Kubota Corp | 複合ロール |
US5355932A (en) * | 1992-03-06 | 1994-10-18 | Hitachi Metals, Ltd. | Method of producing a compound roll |
JP2841276B2 (ja) * | 1994-06-29 | 1998-12-24 | 川崎製鉄株式会社 | 熱間圧延用ロール外層材及び熱間圧延用ロールの製造方法 |
JP3468380B2 (ja) * | 1994-09-26 | 2003-11-17 | 日立金属株式会社 | 組立式圧延用ロール |
JP3412590B2 (ja) * | 2000-01-17 | 2003-06-03 | 関東特殊製鋼株式会社 | 圧延用ロール |
EP1975265B1 (en) * | 2005-12-28 | 2019-05-08 | Hitachi Metals, Ltd. | Centrifugally cast composite roll |
JP5121276B2 (ja) * | 2007-03-30 | 2013-01-16 | 株式会社クボタ | 高速度鋼系合金複合製品 |
CN103692221B (zh) * | 2013-11-21 | 2016-08-17 | 龙钢集团华山冶金设备有限公司 | 一种超强耐磨复合轧辊的制备方法 |
-
2017
- 2017-08-30 BR BR112019004312-8A patent/BR112019004312B1/pt active IP Right Grant
- 2017-08-30 WO PCT/JP2017/031081 patent/WO2018043534A1/ja active Application Filing
- 2017-08-30 EP EP17846538.1A patent/EP3488942A4/en active Pending
- 2017-08-30 CN CN201780053764.9A patent/CN109641251B/zh active Active
- 2017-08-30 JP JP2017558592A patent/JP6304466B1/ja active Active
- 2017-08-30 KR KR1020197006147A patent/KR102228851B1/ko active IP Right Grant
- 2017-09-01 TW TW106129885A patent/TWI650430B/zh active
Patent Citations (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS4869719A (ja) * | 1971-12-23 | 1973-09-21 | ||
JPS576502B2 (ja) | 1972-10-30 | 1982-02-05 | ||
JPS5839906B2 (ja) | 1973-07-13 | 1983-09-02 | 住友電気工業株式会社 | 熱間線材用ロ−ル |
JPS60177945A (ja) * | 1984-02-24 | 1985-09-11 | Kubota Ltd | 耐摩耗鋳物の遠心力鋳造法 |
JPS6160858A (ja) * | 1984-08-29 | 1986-03-28 | Kubota Ltd | 耐摩耗鋳物 |
JPS61182862A (ja) * | 1985-02-09 | 1986-08-15 | Kubota Ltd | 耐摩耗複合鋳物の製造方法 |
JPH04141553A (ja) | 1990-10-01 | 1992-05-15 | Hitachi Metals Ltd | 熱間圧延用複合ロール |
JPH04365836A (ja) | 1990-10-01 | 1992-12-17 | Kawasaki Steel Corp | 圧延用ロール外層材 |
JPH051350A (ja) | 1990-11-21 | 1993-01-08 | Kawasaki Steel Corp | 圧延用ロール外層材 |
JPH0860289A (ja) | 1994-08-24 | 1996-03-05 | Nippon Steel Corp | 遠心鋳造複合ロール |
JP2004243341A (ja) | 2003-02-12 | 2004-09-02 | Hitachi Metals Ltd | 超硬合金製圧延用複合ロール |
JP2004268140A (ja) | 2003-02-17 | 2004-09-30 | Hitachi Metals Ltd | 板圧延用超硬合金製複合ロール |
WO2006030795A1 (ja) | 2004-09-13 | 2006-03-23 | Hitachi Metals, Ltd. | 圧延ロール用遠心鋳造外層及びその製造方法 |
JP2006175456A (ja) | 2004-12-21 | 2006-07-06 | Hitachi Metals Ltd | 超硬合金製圧延用複合ロール |
Non-Patent Citations (6)
Title |
---|
HASHIMOTO ET AL., SHINNITTETSU GIHO (NIPPON STEEL TECHNICAL REPORT, vol. 355, no. 1995, pages 76 |
HASHIMOTO, SEITETSU KENKYU (IRON-MAKING RESEARCH, vol. 338, 1990, pages 62 |
KAIZO MONMA: "Iron and steel materials, Revised edition", JIKKYO SHUPPAN, 1981, pages 368 |
KAMATA ET AL., HITACHI HYORON (HITACHI REVIEW, vol. 72, no. 5, 1990, pages 69 |
MATSUNAGA ET AL., ANALYTICAL TECHNIQUE FOR INCREASING SERVICE LIFE OF ROLLS, 1999, pages 11 |
See also references of EP3488942A4 |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2018039047A (ja) * | 2016-09-02 | 2018-03-15 | Jfeスチール株式会社 | 耐摩耗性に優れた圧延用ロール外層材および圧延用複合ロール |
CN108568502A (zh) * | 2018-05-18 | 2018-09-25 | 东北大学 | 一种制备成分梯度铝合金材料的装置及方法 |
CN108568502B (zh) * | 2018-05-18 | 2019-09-17 | 东北大学 | 一种制备成分梯度铝合金材料的装置及方法 |
WO2019218376A1 (zh) * | 2018-05-18 | 2019-11-21 | 东北大学 | 一种制备成分梯度铝合金材料的装置及方法 |
CN109465418A (zh) * | 2018-12-12 | 2019-03-15 | 中钢集团邢台机械轧辊有限公司 | 一种辊压机辊套及其制造方法 |
JP2022085966A (ja) * | 2020-11-30 | 2022-06-09 | 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 |
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 |
Also Published As
Publication number | Publication date |
---|---|
TW201812044A (zh) | 2018-04-01 |
JPWO2018043534A1 (ja) | 2018-08-30 |
CN109641251B (zh) | 2020-12-18 |
BR112019004312B1 (pt) | 2024-02-27 |
BR112019004312A2 (pt) | 2019-05-28 |
EP3488942A4 (en) | 2019-10-30 |
JP6304466B1 (ja) | 2018-04-04 |
EP3488942A1 (en) | 2019-05-29 |
CN109641251A (zh) | 2019-04-16 |
KR102228851B1 (ko) | 2021-03-16 |
KR20190035834A (ko) | 2019-04-03 |
TWI650430B (zh) | 2019-02-11 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP6304466B1 (ja) | 圧延用ロール外層材および圧延用複合ロール | |
EP3050636B1 (en) | Centrifugally cast, hot-rolling composite roll | |
EP3050637B1 (en) | Centrifugally cast, hot-rolling composite roll | |
EP2902124B1 (en) | Hot-rolling composite roll produced by centrifugal casting | |
TW201329250A (zh) | 耐疲勞性優異之熱軋用離心鑄造製軋輥外層材以及熱軋用離心鑄造製複合軋輥 | |
WO2018042929A1 (ja) | 圧延用ロール外層材および圧延用複合ロール | |
JP7302232B2 (ja) | 熱間圧延用遠心鋳造複合ロール及びその製造方法 | |
CN110114155B (zh) | 轧制用复合辊 | |
WO2020203571A1 (ja) | 遠心鋳造製圧延用複合ロール及びその製造方法 | |
JP7396256B2 (ja) | 圧延用ロール外層材及び圧延用複合ロール | |
JP6292362B1 (ja) | 熱間圧延用ロール外層材および熱間圧延用複合ロール | |
JP5516545B2 (ja) | 耐疲労性に優れた熱間圧延用遠心鋳造製ロール外層材および熱間圧延用遠心鋳造製複合ロール | |
JP6518314B2 (ja) | 圧延用複合ロール | |
JP5867143B2 (ja) | 耐疲労性に優れた熱間圧延用遠心鋳造製ロール外層材および熱間圧延用遠心鋳造製複合ロール、ならびにそれらの製造方法 | |
JP2007196257A (ja) | 圧延用ロール | |
JP2507765B2 (ja) | 高速度工具鋼 | |
JPH108212A (ja) | 熱間圧延用ロール | |
JP5327342B2 (ja) | 耐疲労性に優れた熱間圧延用遠心鋳造製ロール外層材および熱間圧延用遠心鋳造製複合ロール | |
CN114555252B (zh) | 热轧用离心铸造复合辊 | |
JP2018161655A (ja) | 熱間圧延用ロール外層材および熱間圧延用複合ロール | |
JP5867144B2 (ja) | 耐疲労性に優れた熱間圧延用遠心鋳造製ロール外層材および熱間圧延用遠心鋳造製複合ロール、ならびにそれらの製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
WWE | Wipo information: entry into national phase |
Ref document number: 2017558592 Country of ref document: JP |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 17846538 Country of ref document: EP Kind code of ref document: A1 |
|
ENP | Entry into the national phase |
Ref document number: 20197006147 Country of ref document: KR Kind code of ref document: A |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
ENP | Entry into the national phase |
Ref document number: 2017846538 Country of ref document: EP Effective date: 20190221 |
|
REG | Reference to national code |
Ref country code: BR Ref legal event code: B01A Ref document number: 112019004312 Country of ref document: BR |
|
ENP | Entry into the national phase |
Ref document number: 112019004312 Country of ref document: BR Kind code of ref document: A2 Effective date: 20190301 |