EP3479915B1 - Roll outer layer material for hot rolling and composite roll for hot rolling - Google Patents
Roll outer layer material for hot rolling and composite roll for hot rolling Download PDFInfo
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- EP3479915B1 EP3479915B1 EP17848389.7A EP17848389A EP3479915B1 EP 3479915 B1 EP3479915 B1 EP 3479915B1 EP 17848389 A EP17848389 A EP 17848389A EP 3479915 B1 EP3479915 B1 EP 3479915B1
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- hot
- outer layer
- roll
- rolling
- hot rolling
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- 238000005098 hot rolling Methods 0.000 title claims description 90
- 239000000463 material Substances 0.000 title claims description 60
- 239000002131 composite material Substances 0.000 title claims description 17
- 229910052720 vanadium Inorganic materials 0.000 claims description 37
- 229910052758 niobium Inorganic materials 0.000 claims description 34
- 229910052799 carbon Inorganic materials 0.000 claims description 32
- 239000011159 matrix material Substances 0.000 claims description 31
- 229910052750 molybdenum Inorganic materials 0.000 claims description 31
- 229910052804 chromium Inorganic materials 0.000 claims description 29
- 229910052721 tungsten Inorganic materials 0.000 claims description 25
- 229910052759 nickel Inorganic materials 0.000 claims description 21
- 229910001563 bainite Inorganic materials 0.000 claims description 19
- 229910000734 martensite Inorganic materials 0.000 claims description 19
- 239000000203 mixture Substances 0.000 claims description 10
- 239000012535 impurity Substances 0.000 claims description 6
- 239000010410 layer Substances 0.000 description 88
- 150000001247 metal acetylides Chemical class 0.000 description 38
- 230000000052 comparative effect Effects 0.000 description 28
- 238000005096 rolling process Methods 0.000 description 21
- 238000009661 fatigue test Methods 0.000 description 19
- 230000000694 effects Effects 0.000 description 18
- 238000010438 heat treatment Methods 0.000 description 15
- 230000005496 eutectics Effects 0.000 description 12
- 238000005259 measurement Methods 0.000 description 12
- 238000000034 method Methods 0.000 description 12
- 229910001566 austenite Inorganic materials 0.000 description 10
- 238000005266 casting Methods 0.000 description 10
- 229910000831 Steel Inorganic materials 0.000 description 9
- 238000001816 cooling Methods 0.000 description 9
- 239000010959 steel Substances 0.000 description 9
- 238000012360 testing method Methods 0.000 description 9
- 238000009750 centrifugal casting Methods 0.000 description 8
- 230000003247 decreasing effect Effects 0.000 description 8
- 230000000717 retained effect Effects 0.000 description 8
- 230000007547 defect Effects 0.000 description 7
- 238000004090 dissolution Methods 0.000 description 7
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- 230000015572 biosynthetic process Effects 0.000 description 6
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- 239000002184 metal Substances 0.000 description 6
- 229910052751 metal Inorganic materials 0.000 description 6
- 238000007788 roughening Methods 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 230000001965 increasing effect Effects 0.000 description 5
- 230000006698 induction Effects 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 238000005498 polishing Methods 0.000 description 4
- 229910001018 Cast iron Inorganic materials 0.000 description 3
- 229910001141 Ductile iron Inorganic materials 0.000 description 3
- 239000000498 cooling water Substances 0.000 description 3
- 230000005484 gravity Effects 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 238000005496 tempering Methods 0.000 description 3
- 229910000997 High-speed steel Inorganic materials 0.000 description 2
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 2
- 238000005253 cladding Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000002708 enhancing effect Effects 0.000 description 2
- 238000005530 etching Methods 0.000 description 2
- 238000010348 incorporation Methods 0.000 description 2
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- 229910017604 nitric acid Inorganic materials 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 229910001562 pearlite Inorganic materials 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 230000002829 reductive effect Effects 0.000 description 2
- 238000003303 reheating Methods 0.000 description 2
- 102200082816 rs34868397 Human genes 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 230000003068 static effect Effects 0.000 description 2
- 229910000677 High-carbon steel Inorganic materials 0.000 description 1
- 239000003575 carbonaceous material Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
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- 239000000126 substance Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 229910052845 zircon Inorganic materials 0.000 description 1
- GFQYVLUOOAAOGM-UHFFFAOYSA-N zirconium(iv) silicate Chemical compound [Zr+4].[O-][Si]([O-])([O-])[O-] GFQYVLUOOAAOGM-UHFFFAOYSA-N 0.000 description 1
Images
Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B27/00—Rolls, roll alloys or roll fabrication; Lubricating, cooling or heating rolls while in use
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D19/00—Casting in, on, or around objects which form part of the product
- B22D19/08—Casting in, on, or around objects which form part of the product for building-up linings or coverings, e.g. of anti-frictional metal
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D13/00—Centrifugal casting; Casting by using centrifugal force
- B22D13/02—Centrifugal casting; Casting by using centrifugal force of elongated solid or hollow bodies, e.g. pipes, in moulds rotating around their longitudinal axis
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D19/00—Casting in, on, or around objects which form part of the product
- B22D19/16—Casting in, on, or around objects which form part of the product for making compound objects cast of two or more different metals, e.g. for making rolls for rolling mills
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- 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
- B21B27/032—Rolls for sheets or strips
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D5/00—Heat treatments of cast-iron
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/38—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for roll bodies
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C37/00—Cast-iron alloys
Definitions
- the present invention concerns a composite roll for hot rolling and relates especially to an outer layer material for a hot rolling mill roll and a composite roll for hot rolling that are suitable for a hot finishing mill for steel sheets.
- Patent Literature 1 proposes an outer layer material of a rolling mill roll containing C: 1.5 to 3.5%, Ni: 5.5% or less, Cr: 5.5 to 12.0%, Mo: 2.0 to 8.0%, V: 3.0 to 10.0%, and Nb: 0.5 to 7.0%, where Nb and V are contained such that the contents of Nb, V, and C satisfy a specific relationship and that a ratio of Nb to V falls within a specific range.
- Nb and V are contained such that the contents of Nb, V, and C satisfy a specific relationship and that a ratio of Nb to V falls within a specific range.
- Patent Literature 2 proposes an outer layer material of a rolling mill roll containing C: 1.5 to 3.5%, Cr: 5.5 to 12.0%, Mo: 2.0 to 8.0%, V: 3.0 to 10.0%, and Nb: 0.5 to 7.0%, where Nb and V are contained such that the contents of Nb, V, and C satisfy a specific relationship and that a ratio of Nb to V falls within a specific range.
- Nb and V are contained such that the contents of Nb, V, and C satisfy a specific relationship and that a ratio of Nb to V falls within a specific range.
- Patent Literature 3 proposes a centrifugally cast composite roll having excellent fatigue resistance of a roll surface layer in a hot rolling environment by adjusting the contents of C, Mo, V, and Nb in the composition containing C: 2.2 to 2.6%, Cr: 5.0 to 8.0%, Mo: 4.4 to 6.0%, V: 5.3 to 7.0%, and Nb 0.6 to 1.3% so that Mo + V and C - 0.24V - 0.13Nb fall within specific ranges.
- Patent Literature 4 proposes an outer layer material of a rolling mill roll containing C: 1.3 to 2.2%, Si: 0.3 to 1.2%, Mn: 0.1 to 1.5%, Cr: 2.0 to 9.0%, Mo: 9.0% or less, V: 4.0 to 15.0%, and one or two or more of W: 20.0% or less, Ni: 5.0% or less, and Co: 10.0% or less, with the balance substantially being Fe and incidental impurities, where a size of a carbide dispersed in a microstructure falls within a specific range.
- Patent Literature 4 can decrease pit defects by lowering the amount of eutectic carbides that tend to be formed as coarse carbides.
- Patent Literature 5 (PTL 5) describes a three-layer composite sleeve roll comprising an outer layer made of high-speed material, an intermediate layer welded to the outer layer and an inner layer welded to the intermediate layer.
- the chemical composition of the outer layer contains, in mass%, C: 1.0 to 3.0%, SI: 0.1 to 2.0%, NN: 0.1 to 2.0%, NI: 0.1 to 1.0%, CR: 3.0 to 10.0%, MO: 1.0 to 9.0%, W: 0.1 to 1.0% and V and/or NB: 3.0 to 10.0% in total, the balance being FE and unavoidable impurities.
- Recent rolling technology has been making progress at a remarkable rate for further improving the quality and grade of rolled steel sheets. At the same time, lower costs for rolling are highly demanded. The environment in which rolls are used has thus become increasingly severe. Accordingly, conventional designing of roll materials by focusing on carbides alone occasionally leads to a case in which formation of pit defects cannot be decreased.
- the present invention has been made in view of the above, and an object of the present invention is to provide an outer layer material for a hot rolling mill roll and a composite roll for hot rolling that have decreased pit defects on a roll surface and excellent resistance to surface roughening while ensuring wear resistance.
- the present inventors closely investigated the sites where pit defects on the surface of a hot rolling mill roll arise. As a result, it was revealed that pit defects are pit-like chips resulting from propagation of cracks that originate from eutectic carbides (primarily, M 2 C-, M 6 C-, M 7 C 3 -, and M 23 C 6 -type carbides). In addition to conventionally focusing on the type and size of the carbides, the present inventors considered that lowering the propagation rate of cracks in a matrix microstructure is effective for decreasing pit defects, thereby completing the present invention.
- eutectic carbides primarily, M 2 C-, M 6 C-, M 7 C 3 -, and M 23 C 6 -type carbides.
- Molten metal in a high-frequency induction furnace, having a composition that varies within the following ranges containing, in mass%, Si: 0.1 to 1.5%, Mn: 0.1 to 1.5%, C: 1.6 to 3.5%, Cr: 3.5 to 9.0%, Mo: 2.1 to 7.0%, V: 4.1 to 8.5%, Nb: 0.3 to 4.6%, Ni: 0.02 to 3.6%, Co: 0.3 to 8.0%, and W: 0.2 to 8.0%, with the balance being Fe and incidental impurities, was cast, by a centrifugal casting method, into a ring roll material (outer diameter: 250 mm ⁇ , width: 65 mm, thickness 55 mm) that corresponds to an outer layer material of a roll.
- a ring roll material outer diameter: 250 mm ⁇ , width: 65 mm, thickness 55 mm
- a pouring temperature was set to 1,450°C to 1,530°C, and a centrifugal force in the circumferential portion of the ring roll material was set to 180G as a gravity multiple.
- the hardness HS of 78 to 86 was achieved by performing quenching and tempering after casting. Quenching was performed by heating to a heating temperature of 1,070°C and air cooling. Tempering was performed at a temperature of 530°C to 570°C twice or three times depending on the components such that the amount of retained austenite in volume% became less than 10%.
- a specimen for a hot-rolling fatigue test (outer diameter 60 mm ⁇ , thickness 10 mm) was taken from the obtained ring roll material and subjected to a hot-rolling fatigue test that disclosed in Japanese Unexamined Patent Application Publication No. 2010-101752 to achieve reproducible assessment of fatigue resistance of a work roll for hot rolling in an actual machine.
- a notch (depth t: 1.2 mm, length in circumferential direction L: 0.8 mm) as illustrated in Fig. 1 was introduced into two sites on the outer surface of the fatigue specimen by discharge machining (wire-cut) using a 0.2 mm ⁇ wire. The ends on the rolling surface of the fatigue specimen were chamfered at 1.2C.
- the hot-rolling fatigue test was performed in a two-disk rolling-sliding mode between the specimen having notches (specimen for hot-rolling fatigue test) and a heated loading piece as illustrated in Fig. 1 .
- the specimen 1 (specimen for hot-rolling fatigue test) was rotated at 700 rpm and simultaneously cooled with cooling water 2 while the loading piece 4 (material: S45C, outer diameter: 190 mm ⁇ , width: 15 mm) heated to 800°C by a high-frequency induction heating coil 3 was pressed against the rotating specimen 1 under a load of 980 N and rolled at a slip rate of 9%.
- the specimen for a hot-rolling fatigue test 1 was rotated until breaking at two notches 5 introduced thereinto, the number of rolling rotations until breakage at each notch was counted, and the average was regarded as hot-rolling fatigue life.
- a hot-rolling fatigue life exceeding 350,000 times was evaluated as a remarkably excellent hot-rolling fatigue life.
- microstructure observation of the obtained ring roll material was performed. Microstructure observation was performed with an optical microscope after taking a 10 ⁇ 10 ⁇ 5 mm specimen (5 mm in ring thickness direction) for microstructure observation at any position 10 mm inside the outer surface of the ring roll material, mirror-polishing the 10 ⁇ 10 mm surface, and etching with Nital (5 volume% nitric acid + ethanol) for about 10 seconds.
- EBSD measurement was performed after taking a specimen for measurement (5 mm ⁇ 10 mm ⁇ 5 mm) at any position 10 mm inside the outer surface of the obtained ring roll material and mirror-polishing the 5 mm ⁇ 10 mm surface.
- the measurement of a minor axis was performed by electron backscatter diffraction (EBSD) in a region of 10,000 ⁇ m 2 or more at an accelerating voltage of 15 kV and a step size of 0.1 ⁇ m.
- Boundary lines were drawn at sites with misorientation of 15° or more from neighboring measurement points, minor axes of 20 crystals with a major axis of 5 ⁇ m or more were measured on the measurement surface by regarding a region surrounded by the boundary lines as one crystal as illustrated in Fig. 2 , and the average value was calculated.
- a relationship between hot-rolling fatigue life and (%C - %V ⁇ 0.177 - %Nb ⁇ 0.129 - %Cr ⁇ 0.099 - %Mo ⁇ 0.063 - %W ⁇ 0.033) + (%Ni) is shown in Fig. 3
- a relationship between hot-rolling fatigue life and the minor axis of tempered martensite or bainite is shown in Fig. 4 .
- Fig. 3 reveals that the hot-rolling fatigue life is remarkably enhanced when the expression (%C - %V ⁇ 0.177 - %Nb ⁇ 0.129 - %Cr ⁇ 0.099 - %Mo ⁇ 0.063 - %W ⁇ 0.033) + (%Ni) is 0.05 or more and 4.0 or less.
- V, Cr, Mo, Nb, and W are elements that tend to form carbides
- the expression (%C - %V ⁇ 0.177 - %Nb ⁇ 0.129 - %Cr ⁇ 0.099 - %Mo ⁇ 0.063 - %W ⁇ 0.033) represents the amount of carbon dissolved in a matrix.
- an outer layer material for a hot rolling mill roll and a composite roll for hot rolling that have a remarkably lowered propagation rate of cracks.
- surface damage due to hot rolling such as surface roughening and chipping, can be decreased, thereby extending a continuous rolling distance and enhancing roll life.
- An outer layer material for a hot rolling mill roll of the present invention is manufactured by a casting method, such as a publicly known centrifugal casting method or the continuous pouring process for cladding, and applied to an outer layer material of a composite roll for hot rolling, which is suitable for hot finish rolling, although the outer layer material may be used as a ring roll or a sleeve roll without additional material.
- a composite roll for hot rolling of the present invention is composed of an outer layer and an inner layer that is integrally fused.
- an intermediate layer may be provided between the outer layer and the inner layer.
- an inner layer may be integrally fused with an intermediate layer that has been integrally fused with an outer layer.
- each inner layer or intermediate layer is not particularly limited, and the inner layer is preferably spheroidal graphite cast iron (ductile cast iron) or forged steel, while the intermediate layer is preferably high-carbon material containing C: 1.5 to 3.0 mass%.
- C acts to increase the hardness of a matrix through dissolution and to enhance wear resistance of an outer layer material of a roll through formation of hard carbides by bonding with carbide-forming elements.
- the amount of eutectic carbides varies according to C content. Eutectic carbides affect characteristics of rolling applications. When C content is less than 2.0%, an insufficient amount of eutectic carbides increases frictional force during rolling and destabilizes rolling, while a low amount of C dissolved in a matrix microstructure lowers hot-rolling fatigue resistance.
- C is limited to the range of 2.0 to 3.0% and is preferably 2.1 to 2.8%.
- Si is an element that acts as a deoxidizing agent and enhances casting properties of molten metal. To obtain such effects, a content of 0.2% or more is required. Meanwhile, when a content exceeds 1.0%, the effects level off, effects commensurate with the content cannot be expected, economical disadvantages thus result, and worse still a matrix microstructure is embrittled in some cases. Accordingly, Si is limited to 0.2 to 1.0% and is preferably 0.3 to 0.7%.
- Mn is an element that acts to fix S as MnS to suppress the effect of S and effectively enhances hardenability through partial dissolution in a matrix microstructure. To obtain such effects, a content of 0.2% or more is required. Meanwhile, when a content exceeds 1.0%, the effects level off, effects commensurate with the content thus cannot be expected, and worse still the material is embrittled in some cases. Accordingly, Mn is limited to 0.2 to 1.0% and is preferably 0.3 to 0.8%.
- Cr is an element that acts to enhance wear resistance primarily through formation of eutectic carbides by bonding with C and to stabilize rolling by lowering the frictional force with steel sheets during rolling and decreasing surface damage to rolls. To obtain such effects, a content of 4.0% or more is required. Meanwhile, when a content exceeds 7.0%, fatigue resistance is reduced due to increased coarse eutectic carbides. Accordingly, Cr is limited to the range of 4.0 to 7.0% and is preferably 4.3 to 6.5%.
- Mo is an element that forms hard carbides by bonding with C to enhance wear resistance. Moreover, Mo dissolves in hard MC-type carbides composed of bonded V, Nb, and C to strengthen the carbides and dissolves in eutectic carbides to increase fracture resistance of the carbides. Through such actions, Mo enhances wear resistance and fatigue resistance of an outer layer material of a roll. To obtain such effects, a content of 3.0% or more is required. Meanwhile, when a content exceeds 6.5%, Mo-based brittle carbides are formed, thereby lowering hot-rolling fatigue resistance and lowering fatigue resistance. Accordingly, Mo is limited to the range of 3.0 to 6.5% and is preferably 3.5 to 6.0%.
- V is an important element in the present invention to impart both wear resistance and fatigue resistance of rolls.
- V is an element that enhances wear resistance through formation of extremely hard carbides (MC-type carbides) and remarkably enhances fatigue resistance as an outer layer material of a roll by effectively acting to enable divided and dispersed precipitation of eutectic carbides, thereby enhancing hot-rolling fatigue resistance. Such effects become evident at a content of 5.0% or more. Meanwhile, a content exceeding 7.5% coarsens MC-type carbides and thus destabilizes various characteristics of rolling mill rolls. Accordingly, V is limited to the range of 5.0 to 7.5% and is preferably 5.2 to 7.0%.
- Nb enhances wear resistance, especially fatigue resistance by acting to strengthen MC-type carbides through dissolution therein and to thus increase fracture resistance of MC-type carbides. Dissolution of Nb and Mo together in carbides remarkably enhances wear resistance and fatigue resistance.
- Nb is an element that acts to suppress fracture of eutectic carbides through promoted division of eutectic carbides and enhances fatigue resistance of an outer layer material of a roll. Further, Nb also acts to suppress segregation of MC-type carbides during centrifugal casting. Such effects become evident at a content of 0.5% or more. Meanwhile, when a content exceeds 3.0%, growth of MC-type carbides in molten metal is promoted, thereby impairing hot-rolling fatigue resistance. Accordingly, Nb is limited to the range of 0.5 to 3.0% and is preferably 0.8 to 1.5%.
- Ni is an element that lowers the transformation temperature of austenite during heat treatment through dissolution in a matrix and enhances hardenability of the matrix. To obtain such effects, a content of 0.05% or more is required. Meanwhile, when a content exceeds 3.0%, the transformation temperature of austenite becomes excessively low and hardenability is enhanced, thereby causing austenite to be readily retained after heat treatment. Such retained austenite lowers hot-rolling fatigue resistance through generation of cracks during hot rolling, for example. Accordingly, Ni is limited to the range of 0.05 to 3.0%. Due to ease of operation, i.e., possible refining of the crystal size of a matrix microstructure even at a slow cooling rate during heat treatment, the content is preferably 0.2 to 3.0%.
- Co is an element that acts to strengthen a matrix especially at a high temperature through dissolution in the matrix and to enhance fatigue resistance. To obtain such effects, a content of 0.2% or more is required. Meanwhile, when a content exceeds 5.0%, the effects level off, effects commensurate with the content cannot be expected, and economical disadvantages thus result. Accordingly, Co is limited to the range of 0.2 to 5.0% and is preferably 0.5 to 3.0%.
- W is an element that acts to strengthen a matrix especially at a high temperature through dissolution in the matrix and to enhance fatigue resistance. W also enhances wear resistance through formation of M 2 C- or M 6 C-type carbides. To obtain such effects, a content of 0.5% or more is required. Meanwhile, when a content exceeds 5.0%, not only do the effects level off, but also hot-rolling fatigue resistance is reduced through the formation of coarse M 2 Cor M 6 C-type carbides. Accordingly, W is limited to the range of 0.5 to 5.0% and is preferably 1.0 to 3.5%.
- C, Cr, Mo, V, Nb, Ni, and W are contained in the above-mentioned ranges and are also contained, through adjustment, so as to satisfy the following expression (1): 0.05 ⁇ % C ⁇ % V ⁇ 0.177 ⁇ % Nb ⁇ 0.129 ⁇ % Cr ⁇ 0.099 ⁇ % Mo ⁇ 0.063 ⁇ % W ⁇ 0.033 + % Ni ⁇ 4.0 where %C, %V, %Nb, %Cr, %Mo, %W, and %Ni each represent the respective content of each respective element (mass%).
- V, Cr, Mo, Nb, and W are elements that tend to form carbides
- the expression (%C - %V ⁇ 0.177 - %Nb ⁇ 0.129 - %Cr ⁇ 0.099 - %Mo ⁇ 0.063 - %W ⁇ 0.033) represents the amount of carbon dissolved in a matrix.
- the expression (%C - %V ⁇ 0.177 - %Nb ⁇ 0.129 - %Cr ⁇ 0.099 - %Mo ⁇ 0.063 - %W ⁇ 0.033) + (%Ni) is thus the sum of the amount of carbon and Ni dissolved in the matrix.
- the balance other than the components described above is Fe and incidental impurities.
- a matrix microstructure is a tempered martensite and a bainite microstructure, and a minor axis of tempered martensite or bainite is 0.5 to 3.0 ⁇ m.
- a tempered martensite and/or a bainite microstructure is preferably contained in 85% or more of the matrix microstructure and more preferably contained in 90% or more in view of hot-rolling fatigue resistance.
- the balance includes retained austenite and/or pearlite.
- the number of cooling steps repeated after heating to and retaining at 500°C to 570°C may be controlled.
- a minor axis of tempered martensite or bainite In a component system in which a minor axis of tempered martensite or bainite is less than 0.5 ⁇ m, it becomes difficult to decrease the amount of retained austenite even by repeated tempering due to excessively lowered transformation temperature, and hot-rolling fatigue resistance lowers due to possible crack generation during hot rolling caused by retained austenite. Meanwhile, when a minor axis of tempered martensite or bainite exceeds 3.0 ⁇ m, a propagation rate of cracks in the matrix microstructure is fast, and hot-rolling fatigue resistance thus lowers.
- a minor axis of tempered martensite or bainite is preferably limited to the range of 0.5 to 3.0 ⁇ m and preferably to the range of 0.5 to 2.0 ⁇ m in view of hot-rolling fatigue resistance.
- components and a cooling rate may be controlled such that the transformation temperature of the matrix falls within the range of 200°C to 400°C.
- an outer layer material is preferably manufactured by a casting method, such as a publicly known centrifugal casting method or the continuous pouring process for cladding.
- a casting method such as a publicly known centrifugal casting method or the continuous pouring process for cladding.
- the present invention is obviously not limited to these methods.
- molten metal having the above-described composition for an outer layer material of a roll is first poured into a rotating mold whose inner surface is covered with 1 to 5 mm-thick refractory containing zircon and the like as a main material to achieve a predetermined thickness and then centrifugally cast.
- the number of rotations of the mold is preferably set such that a gravity multiple applied to the outer surface of the roll falls within the range of 120 to 220G.
- molten metal having an intermediate layer composition is preferably poured into the rotating mold during solidification or after completing solidification of the outer layer material of a roll and then centrifugally cast.
- a composite roll is preferably formed by terminating rotation of the mold after the outer layer or the intermediate layer has been completely solidified, allowing the mold to stand, and then performing static casting of an inner layer material. Through this step, the inner surface side of the outer layer material of a roll is redissolved to fuse as one body the outer layer and the inner layer, or the outer layer and the intermediate layer, as well as the intermediate layer and the inner layer.
- spheroidal graphite cast iron, compacted vermicular graphite cast iron (CV cast iron), and so forth having excellent casting properties and mechanical properties are preferably used.
- an outer layer and an inner layer are integrally fused, and consequently, about 1 to 8 % components of the outer layer material are incorporated into the inner layer.
- Incorporation of carbide-forming elements, such as Cr and V, contained in the outer layer material into the inner layer embrittles the inner layer. Accordingly, the ratio of incorporation of outer layer components into an inner layer is preferably limited to less than 6%.
- an intermediate layer graphitized steel, high-carbon steel, hypoeutectic cast iron, or the like is preferably used as an intermediate layer material.
- the intermediate layer and the outer layer are similarly fused as one body, and outer layer components in the range of 10 to 95% are incorporated into the intermediate layer. From a viewpoint of decreasing the amount of outer layer components incorporated into an inner layer, it is essential to decrease the amount of outer layer components incorporated into the intermediate layer as much as possible.
- a composite roll for hot rolling of the present invention is preferably heat-treated after casting.
- a step of heating to 950°C to 1,100°C and air cooling or air blast cooling, and further, a step of cooling after heating to and retaining at 500°C to 570°C twice or more are preferably performed.
- it becomes possible to achieve the above-mentioned suitable minor-axis size by adjusting a cooling rate in accordance with components so that the transformation temperature falls within the range of 200°C to 400°C.
- the number of the step repeated may be set such that 85% or more of a matrix microstructure becomes tempered martensite and/or bainite.
- the hardness of a composite roll for hot rolling of the present invention is preferably 79 to 88HS (Shore hardness) and more preferably 80 to 86HS. Wear resistance deteriorates when the hardness is lower than 80HS, whereas it becomes difficult to remove, by grinding, cracks formed on the surface of a hot rolling mill roll during hot rolling when the hardness exceeds 86HS. To ensure the above hardness in a stable manner, it is preferable to adjust a heat treatment temperature and a heat treatment time after casting.
- Molten metal, in a high-frequency induction furnace, having the composition for an outer layer material of a roll shown in Table 1 was formed into ring test materials (ring rolls; outer diameter: 250 mm ⁇ , width 65 mm, thickness 55 mm) by centrifugal casting.
- the pouring temperature was set to 1,450°C to 1,530°C, and the centrifugal force in the circumferential portion of the respective ring roll materials was set to 180G as a gravity multiple.
- each ring test material was quenched by reheating to a reheating temperature of 1,070°C followed by air-cooling and tempered at a temperature of 530°C to 570°C twice or three times depending on components to adjust the amount of retained austenite, in volume%, to less than 10% and the hardness to 78 to 86HS.
- a hardness specimen, a specimen for a hot-rolling fatigue test, and a specimen for EBSD measurement were taken from each obtained ring test material, and a hardness test, a hot-rolling fatigue test, and a microstructure observation test were performed.
- Vickers hardness HV50 was measured according to JIS Z 2244 by using a Vickers hardness tester (test force: 50 kgf (490 N)) for the obtained hardness specimen and converted into Shore hardness HS by using a JIS conversion table.
- the hardness was obtained by setting 10 measurement points and calculating the average after subtracting the maximum and minimum values.
- a hot-rolling fatigue test method was as follows. A specimen for a hot-rolling fatigue test (outer diameter 60 mm ⁇ , thickness 10 mm, chamfered) was taken from each obtained ring test material. A notch (depth t: 1.2 mm, length in circumferential direction L: 0.8 mm) as illustrated in Fig. 1 was introduced into two sites (positions 180° apart) on the outer surface of the specimen for a hot-rolling fatigue test by discharge machining (wire-cut) using a 0.20 mm ⁇ wire. The hot-rolling fatigue test was performed in a two-disk rolling-sliding mode between the specimen and a loading material as illustrated in Fig. 1 .
- the specimen 1 was rotated at 700 rpm and simultaneously cooled with cooling water 2 while the loading piece 4 (material: S45C, outer diameter: 190 mm ⁇ , width: 15 mm, C1-chamfered) heated to 800°C by a high-frequency induction heating coil 3 was brought into contact with the rotating test piece 1 under a load of 980 N and rolled at a slip rate of 9%.
- the specimen for a hot-rolling fatigue test 1 was rotated until breaking at two notches 5 introduced thereinto, the number of rolling rotations until breakage at each notch was counted, and the average was regarded as hot-rolling fatigue life. A hot-rolling fatigue life exceeding 350,000 times was evaluated as a remarkably excellent hot-rolling fatigue life.
- Microstructure observation was performed with an optical microscope after taking a 10 ⁇ 10 ⁇ 5 mm specimen for microstructure observation (5 mm in ring thickness direction) at any position 10 mm inside the outer surface of the ring roll material, mirror-polishing the 10 ⁇ 10 mm surface, and etching with Nital (5 volume% nitric acid + ethanol) for about 10 seconds.
- the minor axis (short-axis length) of tempered martensite or bainite was obtained by EBSD measurement after taking a specimen for EBSD measurement (5 mm ⁇ 10 mm ⁇ 5 mm) at any position 10 mm inside the outer surface of each obtained ring roll material and mirror-polishing the 5 mm ⁇ 10 mm surface.
- the EBSD measurement was performed in a region of 10,000 ⁇ m 2 or more at an accelerating voltage of 15 kV and a step size of 0.1 ⁇ m.
- boundary lines were drawn at sites with misorientation of 15° or more from neighboring measurement points as illustrated in Fig. 2 , the minor axis was measured for 20 crystals with a major axis of 10 ⁇ m or more on the measurement surface by regarding a region surrounded by the boundary lines as one crystal, and the average was calculated.
- the hot-rolling fatigue life was remarkably enhanced, and an excellent hot-rolling fatigue life exceeding 350,000 times was exhibited.
- 85% or more of the matrix microstructure was confirmed to be tempered martensite and/or bainite in all the Examples.
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PCT/JP2017/023663 WO2018047444A1 (ja) | 2016-09-07 | 2017-06-28 | 熱間圧延用ロール外層材および熱間圧延用複合ロール |
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JP (1) | JP6292362B1 (ko) |
KR (1) | KR102234330B1 (ko) |
CN (1) | CN109641250B (ko) |
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JP7400771B2 (ja) * | 2021-05-20 | 2023-12-19 | Jfeスチール株式会社 | 熱間圧延用ロール外層材および熱間圧延用複合ロール |
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JP2715199B2 (ja) | 1990-10-01 | 1998-02-18 | 川崎製鉄株式会社 | 圧延用ロール外層材 |
JP2715205B2 (ja) | 1990-11-21 | 1998-02-18 | 川崎製鉄株式会社 | 圧延用ロール外層材 |
JP3962838B2 (ja) | 1998-08-03 | 2007-08-22 | 日立金属株式会社 | 熱間圧延用ロール |
JP3440894B2 (ja) * | 1998-08-05 | 2003-08-25 | Jfeスチール株式会社 | 伸びフランジ性に優れる高強度熱延鋼板およびその製造方法 |
JP2005246391A (ja) * | 2004-03-01 | 2005-09-15 | Nippon Steel Corp | 3層複合スリーブロール |
CN100485075C (zh) * | 2007-04-03 | 2009-05-06 | 西安交通大学 | 一种高碳高钒高速钢复合轧辊及其热处理方法 |
JP5136138B2 (ja) | 2008-03-18 | 2013-02-06 | Jfeスチール株式会社 | 熱間圧延用遠心鋳造製複合ロール |
CN101831590B (zh) * | 2009-03-10 | 2011-07-06 | 江苏东冶轧辊有限公司 | 高硼低合金高速钢轧辊及其制造方法 |
SE535101C2 (sv) * | 2010-01-11 | 2012-04-17 | Sandvik Intellectual Property | Musiksträng |
EP2745944B1 (en) * | 2011-09-21 | 2018-12-19 | Hitachi Metals, Ltd. | Centrifugal casted composite roller for hot rolling and method for producing same |
RU2610645C2 (ru) * | 2011-11-21 | 2017-02-14 | Хитачи Металз, Лтд. | Центробежнолитой составной валок и способ его изготовления |
JP5862526B2 (ja) * | 2012-09-13 | 2016-02-16 | Jfeスチール株式会社 | 熱間圧延用ロール外層材および熱間圧延用複合ロール |
JP5949596B2 (ja) * | 2013-03-01 | 2016-07-06 | Jfeスチール株式会社 | 熱間圧延用ロール外層材、および熱間圧延用複合ロール |
TWI633945B (zh) * | 2013-05-02 | 2018-09-01 | 日商日立金屬股份有限公司 | Composite roll for hot rolling by centrifugal casting |
JP5950048B2 (ja) * | 2013-09-25 | 2016-07-13 | 日立金属株式会社 | 遠心鋳造製熱間圧延用複合ロール |
JP6331129B2 (ja) * | 2014-03-31 | 2018-05-30 | 日立金属株式会社 | 圧延用複合ロール及びその製造方法 |
CN104018076B (zh) * | 2014-06-25 | 2016-06-15 | 武汉钢铁(集团)公司 | 一种耐高温钢筋及生产方法 |
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BR112019003360A2 (pt) | 2019-06-04 |
CN109641250A (zh) | 2019-04-16 |
TW201812028A (zh) | 2018-04-01 |
KR102234330B1 (ko) | 2021-03-30 |
WO2018047444A1 (ja) | 2018-03-15 |
KR20190029716A (ko) | 2019-03-20 |
JPWO2018047444A1 (ja) | 2018-09-06 |
EP3479915A1 (en) | 2019-05-08 |
EP3479915A4 (en) | 2019-08-07 |
CN109641250B (zh) | 2020-11-03 |
TWI655295B (zh) | 2019-04-01 |
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