WO2020032144A1 - 圧延用遠心鋳造複合ロール及びその製造方法 - Google Patents
圧延用遠心鋳造複合ロール及びその製造方法 Download PDFInfo
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- WO2020032144A1 WO2020032144A1 PCT/JP2019/031259 JP2019031259W WO2020032144A1 WO 2020032144 A1 WO2020032144 A1 WO 2020032144A1 JP 2019031259 W JP2019031259 W JP 2019031259W WO 2020032144 A1 WO2020032144 A1 WO 2020032144A1
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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
- B21B27/02—Shape or construction of rolls
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- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D13/00—Centrifugal casting; Casting by using centrifugal force
- B22D13/02—Centrifugal casting; Casting by using centrifugal force of elongated solid or hollow bodies, e.g. pipes, in moulds rotating around their longitudinal axis
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/30—Stress-relieving
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- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C37/00—Cast-iron alloys
- C22C37/06—Cast-iron alloys containing chromium
- C22C37/08—Cast-iron alloys containing chromium with nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C37/00—Cast-iron alloys
- C22C37/10—Cast-iron alloys containing aluminium or silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- 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
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/56—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.7% by weight of carbon
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- 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
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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
- B21B27/02—Shape or construction of rolls
- B21B27/021—Rolls for sheets or strips
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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
- B21B27/02—Shape or construction of rolls
- B21B27/03—Sleeved rolls
- B21B27/032—Rolls for sheets or strips
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D13/00—Centrifugal casting; Casting by using centrifugal force
- B22D13/02—Centrifugal casting; Casting by using centrifugal force of elongated solid or hollow bodies, e.g. pipes, in moulds rotating around their longitudinal axis
- B22D13/026—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 vertical
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- 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
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Definitions
- the present invention relates to a centrifugally cast composite roll for rolling in which an outer layer excellent in wear resistance and a shaft core excellent in toughness are welded and integrated, and a method for producing the same, and in particular, a finish rolling work for a hot strip mill of a thin steel plate.
- the present invention relates to a centrifugally cast composite roll suitable for rolling and a method for producing the same.
- a heated slab having a thickness of several hundred mm manufactured by continuous casting or the like is rolled into a steel plate having a thickness of several to several tens mm by a hot strip mill having a rough rolling mill and a finishing rolling mill.
- the finishing mill is usually a series of five to seven stand quadruple mills.
- the first to third stands are referred to as a first stand
- the fourth to seventh stands are referred to as a second stand.
- a composite solid roll in which an outer layer of a high-alloy grain cast iron material or a high chromium cast iron material and an inner layer of cast iron or cast steel are welded and integrated in the past has been used.
- a composite roll using a high-speed steel material having improved wear resistance as an outer layer has been used.
- This high-speed steel contains a large amount of alloying elements such as Cr, Mo, V, W, etc., and crystallizes very hard carbide, and exhibits excellent wear resistance.
- the compressive residual stress acts as a tensile stress that peels the outer layer in the roll radial direction
- the risk of inducing delayed fracture such as peeling of the outer layer increases. Once cracks occur, it is necessary to replace rolling rolls, which not only reduces the efficiency of the rolling operation but also increases costs. Therefore, although the high-speed roll has both excellent wear resistance and toughness, the overall performance as a roll for rolling is not always sufficient.
- Japanese Patent Application Laid-Open No. 2015-205342 discloses that, on a mass basis, C: 1.0 to 3.0%, Si: 0.3 to 2.0%, Mn: 0.1 to 1.6%, Ni: 0.1 to 3.0% , Cr: 3.0 to 10.0%, Mo: 2.0 to 10.0%, W: 0.01 to 8.0%, V: 4.0 to 10.0%, and Nb: 0.1 to 6.0%, with the balance being Fe and inevitable impurities.
- a shaft core portion made of ductile cast iron, and a cast iron intermediate layer, the content of V near the boundary with the shaft core portion in the intermediate layer, the V content in the rejection diameter of the outer layer
- a centrifugally cast hot rolling composite roll having a Cr content of 55% or less and a Cr content in the middle layer near the boundary with the axis core is 50% or more of the Cr content in the rejection diameter of the outer layer; Is disclosed.
- This roll has excellent abrasion resistance, has good welding of the outer layer, the intermediate layer and the shaft core, and has a compressive residual stress of 150 to 500 MPa in the outer layer so as not to promote the development of cracks.
- the composite roll using the above-mentioned high-speed steel for the outer layer has not been improved in seizure resistance and is not sufficient from the viewpoint of reducing the occurrence of drawing accidents. Therefore, there is a demand for a high-speed roll having both high abrasion resistance and seizure resistance as well as high resistance to drawing accidents.
- WO 2015/045985 A1 discloses that an outer layer formed by centrifugal casting and an inner layer made of ductile cast iron are welded and integrated, and the outer layer has a C: 1.6 to 3% and a Si: 0.3 to 0.3% by mass.
- the outer layer of these centrifugally cast hot roll composite rolls is excellent in abrasion resistance, seizure resistance (accident resistance) and surface roughness resistance, but may not be able to obtain low compressive residual stress. However, it is not always sufficient in terms of suppressing crack growth and preventing delayed fracture.
- WO 2015/045720 A1 discloses that an outer layer formed by centrifugal casting and an inner layer made of ductile cast iron are welded and integrated, and the outer layer has a C of 1.3 to 3.7% and a Si of 0.3 to 3% based on mass.
- JP-A-6-179947 is a centrifugally cast composite roll comprising an outer layer material and a shaft material of ordinary cast iron or ductile cast iron welded and integrated with the outer layer material, wherein the outer layer material has a C: 1.5 to 3.5.
- a centrifugally cast composite roll that contains and satisfies the following formula: V + 1.8Nb ⁇ 7.5C-6.0% (%), Mo + 3.0W ⁇ 14.0, and 0.2 ⁇ Nb / V ⁇ 0.8, and the balance is Fe and unavoidable impurities. Is disclosed. However, although the outer layer of this centrifugally cast composite roll is excellent in wear resistance and accident resistance, low compressive residual stress may not be obtained, and it is not always sufficient from the viewpoint of suppressing crack growth and preventing delayed fracture. There was nothing.
- an object of the present invention is to provide a centrifugally cast composite roll for rolling that has a low compressive residual stress over the entire area of the outer layer used for rolling and has both excellent wear resistance and seizure resistance, and a method for producing the same. .
- the centrifugally cast composite roll for rolling of the present invention is formed by welding and integrating the outer layer and the inner layer,
- the outer layer is 1.70 to 2.70% C, 0.3 to 3% Si, 0.1 to 3% Mn, 1.1 to 3.0% Ni, 4.0 to 10% Cr, 2.0 to 7.5% by mass.
- % Mo 3 to 6.0% V, 0.1 to 2% W, 0.2 to 2% Nb, 0.01 to 0.2% B, and 0.01 to 0.1% N, with the balance being Fe and an Fe-based alloy consisting of unavoidable impurities
- the inner layer is made of ductile cast iron.
- the compressive residual stress in the circumferential direction at the disposal diameter of the outer layer is preferably 150 to 350 ° MPa.
- the outer layer preferably has a Shore hardness at the initial diameter of 70 to 90.
- the outer layer and the inner layer are welded and integrated, and the outer layer is 1.70 to 2.70% of C, 0.3 to 3% of Si, 0.1 to 3% of Mn, and 1.1 to 3.0% of Ni, based on mass. 4.0 to 10% Cr, 2.0 to 7.5% Mo, 3 to 6.0% V, 0.1 to 2% W, 0.2 to 2% Nb, 0.01 to 0.2% B, 0.01 to 0.2%
- the centrifugally cast composite roll for rolling according to the present invention has a structure in which an outer layer and an inner layer are directly welded and integrated, has both excellent wear resistance and seizure resistance, and has a circumferential direction at the rejection diameter of the outer layer.
- the compressive residual stress in the circumferential direction on the outer layer surface is further lower than at the time of the rejection diameter, which is the minimum usable diameter, and the circumferential diameter at the rejection diameter
- FIG. 2 is an exploded cross-sectional view showing an example of a stationary casting mold used to manufacture a centrifugal casting composite roll for rolling. It is sectional drawing which shows an example of the casting mold for static casting used for manufacturing the centrifugal casting composite roll for rolling. It is the schematic which shows a friction thermal shock test machine.
- FIG. 1 shows a centrifugally cast composite roll 10 for rolling comprising an outer layer 1 formed by a centrifugal casting method and an inner layer 2 welded and integrated with the outer layer 1.
- the inner layer 2 made of ductile cast iron has a body 21 welded to the outer layer 1 and shafts 22 and 23 integrally extending from both ends of the body 21.
- [1] centrifugal casting composite roll for rolling (A) Outer layer
- the Fe-based alloy that forms the outer layer of the centrifugal casting is 1.70 to 2.70% of C, 0.3 to 3% of Si, 0.1 to 3% of Mn, and 1.1 to 3.0% of Ni, based on mass. 4.0 to 10% Cr, 2.0 to 7.5% Mo, 3 to 6.0% V, 0.1 to 2% W, 0.2 to 2% Nb, 0.01 to 0.2% B, 0.01 to 0.2% It has a chemical composition of 0.1% N, with the balance being Fe and unavoidable impurities.
- the outer layer Fe-based alloy further contains at least one selected from the group consisting of 0.1 to 10% Co, 0.01 to 0.5% Zr, 0.005 to 0.5% Ti, and 0.001 to 0.5% Al on a mass basis. You may.
- C 1.70 to 2.70 mass% C combines with V, Cr, Mo, Nb and W to form a hard carbide and contributes to the improvement of the wear resistance of the outer layer.
- C is less than 1.70% by mass, the crystallization amount of the hard carbide is too small, so that sufficient wear resistance cannot be imparted to the outer layer.
- C exceeds 2.70% by mass, the toughness of the outer layer is reduced due to the crystallization of excessive carbides, and the crack resistance is reduced, so that the cracks due to rolling become deeper and the roll loss at the time of reshaping increases.
- the lower limit of the C content is preferably 1.75% by mass, and more preferably 1.80% by mass.
- the upper limit of the C content is preferably 2.65% by mass, and more preferably 2.60% by mass. As an example of the range of the C content, it is preferably 1.75 to 2.65% by mass, and more preferably 1.80 to 2.60% by mass.
- Si 0.3 to 3% by mass Si has the effect of reducing oxide defects by deoxidizing the molten metal, improving the seizure resistance by forming a solid solution in the matrix, and improving the fluidity of the molten metal to prevent casting defects. If Si is less than 0.3% by mass, the deoxidizing action of the molten metal is insufficient, the fluidity of the molten metal is insufficient, and the defect generation rate is high. On the other hand, if Si exceeds 3% by mass, the alloy matrix becomes brittle, and the toughness of the outer layer decreases.
- the lower limit of the Si content is preferably 0.4% by mass, more preferably 0.5% by mass, and most preferably 0.6% by mass.
- the upper limit of the Si content is preferably 2.7% by mass, more preferably 2.5% by mass, and most preferably 2% by mass. You. When the range of the Si content is exemplified, it is preferably 0.4 to 2.7% by mass, more preferably 0.5 to 2.5% by mass, and most preferably 0.6 to 2% by mass.
- Mn 0.1 to 3% by mass
- Mn has an action of fixing S as MnS in addition to the deoxidizing action of the molten metal. Since MnS has a lubricating effect and is effective in preventing seizure of the rolled material, it is preferable to contain a desired amount of MnS. If Mn is less than 0.1% by mass, the effect of the addition is insufficient. On the other hand, if Mn exceeds 3% by mass, no further effect is obtained.
- the lower limit of the Mn content is preferably 0.2% by mass, more preferably 0.3% by mass.
- the upper limit of the Mn content is preferably 2.4% by mass, more preferably 1.8% by mass, and most preferably 1% by mass. As an example of the range of the Mn content, it is preferably 0.2 to 2.4% by mass, more preferably 0.3 to 1.8% by mass, and most preferably 0.3 to 1% by mass.
- Ni 1.1 to 3.0 mass% Since Ni has an effect of improving the hardenability of the matrix, if Ni is added to a large composite roll, generation of pearlite during cooling can be prevented, and the hardness of the outer layer can be improved. In addition, since the hardenability is improved, the cooling rate for securing the hardness of the outer layer can be reduced, which has the effect of reducing the compressive residual stress. If the Ni content is less than 1.1% by mass, the effect of the addition is not sufficient. If the Ni content exceeds 3.0% by mass, austenite is excessively stabilized and the hardness is hardly improved.
- the lower limit of the Ni content is preferably 1.2% by mass, more preferably 1.3% by mass, and most preferably 1.4% by mass.
- the upper limit of the Ni content is preferably 2.9% by mass, more preferably 2.8% by mass, and most preferably 2.7% by mass.
- Illustrating the range of the Ni content is preferably 1.2 to 2.9% by mass, more preferably 1.3 to 2.8% by mass, and most preferably 1.4 to 2.7% by mass.
- (e) Cr 4.0 to 10% by mass Cr is an element effective for maintaining the hardness by making the matrix bainite or martensite and maintaining the wear resistance. If the Cr content is less than 4.0% by mass, the effect is insufficient, and if the Cr content exceeds 10% by mass, the toughness of the base structure decreases.
- the lower limit of the Cr content is preferably 4.1% by mass, and more preferably 4.2% by mass.
- the upper limit of the Cr content is preferably 7.5% by mass, and more preferably 7.3% by mass.
- the range of the Cr content is, for example, preferably 4.1 to 7.5% by mass, and more preferably 4.2 to 7.3% by mass.
- Mo 2.0 to 7.5 mass% Mo combines with C to form hard carbides (M 6 C, M 2 C), increasing the hardness of the outer layer and improving the hardenability of the matrix. If Mo is less than 2.0% by mass, formation of hard carbides is particularly insufficient, so that their effects are insufficient. On the other hand, if Mo exceeds 7.5% by mass, the toughness of the outer layer decreases.
- the lower limit of the Mo content is preferably 3.0% by mass, more preferably 3.2% by mass.
- the upper limit of the Mo content is preferably 7.0% by mass, more preferably 6.5% by mass, and most preferably 6.0% by mass. Illustrating the range of the Mo content is preferably 3.0 to 7.0% by mass, more preferably 3.2 to 6.5% by mass, and most preferably 3.2 to 6.0% by mass.
- V 3 to 6.0% by mass
- V is an element that combines with C to form hard MC carbide.
- MC carbide has a Vickers hardness HV of 2500-3000 and is the hardest of carbides. If V is less than 3% by mass, the effect of the addition is insufficient. On the other hand, if V exceeds 6.0% by mass, the MC carbide having a low specific gravity is concentrated inside the outer layer due to the centrifugal force during centrifugal casting, which causes not only significant segregation of the MC carbide in the radial direction but also coarsening of the MC carbide. The alloy structure becomes coarse, and the surface is easily roughened during rolling.
- the lower limit of the V content is preferably 3.2% by mass, and more preferably 3.5% by mass.
- the upper limit of the V content is preferably 5.8% by mass, more preferably 5.6% by mass, and most preferably 5.5% by mass.
- the range of the V content it is preferably from 3.2 to 5.8% by mass, more preferably from 3.5 to 5.6% by mass, and most preferably from 3.5 to 5.5% by mass.
- W 0.1 to 2% by mass W combines with C to form a hard carbide such as hard M 6 C and contributes to the improvement of the wear resistance of the outer layer. It also has the effect of forming a solid solution in MC carbide to increase its specific gravity and reduce segregation. If W is less than 0.1% by mass, the effect of the addition is insufficient. On the other hand, when W exceeds 2% by mass, the amount of M 6 C carbide increases, the structure becomes inhomogeneous, and the skin becomes rough.
- the lower limit of the W content is preferably 0.2% by mass.
- the upper limit of the W content is preferably 1.9% by mass, more preferably 1.8% by mass. Illustrating the range of the W content is preferably 0.2 to 1.9% by mass, and more preferably 0.2 to 1.8% by mass.
- Nb 0.2 to 2% by mass
- Nb also combines with C to form hard MC carbides.
- Nb forms a solid solution in the MC carbide to strengthen the MC carbide, thereby improving the wear resistance of the outer layer.
- NbC-based MC carbide has a smaller difference in specific gravity from the molten metal than VC-based MC carbide, segregation of MC carbide is reduced. If Nb is less than 0.2% by mass, the effect of the addition is insufficient. On the other hand, if Nb exceeds 2% by mass, the MC carbides agglomerate, making it difficult to obtain a sound outer layer.
- the lower limit of the Nb content is preferably 0.4% by mass, more preferably 0.5% by mass.
- the upper limit of the Nb content is preferably 1.9% by mass, more preferably 1.8% by mass, and most preferably 1.7% by mass.
- the range of the Nb content is exemplified, it is preferably 0.4 to 1.9% by mass, more preferably 0.5 to 1.8% by mass, and most preferably 0.5 to 1.7% by mass.
- B 0.01 to 0.2 mass% B forms a solid boride having a lubricating action while forming a solid solution in the carbide, and improves seizure resistance. Since the lubricating action of the carbon boride is remarkably exhibited particularly at high temperatures, it is effective in preventing seizure when the hot-rolled material bites. Further, B is effective in improving the hardness, and it is considered that the hardness of the outer layer is secured and contributes to the reduction of the compressive residual stress. If B is less than 0.01% by mass, a sufficient lubricating effect cannot be obtained. On the other hand, when B exceeds 0.2% by mass, the outer layer becomes brittle.
- the lower limit of the B content is preferably 0.02% by mass, and more preferably 0.03% by mass. Further, the upper limit of the B content is preferably 0.18% by mass, and more preferably 0.15% by mass. When the range of the B content is exemplified, it is preferably 0.02 to 0.18% by mass, and more preferably 0.03 to 0.15% by mass.
- N 0.01 to 0.1 mass% N has the effect of refining carbides. If N is less than 0.01% by mass, the effect of refining carbides is insufficient. When N exceeds 0.1% by mass, the outer layer becomes brittle.
- the lower limit of the N content is preferably 0.015% by mass, and more preferably 0.02% by mass.
- the upper limit of the N content is preferably 0.09% by mass, and more preferably 0.08% by mass.
- the range of the N content is exemplified, it is preferably 0.015 to 0.09% by mass, and more preferably 0.02 to 0.08% by mass.
- the outer layer further comprises at least one member selected from the group consisting of 0.1 to 10% Co, 0.01 to 0.5% Zr, 0.005 to 0.5% Ti, and 0.001 to 0.5% Al on a mass basis. It may contain an element. The outer layer may further contain 0.3% by mass or less of S.
- Co 0.1 to 10% by mass
- Co forms a solid solution in the matrix, has an effect of increasing the hot hardness of the matrix, and improving abrasion resistance and surface roughness resistance. If Co is less than 0.1% by mass, there is almost no effect of addition, and if Co exceeds 10% by mass, further improvement cannot be obtained.
- the lower limit of the Co content is more preferably 1% by mass.
- the upper limit of the Co content is more preferably 7% by mass, and most preferably 6% by mass.
- the range of the Co content is, for example, more preferably 1 to 7% by mass, and most preferably 1 to 6% by mass.
- Zr 0.01 to 0.5% by mass
- Zr combines with C to form MC carbides and improves wear resistance.
- Zr forms an oxide in the molten metal, and since this oxide acts as a crystal nucleus, the solidified structure becomes fine.
- Zr increases the specific gravity of MC carbide, and is effective in preventing segregation.
- the amount of Zr added is preferably 0.01% by mass or more.
- Zr exceeds 0.5% by mass, inclusions are not preferable because they become inclusions.
- the upper limit of the Zr content is more preferably 0.3% by mass.
- the lower limit of the Zr content is more preferably 0.02% by mass. Illustrating the range of the Zr content is more preferably 0.02 to 0.3% by mass.
- Ti 0.005 to 0.5 mass% Ti combines with C and N to form hard particulate compounds such as TiC, TiN and TiCN. Since these serve as nuclei of MC carbides, they have an effect of homogeneously dispersing MC carbides and contribute to improvement of wear resistance and surface roughening resistance. To obtain this effect, the amount of Ti added is preferably 0.005% by mass or more. However, when the Ti content exceeds 0.5% by mass, the viscosity of the molten metal increases, and casting defects easily occur.
- the upper limit of the Ti content is more preferably 0.3% by mass, and most preferably 0.2% by mass. In order to obtain a sufficient effect of addition, the lower limit of the Ti content is more preferably 0.01% by mass.
- the range of the Ti content is, for example, more preferably 0.01 to 0.3% by mass, and most preferably 0.01 to 0.2% by mass.
- Al 0.001 to 0.5 mass%
- Al has a high affinity for oxygen and thus acts as a deoxidizer.
- Al combines with N and O, and the formed oxides, nitrides, oxynitrides, and the like are suspended in the molten metal to become nuclei and crystallize MC carbides finely and uniformly.
- the outer layer becomes brittle.
- the upper limit of the Al content is more preferably 0.3% by mass, and most preferably 0.2% by mass.
- the lower limit of the Al content is more preferably 0.01% by mass.
- the range of the Al content is, for example, more preferably 0.01 to 0.3% by mass, and most preferably 0.01 to 0.2% by mass.
- S 0.3% by mass or less S may be contained in an amount of 0.3% by mass or less when using the lubricity of MnS as described above. If it exceeds 0.3% by mass, embrittlement of the outer layer occurs.
- the upper limit of the S content is more preferably 0.2% by mass, and most preferably 0.15% by mass. Further, the lower limit of the S content is more preferably 0.05% by mass.
- the range of the S content is exemplified, it is more preferably 0.05 to 0.2% by mass, and most preferably 0.05 to 0.15% by mass.
- S is preferably 0.1% by mass or less, more preferably 0.05% by mass or less, and most preferably 0.03% by mass or less in order to suppress embrittlement of the outer layer.
- the remainder of the composition of the outer layer consists of Fe and inevitable impurities.
- P causes deterioration of the mechanical properties, so it is preferable to reduce P as much as possible.
- the content of P is preferably 0.1% by mass or less.
- elements such as Cu, Sb, Te, and Ce may be contained within a range that does not impair the properties of the outer layer.
- the total amount of unavoidable impurities is preferably 0.7% by mass or less.
- the microstructure of the outer layer is (a) MC carbide, (b) M 2 C or M 6 C carbide (Mo-based carbide) mainly composed of Mo, or M 7 C 3 or M 23 mainly composed of Cr. carbides of C 6 (Cr-based carbide), consisting of (c) carbon boride, and (d) a base.
- Carbon borides generally have a composition of M (C, B).
- the metal M is mainly at least one of Fe, Cr, Mo, V, Nb, and W, and the ratio of the metals M, C, and B changes depending on the composition.
- no graphite is present in the outer layer structure.
- the outer layer of the composite roll for rolling has a hard MC carbide, a Mo-based carbide, or a Cr-based carbide, and thus has excellent wear resistance, and also has excellent seizure resistance because it contains a carbon boride.
- the inner layer of the composite roll for rolling is formed of ductile cast iron (spheroidal graphite cast iron) having excellent toughness.
- the preferred composition of ductile cast iron is 2.4-3.6% C, 1.5-3.5% Si, 0.1-2% Mn, 0.1-2% Ni, less than 0.7% Cr, less than 0.7% Mo, by weight, It contains 0.01-1% V, 0-0.5% W, 0-0.2% Nb, and 0.01-0.1% Mg, with the balance being Fe and unavoidable impurities.
- ductile cast iron is used for the inner layer, it is possible to prevent the composite roll from being damaged by the rolling load at the finishing stand.
- the P content is preferably 0.1% by mass or less
- the S content is preferably 0.05% by mass or less
- N is preferably 0.07% by mass or less.
- B inhibits the graphitization of the inner layer, it is preferably less than 0.05% by mass.
- elements such as Zr, Co, Ti, and Al are contained in the outer layer, elements such as Zr, Co, Ti, and Al are also included as inevitable impurities, and further, Ba, Cu, Sb, Te, Ce, rare earth metal elements, and the like. Are inevitable impurities, but the total content of these elements is preferably 0.7% by mass or less.
- the compressive residual stress in the circumferential direction at the disposal diameter of the outer layer is preferably from 150 to 350 MPa, more preferably from 160 to 300 MPa. . For this reason, even if a drawing accident is encountered, cracks are unlikely to be formed on the outer layer surface, and even if cracks are formed, cracks are hardly developed.
- the outer layer disposal diameter is the diameter at the maximum usable depth of the outer layer. For example, in the case of a composite roll having an outer diameter of 600 to 850 mm, the maximum usable depth of the outer layer is 40 to 60 from the initial diameter.
- the maximum usable depth of the outer layer is about 30 to 60 mm from the initial diameter.
- the outer layer waste diameter can be determined according to the specifications of the rolling mill.
- the inner surface of the outer layer dissolves to some extent, so that the boundary between the outer layer and the inner layer in the product has a larger diameter than the inner surface of the outer layer. Since the boundary between the outer layer and the inner layer after welding is inevitably uneven, the rejected diameter of the outer layer should be set to a safe margin so that the boundary does not enter the rolling section. Is set so that the diameter becomes larger than the boundary of.
- the thickness of the outer layer at the disposal diameter is preferably 8 mm or more.
- the outer layer preferably has a Shore hardness of 70 to 90 at the initial diameter surface, more preferably 75 to 85. Therefore, the wear resistance of the outer layer is ensured.
- the initial diameter of the outer layer is a diameter when the outer layer as centrifugally cast is ground to make it usable, and the grinding process is repeated from that diameter (initial diameter) until the discarded diameter is used.
- the initial diameter of the outer layer is the diameter of the outer surface of a normally centrifugally cast outer surface when it is removed by a depth of 5 to 30 mm.
- the distance from the outer diameter of the roll at the time of the disposal diameter to the welding boundary between the intermediate layer and the inner layer is preferably 8 mm or more.
- an intermediate layer having an intermediate composition between the outer layer and the inner layer can be provided for the purpose of forming a buffer layer between the outer layer and the inner layer.
- the thickness of the intermediate layer is preferably 8 to 30 mm.
- the size of the centrifugally cast composite rolling roll of the present invention is not particularly limited, but a preferred example is that the outer layer has an outer diameter of 200 to 1300 mm, the roll body length is 500 to 6000 mm, and the outer layer is rolled.
- the thickness of the used layer is 25 to 200 mm.
- the method for producing a centrifugal casting composite roll for rolling comprises: (1) a step of centrifugally casting the outer layer with a rotating cylindrical mold for centrifugal casting; and (2) Casting the molten metal for the inner layer into the cavity of the outer layer.
- the outer layer is heated again to the austenitizing temperature or higher, and the temperature from the reheating temperature to 600 ° C. is 10 to 10 ° C. It is characterized by cooling at a cooling rate of 60 ° C./hr.
- the reheating of the outer layer can be performed by (a) heating the outer layer again after manufacturing a centrifugally cast composite roll composed of the welded and integrated outer layer and the inner layer, or (b) heating the inner surface of the outer layer with the cast inner layer molten metal. This includes both cases where the side is reheated.
- the reheating temperature of the outer layer is the temperature at which the outer surface of the outer layer is reheated in the case of (a), and the temperature at which the inner surface of the outer layer is reheated by casting the inner layer molten metal in the case of (b).
- the first essential condition in the method of the present invention is that the reheating temperature of the outer layer is higher than the austenitizing temperature ⁇ .
- the austenitizing temperature ⁇ of the Fe-based alloy forming the outer layer of the present invention is 800 to 840 ° C. Therefore, the reheating temperature of the outer layer is 800 ° C. or higher. Since the boundary between the outer layer and the inner layer may be re-melted due to the re-heating of the outer layer and defects may occur, the upper limit of the re-heating temperature of the outer layer is set to a temperature at which the boundary between the outer layer and the inner layer does not re-melt. Specifically, the reheating temperature of the outer layer is preferably from 800 to 1200 ° C.
- the second essential condition in the method of the present invention is to cool from the reheating temperature to 600 ° C. at a cooling rate of 10 to 60 ° C./hr. If the cooling rate from the reheating temperature to 600 ° C. is less than 10 ° C./hr, the hardness of the outer layer becomes too low, and if it exceeds 60 ° C./hr, the compressive residual stress of the outer layer becomes too large.
- the lower limit of the cooling rate from the reheating temperature to 600 ° C is preferably 15 ° C / hr, and the upper limit is preferably 55 ° C / hr.
- Preferred cooling rates between the reheating temperature and 600 ° C. are, for example, 15-55 ° C./hr.
- the steel is cooled to 600 ° C. while maintaining austenite without causing pearlite transformation.
- the cooling rate after cooling to 600 ° C. is not limited.
- a centrifugally cast composite roll may be allowed to cool in a casting mold.
- tempering After cooling from 600 ° C. to normal temperature to 450 ° C., it is preferable to perform tempering at a temperature of 500 to 550 ° C. By tempering, high toughness can be obtained while maintaining sufficient wear resistance.
- FIGS. 2A and 2B show an example of a stationary casting mold used for casting the inner layer 2 after centrifugally casting the outer layer 1 with the cylindrical mold 30 for centrifugal casting.
- the stationary casting mold 100 includes a cylindrical mold 30 having an outer layer 1 on an inner surface, and an upper mold 40 and a lower mold 50 provided at upper and lower ends thereof.
- the cylindrical mold 30 includes a mold body 31, a sand mold 32 formed inside the mold body 31, and a sand mold 33 formed at the lower end of the mold body 31 and the sand mold 32.
- the upper mold 40 includes a mold body 41 and a sand mold 42 formed inside thereof.
- the lower mold 50 includes a mold body 51 and a sand mold 52 formed inside the mold body 51.
- the lower die 50 is provided with a bottom plate 53 for holding the inner layer molten metal.
- the inner surface of the outer layer 1 in the cylindrical mold 30 has a cavity 60a for forming the core 21 of the inner layer 2
- the upper mold 40 has a cavity 60b for forming the shaft portion 23 of the inner layer 2
- the lower mold 50 has a cavity 60c for forming the shaft portion 22 of the inner layer 2.
- the centrifugal casting method using the cylindrical mold 30 may be any of a horizontal type, an inclined type and a vertical type.
- the stationary casting mold 100 is configured.
- the cavity 60a in the outer layer 1 communicates with the cavity 60b of the upper mold 40 and the cavity 60c of the lower mold 50 to form the cavity 60 integrally forming the entire inner layer 1.
- An intermediate layer can be formed by centrifugal casting on the inner surface of the outer layer cast by centrifugal casting as a buffer layer between the inner layer and the inner layer.
- Examples 1-4 and Comparative Examples 1-2 The cylindrical mold 30 having the structure shown in FIG. 2 (a) was installed in a horizontal centrifugal casting machine, and the outer layer 1 was centrifugally cast using each molten metal having the chemical composition shown in Table 1. The gravity multiple at the outer periphery of the outer layer was 120 G. After the outer layer 1 is solidified, the cylindrical mold 30 on which the outer layer 1 is formed is erected on the inner surface, and the cylindrical mold 30 is erected on the hollow lower mold 50 for forming the shaft portion 22. A hollow upper mold 40 for forming the shaft portion 23 was erected on the above to form a stationary casting mold 100 shown in FIG. 2 (b).
- a molten ductile cast iron having a chemical composition shown in Table 1 is poured from the upper opening 43 as a melt for the inner layer, and a graphitized inoculant containing Si is inoculated on the way. did.
- the stationary casting mold 100 was disassembled, and the obtained composite roll was taken out. This composite roll was inserted into the heat treatment furnace, heated to the reheating temperature T ° C shown in Table 2, and held for 2 hours. The heat treatment furnace was controlled to be cooled so as to have the indicated cooling rate.
- the cooling rate was measured by bringing a thermocouple into contact with the outer layer surface, and the average cooling rate between the reheating temperature and 600 ° C. was calculated.
- Each of the centrifugally cast composite rolls at a temperature of less than 600 ° C. was twice tempered at 530 ° C. for 10 hours to obtain a centrifugally cast composite roll in which the inner layer 2 was integrally welded to the inner surface of the outer layer 1.
- Table 3 shows the size of the composite roll as cast.
- each centrifugally cast composite roll was processed and removed to obtain a centrifugally cast composite roll for rolling.
- Table 4 shows the initial diameter and the disposal diameter of each composite roll.
- the Shore hardness and seizure resistance of the outer layer of each composite roll, and the compressive residual stress in the circumferential direction at the disposal diameter of the outer layer were measured by the following methods. Table 4 shows the results.
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Abstract
Description
Cr/(Mo+0.5W)<-2/3[C-0.2(V+1.19Nb)]+11/6 ・・・(1)
により表される関係(ただし、任意成分であるW及びNbを含有しない場合、W=0及びNb=0である。)を満足し、面積率で1~15%のMC炭化物、0.5~20%の炭ホウ化物、及び0.5~20%のMo系炭化物を含有する遠心鋳造製熱間圧延用複合ロールを開示している。また、WO 2015/045985 A1は、遠心鋳造法により形成された外層と、ダクタイル鋳鉄からなる内層とが溶着一体化してなり、前記外層が質量基準で、C:1.6~3%、Si:0.3~2.5%、Mn:0.3~2.5%、Ni:0.1~5%、Cr:2.8~7%、Mo:1.8~6%、V:3.3~6.5%、及びB:0.02~0.12%を含有し、残部がFe及び不可避的不純物からなる化学組成を有し、かつ下記式(1):
Cr/(Mo+0.5W)≧-2/3[C-0.2(V+1.19Nb)]+11/6 ・・・(1)
により表される関係(ただし、任意成分であるW及びNbを含有しない場合、W=0及びNb=0である。)を満足し、面積率で1~15%のMC炭化物、0.5~20%の炭ホウ化物、及び1~25%のCr系炭化物を含有する遠心鋳造製熱間圧延用複合ロールを開示している。しかし、これらの遠心鋳造製熱間圧延用複合ロールの外層は、耐摩耗性、耐焼付き性(耐事故性)及び耐肌荒れ性に優れているが、低圧縮残留応力が得られない場合があり、亀裂進展の抑制や遅れ破壊の防止という観点では必ずしも十分ではないことがあった。
前記外層が質量基準で、1.70~2.70%のCと、0.3~3%のSiと、0.1~3%のMnと、1.1~3.0%のNiと、4.0~10%のCrと、2.0~7.5%のMoと、3~6.0%のVと、0.1~2%のWと、0.2~2%のNbと、0.01~0.2%のBと、0.01~0.1%のNとを含有し、残部がFe及び不可避的不純物からなるFe基合金からなり、
前記内層がダクタイル鋳鉄からなることを特徴とする。
回転する遠心鋳造用円筒状鋳型で前記外層を遠心鋳造する工程、及び前記外層のキャビティに前記内層用溶湯を鋳込む工程を有し、
前記内層の鋳造後又は鋳造中に、前記外層をオーステナイト化温度以上に再度加熱し、
再加熱温度から600℃までの間を10~60℃/hrの冷却速度で冷却することを特徴とする。
(A) 外層
遠心鋳造外層を形成するFe基合金は、質量基準で1.70~2.70%のCと、0.3~3%のSiと、0.1~3%のMnと、1.1~3.0%のNiと、4.0~10%のCrと、2.0~7.5%のMoと、3~6.0%のVと、0.1~2%のWと、0.2~2%のNbと、0.01~0.2%のBと、0.01~0.1%のNとを含有し、残部がFe及び不可避的不純物からなる化学組成を有する。このような組成の外層とすることにより、優れた耐摩耗性及び耐焼付き性を兼備するとともに、外層の廃却径における円周方向の圧縮残留応力が低い遠心鋳造複合ロールを得ることができる。外層のFe基合金はさらに、質量基準で0.1~10%のCo、0.01~0.5%のZr、0.005~0.5%のTi、及び0.001~0.5%のAlからなる群から選ばれた少なくとも一種を含有しても良い。
(a) C:1.70~2.70質量%
CはV、Cr、Mo、Nb及びWと結合して硬質炭化物を生成し、外層の耐摩耗性の向上に寄与する。Cが1.70質量%未満では硬質炭化物の晶出量が少なすぎて外層に十分な耐摩耗性を付与することができない。一方、Cが2.70質量%を超えると過剰な炭化物の晶出により外層の靱性が低下し、耐クラック性が低下するため、圧延によるクラックが深くなり、改削時のロール損失量が増加する。C含有量の下限は好ましくは1.75質量%であり、より好ましくは1.80質量%である。また、C含有量の上限は好ましくは2.65質量%であり、より好ましくは2.60質量%である。C含有量の範囲を例示すると、好ましくは1.75~2.65質量%であり、より好ましくは1.80~2.60質量%である。
Siは溶湯の脱酸により酸化物の欠陥を減少させるとともに、基地に固溶して耐焼付き性を向上させ、さらに溶湯の流動性を向上させて鋳造欠陥を防止する作用を有する。Siが0.3質量%未満では溶湯の脱酸作用が不十分であり、溶湯の流動性も不足し、欠陥発生率が高い。一方、Siが3質量%を超えると合金基地が脆化し、外層の靱性は低下する。Si含有量の下限は好ましくは0.4質量%であり、より好ましくは0.5質量%であり、最も好ましくは0.6質量%である。また、Si含有量の上限は好ましくは2.7質量%であり、より好ましくは2.5質量%であり、最も好ましくは2質量%である。る。Si含有量の範囲を例示すると、好ましくは0.4~2.7質量%であり、より好ましくは0.5~2.5質量%であり、最も好ましくは0.6~2質量%である。
Mnは溶湯の脱酸作用の他に、SをMnSとして固定する作用を有する。MnSは潤滑作用を有し、圧延材の焼き付き防止に効果があるので、所望量のMnSを含有するのが好ましい。Mnが0.1質量%未満ではその添加効果は不十分である。一方、Mnが3質量%を超えてもさらなる効果は得られない。Mn含有量の下限は好ましくは0.2質量%であり、より好ましくは0.3質量%である。また、Mn含有量の上限は好ましくは2.4質量%であり、より好ましくは1.8質量%であり、最も好ましくは1質量%である。Mn含有量の範囲を例示すると、好ましくは0.2~2.4質量%であり、より好ましくは0.3~1.8質量%であり、最も好ましくは0.3~1質量%である。
Niは基地の焼き入れ性を向上させる作用を有するので、大型の複合ロールの場合にNiを添加すると、冷却中のパーライトの発生を防止し、外層の硬さを向上させることができる。また、焼入れ性が向上するため、外層の硬さを確保するための冷却速度を遅くすることができ、圧縮残留応力を低減する効果も有する。Niが1.1質量%未満ではその添加効果は十分でなく、また3.0質量%を超えるとオーステナイトが安定化しすぎ、硬さが向上しにくくなる。Niの含有量の下限は好ましくは1.2質量%であり、より好ましくは1.3質量%であり、最も好ましくは1.4質量%である。また、Ni含有量の上限は好ましくは2.9質量%であり、より好ましくは2.8質量%であり、最も好ましくは2.7質量%である。Ni含有量の範囲を例示すると、好ましくは1.2~2.9質量%であり、より好ましくは1.3~2.8質量%であり、最も好ましくは1.4~2.7質量%である。
Crは基地をベイナイト又はマルテンサイトにして硬さを保持し、耐摩耗性を維持するのに有効な元素である。Crが4.0質量%未満ではその効果が不十分であり、Crが10質量%を超えると、基地組織の靭性が低下する。Crの含有量の下限は好ましくは4.1質量%であり、より好ましくは4.2質量%である。また、Cr含有量の上限は好ましくは7.5質量%であり、より好ましくは7.3質量%である。Cr含有量の範囲を例示すると、好ましくは4.1~7.5質量%であり、より好ましくは4.2~7.3質量%である。
MoはCと結合して硬質炭化物(M6C、M2C)を形成し、外層の硬さを増加させるとともに、基地の焼入れ性を向上させる。Moが2.0質量%未満では特に硬質炭化物の形成が不十分となるのでそれらの効果が不十分である。一方、Moが7.5質量%を超えると、外層の靭性が低下する。Mo含有量の下限は好ましくは3.0質量%であり、より好ましくは3.2質量%である。また、Mo含有量の上限は好ましくは7.0質量%であり、より好ましくは6.5質量%であり、最も好ましくは6.0質量%である。Mo含有量の範囲を例示すると、好ましくは3.0~7.0質量%であり、より好ましくは3.2~6.5質量%であり、最も好ましくは3.2~6.0質量%である。
VはCと結合して硬質のMC炭化物を生成する元素である。MC炭化物は2500~3000のビッカース硬さHVを有し、炭化物の中で最も硬い。Vが3質量%未満では、その添加効果が不十分である。一方、Vが6.0質量%を超えると、比重の軽いMC炭化物が遠心鋳造中の遠心力により外層の内側に濃化し、MC炭化物の半径方向偏析が著しくなるだけでなく、MC炭化物が粗大化して合金組織が粗くなり、圧延時に肌荒れしやすくなる。V含有量の下限は好ましくは3.2質量%であり、より好ましくは3.5質量%である。また、V含有量の上限は好ましくは5.8質量%であり、より好ましくは5.6質量%であり、最も好ましくは5.5質量%である。V含有量の範囲を例示すると、好ましくは3.2~5.8質量%であり、より好ましくは3.5~5.6質量%であり、最も好ましくは3.5~5.5質量%である。
WはCと結合して硬質のM6C等の硬質炭化物を生成し、外層の耐摩耗性向上に寄与する。またMC炭化物にも固溶してその比重を増加させ、偏析を軽減させる作用を有する。Wが0.1質量%未満では、その添加効果が不十分である。一方、Wが2質量%を超えると、M6C炭化物が多くなり、組織が不均質となり、肌荒れの原因となる。W含有量の下限は0.2質量%が好ましい。また、W含有量の上限は好ましくは1.9質量%であり、より好ましくは1.8質量%である。W含有量の範囲を例示すると、好ましくは0.2~1.9質量%であり、より好ましくは0.2~1.8質量%である。
Vと同様に、NbもCと結合して硬質MC炭化物を生成する。NbはV及びMoとの複合添加により、MC炭化物に固溶してMC炭化物を強化し、外層の耐摩耗性を向上させる。NbC系のMC炭化物は、VC系のMC炭化物より溶湯との比重差が小さいので、MC炭化物の偏析を軽減させる。Nbが0.2質量%未満では、その添加効果が不十分である。一方、Nbが2質量%を超えると、MC炭化物が凝集し、健全な外層を得にくくなる。Nb含有量の下限は好ましくは0.4質量%であり、より好ましくは0.5質量%である。また、Nb含有量の上限は好ましくは1.9質量%であり、より好ましくは1.8質量%であり、最も好ましくは1.7質量%である。Nb含有量の範囲を例示すると、好ましくは0.4~1.9質量%であり、より好ましくは0.5~1.8質量%であり、最も好ましくは0.5~1.7質量%である。
Bは炭化物に固溶するとともに、潤滑作用を有する炭ホウ化物を形成し、耐焼付き性を向上させる。炭ホウ化物の潤滑作用は特に高温で顕著に発揮されるので、熱間圧延材のかみ込み時の焼き付き防止に効果的である。またBは硬さ向上に効果があり、外層の硬さを確保して圧縮残留応力の低減に寄与することが考えられる。Bが0.01質量%未満では十分な潤滑作用が得られない。一方、Bが0.2質量%を超えると外層が脆化する。B含有量の下限は好ましくは0.02質量%であり、より好ましくは0.03質量%である。また、B含有量の上限は好ましくは0.18質量%であり、より好ましくは0.15質量%である。B含有量の範囲を例示すると、好ましくは0.02~0.18質量%であり、より好ましくは0.03~0.15質量%である。
Nは炭化物を微細化する効果を有する。Nが0.01質量%未満であると、炭化物の微細化効果が不十分である。また、Nが0.1質量%を超えると外層が脆化する。十分な炭化物微細化効果を得るには、N含有量の下限は好ましくは0.015質量%であり、より好ましくは0.02質量%である。また、N含有量の上限は好ましくは0.09質量%であり、より好ましくは0.08質量%である。N含有量の範囲を例示すると、好ましくは0.015~0.09質量%であり、より好ましくは0.02~0.08質量%である。
外層はさらに、質量基準で0.1~10%のCo、0.01~0.5%のZr、0.005~0.5%のTi、及び0.001~0.5%のAlからなる群から選ばれた少なくとも一種の元素を含有しても良い。外層はさらに0.3質量%以下のSを含有しても良い。
Coは基地中に固溶し、基地の熱間硬さを増加させ、耐摩耗性及び耐肌荒れ性を改善する効果を有する。Coが0.1質量%未満では添加効果はほとんどなく、また10質量%を超えてもさらなる向上は得られない。Co含有量の下限はより好ましくは1質量%である。また、Co含有量の上限はより好ましくは7質量%、最も好ましくは6質量%である。Co含有量の範囲を例示すると、より好ましくは1~7質量%であり、最も好ましくは1~6質量%である。
V及びNbと同様に、ZrはCと結合してMC炭化物を生成し、耐摩耗性を向上させる。また、Zrは溶湯中で酸化物を生成し、この酸化物が結晶核として作用するために、凝固組織が微細になる。さらに、ZrはMC炭化物の比重を増加させ、偏析防止に効果がある。この効果を得るために、Zrの添加量は0.01質量%以上であるのが好ましい。しかし、Zrが0.5質量%を超えると、介在物となるので好ましくない。Zr含有量の上限はより好ましくは0.3質量%である。また、十分な添加効果を得るためには、Zr含有量の下限はより好ましくは0.02質量%である。Zr含有量の範囲を例示すると、より好ましくは0.02~0.3質量%である。
TiはC及びNと結合し、TiC、TiN及びTiCNのような硬質の粒状化合物を形成する。これらはMC炭化物の核となるため、MC炭化物の均質分散効果があり、耐摩耗性及び耐肌荒れ性の向上に寄与する。この効果を得るために、Tiの添加量は0.005質量%以上であるのが好ましい。しかし、Ti含有量が0.5質量%を超えると、溶湯の粘性が増加し、鋳造欠陥が発生しやすくなる。Ti含有量の上限はより好ましくは0.3質量%であり、最も好ましくは0.2質量%である。また、十分な添加効果を得るためには、Ti含有量の下限はより好ましくは0.01質量%である。Ti含有量の範囲を例示すると、より好ましくは0.01~0.3質量%であり、最も好ましくは0.01~0.2質量%である。
Alは酸素との親和性が高いため、脱酸剤として作用する。また、AlはN及びOと結合し、形成された酸化物、窒化物、酸窒化物等は溶湯中に懸濁されて核となり、MC炭化物を微細均一に晶出させる。しかし、Alが0.5質量%を超えると、外層が脆くなる。また、Alが0.001質量%未満ではその効果が十分でない。Al含有量の上限はより好ましくは0.3質量%であり、最も好ましくは0.2質量%である。また十分な添加効果を得るためには、Al含有量の下限はより好ましくは0.01質量%である。Al含有量の範囲を例示すると、より好ましくは0.01~0.3質量%であり、最も好ましくは0.01~0.2質量%である。
Sは、前述のようにMnSの潤滑性を利用する場合には0.3質量%以下含有しても良い。0.3質量%を超えると外層の脆化が起こる。MnSの潤滑性を利用する場合には、S含有量の上限はより好ましくは0.2質量%であり、最も好ましくは0.15質量%である。また、S含有量の下限はより好ましくは0.05質量%である。S含有量の範囲を例示すると、より好ましくは0.05~0.2質量%であり、最も好ましくは0.05~0.15質量%である。一方、MnSの潤滑性を利用しない場合には、外層の脆化を抑えるため、Sは、0.1質量%以下が好ましく、0.05質量%以下がより好ましく、0.03質量%以下が最も好ましい。
外層の組成の残部はFe及び不可避的不純物からなる。不可避的不純物のうち、Pは機械的性質の劣化を招くので、できるだけ少なくするのが好ましい。具体的には、Pの含有量は0.1質量%以下が好ましい。その他の不可避的不純物として、Cu、Sb、Te、Ce等の元素を外層の特性を損なわない範囲で含有しても良い。外層の優れた耐摩耗性及び耐事故性を確保するために、不可避的不純物の合計量は0.7質量%以下であるのが好ましい。
外層の組織は、(a) MC炭化物、(b) Moを主体とするM2CやM6Cの炭化物(Mo系炭化物)又はCrを主体とするM7C3やM23C6の炭化物(Cr系炭化物)、(c) 炭ホウ化物、及び(d) 基地からなる。炭ホウ化物は一般にM(C, B)の組成を有する。ただし、金属Mは主にFe、Cr、Mo、V、Nb及びWの少なくとも一種であり、金属M,C及びBの割合は組成により変化する。外層組織には黒鉛が存在しないのが好ましい。圧延用複合ロールの外層は、硬質のMC炭化物、Mo系炭化物又はCr系炭化物を有するので、耐摩耗性に優れ、かつ炭ホウ化物を含有するために耐焼付き性に優れている。
圧延用複合ロールの内層は強靭性に優れたダクタイル鋳鉄(球状黒鉛鋳鉄)により形成する。ダクタイル鋳鉄の好ましい組成は、質量基準で2.4~3.6%のC、1.5~3.5%のSi、0.1~2%のMn、0.1~2%のNi、0.7%未満のCr、0.7%未満のMo、0.01~1%のV、0~0.5%のW、0~0.2%のNb、及び0.01~0.1%のMgを含有し、残部がFe及び不可避的不純物からなる。内層にダクタイル鋳鉄を用いると、仕上げスタンドでの圧延荷重により複合ロールが破損するのを防止できる。
本発明の圧延用遠心鋳造複合ロールにおいては、外層の廃却径における円周方向の圧縮残留応力は150~350 MPaであるのが好ましく、160~300 MPaであるのがより好ましい。このため、絞り事故に遭遇したとしても、外層表面にクラックが入りにくく、仮にクラックが入った場合であってもクラック進展が起こりにくい。なお、外層の廃却径は外層の使用可能な最大深さにおける直径であり、例えば600~850 mmの外径の複合ロールの場合、外層の使用可能な最大深さは初径から40~60 mm程度であり、450~600mm未満の外径の複合ロールの場合、外層の使用可能な最大深さは初径から30~60mm程度である。この範囲で外層の廃却径を圧延機の仕様に応じて決めることができる。
本発明の圧延用遠心鋳造複合ロールについて説明したが、外層と内層の間に緩衝層を形成する目的で、外層と内層の中間的組成の中間層を設けることができる。中間層の厚さは8~30 mmが好ましい。
本発明の遠心鋳造製複合圧延ロールのサイズは特に限定されないが、好ましい例は、外層の外径が200~1300 mmで、ロール胴長が500~6000 mmで、外層の圧延使用層の厚さが25~200 mmである。
本発明の圧延用遠心鋳造複合ロールの製造方法は、(1) 回転する遠心鋳造用円筒状鋳型で前記外層を遠心鋳造する工程、及び(2) 前記外層のキャビティに前記内層用溶湯を鋳込む工程を有し、前記内層の鋳造中又は鋳造後に、前記外層をオーステナイト化温度以上に再度加熱し、再加熱温度から600℃までの間を10~60℃/hrの冷却速度で冷却することを特徴とする。
図2(a) に示す構造の円筒状鋳型30を水平型の遠心鋳造機に設置し、表1に示す化学組成の各溶湯を用いて外層1を遠心鋳造した。外層外周における重力倍数は120 Gであった。外層1が凝固した後、内面に外層1が形成された円筒状鋳型30を起立させ、軸部22形成用の中空状下型50の上に円筒状鋳型30を立設し、円筒状鋳型30の上に軸部23形成用の中空状上型40を立設し、図2(b) に示す静置鋳造用鋳型100を構成した。
各複合ロールの外層の初径表面のショア硬さをJIS Z 2246に基づき測定した。
各複合ロールの外層のロール軸方向中央部を廃却径まで除去し、廃却径における外層表面の円周方向圧縮残留応力をX線回折残留応力測定装置により測定した。
耐焼付き性を評価するため、図3に示す摩擦熱衝撃試験機を用いて、外層の軸方向端部から切り出した試験片(25 mm×30 mm×25 mm)に対して焼付き試験を行った。摩擦熱衝撃試験機は、ラック71に重り72を落下させることによりピニオン73を回動させ、試験片74に噛み込み材75(材質:軟鋼)を強く接触させるものである。焼付きの程度を焼付き面積率により以下の通り評価した。焼付き面積率が小さいほど耐焼付き性(耐事故性)が良い。
○:焼付きが少ない(焼付き面積率が40%未満)。
△:焼付きが多い(焼付き面積率が40%以上60%未満)。
×:焼付きが著しい(焼付き面積率が60%以上)。
2・・・内層
10・・・圧延用遠心鋳造複合ロール
21・・・胴芯部
22,23・・・軸部
30・・・遠心鋳造用円筒状鋳型
31,41,51・・・鋳型本体
32,33,42,52・・・砂型
40・・・静置鋳造用上型
50・・・静置鋳造用下型
60,60a,60b,60c・・・キャビティ
100・・・静置鋳造用鋳型
Claims (5)
- 外層と内層とが溶着一体化してなる圧延用遠心鋳造複合ロールであって、
前記外層が、質量基準で1.70~2.70%のCと、0.3~3%のSiと、0.1~3%のMnと、1.1~3.0%のNiと、4.0~10%のCrと、2.0~7.5%のMoと、3~6.0%のVと、0.1~2%のWと、0.2~2%のNbと、0.01~0.2%のBと、0.01~0.1%のNとを含有し、残部がFe及び不可避的不純物からなるFe基合金からなり、
前記内層がダクタイル鋳鉄からなることを特徴とする圧延用遠心鋳造複合ロール。 - 請求項1に記載の圧延用遠心鋳造複合ロールにおいて、前記外層の廃却径における円周方向の圧縮残留応力が150~350 MPaであることを特徴とする圧延用遠心鋳造複合ロール。
- 請求項1又は2に記載の圧延用遠心鋳造複合ロールにおいて、前記外層の初径におけるショア硬さが70~90であることを特徴とする圧延用遠心鋳造複合ロール。
- 外層と内層とが溶着一体化してなる圧延用遠心鋳造複合ロールを製造する方法であって、
前記外層が、質量基準で1.70~2.70%のCと、0.3~3%のSiと、0.1~3%のMnと、1.1~3.0%のNiと、4.0~10%のCrと、2.0~7.5%のMoと、3~6.0%のVと、0.1~2%のWと、0.2~2%のNbと、0.01~0.2%のBと、0.01~0.1%のNとを含有し、残部がFe及び不可避的不純物からなるFe基合金からなり、
前記内層がダクタイル鋳鉄からなり、
回転する遠心鋳造用円筒状鋳型で前記外層を遠心鋳造する工程、及び前記外層のキャビティに前記内層用溶湯を鋳込む工程を有し、
前記内層の鋳造後又は鋳造中に、前記外層をオーステナイト化温度以上に再度加熱し、
再加熱温度から600℃までの間を10~60℃/hrの冷却速度で冷却することを特徴とする圧延用遠心鋳造複合ロールの製造方法。 - 請求項4に記載の圧延用遠心鋳造複合ロールの製造方法において、前記遠心鋳造複合ロールを600℃から常温~450℃まで冷却した後、500~550℃の温度で焼戻処理を行うことを特徴とする圧延用遠心鋳造複合ロールの製造方法。
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Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN114561601A (zh) * | 2022-02-28 | 2022-05-31 | 连云港德耀机械科技有限公司 | 一种轧辊用高速合金钢及其制备方法 |
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Families Citing this family (4)
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US11628481B2 (en) * | 2019-04-03 | 2023-04-18 | Nippon Steel Rolls Corporation | Centrifugally cast composite roll for rolling and method of manufacturing the same |
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Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06179947A (ja) | 1992-12-15 | 1994-06-28 | Kawasaki Steel Corp | 遠心鋳造製複合ロール |
JPH0860289A (ja) | 1994-08-24 | 1996-03-05 | Nippon Steel Corp | 遠心鋳造複合ロール |
JPH1143736A (ja) * | 1997-07-24 | 1999-02-16 | Kubota Corp | 耐肌荒れ性にすぐれる黒鉛晶出ハイス系鋳鉄材 |
JP2000160277A (ja) * | 2000-01-01 | 2000-06-13 | Kubota Corp | 複合ロール |
WO2015045985A1 (ja) | 2013-09-25 | 2015-04-02 | 日立金属株式会社 | 遠心鋳造製熱間圧延用複合ロール |
WO2015045720A1 (ja) | 2013-09-25 | 2015-04-02 | 日立金属株式会社 | 遠心鋳造製複合ロール及びその製造方法 |
WO2015045984A1 (ja) | 2013-09-25 | 2015-04-02 | 日立金属株式会社 | 遠心鋳造製熱間圧延用複合ロール |
JP2015205342A (ja) | 2014-04-11 | 2015-11-19 | 日立金属株式会社 | 遠心鋳造製熱間圧延用複合ロール |
JP2016180168A (ja) * | 2015-03-25 | 2016-10-13 | 日立金属株式会社 | 連続鋳掛け肉盛鋳造製圧延用複合ロール |
Family Cites Families (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3019240B2 (ja) * | 1992-11-11 | 2000-03-13 | 川崎製鉄株式会社 | 遠心鋳造製複合ロール |
JP3438336B2 (ja) | 1994-07-07 | 2003-08-18 | Jfeスチール株式会社 | 高速度鋼系圧延用ロール外層材 |
CN100494447C (zh) * | 2007-12-04 | 2009-06-03 | 北京工业大学 | 一种离心复合改进型无限冷硬铸铁轧辊及其制备方法 |
KR101956652B1 (ko) * | 2011-09-21 | 2019-03-11 | 히타치 긴조쿠 가부시키가이샤 | 열간 압연용 원심 주조 복합 롤 및 그 제조 방법 |
ES2572528T3 (es) * | 2011-10-19 | 2016-06-01 | Jfe Steel Corporation | Material de capa de superficie de rodillo para laminación en caliente con resistencia a la fatiga excelente producido mediante colada centrífuga, y rodillo de material compuesto para laminación en caliente producido a través de colada centrífuga |
JP5423930B2 (ja) * | 2011-11-21 | 2014-02-19 | 日立金属株式会社 | 遠心鋳造製複合圧延ロール及びその製造方法 |
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 |
US9358758B2 (en) * | 2013-05-02 | 2016-06-07 | Hitachi Metals, Ltd. | Centrifugally cast hot-rolling composite roll |
MX2016016893A (es) * | 2014-06-27 | 2017-03-27 | Jfe Steel Corp | Rodillo de calibre de colada centrifuga para tren de laminacion en caliente. |
JP6948556B2 (ja) * | 2016-03-31 | 2021-10-13 | 日立金属株式会社 | 遠心鋳造製熱間圧延用複合ロールの製造方法 |
US11052440B2 (en) | 2016-03-31 | 2021-07-06 | Hitachi Metals, Ltd. | Outer layer of rolling roll and composite roll for rolling |
-
2019
- 2019-08-07 WO PCT/JP2019/031259 patent/WO2020032144A1/ja unknown
- 2019-08-07 KR KR1020217001433A patent/KR20210040940A/ko not_active Application Discontinuation
- 2019-08-07 US US17/258,492 patent/US11389847B2/en active Active
- 2019-08-07 CN CN201980051241.XA patent/CN112512709B/zh active Active
- 2019-08-07 BR BR112020026751-1A patent/BR112020026751A2/pt unknown
- 2019-08-07 EP EP19846099.0A patent/EP3821992B1/en active Active
- 2019-08-07 JP JP2020535858A patent/JP7400718B2/ja active Active
Patent Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH06179947A (ja) | 1992-12-15 | 1994-06-28 | Kawasaki Steel Corp | 遠心鋳造製複合ロール |
JPH0860289A (ja) | 1994-08-24 | 1996-03-05 | Nippon Steel Corp | 遠心鋳造複合ロール |
JPH1143736A (ja) * | 1997-07-24 | 1999-02-16 | Kubota Corp | 耐肌荒れ性にすぐれる黒鉛晶出ハイス系鋳鉄材 |
JP2000160277A (ja) * | 2000-01-01 | 2000-06-13 | Kubota Corp | 複合ロール |
WO2015045985A1 (ja) | 2013-09-25 | 2015-04-02 | 日立金属株式会社 | 遠心鋳造製熱間圧延用複合ロール |
WO2015045720A1 (ja) | 2013-09-25 | 2015-04-02 | 日立金属株式会社 | 遠心鋳造製複合ロール及びその製造方法 |
WO2015045984A1 (ja) | 2013-09-25 | 2015-04-02 | 日立金属株式会社 | 遠心鋳造製熱間圧延用複合ロール |
JP2015205342A (ja) | 2014-04-11 | 2015-11-19 | 日立金属株式会社 | 遠心鋳造製熱間圧延用複合ロール |
JP2016180168A (ja) * | 2015-03-25 | 2016-10-13 | 日立金属株式会社 | 連続鋳掛け肉盛鋳造製圧延用複合ロール |
Non-Patent Citations (1)
Title |
---|
See also references of EP3821992A4 |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN114561601A (zh) * | 2022-02-28 | 2022-05-31 | 连云港德耀机械科技有限公司 | 一种轧辊用高速合金钢及其制备方法 |
CN115896636A (zh) * | 2022-12-22 | 2023-04-04 | 石家庄石特轧辊有限公司 | 一种高硬度轧辊的制备方法 |
Also Published As
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US20210154712A1 (en) | 2021-05-27 |
JPWO2020032144A1 (ja) | 2021-08-10 |
CN112512709B (zh) | 2023-06-02 |
EP3821992A1 (en) | 2021-05-19 |
KR20210040940A (ko) | 2021-04-14 |
EP3821992B1 (en) | 2023-01-18 |
JP7400718B2 (ja) | 2023-12-19 |
EP3821992A4 (en) | 2021-05-19 |
US11389847B2 (en) | 2022-07-19 |
BR112020026751A2 (pt) | 2021-03-30 |
CN112512709A (zh) | 2021-03-16 |
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