EP2979774A1 - Verfahren zur herstellung von ringförmigen formkörpern - Google Patents

Verfahren zur herstellung von ringförmigen formkörpern Download PDF

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Publication number
EP2979774A1
EP2979774A1 EP14775622.5A EP14775622A EP2979774A1 EP 2979774 A1 EP2979774 A1 EP 2979774A1 EP 14775622 A EP14775622 A EP 14775622A EP 2979774 A1 EP2979774 A1 EP 2979774A1
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EP
European Patent Office
Prior art keywords
annular
formed body
annular formed
strain
forging
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP14775622.5A
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English (en)
French (fr)
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EP2979774A4 (de
EP2979774B1 (de
Inventor
Hiroaki Kikuchi
Hideo Takizawa
Yuji Ishiwari
Jun Ohsone
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Proterial Ltd
Original Assignee
Hitachi Metals Ltd
Hitachi Metals MMC Superalloy Ltd
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Publication of EP2979774A1 publication Critical patent/EP2979774A1/de
Publication of EP2979774A4 publication Critical patent/EP2979774A4/de
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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B5/00—Extending closed shapes of metal bands by rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
    • B21K21/00—Making hollow articles not covered by a single preceding sub-group
    • B21K21/06—Shaping thick-walled hollow articles, e.g. projectiles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21H—MAKING PARTICULAR METAL OBJECTS BY ROLLING, e.g. SCREWS, WHEELS, RINGS, BARRELS, BALLS
    • B21H1/00—Making articles shaped as bodies of revolution
    • B21H1/06—Making articles shaped as bodies of revolution rings of restricted axial length
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
    • B21K1/00—Making machine elements
    • B21K1/28—Making machine elements wheels; discs
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
    • B21K1/00—Making machine elements
    • B21K1/76—Making machine elements elements not mentioned in one of the preceding groups
    • B21K1/761—Making machine elements elements not mentioned in one of the preceding groups rings
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
    • B21K3/00—Making engine or like machine parts not covered by sub-groups of B21K1/00; Making propellers or the like
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
    • 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
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon

Definitions

  • the present invention relates to a method for manufacturing an annular formed body, which is used as a stock in producing an annular product such as a turbine disk for aircraft engines, for example.
  • the turbine disk is an annular member having a through-hole and is configured to rotate together with plural turbine blades, which are arranged on the outer circumferential side thereof.
  • turbine disks have superior low cycle fatigue characteristics.
  • turbine disks it is necessary for turbine disks to have high creep strength characteristics because centrifugal force is applied to the outer circumferential portion due to the high-speed rotation around the axis under high temperatures.
  • turbine disks have a high tensile strength and a high yield strength.
  • annular formed bodies to be used for turbine disks are produced and output by forging a material with a high heat resistance constituted by a Ni-based superalloy and cutting the obtained annular forged body, as discussed in Patent Documents 1 and 2, for example. More specifically, strain is imparted to an annular formed body and crystal grains of the material are refined by forging, and thereby the tensile strength, the fatigue strength, and the like are improved.
  • Non-Patent Document 1 a large hydraulic-control forging press with a capacity of several tens of thousands of tons becomes necessary (e.g., see Non-Patent Document 1).
  • a method of forming an annular formed body by ring rolling may be used instead of molding an annular formed body by using a forging press.
  • the cost of equipment can be reduced, and it becomes easy to responsively produce large annular formed bodies.
  • the anisotropy of mechanical characteristics (strength characteristics) more easily occur in ring-rolled products than in press-forged products, and thus, ring rolling is not suitable for production of products that require the isotropy of mechanical characteristics such as turbine disks.
  • a method in which an annular formed body is molded by a combination of a forging press and ring rolling may be used; however, if this method is used, a problem may arise such that it becomes necessary to further carry out final forging after the ring rolling to obtain a desired uniform and fine structure, that the production processes may thus become complex, and that the production costs may become high.
  • Patent Document 3 a method is presented in which a forging process and a ring rolling process are used in combination, and in the forging process, hot forging is carried out a plurality of times in which strain for a forged body in the circumferential direction ⁇ 1, strain for the forged body in the height direction ⁇ h, and a strain ratio between these values ⁇ h/ ⁇ 1 are controlled to appropriate values, which thereby enables production of an annular formed body having a fine crystal structure with an excellent uniformity being secured at low costs.
  • Non-Patent Document 1 " Year 2002 Research Report - Report Regarding Development of innovative Members Using Ultra-Large Forging Press Machine", (New Energy and Industrial Technology Development Organization, March 2003, pp. 10-11 and pp. 37-41 )
  • annular formed bodies discussed in Patent Document 3, and as a result, it has been concluded that indeed, an annular formed body with fine crystal grains with a uniform grain size can be obtained by carrying out hot forging in which strain for a forged body in the circumferential direction ⁇ 1, strain for the forged body in the height direction ⁇ h, and a strain ratio between these values ⁇ h/ ⁇ 1 are controlled to appropriate values; however, in producing large, thick annular formed bodies, for example, the grain sizes of the annular formed bodies are not uniform in some cases due to uneven operation conditions and the like.
  • the present invention has been made in consideration of these circumstances, and an object of the present invention is to provide a method for manufacturing an annular formed body capable of producing annular formed bodies having excellently high mechanical strengths while ensuring the uniformity of their structure stably and at low cost.
  • a method for manufacturing an annular formed body includes a forging step of forging an alloy piece to provide a forged body having a disc shape, and a ring rolling step of ring-rolling an annular intermediate body prepared by forming a through-hole in the forged body to provide an annular formed body and is characterized in that the forging step comprises at least two of hot forging steps, each of the hot forging steps being carried out under conditions that a strain rate is at most 0.5 s -1 , an absolute value ⁇ 1 of strain to the forged body in its circumferential direction is at least 0.3, an absolute value ⁇ h of strain to the forged body in its height direction is at least 0.3, and a ratio ⁇ h/ ⁇ 1 between the absolute values of strain is within a range from 0.4 to 2.5.
  • the strain rate in the forging step is at most 0.5 s -1 .
  • the temperature inside the forged body is excessively increased due to the processing heat (i.e., a phenomenon known as "heat build-up") which coarsens the crystal grains inside the forged body.
  • the crystal grains inside the forged body cannot be refined, because sufficient strain cannot be imparted to the inside of the forged body.
  • the strain rate is controlled to be within a range of 0.5 s -1 or less, and thus, the difference between the temperature on the surface of the forged body and the temperature in the inside thereof during the forging can be smaller, allowing the structure to be more uniform.
  • the strain rate in the forging step is preferably at most 0.15 s -1 .
  • strain rate s - 1 2 / 3 ⁇ ⁇ h 2 + ⁇ ⁇ 2 + - ⁇ h - ⁇ ⁇ 2 forging time s
  • the absolute value ⁇ 1 of the strain in the circumferential direction is set at a large value of at least 0.3, and thus, the amount of strain in the circumferential direction to be imparted to the annular intermediate body in the ring rolling step can be relatively reduced. Furthermore, because the absolute value ⁇ h of the strain to be imparted in the height direction is set at a large value of 0.3 or more, the strain to be imparted in the height direction, which is difficult to impart by ring rolling, can be securely imparted by a sufficient amount.
  • the working ratio in the ring rolling step can be lowered, the anisotropy of the strength properties of the annular formed body is suppressed while the isotropy is increased, and as a result, a fine crystal structure can be obtained in which sufficient uniformity is secured.
  • the ratio ⁇ h/ ⁇ 1 denotes the balance among the directions of the strain to be imparted, and is an index for controlling the variation of relative positions in the material before and after the process.
  • the corresponding numerical value necessarily becomes "0" or close to "0" due to the production method, and thus, it is essential to appropriately set the ratio of strain to be imparted in the height direction in the forging step in order to suppress the anisotropy; however, if the ratio ⁇ h/ ⁇ 1 is lower than 0.4, the effect thereof may be insufficient.
  • the ratio ⁇ h/ ⁇ 1 exceeds 2.5, the distribution of the strain to be imparted in the height direction may become excessive, the plastic flow may thus become instable, and as a result, the axial symmetry, which is essential in imparting uniformity, may degrade.
  • the ratio ⁇ h/ ⁇ 1 between the absolute values of strain is controlled to be within a range from 0.4 to 2.5, and thereby stabilizing the plastic flow and securing the axial symmetry to make the structure uniform.
  • hot rolling may be carried out so that an absolute value ⁇ 2 of strain to the annular formed body in its circumferential direction of at least 0.5 can be imparted to the annular formed body, and thus, the grain size in a product region of the annular formed body can be an ASTM grain size number of at least 8.
  • the crystal grains in the product region of the annular formed body to be processed and machined into a product is securely refined to an ASTM grain size number of at least 8. Accordingly, the mechanical strengths of the product obtained from the annular formed body can be securely increased.
  • ASTM grain size number is determined in conformity to the standards defined by ASTM E122 by the American Society for Testing and Materials (ASTM).
  • a difference among grain sizes in a product region of a cross section of the annular formed body along a direction including an axis of the annular formed body is within a range of ⁇ 2 by ASTM grain size numbers.
  • a grain size of the forged body in the forging step may be controlled to an ASTM grain size number of at least 7.
  • the grain size of the forged body can be refined to an ASTM grain size number of at least 7.
  • the structure of the annular formed body can be refined while the amount of the strain to be imparted in the subsequent ring rolling step is reduced.
  • the annular intermediate body may be formed so that a ratio T/H between a thickness T of the annular intermediate body in its radial direction and a height H of the annular intermediate body in its axial direction is controlled to be within a range from 0.6 to 2.3, and then the annular intermediate body may be ring-rolled so that a difference between grain sizes at plural equivalent positions of the annular formed body uniformly arranged along its circumferential direction is within ⁇ 1.5 by ASTM grain size numbers.
  • the above-described ratio T/H is controlled to be within the range of 0.6 to 2.3, stability of rolling can be obtained, which is essential to impart uniformity. Specifically, in a region in which the ratio T/H is below 0.6, the area of contact among both rolls used in the rolling (a main roll and a mandrel roll) and the material becomes large, and thus, the degree of influence from heat release relatively increases, and as a result, it becomes difficult to obtain the circumferential uniformity. In contrast, as the ratio T/H increases, it becomes easier for buckling to occur. Specifically, in a region in which the ratio T/H is greater than 2.3, the above-described tendency becomes greater, and it thereby becomes difficult to obtain the circumferential uniformity.
  • the alloy piece may be made of a Ni-based alloy.
  • the forging step is preferably carried out at a temperature from 950°C to 1,075°C, or the ring rolling step is preferably carried out at a temperature from 900°C to 1,050°C.
  • a method can be provided for manufacturing an annular formed body capable of producing annular formed bodies having superior high mechanical strengths while ensuring uniformity of their structure stably and at low costs.
  • An annular formed body 10 according to the present embodiment is used as a stock for molding turbine disks of engines of aircraft.
  • the annular formed body 10 has through-holes and has an annular shape around an axis O, and is provided with a main body 11, an inner protrusion 12 that protrudes from the main body 11 toward a radial inward direction, and an outer protrusion 13 that protrudes from the main body 11 toward a radial outward direction.
  • the annular formed body 10 is constituted by a Ni-based superalloy having excellent heat resistance, and in the present embodiment, the annular formed body 10 is constituted by a Ni-based alloy "Alloy718".
  • the Ni-based alloy Alloy718 has an alloy composition including 50.00 to 55.00% by mass of Ni, 17.0 to 21.0% by mass of Cr, 4.75 to 5.60% by mass of Nb, 2.8 to 3.3% by mass of Mo, 0.65 to 1.15% by mass of Ti, 0.20 to 0.80% by mass of Al, and 0.01 to 0.08% by mass of C, and the balance of Fe with inevitable impurities.
  • the grain size of the structure in a desired region (not shown) to be machined into a turbine disk (i.e., product) (hereinbelow, this region will be referred to as a "product region") is an ASTM grain size number of at least 8.
  • virtual planes VS1, VS2 illustrated in FIG. 2 are cross sections of the annular formed body 10 along a direction including an axis O of the annular formed body 10, i.e., the virtual planes VS1, VS2 are set at mutually equivalent positions determined by evenly dividing the annular formed body 10 along the circumferential direction.
  • the annular formed body 10 ensures the uniformity because the difference between the grain sizes in the structure of a product region in the cross section of the virtual plane VS1 (or VS2) is within ⁇ 2 by the difference in the ASTM grain size number,.
  • the difference in the sizes of the crystal grain at the mutually equivalent positions of the annular formed body 10 in the circumferential direction, i.e., the difference between the grain size in the virtual plane VS1 and the grain size in the virtual plane VS2 is within ⁇ 1.5 by the difference by ASTM grain size numbers.
  • molten metal of the Ni-based alloy Alloy718 is prepared by smelting.
  • a melted raw material is prepared so that its components are within the above-described ranges of the components of the Ni-based alloy Alloy718, and an ingot is produced by performing vacuum induction melting (VIM).
  • VIM vacuum induction melting
  • ESR electro slag remelting
  • this ingot is remelted by electro slag remelting (ESR) to produce an ingot again.
  • ESR electro slag remelting
  • VAR vacuum arc remelting
  • hot forging is performed to produce a cylindrical billet (alloy piece).
  • the billet is formed so as to have a diameter of 7 to 12 inches (more specifically, 165 to 315 mm), for example.
  • the structure of the produced billet is of ASTM No. 6, approximately, by ASTM grain size numbers.
  • the billet is forged so that the billet is pressed in the direction of the axis of the billet to prepare a forged body having a disc-like shape.
  • hot forging is performed at least twice so that an absolute value ⁇ 1 of strain to the forged body in the circumferential direction is 0.3 or higher, an absolute value ⁇ h of strain to the forged body in the height direction is 0.3 or higher, and a ratio ⁇ h/ ⁇ 1 between the absolute values of the strain is within a range of 0.4 to 2.5 in a state in which the billet has been heated to a temperature ranging from 950 to 1,075 °C, for example.
  • the strain rate in the hot forging in the forging step S2 is set to 0.5 s -1 or less.
  • the hot forging in the forging step S2 is implemented by using a hydraulic-control forging press apparatus.
  • the hydraulic-control forging press apparatus is capable of adjusting the strain rate by hydraulic control during forging within the above-described ranges with a high accuracy.
  • the strain rate in the hot forging in the forging step S2 is set at 0.01 s -1 or greater.
  • the absolute value ⁇ 1 of the amount of strain imparted in the circumferential direction is set at 0.3 or more.
  • the absolute value ⁇ h of the amount of strain imparted in the height direction along the axis direction of the forging is set to be greater than 0.3.
  • the height of the forged body is adjusted by the forging step S2 to approximately 60 mm to 500 mm, for example.
  • the forging step described above sufficient strain is imparted to the forged body and the grain size of the forged body is refined to ASTM No. 7 or more by ASTM grain size numbers.
  • a through-hole having a circular cross section is formed in the center of the obtained forged body by using a water cutter. Furthermore, intermediate ring rolling is performed after forming the through-hole where necessary. By performing the perforation and intermediate ring rolling step S3, an annular intermediate body 20 is produced.
  • the annular intermediate body 20 has a circumferentially perpendicular cross section with a substantially polygonal shape as illustrated in FIG. 4 , and includes a base portion 21 having a circumferentially perpendicular cross section with a substantially polygonal shape and an upper surface and a lower surface extending in a direction substantially perpendicular to an axis O; an inner protrusion 22 radially and inwardly protruding from the base portion 21; and an outer protrusion 23 radially and outwardly protruding from the base portion 21.
  • the annular intermediate body 20 is ring-rolled.
  • the ring rolling is implemented by hot rolling performed at a temperature in a range of 900 °C to 1,050 °C, for example.
  • a ring rolling apparatus 30 includes a main roll 40 arranged on an outer circumferential side of the annular intermediate body 20; a mandrel roll 50 arranged on an inner circumferential side of the annular intermediate body 20; and a pair of axial rolls 31, 32 that contact end surfaces (in the present embodiment, the upper surface and the lower surface of the base portion 21) of the annular intermediate body 20 in the direction of the axis O.
  • the main roll 40 and the mandrel roll 50 are arranged so that the rotation axes thereof are in parallel to each other and configured to nip and press the annular intermediate body 20 from the inner circumferential side and the outer circumferential side thereof and roll the annular intermediate body 20 while circumferentially turning the annular intermediate body 20.
  • the pair of axial rolls 31, 32 is configured to nip and press the annular intermediate body 20 in the direction of the axis O and control the dimension of the annular intermediate body 20 in the height direction.
  • an accommodation recess 41 in which a part of the annular intermediate body 20 can be accommodated is arranged on an outer circumferential portion of the main roll 40, and in the present embodiment, the accommodation recess 41 has a depth sufficient to accommodate the outer protrusion 23, the base portion 21, and an outer circumferential portion of the inner protrusion 22 of the annular intermediate body 20. Furthermore, on a bottom 41A of this accommodation the recessed portion 41, a first molding groove 42 for molding the outer protrusion 13 of the annular formed body 10 is formed so as to be grooved in a radially inward direction in relation to the main roll 40 (rightward in FIG. 6 ). The first molding groove 42 has a depth equivalent to the height of protrusion of the outer protrusion 13 to be molded.
  • an engagement portion 51 which can engage with the main roll 40 in an inside of the accommodation recess 41, is arranged in the outer circumferential portion of the mandrel roll 50, while on an outer peripheral surface of the engagement portion 51, a second molding groove 52 for molding the inner protrusion 12 of the annular formed body 10 is formed so as to be grooved in a radially inward direction in relation to the mandrel roll 50 (leftward in FIG. 6 ).
  • the second molding groove 52 has a depth equivalent to the height of protrusion of the inner protrusion 12 to be molded.
  • the main roll 40 and the mandrel roll 50 configured as described above operate so as to come close to each other, and thereby the annular intermediate body 20 is nipped and pressed between the main roll 40 and the mandrel roll 50.
  • the main roll 40 and the mandrel roll 50 come close to each other while the main roll 40 is turned around the rotation axis of the main roll 40, and thereby, the annular intermediate body 20 is turned around the axis O due to frictional resistance generated between the annular intermediate body 20 and the main roll 40.
  • the mandrel roll 50 is configured rotatable around the rotation axis of the mandrel roll 50, and is drivenly rotated due to frictional resistance generated between the annular intermediate body 20 and the mandrel roll 50.
  • the annular intermediate body 20 plastically deforms as it is filled into the insides of the accommodation recess 41 and the first molding groove 42 of the main roll 40 and the inside of the second molding groove 52 of the mandrel roll 50, and thereby the annular formed body 10 is molded.
  • the inner protrusion 12 of the annular formed body 10 is plastically deformed along the shape of the second molding groove 52.
  • the outer protrusion 13 is plastically deformed along the shape of the first molding groove 42.
  • the annular intermediate body 20 is plastically deformed so as to extend in the circumferential direction and the inner diameter and the outer diameter thereof are enlarged, and thereby the annular formed body 10 illustrated in FIG. 7 is produced.
  • an absolute value ⁇ 2 of the strain in the annular formed body 10 in the circumferential direction of 0.5 or more is imparted.
  • the hot rolling is performed at least once or more to set the total value of strain absolute values ⁇ 2 to be within a range of 0.5 to 1.3.
  • the annular formed body 10 produced in the above-described manner is subjected to adjustment of properties by heat treatment, molded into a final shape by cutting, to be formed into a turbine disk for engines for aircraft.
  • the strain rate in the forging step S2 for producing the forged body by forging the billet is 0.5 s -1 or less, and thereby, excessive rise of temperature inside the forged body (a phenomenon known as "heat build-up", which may occur due to processing heat, can be prevented. Accordingly, the difference between the temperature on the surface of the forged body and that in the inside thereof during the forging can be controlled to be small, and thereby the structure of the forged body can be unified. In order to reliably obtain these effects, it is preferable that the strain rate in the forging step S2 be set at 0.15 s -1 or less.
  • a high value of 0.3 or more is set as the absolute value ⁇ 1 of the strain in the circumferential direction in the forging step S2
  • the ratio of the amount of the strain in the circumferential direction to be imparted to the annular intermediate body 20 in the ring rolling step S4 can be reduced.
  • a high value of 0.3 or more is set as the absolute value ⁇ h of the strain in the height direction, the amount of the strain in the height direction, which is otherwise difficult to impart, can be sufficiently imparted in the ring rolling step S4.
  • the working ratio in the ring rolling step S4 can be reduced, the anisotropy of the strength properties of the annular formed body 10 is suppressed while the isotropy is increased, and as a result, a fine crystal structure can be obtained in which sufficient uniformity is ensured.
  • the ratio ⁇ h/ ⁇ 1 between the absolute value ⁇ 1 of the strain in the circumferential direction and the absolute value ⁇ h of the strain in the height direction a sufficient ratio of the strain to be imparted in the height direction can be ensured, and as a result, the uniformity of the structure can be ensured even if sufficient strain cannot be imparted in the height direction in the subsequent ring rolling step S4.
  • the ratio ⁇ h/ ⁇ 1 is 2.5 or less, the distribution in the height direction would not be excessive, and thus, the plastic flow becomes stable, and thereby the axial symmetry of the plastic flow essential for imparting uniformity can be ensured.
  • the ratio ⁇ h/ ⁇ 1 between the absolute values of the strain be 0.6 to 2.1. Accordingly, the axial symmetry of the plastic flow can be increased, and thus, the uniformity of the structure can be more reliably ensured.
  • the absolute value ⁇ 1 of the amount of strain to be imparted in the circumferential direction is set at 0.3 or higher and the absolute value ⁇ h of the amount of strain to be imparted in the height direction along the axis of the forged body is set at 0.3 or higher in the forging step S2, coarsening of the crystal grains, which may occur due to rise of temperature inside the forged body because of the processing heat, can be prevented.
  • the crystal grains in the product region of the annular formed body 10 is securely refined to an ASTM grain size number of at least 8. Accordingly, the mechanical strengths of the product obtained from the annular formed body 10 are reliably increased.
  • ⁇ 2 be 1.3 or less.
  • the grain size of the annular formed body 10 is preferably an ASTM grain size number of 8 to 13. Thus, the mechanical strengths of the product obtained from the annular formed body 10 can be reliably increased.
  • the grain size of the forged body can be refined to an ASTM grain size number of at least 7.
  • the structure of the annular formed body 10 can be refined while the amount of the strain to be imparted in the subsequent ring rolling step is reduced.
  • the ring rolling is performed after molding the annular intermediate body 20 so that the ratio T/H between the radial thickness and the height H of the annular intermediate body 20 is within a range from 0.6 to 2.3, the difference between the grain sizes at the mutually equivalent positions on the annular formed body 10 along the circumferential direction can be reduced within ⁇ 1.5 by ASTM grain size numbers.
  • the annular formed body 10 obtained by molding the annular intermediate body 20 sufficiently high uniformity of the grain sizes in the circumferential direction can be ensured.
  • the above-described ratio T/H is controlled to be within the range of 0.6 to 2.3, stability of rolling can be obtained, which is essential to impart uniformity. Specifically, in a region in which the ratio T/H is below 0.6, the area of contact among both rolls used in the rolling (the main roll 40 and the mandrel roll 50) and the material becomes large, and thus, the degree of influence from heat release relatively increases, and as a result, it becomes difficult to obtain the circumferential uniformity. In contrast, as the ratio T/H becomes higher, it becomes easier for buckling to occur. Specifically, in a region in which the ratio T/H is higher than 2.3, the above-described tendency becomes higher, and it thereby becomes difficult to obtain the circumferential uniformity.
  • annular formed bodies As described above, according to the method for manufacturing an annular formed body which is the present embodiment, it is made possible to produce annular formed bodies, in which the uniformity of the structure is ensured and the mechanical strengths are sufficiently high, in a reliable manner and at low costs.
  • the present invention is not limited to the embodiment described above, and can also be implemented by various modifications and alterations within a scope not exceeding the gist of the present invention.
  • the shape of the annular formed body 10 and the annular intermediate body 20 is not limited to the present embodiment, and the design can be modified as necessary in consideration of the shape of the annular product such as a turbine disk to be produced.
  • the annular formed body 10 and the annular intermediate body 20 are constituted by Ni-base alloy Alloy718 as described above; however, the material of the annular formed body 10 and the annular intermediate body 20 is not limited to this, and the annular formed body 10 and the annular intermediate body 20 may be constituted of other materials (e.g., Waspaloy (registered trademark) (United Technology Inc.), Alloy720, Co-based alloys, and Fe-based alloys).
  • Waspaloy registered trademark
  • Alloy720 Co-based alloys
  • Fe-based alloys Fe-based alloys
  • molten metal for the Ni-based alloy, Alloy718, is smelted and the billet is produced by casting, but the present invention is not limited to this.
  • a billet may be produced by powder molding and the produced billet is then subjected to the forging step and the ring rolling step.
  • the billet may be produced by double melting (VIM + ESR or VIM + VAR) instead of producing the billet by the above-described triple melting.
  • the present embodiment includes the perforation step for forming the through-hole in the center of the disc-like forged body by using the water cutter, but the present invention is not limited to this.
  • the through-hole may be formed by means other than the water cutter.
  • the through-hole may be formed at the time of the forging, and thus, the perforation step may be omitted.
  • the perforation may be performed in the course of the forging step by using the water cutter or the like.
  • annular formed body 10 is molded by the ring rolling step S4 illustrated in FIG. 3 and before the heat treatment step S5 illustrated in FIG. 3 is performed, additional processes such as partial forging may be performed in order to impart a shape to the annular formed body 10 or to adjust its dimensions.
  • the mutually equivalent positions (the virtual planes VS1, VS2) on the annular formed body 10 determined by evenly dividing the annular formed body 10 into halves in the circumferential direction are used as the reference positions for controlling the difference between the grain size on the virtual plane VS1 and the grain size on the virtual plane VS2 within ⁇ 1.5 by ASTM grain size numbers; however, the number of the virtual planes used for the comparison is not limited to two.
  • the difference between the grain sizes at the mutually equivalent positions determined by evenly dividing the annular formed body 10 into threes along the circumferential direction may be controlled to be within ⁇ 1.5 by ASTM grain size numbers instead of determining the difference between the grain sizes at the mutually equivalent positions determined by evenly dividing the annular formed body 10 into twos.
  • the circumferential positions in the annular formed body 10 at which the mutually equivalent positions are to be set are not limited to those described above in the present embodiment.
  • molten metal for the Ni-based alloy, Alloy718, was smelted. Specifically, the melting raw material was prepared so that it would satisfy the condition for the range of components of the Ni-based alloy, Alloy718, mentioned in the embodiment described above. Then triplex melting was carried out on this molten metal. Specifically, vacuum induction melting (VIM), electro slag remelting (ESR), and vacuum arc remelting (VAR) were carried out to produce a cylindrical billet with a diameter of 254 mm.
  • VIM vacuum induction melting
  • ESR electro slag remelting
  • VAR vacuum arc remelting
  • the billet was subjected to the forging step to prepare a disc-like forged body.
  • hot forging was performed twice in which the billet was heated to 1,000 °C.
  • the forging step was carried out under the following conditions illustrated in Table 1 with respect to the absolute value ⁇ 1 of strain to the forged body in the circumferential direction, the absolute value ⁇ h of strain to the forged body in the height direction, the ratio ⁇ h/ ⁇ 1 between the absolute values of the strain, and the strain rate.
  • the through-hole was formed by a water cutter in the center of the forged body to prepare an annular intermediate body 20.
  • the annular intermediate body 20 was molded so that the ratio T/H between its thickness T and its height H would be the value illustrated in Table 1.
  • the annular intermediate body 20 was subjected to ring rolling.
  • hot rolling was carried out twice in which the annular intermediate body 20 was heated to 1,000 °C.
  • the ring rolling was performed so that the total sum of the absolute value ⁇ 2 of the circumferential strain in the annular formed body 10 would satisfy the following conditions illustrated in Table 1 by performing the hot forging twice.
  • the annular formed body 10 was subjected to heat treatment.
  • a direct ageing material a material was prepared that had undergone an aging treatment under conditions of 718 °C/8 hours + 621 °C/8 hours + air cooling (A.C.).
  • A.C. As a solution aging material, a material was prepared that had undergone an aging treatment under conditions of 718 °C/8 hours + air cooling (A.C.) after solution treatment under conditions of 970 °C/1 hour + water quenching (W.Q.) performed after the ring rolling.
  • FIG. 8 illustrates the correlation between the tensile strength and the reduction
  • FIG. 9 illustrates the correlation between the yield strength and the reduction.
  • Examples 1 to 4 of the present invention in which the rates of strain in the forging step was 0.5 s -1 or less, the difference between the maximum grain size and the average grain size around the maximum grain size was small, and it was observed that the structures were sufficiently unified. It was estimated that the sufficiently unified structures were obtained due to the small difference between the temperature on the surface and the temperature in the inside of the forged body during the forging, which was achieved by controlling the strain rate being in the range of 0.5 s -1 or less. Note that in Examples 1, 2, and 4 of the present invention in which the strain rates were controlled to be within the range of 0.15 s -1 or less, the structures were better unified.
  • Example 1 of the present invention was better than Comparative Example 2 in terms of all of the tensile strength, the 0.2% yield strength, and the reduction.
  • Example 1 of the present invention the isotropy of the strength characteristics increased, and Example 1 of the present invention had a fine crystal grain structure in which sufficient structural uniformity was ensured.
  • annular formed bodies in which the uniformity of the structure is ensured and the mechanical strengths are sufficiently high can be produced stably and at low costs. Accordingly, the method for manufacturing an annular formed body of the present invention can be suitably used in production of turbine disks and the like of engines for aircraft.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Materials Engineering (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Forging (AREA)
  • Pistons, Piston Rings, And Cylinders (AREA)
  • Wire Processing (AREA)
  • Rolling Contact Bearings (AREA)
EP14775622.5A 2013-03-28 2014-03-28 Verfahren zur herstellung von ringförmig geformten körper Active EP2979774B1 (de)

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JP2013069205A JP6292761B2 (ja) 2013-03-28 2013-03-28 環状成形体の製造方法
PCT/JP2014/059277 WO2014157662A1 (ja) 2013-03-28 2014-03-28 環状成形体の製造方法

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RU2699428C1 (ru) * 2018-05-28 2019-09-05 Федеральное государственное автономное образовательное учреждение высшего образования "Уральский федеральный университет имени первого Президента России Б.Н. Ельцина" Способ ковки раскатных колец
EP3854901A4 (de) * 2018-09-19 2022-06-08 Hitachi Metals, Ltd. Verfahren zur herstellung von ringgewalztem material aus fe-ni-basierter super-hitzebeständiger legierung
EP3854902A4 (de) * 2018-09-19 2022-06-22 Hitachi Metals, Ltd. Verfahren zur herstellung von ringgewalztem material aus fe-ni-basierter super-hitzebeständiger legierung

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CN105436365B (zh) * 2015-12-08 2017-10-03 山西冠力法兰有限公司 应用于辗环设备生产平板类二合一锻件的模具及方法
JP6854484B2 (ja) * 2017-06-29 2021-04-07 大同特殊鋼株式会社 リング状素材の圧延方法
CN114682728A (zh) * 2017-11-17 2022-07-01 美题隆公司 用铍铜合金制作金属环的方法及金属环
RU2703764C1 (ru) * 2019-02-21 2019-10-22 Акционерное общество "Металлургический завод "Электросталь" Способ изготовления крупногабаритной кольцевой детали газотурбинного двигателя из жаропрочного сплава на никелевой основе
JP7121929B2 (ja) * 2019-12-25 2022-08-19 日立金属株式会社 リング圧延材の製造方法
RU2741046C1 (ru) * 2020-07-27 2021-01-22 Акционерное общество "Металлургический завод "Электросталь" Способ изготовления крупногабаритного сложноконтурного кольцевого изделия из жаропрочного сплава на никелевой основе
CN115156455A (zh) * 2022-08-09 2022-10-11 上海电气上重铸锻有限公司 一种带全截面凸台的圆环形或弧形锻件的锻造成形方法
CN115592055A (zh) * 2022-10-10 2023-01-13 江苏保捷锻压有限公司（Cn） 一种环状零件外径多台阶锻造工艺

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EP3854901A4 (de) * 2018-09-19 2022-06-08 Hitachi Metals, Ltd. Verfahren zur herstellung von ringgewalztem material aus fe-ni-basierter super-hitzebeständiger legierung
EP3854902A4 (de) * 2018-09-19 2022-06-22 Hitachi Metals, Ltd. Verfahren zur herstellung von ringgewalztem material aus fe-ni-basierter super-hitzebeständiger legierung

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ES2932530T3 (es) 2023-01-20
WO2014157662A1 (ja) 2014-10-02
MX2015013639A (es) 2016-06-02
CN105228771A (zh) 2016-01-06
JP2014188580A (ja) 2014-10-06
JP6292761B2 (ja) 2018-03-14
RU2015146287A (ru) 2017-05-04
EP2979774A4 (de) 2016-09-28
RU2631221C2 (ru) 2017-09-19
EP2979774B1 (de) 2022-11-16

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