WO2017204286A1 - ALLIAGE À BASE DE Ni POUR MATRICE DE FORGEAGE À CHAUD, MATRICE DE FORGEAGE À CHAUD L'UTILISANT ET PROCÉDÉ DE FABRICATION DE PRODUIT FORGÉ - Google Patents

ALLIAGE À BASE DE Ni POUR MATRICE DE FORGEAGE À CHAUD, MATRICE DE FORGEAGE À CHAUD L'UTILISANT ET PROCÉDÉ DE FABRICATION DE PRODUIT FORGÉ Download PDF

Info

Publication number
WO2017204286A1
WO2017204286A1 PCT/JP2017/019488 JP2017019488W WO2017204286A1 WO 2017204286 A1 WO2017204286 A1 WO 2017204286A1 JP 2017019488 W JP2017019488 W JP 2017019488W WO 2017204286 A1 WO2017204286 A1 WO 2017204286A1
Authority
WO
WIPO (PCT)
Prior art keywords
hot
die
based alloy
forging
alloy
Prior art date
Application number
PCT/JP2017/019488
Other languages
English (en)
Japanese (ja)
Inventor
翔悟 鈴木
友典 上野
宙也 青木
Original Assignee
日立金属株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 日立金属株式会社 filed Critical 日立金属株式会社
Priority to US16/304,075 priority Critical patent/US20200340081A1/en
Priority to JP2018519601A priority patent/JPWO2017204286A1/ja
Publication of WO2017204286A1 publication Critical patent/WO2017204286A1/fr

Links

Images

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J13/00—Details of machines for forging, pressing, or hammering
    • B21J13/02—Dies or mountings therefor
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
    • B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J3/00—Lubricating during forging or pressing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B21J5/02—Die forging; Trimming by making use of special dies ; Punching during forging
    • B21J5/025—Closed die forging
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/10—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 Ni-based alloy for hot dies, a hot forging die using the same, and a method for producing a forged product.
  • the forging material is heated to a predetermined temperature in order to reduce deformation resistance. Since a heat-resistant alloy has high strength even at high temperatures, a hot forging die used for forging requires high mechanical strength at high temperatures. Further, in hot forging, when the temperature of the hot forging die is lower than that of the forging material, the workability of the forging material is reduced due to heat removal. For example, a product made of a difficult-to-work material such as Alloy 718 or Ti alloy Forging is performed by heating a hot forging die together with the material. Accordingly, the hot forging die must have a high mechanical strength at a temperature equal to or close to the temperature at which the forging material is heated.
  • the hot forging referred to in the present invention includes hot die forging in which the temperature of the hot forging die is brought close to the temperature of the forging material and constant temperature forging in which the temperature is the same as that of the forging material.
  • the Ni-based superalloy described above is advantageous in that it has a high high temperature compressive strength, but in terms of oxidation resistance, a fine scale of nickel oxide scatters from the mold surface during cooling after heating in the atmosphere. Therefore, there is a risk of work environment deterioration and shape deterioration.
  • the problem of oxidation of the mold surface and the accompanying scattering of the scale is a big problem in maximizing the effect that it can be used in the atmosphere.
  • An object of the present invention is a Ni-based alloy for hot dies having high high temperature compressive strength and good oxidation resistance, and capable of suppressing deterioration of working environment and shape deterioration, and hot forging die using the same And a method for producing a forged product using the hot forging die.
  • the present inventor has studied the deterioration of the working environment and shape deterioration due to oxidation of the mold surface and the accompanying scale scattering, and has found a composition having high high temperature compressive strength and good oxidation resistance, and has reached the present invention. That is, the present invention is W: 7.0-12.0%, Mo: 4.0-11.0%, Al: 5.0-7.5%, Cr: 0.5-7.5%, the balance Is a Ni-based alloy for hot molds made of Ni and inevitable impurities. In the present invention, in addition to the above composition, 0.5 to 7.0% Ta can be further contained.
  • the present invention in addition to the above composition, Zr: 0.001 to 0.5%, Hf: 0.001 to 0.5%, rare earth element: 0.001 to 0.2%, Y: 0.0.
  • One or more elements selected from elements of 001 to 0.2% and Mg: 0.001 to 0.03% can be contained.
  • the 0.2% compressive strength at a test temperature of 1000 ° C. and a strain rate of 10 ⁇ 3 / sec is preferably 500 MPa or more. More preferably, the 0.2% compressive strength at a test temperature of 1100 ° C. and a strain rate of 10 ⁇ 3 / sec is 350 MPa or more.
  • the present invention is also a hot forging die using the Ni-based alloy for hot die.
  • an antioxidant coating layer is provided on at least one of the molding surface and the side surface of the hot forging die.
  • the present invention also includes a first step of heating the forging material and a second step of hot forging the forging material heated in the first step using the hot forging die.
  • This is a method for producing a forged product. More preferably, in the method for producing a forged product, the second step is performed by heating the hot forging die to 1000 ° C. or higher.
  • Ni-based alloy for hot dies having high high temperature compressive strength and good oxidation resistance By using the Ni-based alloy for hot dies having high high temperature compressive strength and good oxidation resistance according to the present invention, it is possible to suppress deterioration of the working environment and shape deterioration in hot forging.
  • the unit of chemical composition is mass%.
  • ⁇ W: 7.0 to 12.0%> W forms a solid solution in the austenite matrix and also forms a solid solution in the gamma prime phase ( ⁇ ′ phase) based on Ni 3 Al, which is a precipitation strengthening phase, to increase the high temperature strength of the alloy.
  • ⁇ ′ phase gamma prime phase
  • W crystallizes a body-centered cubic ⁇ - (Mo, W) phase consisting of a solid solution of W and Mo at the grain boundary to increase the grain boundary strength of the alloy and at the same time enhance the machinability of the alloy.
  • Mo, W body-centered cubic ⁇ - (Mo, W) phase consisting of a solid solution of W and Mo at the grain boundary to increase the grain boundary strength of the alloy and at the same time enhance the machinability of the alloy.
  • W has an action of reducing oxidation resistance.
  • the W content in the Ni-based alloy in the present invention is set to 7.0 to 12.0%.
  • a preferable lower limit for obtaining the effect of W more reliably is 10.0%, and a preferable upper limit of W is 11.0%.
  • Mo dissolves in the austenite matrix and also dissolves in the gamma prime phase based on Ni 3 Al, which is a precipitation strengthening phase, to increase the high temperature strength of the alloy.
  • Mo has the effect
  • the Mo content in the Ni-base superalloy according to the present invention is set to 4.0 to 11.0%.
  • the preferable lower limit of Mo when Ta is not added is preferably 7.0%, and more preferably 9.5%.
  • the upper limit of preferable Mo is 10.5, More preferably, it is 10.2%.
  • Al binds to Ni to precipitate a gamma prime phase composed of Ni 3 Al, increases the high temperature strength of the alloy, generates an alumina film on the surface of the alloy, and has an effect of imparting oxidation resistance to the alloy.
  • the Al content in the Ni-base superalloy according to the present invention is set to 5.0 to 7.5%.
  • a preferable lower limit for obtaining the effect of Al more surely is 5.5%, and more preferably 6.1%.
  • the upper limit of preferable Al is 6.7%, More preferably, it is 6.5%.
  • ⁇ Cr: 0.5-7.5%> Cr has the effect of promoting the formation of a continuous layer of alumina on or in the alloy surface and improving the oxidation resistance of the alloy. Therefore, it is necessary to add 0.5% or more of Cr.
  • Cr is added together with Al, W, and Mo, 3.0 to 7.5% of Cr achieves high compressive strength at 1000 ° C. as shown in Table 4 and FIG.
  • the Cr content is 3.0% or less, high compressive strength can be obtained even at 1000 to 1100 ° C.
  • the addition of Cr in a range exceeding 7.5% must be avoided because the compressive strength at 1000 ° C. or higher is lowered.
  • the addition of Cr is not necessarily disadvantageous for the high temperature strength.
  • 0.5 to 7.5% Cr is added together with Al, W, and Mo, the high temperature strength is rather increased, while maintaining the high temperature strength.
  • the fact that the oxidation resistance can be improved has been clarified by the present invention.
  • a preferable lower limit for obtaining the effect of Cr more reliably is 1.3%, and a preferable upper limit of Cr is 3.0%.
  • the Ni-base superalloy according to the present invention can contain Ta.
  • Ta is a solid solution in which Al sites are replaced with a gamma prime phase composed of Ni 3 Al to increase the high temperature strength of the alloy, and to improve the adhesion and oxidation resistance of the oxide film formed on the alloy surface, Has the effect of improving the oxidation resistance of the alloy.
  • the content of Ta is too large, there is also an effect of easily precipitating a harmful phase such as a TCP (Topologically Closed Packed) phase.
  • the Ta content when containing Ta in the present invention is 0.5 to 7.0%.
  • a preferable lower limit for obtaining the effect of Ta more reliably is 2.5%
  • a preferable upper limit of Ta is 6.5%.
  • the Ni-base superalloy according to the present invention can contain one or more elements selected from Zr, Hf, rare earth elements, Y and Mg. Zr, Hf, rare earth elements, and Y suppress diffusion of metal ions and oxygen at the grain boundary due to segregation at the grain boundary of the oxide film.
  • the suppression of the grain boundary diffusion reduces the growth rate of the oxide film, and improves the adhesion between the film and the alloy by changing the growth mechanism that promotes the peeling of the oxide film. That is, these elements have the effect of improving the oxidation resistance of the alloy by reducing the growth rate and improving the film adhesion described above.
  • Mg also forms S and sulfides that reduce the adhesion of the coating by segregating at the interface between the oxide coating and the alloy and inhibiting their chemical bonds, and improves adhesion by preventing S segregation. And has the effect of improving the oxidation resistance of the alloy.
  • La is preferably used. This is because La has a great effect of improving oxidation resistance.
  • La has an effect of preventing segregation of S in addition to the above-described suppression of diffusion, and since these effects are excellent, La is preferably selected from rare earth elements.
  • Y has the same effect as La, so addition of Y is also preferable, and it is particularly preferable to use two or more kinds including La and Y.
  • Hf or Zr is preferably used, and Hf is particularly preferably used.
  • Hf has a small effect of preventing segregation of S. Therefore, when Mg is added simultaneously with Hf, oxidation resistance is further improved. For this reason, it is more preferable to use two or more elements including Hf and Mg when the mechanical properties as well as the oxidation resistance are reduced.
  • the upper limit of each content of Zr and Hf in the present invention is 0.5%.
  • the upper limit with preferable content of each of Zr and Hf is 0.2%, More preferably, it is 0.1%. Since the rare earth element, Y has a higher effect of lowering the toughness than Zr and Hf, the upper limit of the content of each of these elements in the present invention is 0.2%, and the preferable upper limit is 0.1%.
  • the lower limit in the case of containing Zr, Hf, rare earth element, and Y is 0.001%.
  • Zr, Hf, rare earth elements, and the preferable lower limit to sufficiently exhibit the effect of Y is 0.005%, more preferably 0.01% or more.
  • Mg needs only to be contained in an amount necessary for forming the impurities S and sulfides contained in the alloy, the Mg content is set to 0.001 to 0.03%.
  • a preferable upper limit of Mg is 0.01%.
  • the lower limit is preferably 0.005%.
  • Ni is a main element constituting a gamma phase and constitutes a gamma prime phase together with Al, Ta, Mo, and W.
  • S is particularly preferably 0.003% or less.
  • At least one of the molding surface and the side surface of the hot forging die having the above alloy composition can be a surface having an antioxidant coating layer.
  • the antioxidant described above is preferably an inorganic material composed of one or more of nitride, oxide, and carbide. This is because a dense oxygen barrier film is formed by a nitride, oxide, or carbide coating layer to prevent oxidation of the mold base material.
  • the coating layer may be a single layer of any one of nitride, oxide, and carbide, or may have a laminated structure in which any two or more of nitride, oxide, and carbide are combined. Furthermore, the coating layer may be a mixture of two or more of nitride, oxide, and carbide.
  • the hot forging die using the Ni-based alloy for hot die of the present invention described above has high high temperature compressive strength and good oxidation resistance, and oxygen and die in the atmosphere at high temperature. Oxidation of the mold surface due to the contact of the base material and scale scattering associated therewith can be prevented, and deterioration of the working environment and shape deterioration can be more reliably prevented.
  • ⁇ Method for manufacturing forged products> A typical process in the case of producing a forged product using a hot forging die using the Ni-based alloy for hot die of the present invention will be described.
  • the forging material is heated to a predetermined forging temperature. Since the forging temperature varies depending on the material, the temperature is adjusted appropriately.
  • the hot forging die using the Ni-based alloy for hot die of the present invention has the characteristics that can be subjected to constant temperature forging or hot die forging even in the atmosphere at high temperature. It is suitable for hot forging of Ni-base super heat-resistant alloys and Ti alloys.
  • a typical forging temperature is in the range of 1000 to 1150 ° C.
  • the forging material heated in the first step is hot forged (second step) using the hot forging die.
  • the hot forging in the second step is preferably die forging.
  • the Ni-based alloy for hot dies according to the present invention can be hot forged in the atmosphere at a high temperature of 1000 ° C. or higher by using a component with particularly adjusted Cr content.
  • Ingots of Ni-based alloys for hot molds shown in Table 1 were produced by vacuum melting. The unit is mass%. Note that P, S, N, and O contained in the following ingots are each 0.003% or less, and C, Si, Mn, Co, Ti, Nb, and Fe are each 0.03% or less.
  • a 10 mm square cube was cut out from each of the above ingots, and the surface was polished to the equivalent of No. 1000 to produce an oxidation resistance test piece, and the oxidation resistance was evaluated.
  • the oxidation resistance test two types of tests were conducted: a test simulating long-time use and a test simulating repeated use when used in the atmosphere as a die for hot forging.
  • test pieces of Examples 1 to 10 and Comparative Examples 1 and 2 were used, and the test pieces were placed in a ceramic crucible made of SiO 2 and Al 2 O 3. Put it in a furnace heated to 1100 ° C. and hold it at 1100 ° C. for a predetermined time, then remove the crucible containing the test piece from the furnace and immediately put it into the crucible after removal to prevent the scale from peeling off the crucible.
  • a heating test was performed in which air-cooling was performed with the same material covered. In the heating test, in order to evaluate the oxidation resistance with respect to long-term use, each test piece was tested with a holding time of 3 hours and 8 hours, respectively.
  • the surface area of the test piece and the mass of the crucible containing the test piece were measured before the heating test, and after cooling to room temperature after the heating test, the mass of the crucible containing the test piece was measured.
  • Table 2 shows the mass change per unit surface area of the test piece calculated in the heating test for each holding time.
  • the unit of mass change is mg / cm 2 . From Table 2, in Examples 1 to 10 of the present invention to which Cr was added, the amount of scale generation was suppressed compared to Comparative Examples 1 and 2 to which Cr was not added, and the weight change after 8 hours was less than half. It can be seen that it has good oxidation resistance against long-term use due to the addition of Cr.
  • the test pieces of Examples 1, 4 to 10 and Comparative Example 1 were used and placed on a ceramic container made of SiO 2 and Al 2 O 3 .
  • a heating test was performed in which the sample was put into a furnace heated to 1100 ° C., held at 1100 ° C. for 3 hours, and then taken out of the furnace and air-cooled.
  • the heating test was repeated 5 times by cooling and re-charging. For each test piece, the surface area and mass of the test piece were measured before the first heating test, and after cooling to room temperature after the first to fifth heating tests, the surface scale was removed with a blower. The mass was measured.
  • Mass change (mass after test ⁇ mass before first test) / surface area before first test
  • Table 3 shows the mass change per unit surface area of the test piece calculated after each heating test.
  • the unit of mass change is mg / cm 2 .
  • FIG. 1 shows the relationship between the number of heating tests and the mass change.
  • scale generation scattering
  • the absolute value of mass change is smaller than that of the alloy of Comparative Example 1. It can be seen that it has good oxidation resistance to repeated use.
  • Example 1 in which Y and Zr were added in addition to Cr
  • Example 5 in which Ta was added in addition to Cr
  • scattering of scale was suppressed as compared with Example 4 in which only Cr was added.
  • the oxidation resistance to repeated use is particularly excellent.
  • Examples 6 to 10 in which Hf, La, and Mg are added in addition to Cr and Ta are more excellent in oxidation resistance against repeated use than Examples 1 and 5 described above. I understand.
  • a specimen collection material having a diameter of 8 mm and a height of 12 mm was cut out from each of the ingots of Examples 1 to 10 and Comparative Examples 1 and 2 in Table 1, and the surface was polished to the equivalent of No. 1000 to produce a compression specimen. did.
  • a compression test was performed at 900 ° C., 1000 ° C., and 1100 ° C. under conditions of a strain rate of 10 ⁇ 3 / sec and a compression rate of 10%.
  • a 0.2% compressive strength was derived from the stress-strain curve obtained by the compression test, and the high temperature compressive strength was evaluated.
  • This compression test is a test for checking whether or not the mold for hot forging has a sufficient compressive strength even at a high temperature, and if it is 300 MPa or more, it can be said to have a sufficient strength. Preferably it is 350 MPa or more.
  • Table 4 shows the 0.2% compressive strength at each test temperature of the test pieces of Examples 1 to 10 and Comparative Examples 1 and 2.
  • FIG. 2 illustrates the relationship between the test temperatures of Examples 1 to 5 and Comparative Example 1 and 0.2% compressive strength. From Table 4, it can be seen that the compressive strength at a strain rate of 10 ⁇ 3 / sec at 1000 ° C. in Examples 1 to 5 is 500 MPa or more. It can be seen that in Examples 1, 4 to 10 having preferable Cr amounts, the compressive strength at a strain rate of 10 ⁇ 3 / sec at 1100 ° C. is 350 MPa or more. Further, from FIG. 2, the compressive strength at 1000 ° C.
  • FIG. 3 shows a photograph of the appearance of the surface of the mold for hot dies after heating the mold for hot dies coated with an antioxidant at 1000 ° C. or higher in the atmosphere. As can be seen from FIG. 3, it can be seen that there is no peeling of the antioxidant applied to the surface of the hot mold. Also, no scattering of scale was confirmed. From this, it is understood that the oxidation of the mold and the scattering of the scale are prevented by the antioxidant.
  • the Ni-based alloy for hot dies of the present invention has both sufficient oxidation resistance and high compressive strength at high temperatures even when used for hot forging in the atmosphere. .
  • scale peeling can be remarkably reduced, so that deterioration of work environment and shape deterioration can be suppressed.
  • a hot forging die is produced using the Ni-based alloy for hot die of the present invention, and an application layer of an antioxidant is formed on at least one of the molding surface or the side surface, the work is further improved.
  • shape degradation can also be prevented. Therefore, it can be seen that the hot forging die made of the Ni-based alloy for hot die of the present invention is suitable for hot die forging and isothermal forging in the atmosphere.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Forging (AREA)

Abstract

L'invention concerne un alliage à base de Ni pour matrice de forgeage à chaud ayant une résistance élevée à la compression à haute température et une bonne résistance à l'oxydation, et avec lequel la détérioration de l'environnement de travail et la détérioration de la forme peuvent être limitées. L'alliage est un alliage à base de Ni pour matrice chaude composé de 7,0 à 12,0 % de W, 4,0 à 11,0 % de Mo, 5,0 à 7,5 % d'Al, 0,5 à 7,5 % de Cr, le reste étant constitué de Ni et d'impuretés inévitables. En plus de ladite composition, l'alliage peut également contenir de 0,5 à 7,0 % de Ta, ainsi qu'une ou plusieurs espèces choisies parmi 0,001 à 0,5 % de Zr, 0,001 à 0,5 % de Hf, 0,001 à 0,2 % de terres rares, 0,001 à 0,2 % de Y et 0,001 à 0,03 % de Mg. Avec un tel alliage à base de Ni pour matrice de forgeage à chaud, il est possible d'obtenir une résistance de 500 MPa ou plus à une compression de 0,2 % à une température d'essai de 1000 °C et une vitesse de déformation de 10-3/s.
PCT/JP2017/019488 2016-05-26 2017-05-25 ALLIAGE À BASE DE Ni POUR MATRICE DE FORGEAGE À CHAUD, MATRICE DE FORGEAGE À CHAUD L'UTILISANT ET PROCÉDÉ DE FABRICATION DE PRODUIT FORGÉ WO2017204286A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
US16/304,075 US20200340081A1 (en) 2016-05-26 2017-05-25 Nickel-based alloy for hot forging die, hot forging die using same, and method for manufacturing forged product
JP2018519601A JPWO2017204286A1 (ja) 2016-05-26 2017-05-25 熱間金型用Ｎｉ基合金及びそれを用いた熱間鍛造用金型、鍛造製品の製造方法

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2016-104956 2016-05-26
JP2016104956 2016-05-26
JP2017-059698 2017-03-24
JP2017059698 2017-03-24

Publications (1)

Publication Number Publication Date
WO2017204286A1 true WO2017204286A1 (fr) 2017-11-30

Family

ID=60411999

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2017/019488 WO2017204286A1 (fr) 2016-05-26 2017-05-25 ALLIAGE À BASE DE Ni POUR MATRICE DE FORGEAGE À CHAUD, MATRICE DE FORGEAGE À CHAUD L'UTILISANT ET PROCÉDÉ DE FABRICATION DE PRODUIT FORGÉ

Country Status (3)

Country Link
US (1) US20200340081A1 (fr)
JP (1) JPWO2017204286A1 (fr)
WO (1) WO2017204286A1 (fr)

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2019106922A1 (fr) * 2017-11-29 2019-06-06 日立金属株式会社 ALLIAGE À BASE DE Ni POUR MATRICE DE FORMAGE À CHAUD, ET MATRICE DE FORGEAGE À CHAUD L'UTILISANT
WO2019107502A1 (fr) * 2017-11-29 2019-06-06 日立金属株式会社 Alliage à base de ni pour filière chaude, filière de forgeage à chaud l'utilisant, et procédé de fabrication de produits forgés
WO2020059846A1 (fr) * 2018-09-21 2020-03-26 日立金属株式会社 Alliage à base de ni pour matrice de formage à chaud, et matrice de forgeage à chaud obtenue à l'aide de celui-ci
JPWO2021241585A1 (fr) * 2020-05-26 2021-12-02

Families Citing this family (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN115245996B (zh) * 2022-03-09 2023-09-19 江西宝顺昌特种合金制造有限公司 一种uns n06030耐蚀合金锻件及其制备方法
CN114669701B (zh) * 2022-03-30 2023-10-03 江西宝顺昌特种合金制造有限公司 一种gh4080a高温合金锻件及其制备方法

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62116748A (ja) * 1985-11-18 1987-05-28 Hitachi Metals Ltd 単結晶Ｎｉ基超耐熱合金
JPS62234634A (ja) * 1986-04-02 1987-10-14 San Alloy Kogyo Kk 接合型熱間圧縮加工用ダイ
JPH11152583A (ja) * 1997-11-17 1999-06-08 Sumitomo Electric Ind Ltd 被覆金型
JP2016069703A (ja) * 2014-09-30 2016-05-09 日立金属株式会社 ニッケル基鋳造合金及び熱間鍛造金型
JP2016069702A (ja) * 2014-09-30 2016-05-09 日立金属株式会社 ニッケル基鋳造合金の製造方法
WO2017057453A1 (fr) * 2015-09-29 2017-04-06 日立金属株式会社 Matrice pour la forgeage à chaud, procédé pour la fabrication de produit forgé utilisant cette dernière et procédé pour la fabrication de matrice pour le forgeage à chaud
JP2017064741A (ja) * 2015-09-29 2017-04-06 日立金属株式会社 熱間鍛造用金型

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62116748A (ja) * 1985-11-18 1987-05-28 Hitachi Metals Ltd 単結晶Ｎｉ基超耐熱合金
JPS62234634A (ja) * 1986-04-02 1987-10-14 San Alloy Kogyo Kk 接合型熱間圧縮加工用ダイ
JPH11152583A (ja) * 1997-11-17 1999-06-08 Sumitomo Electric Ind Ltd 被覆金型
JP2016069703A (ja) * 2014-09-30 2016-05-09 日立金属株式会社 ニッケル基鋳造合金及び熱間鍛造金型
JP2016069702A (ja) * 2014-09-30 2016-05-09 日立金属株式会社 ニッケル基鋳造合金の製造方法
WO2017057453A1 (fr) * 2015-09-29 2017-04-06 日立金属株式会社 Matrice pour la forgeage à chaud, procédé pour la fabrication de produit forgé utilisant cette dernière et procédé pour la fabrication de matrice pour le forgeage à chaud
JP2017064741A (ja) * 2015-09-29 2017-04-06 日立金属株式会社 熱間鍛造用金型

Cited By (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111433378A (zh) * 2017-11-29 2020-07-17 日立金属株式会社 热作模具用Ni基合金以及使用其的热锻用模具、锻造制品的制造方法
US11326231B2 (en) 2017-11-29 2022-05-10 Hitachi Metals, Ltd. Ni-based alloy for hot-working die, and hot-forging die using same
JPWO2019106922A1 (ja) * 2017-11-29 2019-12-12 日立金属株式会社 熱間金型用Ｎｉ基合金及びそれを用いた熱間鍛造用金型
JPWO2019107502A1 (ja) * 2017-11-29 2019-12-12 日立金属株式会社 熱間鍛造用金型、鍛造製品の製造方法
US11692246B2 (en) 2017-11-29 2023-07-04 Proterial, Ltd. Ni-based alloy for hot-working die, and hot-forging die using same
CN111417736A (zh) * 2017-11-29 2020-07-14 日立金属株式会社 热作模具用Ni基合金以及使用其的热锻用模具
WO2019107502A1 (fr) * 2017-11-29 2019-06-06 日立金属株式会社 Alliage à base de ni pour filière chaude, filière de forgeage à chaud l'utilisant, et procédé de fabrication de produits forgés
WO2019106922A1 (fr) * 2017-11-29 2019-06-06 日立金属株式会社 ALLIAGE À BASE DE Ni POUR MATRICE DE FORMAGE À CHAUD, ET MATRICE DE FORGEAGE À CHAUD L'UTILISANT
WO2020059846A1 (fr) * 2018-09-21 2020-03-26 日立金属株式会社 Alliage à base de ni pour matrice de formage à chaud, et matrice de forgeage à chaud obtenue à l'aide de celui-ci
JP7211561B2 (ja) 2020-05-26 2023-01-24 日立金属株式会社 熱間金型用Ｎｉ基合金およびそれを用いた熱間鍛造用金型
WO2021241585A1 (fr) 2020-05-26 2021-12-02 日立金属株式会社 Alliage à base de ni pour matrice à chaud, et matrice de forgeage à chaud utilisant celui-ci
CN115698350A (zh) * 2020-05-26 2023-02-03 日立金属株式会社 热模具用Ni基合金和使用其的热锻用模具
JPWO2021241585A1 (fr) * 2020-05-26 2021-12-02
CN115698350B (zh) * 2020-05-26 2024-02-13 株式会社博迈立铖 热模具用Ni基合金和使用其的热锻用模具

Also Published As

Publication number Publication date
JPWO2017204286A1 (ja) 2019-04-25
US20200340081A1 (en) 2020-10-29

Similar Documents

Publication Publication Date Title
WO2017204286A1 (fr) ALLIAGE À BASE DE Ni POUR MATRICE DE FORGEAGE À CHAUD, MATRICE DE FORGEAGE À CHAUD L'UTILISANT ET PROCÉDÉ DE FABRICATION DE PRODUIT FORGÉ
JP5582532B2 (ja) Ｃｏ基合金
EP2826877B1 (fr) Superalliage à base de Nickel à forgeage à chaud présentant une excellente résistance aux températures élevées
JP5652730B1 (ja) Ｎｉ基超耐熱合金及びその製造方法
US11692246B2 (en) Ni-based alloy for hot-working die, and hot-forging die using same
WO2016152982A1 (fr) PROCÉDÉ DE PRODUCTION D'UN ALLIAGE À BASE DE Ni À TRÈS HAUTE RÉSISTANCE THERMIQUE
JP4493028B2 (ja) 被削性及び熱間加工性に優れたα−β型チタン合金
JP6646885B2 (ja) 熱間鍛造用金型、鍛造製品の製造方法
JP6476704B2 (ja) ニッケル基鋳造合金及び熱間鍛造金型
WO2020059846A1 (fr) Alliage à base de ni pour matrice de formage à chaud, et matrice de forgeage à chaud obtenue à l'aide de celui-ci
JP2020196951A (ja) 熱間金型用Ｎｉ基合金及びそれを用いた熱間鍛造用金型及びそれを用いた鍛造製品の製造方法
JP6566255B2 (ja) 熱間鍛造用金型
WO2018061317A1 (fr) Procédé de fabrication de matériau extrudé d'alliage très résistant à la chaleur à base de ni, et matériau extrudé d'alliage très résistant à la chaleur à base de ni
JP2020196047A (ja) 鍛造製品の製造方法
JP6425274B2 (ja) Ｎｉ基耐熱合金
JP7211561B2 (ja) 熱間金型用Ｎｉ基合金およびそれを用いた熱間鍛造用金型
JP7485243B1 (ja) 熱間鍛造用金型およびその製造方法
JP2001279386A (ja) 鋳造性に優れたマルエージング鋼およびその製造方法
JP6784954B2 (ja) 熱間鍛造用金型及びそれを用いた鍛造製品の製造方法
JP2022506542A (ja) ２ｘｘｘアルミニウムリチウム合金

Legal Events

Date Code Title Description
ENP Entry into the national phase

Ref document number: 2018519601

Country of ref document: JP

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 17802872

Country of ref document: EP

Kind code of ref document: A1

122 Ep: pct application non-entry in european phase

Ref document number: 17802872

Country of ref document: EP

Kind code of ref document: A1