EP3685942A1 - Poudre ramollie d'alliage à base de ni et procédé de production de ladite poudre ramollie - Google Patents

Poudre ramollie d'alliage à base de ni et procédé de production de ladite poudre ramollie Download PDF

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EP3685942A1
EP3685942A1 EP19817113.4A EP19817113A EP3685942A1 EP 3685942 A1 EP3685942 A1 EP 3685942A1 EP 19817113 A EP19817113 A EP 19817113A EP 3685942 A1 EP3685942 A1 EP 3685942A1
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mass
powder
temperature
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EP3685942A4 (fr
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Mitsubishi Heavy Industries Ltd
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Mitsubishi Hitachi Power Systems Ltd
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/0433—Nickel- or cobalt-based alloys
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/05—Metallic powder characterised by the size or surface area of the particles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/14—Treatment of metallic powder
    • B22F1/142—Thermal or thermo-mechanical treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F5/00—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product
    • B22F5/04—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of turbine blades
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/16—Making metallic powder or suspensions thereof using chemical processes
    • B22F9/18—Making metallic powder or suspensions thereof using chemical processes with reduction of metal compounds
    • B22F9/20—Making metallic powder or suspensions thereof using chemical processes with reduction of metal compounds starting from solid metal compounds
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/047—Making non-ferrous alloys by powder metallurgy comprising intermetallic compounds
    • 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
    • C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
    • 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
    • C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
    • 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/10—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying using centrifugal force

Definitions

  • the present invention relates to the technology of Ni (nickel)-based alloy articles and, in particular, to a Ni-based alloy softened powder that is formed of a high precipitation-strengthened Ni-based alloy material and is suitable for powder metallurgy and a method for manufacturing the softened powder.
  • precipitation-strengthened Ni-based alloy materials have been widely used for high-temperature turbine members.
  • a high precipitation-strengthened Ni-based alloy material is used wherein the percentage of a ⁇ ' (gamma prime) phase (e.g., Ni 3 (Al,Ti) phase) precipitated in a ⁇ (gamma) phase (matrix) has been increased.
  • a ⁇ ' (gamma prime) phase e.g., Ni 3 (Al,Ti) phase
  • matrix e.g., Ni 3 (Al,Ti) phase
  • An example of such high precipitation-strengthened Ni-based alloy material is an Ni-based alloy material wherein at least 30 vol. % of the ⁇ ' phase has been precipitated.
  • the precipitation-strengthened Ni-based alloy material has a weak point in that if a volume percentage of the ⁇ ' phase is increased so as to increase high-temperature properties of high-temperature members, processability and formability become worse, causing a production yield of the high-temperature members to decrease (i.e., result in increase in production costs). Accordingly, along with the studies to improve properties of high-temperature members, various studies to stably produce the high-temperature members have also been carried out.
  • Patent Literature 1 JP Hei 9 (1997)-302450 A) discloses a method of making Ni-based superalloy articles having a controlled grain size from a forging preform.
  • the method includes the following steps of: providing an Ni-based superalloy preform having a recrystallization temperature, a ⁇ '-phase solvus temperature and a microstructure comprising a mixture of ⁇ and ⁇ ' phases, wherein the ⁇ ' phase occupies at least 30% by volume of the Ni-based superalloy; hot die forging the superalloy preform at a temperature of at least approximately 1600°F, but below the ⁇ '-phase solvus temperature and a strain rate from approximately 0.03 to approximately 10 per second to form a hot die forged superalloy work piece; isothermally forging the hot die forged superalloy workpiece to form the finished article; supersolvus heat treating the finished article to produce a substantially uniform grain microstructure of approximately ASTM 6 to 8; and cooling the article from the supersolvus heat treatment temperature
  • Patent Literature 1 it seems to be possible to produce a forged article at a high production yield without cracking of the forged article even using an Ni-based alloy material in which the ⁇ ' phase occupies relatively high volume percent.
  • Patent Literature 1 conducts the hot die forging process with superplastic deformation at a low strain rate and the subsequent isothermally forging process, special production equipment as well as long work time is required (i.e., result in high equipment costs and high process costs). These would be the weak points of the technique taught in Patent Literature 1.
  • Patent Literature 2 JP 5869624 B2 discloses a method for manufacturing an Ni-based alloy softened article made up of an Ni-based alloy in which the solvus temperature of the ⁇ ' phase is 1050°C or higher.
  • the method includes a raw material preparation step to prepare an Ni-based alloy raw material to be used for the subsequent softening treatment step, and a softening treatment step to soften the Ni-based alloy raw material in order to increase processability.
  • the softening treatment step is performed in a temperature range which is lower than the solvus temperature of the ⁇ ' phase.
  • the softening treatment step includes a first substep to subject the Ni-based alloy raw material to hot forging at a temperature lower than the solvus temperature of the ⁇ ' phase, and a second substep to obtain an Ni-based alloy softened material containing 20 vol. % or more of incoherent ⁇ ' phase particles precipitated on grain boundaries of the ⁇ phase (matrix of the Ni-based alloy) grains, by slowly cooling the above forged material from the temperature lower than the ⁇ ' phase solvus temperature at a cooling rate of 100°C/h or less.
  • the technique taught in Patent Literature 2 can be said to be an epoch-making technique that enables the processing and forming of the high precipitation-strengthened Ni-based alloy material at low costs.
  • a superhigh precipitation-strengthened Ni-based alloy material such as that containing 45 vol. % or more of ⁇ ' phase (e.g., Ni-based alloy material in which 45 to 80 vol. % of ⁇ ' phase is precipitated)
  • a conventional forging apparatus not equipped with an especial heating and thermal keeping mechanism is used for the hot forging process performed at a temperature lower than the ⁇ ' phase solvus temperature (i.e., temperature range in which two phases, ⁇ and ⁇ ' phases, coexist)
  • the temperature decreases during the hot forging process (causing undesired precipitation of the ⁇ ' phase), resulting to be prone to decrease a production yield.
  • one technique to manufacture a formed/molded article of a hard-to-work material at low cost is powder metallurgy using metal powder.
  • Patent Literature 3 discloses a method of making an article having a controlled grain size from an Ni-based superalloy.
  • the method includes a forging step, a heating step and a cooling step.
  • a fine-grain Ni-based superalloy preform e.g. consolidated metal powder preform
  • the forged article is subjected to an extended subsolvus heat treatment at a temperature that is higher than the recrystallization temperature and lower than the ⁇ ' phase solvus temperature.
  • the alloy article is subsequently cooled from the subsolvus temperature at a predetermined cooling rate to precipitate the ⁇ ' phase in the alloy article and control the precipitation distribution.
  • Patent Literature 3 uses powder metallurgy merely as a means of reducing the grain size of the preform to be forged so as to control the grain size of the finished Ni-based superalloy article, and it contains no teaching or suggestion as to techniques to improve forming/molding processability of hard-to-work materials.
  • High precipitation-strengthened Ni-based alloy materials cannot be regarded as having excellent forming/molding processability. This is true even for those in powder form due to the hardness of each powder particle. Conventionally, therefore, application of powder metallurgy has inevitably required working at high temperature and/or high pressure, making it difficult to dramatically reduce the manufacturing cost of high precipitation-strengthened Ni-based alloy articles. In other words, an Ni-based alloy powder with excellent forming/molding processability suitable for powder metallurgy would dramatically reduce the manufacturing cost of high precipitation-strengthened Ni-based alloy articles.
  • the present invention has been made in view of the foregoing circumstances, and it has an objective to provide an Ni-based alloy softened powder that is formed of a high precipitation-strengthened Ni-based alloy material, has better forming/molding processability than ever before, and is suitable for powder metallurgy and a method for manufacturing the softened powder.
  • the precursor powder preparation step or the single-phase precursor powder preparation step may include an atomization substep.
  • the equilibrium precipitation amount at 700°C and the solvus temperature of the ⁇ ' phase and the melting point (solidus temperature) of the ⁇ phase can be calculated thermodynamically based on the chemical composition of the Ni-based alloy material.
  • an Ni-based alloy softened powder that is formed of a high precipitation-strengthened Ni-based alloy material, has better forming/molding processability than ever before, and is suitable for powder metallurgy. Also, there can be provided a method for manufacturing the softened powder. Furthermore, by applying powder metallurgy using the Ni-based alloy softened powder, there can be provided a high precipitation-strengthened Ni-based alloy article at a high manufacturing yield (i.e. at lower cost than ever before).
  • FIG. 1 is schematic illustrations showing relationships between a ⁇ phase and a ⁇ ' phase contained in a precipitation-strengthened Ni-based alloy material, (a) a case where the ⁇ ' phase particle precipitates within the ⁇ phase grain; and (b) another case where the ⁇ ' phase particle precipitates on a boundary of the ⁇ phase grain.
  • the grain-boundary ⁇ ' phase particle and the ⁇ phase crystal grain configure an incoherent interface 4
  • dislocation migration within the ⁇ phase crystal grain is not prevented.
  • the grain-boundary ⁇ ' phase does not contribute to the strengthening of the Ni-based alloy material.
  • a major feature of the invention lies in the formation of an Ni-based alloy precursor powder/a single-phase precursor powder composed of a polycrystalline body of ⁇ phase fine crystals or ⁇ single-phase fine crystals and in the production of a softened powder in which the grain-boundary ⁇ ' phase is precipitated on the grain boundaries of ⁇ phase fine crystals that constitute each powder particle in an amount of 20 volume % or more, not in the precipitation of the grain-boundary ⁇ ' phase by performing hot forging on an alloy ingot in a two-phase coexistent temperature range where the ⁇ phase and the ⁇ ' phase are coexistent as in Patent Literature 2.
  • the Ni-based alloy precursor powder/single-phase precursor powder can be regarded as one of the key points of the invention.
  • Diffusion and rearrangement of atoms configuring a ⁇ ' phase are essentially necessary for the generation/precipitation of the ⁇ ' phase. Therefore, when the ⁇ phase crystal grains are large as those in the cast material, the ⁇ ' phase gains are deemed to preferentially precipitate within the ⁇ phase crystal grains where the distance of diffusion and rearrangement of atoms can be short. Besides, it is not denied that the ⁇ ' phase particles precipitate on the boundaries of the ⁇ phase crystal grains even in the cast material.
  • the inventors intensively carried out studies of the techniques to suppress the growth of the ⁇ phase grains even in a temperature range of slightly lower than, equal to or higher than the solvus temperature of the ⁇ ' phase.
  • the particles of an Ni-based alloy powder formed such that it contains an oxygen component in a controlled amount each consist of a polycrystalline body of ⁇ phase fine crystals (i.e. the powder particles each consist of a plurality of ⁇ phase fine crystals, in other words each powder particle contains the grain boundaries of ⁇ phase fine crystals). It was also found that in such powder particles, the grain growth of ⁇ phase fine crystals can be inhibited even if they are heated to a temperature near the solvus temperature of the ⁇ ' phase or equal to or higher than the solvus temperature (i.e.
  • each powder particle does not become a ⁇ phase single-crystalline body and remains to be a polycrystalline body) and that slowly cooling the powder from such a temperature causes precipitation and growth of the grain-boundary ⁇ ' phase on the boundaries of ⁇ phase fine crystals.
  • the present invention has been made based on these findings.
  • FIG. 2 is a flowchart illustrating steps of a method for manufacturing an Ni-based alloy article formed from an Ni-based alloy softened powder according to an embodiment of the invention.
  • the method for manufacturing an Ni-based alloy article formed from an Ni-based alloy softened powder according to an embodiment of the invention roughly includes a precursor powder preparation step (S1), a powder softening high temperature and slow cooling heat treatment step (S2), a molding processing step (S3), and a solution and aging heat treatment step (S4).
  • S1 a precursor powder is prepared such that the powder has a predetermined chemical composition and each powder particle consists of a polycrystalline body of ⁇ phase fine crystals.
  • the precursor powder is subjected to a predetermined high temperature and slow cooling heat treatment so as to produce an Ni-based alloy softened powder in which the grain-boundary ⁇ ' phase is precipitated in an amount of 20 volume % or more.
  • a molded article having a desired shape is formed from the softened powder by a powder metallurgy technique.
  • the molded article is subjected to a solution heat treatment to cause the grain-boundary ⁇ ' phase to enter into solid solution in the ⁇ phase and to an aging heat treatment to precipitate the intra-grain ⁇ ' phase in crystal grains of the ⁇ phase.
  • the precursor powder preparation step S1 and the powder softening high temperature and slow cooling heat treatment step S2 constitute the method for manufacturing an Ni-based alloy softened powder according to an embodiment of the invention.
  • the precursor powder refers to a powder whose particles are basically each formed of a polycrystalline body of ⁇ phase fine crystals with no ⁇ ' phase precipitated on the grain boundaries of the ⁇ phase fine crystals (at least the grain-boundary ⁇ ' phase has not been intentionally precipitated).
  • the softened powder refers to a powder in which the grain-boundary ⁇ ' phase is precipitated in an amount of 20 volume % or more on the grain boundaries of ⁇ phase fine crystals.
  • FIG. 3 is a schematic illustration showing changes in microstructure of an Ni-based alloy powder through the manufacturing method according to an embodiment of the invention.
  • the Ni-based alloy precursor powder prepared in the precursor powder preparation step S1 is a powder whose particles have an average particle size of 500 ⁇ m or less and are formed of a polycrystalline body of ⁇ phase fine crystals.
  • the precursor powder since the precursor powder is strongly influenced by the temperature history (e.g. cooling rate) in the process of its formation, there may exist a mixture of ⁇ phase fine crystals in which no ⁇ ' phase (coherent ⁇ ' phase) is precipitated and ⁇ phase fine crystals in which the intra-grain ⁇ ' phase is partially precipitated within the ⁇ phase fine crystals.
  • the ⁇ phase fine crystals with no intra-grain ⁇ ' phase precipitation and the regions in ⁇ phase fine crystals where no intra-grain ⁇ ' phase is precipitated are considered to be oversaturated with the ⁇ ' phase or in a state of compositional fluctuation before the formation of the ⁇ ' phase.
  • the particles of the precursor powder are basically each formed of a polycrystalline body of ⁇ phase fine crystals, but this should not be construed as denying the possibility that some particles are formed of a ⁇ phase single crystal.
  • most particles of the precursor powder are composed of a polycrystalline body of ⁇ phase fine crystals, but some particles may be formed of a ⁇ phase single crystal.
  • each powder particle is kept to consist of a polycrystalline body of ⁇ phase fine crystals at this stage. In other words, it is important to prevent from excess coarsening of the ⁇ phase fine crystals.
  • ⁇ ' phase particles precipitated on a surface of the powder particle are also regarded as the grain-boundary ⁇ ' phase particles because the surface of powder particle can be regarded as a kind of grain boundaries of the ⁇ phase fine crystals.
  • the obtained softened powder is subsequently formed into a molded article with a desired shape by a powder metallurgy technique (the molding processing step S3).
  • the softened powder according to an embodiment of the invention has a dramatically improved molding processability as compared to conventional high precipitation-strengthened Ni-based alloy powders, the temperature and/or pressure in the molding process can be lowered as compared to conventional ones. This means a reduced device cost and/or a reduced process cost in the molding process.
  • the molded article with a desired shape is subjected to a solution heat treatment to cause most of the grain-boundary ⁇ ' phase to solid-solve into the ⁇ phase (e.g. the grain-boundary ⁇ ' phase is reduced in amount to 10 volume % or less) and then to an aging heat treatment to precipitate the intra-grain ⁇ ' phase in the crystal grains of the ⁇ phase in an amount of 30 volume % or more (the solution and aging heat treatment step S4).
  • the solution and aging heat treatment step S4 the solution and aging heat treatment step S4
  • the obtained Ni-based alloy article can be preferably used for next-generation high-temperature turbine members (e.g., turbine rotor blades, turbine stator blades, rotor disks, combustor members, boiler members, and heat resistant coatings).
  • next-generation high-temperature turbine members e.g., turbine rotor blades, turbine stator blades, rotor disks, combustor members, boiler members, and heat resistant coatings.
  • Patent Literature 2 requires a highly accurate control for producing a softened article in which the incoherent ⁇ ' phase (grain-boundary ⁇ ' phase, inter-grain ⁇ ' phase) is precipitated while intentionally leaving the coherent ⁇ ' phase (intra-grain ⁇ ' phase) to remain.
  • a softened powder is produced such that the grain-boundary ⁇ ' phase is generated/precipitated after the intra-grain ⁇ ' phase is made to disappear once.
  • a softened powder can be obtained by combining the precursor powder preparation step S1, whose industrial difficulty level is low, and the powder softening high temperature and slow cooling heat treatment step S2, whose industrial difficulty level is also low. Therefore, the technique according to the embodiment has a general versatility higher than that of the technique of Patent Literature 2, allowing cost reduction in the entire manufacturing process. It is particularly effective in manufacturing a softened powder formed of a superhigh precipitation-strengthened Ni-based alloy material in which the ⁇ ' phase is precipitated in an amount of 45 volume % or more, for example.
  • an Ni-based alloy precursor powder having a predetermined chemical composition (specifically, a predetermined amount of oxygen component intentionally contained) is prepared.
  • a predetermined chemical composition specifically, a predetermined amount of oxygen component intentionally contained
  • any conventional method or technique can be used to prepare the precursor powder.
  • an atomization substep (S1b) for forming a precursor powder from the master alloy ingot can be performed.
  • a classification substep (S1c) for classifying the precursor powder into an appropriate particle size range may be performed, as needed.
  • Control of the oxygen content can be preferably performed in the atomization substep S1b.
  • Any conventional method or technique can be used for the atomization method except for the control of the oxygen content in the Ni-based alloy.
  • a gas atomization technique and a centrifugal force atomization technique can be preferably used while controlling the oxygen content (oxygen partial pressure) in the atomization atmosphere.
  • the oxygen component content (also referred to as a "content percentage") in the precursor powder is desirably equal to or more than 0.003 mass % (30 ppm) and equal to or less than 0.05 mass % (500 ppm); more desirably 0.005 mass % or more and 0.04 mass % or less; and further desirably 0.007 mass % or more and 0.02 mass % or less. If the oxygen content is less than 0.003 mass %, the growth of the ⁇ phase fine crystals is not sufficiently suppressed; and if the oxygen content is more than 0.05 mass %, the mechanical strength and ductility of the finished Ni-based alloy member deteriorate. Meanwhile, it could be considered that oxygen atoms dissolve in the powder particles or form nuclei or embryos of oxides on the surface or the inside of the powder particles.
  • the chemical composition of the Ni-based alloy which enables the ⁇ ' phase solvus temperature to become 1020°C or higher be adopted; more preferably, the ⁇ ' phase solvus temperature become 1050°C or higher; and further more preferably, the ⁇ ' phase solvus temperature become 1110°C or higher.
  • the chemical composition other than the oxygen component will be described in detail later.
  • the average particle diameter of the precursor powder is preferably from 5 ⁇ m to 500 ⁇ m; more preferably from 10 ⁇ m to 300 ⁇ m; and further more preferably from 20 ⁇ m to 200 ⁇ m. If the average particle diameter of the precursor powder becomes less than 5 ⁇ m, handling performance in the subsequent step S2 deteriorates and powder particles are prone to coalesce together during the step S2, making it difficult to control the average grain diameter of the softened powder. If the average particle diameter of the precursor powder becomes more than 500 ⁇ m, shape controllability and shape accuracy of the molded article in the later molding processing step S3 deteriorate.
  • the average particle diameter of the precursor powder can be measured, for example, by means of a laser diffractometry grain-size distribution measuring apparatus.
  • the particles of the precursor powder are basically each formed of a polycrystalline body of ⁇ phase fine crystals.
  • the average grain size of the ⁇ phase fine crystals is preferably equal to or more than 5 ⁇ m and equal to or less than 50 ⁇ m.
  • the ⁇ ' phase e.g. eutectic ⁇ ' phase directly crystalizing from the liquid phase
  • step S2 the precursor powder prepared in the previous step S1 is heated to a temperature equal to or higher than the ⁇ ' phase solvus temperature in order to solid-solve the ⁇ ' phase particles into the ⁇ phase grains, and then slowly cooled from that temperature to generate and increase the grain-boundary ⁇ ' phase particles, thereby producing a softened powder.
  • slow-cooling start temperature is preferably lower than the ⁇ phase melting temperature (solidus temperature); more preferably at most 35°C higher than the ⁇ ' phase solvus temperature; and further preferably at most 25°C higher than the ⁇ ' phase solvus temperature.
  • the heat treatment atmosphere is preferably a reducing atmosphere (e.g. hydrogen gas atmosphere).
  • this step S2 does not deny the possibility that the intra-grain ⁇ ' phase may not disappear completely as a result of the high temperature and slow cooling heat treatment and may still be present in a trace amount.
  • the grain-boundary ⁇ ' phase is precipitated in an amount of 20 volume % or more
  • a presence of the intra-grain ⁇ ' phase in an amount of 10 volume % or less would be permissible since it would not greatly inhibit the molding processability in the subsequent molding processing step S3.
  • the intra-grain ⁇ ' phase should preferably be present in an amount of 5 volume % or less and more preferably 3 volume % or less.
  • the precursor powder prepared in the precursor powder preparation step S1 contains more oxygen in its alloy composition than conventional Ni-based alloy articles (i.e. it has been controlled to contain oxygen in a larger amount). It is thought that performing a heat treatment on such a precursor powder at a temperature equal to or higher than the solvus temperature of the ⁇ ' phase causes the contained oxygen atoms to combine with metal atoms in the alloy to form local oxides.
  • the thus formed oxide is deemed to suppress the migration of grain boundaries of the ⁇ phase fine crystals (i.e., suppress growth of the ⁇ phase fine crystals). This means that even if the ⁇ ' phase is eliminated in the step S2, it is considered possible to prevent coarsening of the ⁇ phase fine crystals.
  • a softened powder with an excellent molding processability can be obtained by reducing the amount of the intra-grain ⁇ ' phase (coherent ⁇ ' phase) and increasing the amount of the grain-boundary ⁇ ' phase (inter-grain ⁇ ' phase, incoherent ⁇ ' phase).
  • the cooling rate in the slow-cooling process becomes lower, it is more advantageous for the precipitation and growth of the grain-boundary ⁇ ' phase particles.
  • the cooling rate is preferably 100°C/h or less; more preferably 50°C/h or less; and further preferably 10°C/h or less. If the cooling rate is higher than 100°C/h, the intra-grain ⁇ ' phase particles preferentially precipitate, and the advantageous effects of the invention cannot be acquired adequately.
  • the slow cooling should be preferably performed until the precursor powder reaches a temperature equal to or lower than the temperature at which the grain-boundary ⁇ ' phase is precipitated in an amount of 20 volume % or more and more preferably 30 volume % or more.
  • the intra-grain ⁇ ' phase should preferably be precipitated in an amount of 10 volume % or less and more preferably 5 volume % or less.
  • the precipitation amount of the ⁇ ' phase can be measured by microstructure observation and image analysis (e.g. ImageJ, a public domain program developed at the National Institutes of Health in U.S.A.).
  • the end temperature of slow-cooling process is preferably at least 50°C lower than the ⁇ ' phase solvus temperature; more preferably at least 100°C lower than the ⁇ ' phase solvus temperature; and further preferably at least 150°C lower than the ⁇ ' phase solvus temperature.
  • the end temperature of slow-cooling process is preferably at least 100°C lower than the ⁇ ' phase solvus temperature; more preferably at least 150°C lower than the ⁇ ' phase solvus temperature; and further preferably at least 200°C lower than the ⁇ ' phase solvus temperature. More specifically, it is preferable that the slow-cooling process be performed down to a temperature of 1000°C or less and 800°C or more.
  • the cooling from the slow-cooling end temperature is preferably performed at a high cooling rate in order to suppress the precipitation of the intra-grain ⁇ ' phase particles (e.g., the precipitation amount of the intra-grain ⁇ ' phase of at most 10 volume %) during the cooling process.
  • a high cooling rate in order to suppress the precipitation of the intra-grain ⁇ ' phase particles (e.g., the precipitation amount of the intra-grain ⁇ ' phase of at most 10 volume %) during the cooling process.
  • water-cooling or gas-cooling is preferable.
  • the softened powder obtained through the step S2 it is possible to obtain a softened powder having the room-temperature Vickers hardness of 370 Hv or less even by using a superhigh precipitation-strengthened Ni-based alloy material in which the equilibrium amount of precipitation of the ⁇ ' phase at 700°C is 45 volume % or more. It is more preferable for better forming/molding processability that the room-temperature Vickers hardness is 350 Hv or less; and further more preferably 330 Hv or less.
  • FIG. 4 is a flowchart illustrating steps of another method for manufacturing an Ni-based alloy article formed from an Ni-based alloy softened powder according to an embodiment of the invention.
  • the another method for manufacturing an Ni-based alloy article formed from an Ni-based alloy softened powder according to an embodiment of the invention is different from the steps shown in FIG. 2 regarding a method for manufacturing the Ni-based alloy softened powder (the single-phase precursor powder preparation step S1' and the powder softening sub-high temperature and slow cooling heat treatment step S2'), but it is the same as the method shown in FIG. 2 regarding the molding processing step S3 and the solution and aging heat treatment step S4.
  • FIG. 5 is a schematic illustration showing changes in microstructure of an Ni-based alloy powder in the steps S1' and S2'.
  • steps S1' to S2' i.e. the another method for manufacturing an Ni-based alloy softened powder according to an embodiment of the invention
  • steps S1 and S2' will be hereinafter described with reference to FIGs. 4 and 5 focusing on the difference from the steps S1 and S2 described above.
  • the step S1' is a step of preparing a single-phase precursor powder with a predetermined chemical composition whose particles are each formed of a polycrystalline body of ⁇ single-phase fine crystals.
  • a single-phase precursor powder means a powder that can be judged as being ⁇ single-phase based on measurements by scanning electron microscopy-energy dispersive X-ray spectroscopy (SEM-EDX) and/or X-ray diffractometry (XRD) (i.e. no ⁇ ' phase is detected).
  • SEM-EDX scanning electron microscopy-energy dispersive X-ray spectroscopy
  • XRD X-ray diffractometry
  • a master alloy ingot production substep (S1a) similar to that in the step S1 and an atomization substep (S1'b) for forming a single-phase precursor powder are performed.
  • a classification substep (S1c) similar to that in the step S1 may be performed.
  • an atomization method similar to the atomization substep S1b of the step S1 may be used except that the average cooling rate is controlled in a temperature range where the ⁇ ' phase easily generates/precipitates (e.g. 1,100°C to 600°C).
  • the average cooling rate should preferably be controlled to 500°C/min or more, more preferably 1,000°C/min or more, even more preferably 1,500°C/min or more, and the most preferably 2,000°C/min or more.
  • step S1' in particular, the atomization substep S1'b
  • a single-phase precursor powder formed of a polycrystalline body of ⁇ single-phase fine crystals as shown in FIG. 5 .
  • the oxygen content, the average particle size, and the average grain size of the single-phase fine crystals are similar to those of the precursor powder obtained in the step S1.
  • the step S2' is a step of producing an Ni-based alloy softened powder in which the grain-boundary ⁇ ' phase is precipitated in an amount of 20 volume % or more by performing a predetermined sub-high temperature and slow cooling heat treatment on the single-phase precursor powder prepared in the previous step S1'.
  • the sub-high temperature and slow cooling heat treatment is a heat treatment to heat the single-phase precursor powder to a temperature equal to or higher than a temperature 80°C lower than the solvus temperature of the ⁇ ' phase and lower than the solvus temperature and slowly cool the precursor powder from this temperature at a cooling rate of 100°C/h or less.
  • the heating temperature i.e.
  • slow cooling start temperature should preferably be equal to or higher than a temperature 50°C lower than the solvus temperature of the ⁇ ' phase and more preferably equal to or higher than a temperature 30°C lower than the solvus temperature of the ⁇ ' phase.
  • the cooling rate in the slow cooling process should preferably be 50°C/h or less and more preferably 10°C/h or less, as in the step S2.
  • the precursor powder to be used is single-phase, preferential nucleation and grain growth of the grain-boundary ⁇ ' phase occur (see FIG. 5 ). Also, the slow cooling end temperature, cooling from the slow cooling end temperature, the precipitation amount of the grain-boundary ⁇ ' phase as a result of the sub-high temperature and slow cooling heat treatment, and the amount of the intra-grain ⁇ ' phase present in the step S2' are similar to those of the softened powder obtained in the step S2.
  • a temperature equal to or higher than a temperature 80°C lower than the solvus temperature of the ⁇ ' phase and lower than the solvus temperature (referred to as "sub-high temperature" in the invention) is considered to be in a temperature region where the degree of undercooling is small regarding ⁇ ' phase precipitation.
  • the precipitation of the ⁇ ' phase in ⁇ phase crystals i.e. the intra-grain ⁇ ' phase
  • the nucleation frequency of the intra-grain ⁇ ' phase in the sub-high temperature region is considered to be extremely low.
  • heterogenous nucleation has a much lower activation energy than homogenous nucleation and therefore has a sufficiently high nucleation frequency even with a small degree of undercooling.
  • the sub-high temperature and slow cooling heat treatment on the single-phase precursor powder is thought to be a heat treatment to cause preferential nucleation of the heterogenous nucleation-derived grain-boundary ⁇ ' phase by having homogenous nucleation compete against heterogenous nucleation in a temperature range where the degree of undercooling of the ⁇ ' phase is small and subsequently allow for the grain growth of the generated nuclei in the slow cooling process.
  • This model is considered to be applicable to "the preferential nucleation of the grain-boundary ⁇ ' phase and the subsequent grain growth of the grain-boundary ⁇ ' phase" in the powder softening high temperature and slow cooling step S2.
  • FIG. 6 is a flowchart illustrating steps of still another method for manufacturing an Ni-based alloy article formed from an Ni-based alloy softened powder according to an embodiment of the invention.
  • the still another method for manufacturing an Ni-based alloy article formed from an Ni-based alloy softened powder according to this embodiment includes the single-phase precursor powder preparation step S1' followed by the powder softening high temperature and slow cooling heat treatment step S2 in its method for manufacturing the Ni-based alloy softened powder. It may be the same as the method shown in FIG. 2 regarding the molding processing step S3 and the solution and aging heat treatment step S4.
  • the Ni-based alloy material has a chemical composition that allows the equilibrium amount of precipitation of the ⁇ ' phase of from 30 volume % or more and 80 volume % or less at 700°C.
  • a preferable chemical composition in mass percent is as follows: 5% to 25% of Cr; more than 0% to 30% of Co; 1% to 8% of Al; the total amount of Ti, Nb and Ta of between 1% and 10%, inclusive; 10% or less of Fe; 10% or less of Mo; 8% or less of W; 0.1% or less of Zr; 0.1% or less of B; 0.2% or less of C; 2% or less of Hf; 5% or less of Re; 0.003% to 0.05% of O; and other substances (Ni and unavoidable impurities).
  • each component will be described.
  • the Cr component dissolves in the ⁇ phase and also forms an oxide (e.g., Cr 2 O 3 ) coating on the surface of the Ni-based alloy article in an actual use environment, thereby increasing corrosion resistance and oxidation resistance.
  • an oxide e.g., Cr 2 O 3
  • the Cr content is preferably 25 mass % or less.
  • the Co component which is an element similar to Ni, dissolves in the ⁇ phase in substitution for Ni.
  • the Co component can increase corrosion resistance as well as increasing creep strength. It can also decrease the ⁇ ' phase solvus temperature, thereby increasing the high-temperature ductility.
  • excessive adding of the Co accelerates the formation of a harmful phase. Therefore, the Co content is preferably more than 0 mass % and equal to or less than 30 mass %.
  • the Al component is an indispensable component for forming a ⁇ ' phase that is a precipitation-strengthening phase for an Ni-based alloy.
  • the Al component can also contribute to increase in oxidation resistance and corrosion resistance by forming an oxide (e.g., Al 2 O 3 ) coating on the surface of the Ni-based alloy article in an actual use environment.
  • the Al content is preferably equal to or more than 1 mass % and equal to or less than 8 mass % according to a desired amount of ⁇ ' phase precipitation.
  • the Ti component, the Nb component and the Ta component can also form the ⁇ ' phase and increase high-temperature strength.
  • the Ti and Nb components can also increase corrosion resistance. However, excessive adding of those components accelerates the formation of a harmful phase. Therefore, the total amount of Ti, Nb and Ta components is preferably equal to or more than 1 mass % and equal to or less than 10 mass %.
  • the Fe component substitutes the Co component or the Ni component, it is possible to reduce alloy material costs. However, excessive adding of the Fe accelerates the formation of a harmful phase. Therefore, the Fe content is preferably equal to or less than 10 mass %.
  • the Mo component and the W component dissolve in the ⁇ phase and can increase high-temperature strength (so-called solid solution strengthening). Therefore, it is preferable that either one component be added.
  • the Mo component can also increase corrosion resistance. However, excessive adding of those components accelerates the formation of a harmful phase or deteriorates ductility and high-temperature strength. Therefore, the Mo content is preferably equal to or less than 10 mass %, and the W content is preferably equal to or less than 8 mass %.
  • the Zr component, the B component and the C component can strengthen the gain boundaries of the ⁇ phase crystal grains (i.e., strengthening of tensile strength along the direction perpendicular to the grain boundary of the ⁇ phase crystal grain), thereby increasing high-temperature ductility and creep strength.
  • the Zr content is preferably equal to or less than 0.1 mass %
  • the B content is preferably equal to or less than 0.1 mass %
  • the C content is preferably equal to or less than 0.2 mass %.
  • the Hf component can increase oxidation resistance. However, excessive adding of the Hf accelerates the formation of a harmful phase. Therefore, the Hf content is preferably equal to or less than 2 mass %.
  • the Re component can contribute to the solid solution strengthening of the ⁇ phase and increase corrosion resistance.
  • excessive adding of the Re accelerates the formation of a harmful phase.
  • increase of the additive amount will result in increase of alloy material costs.
  • the Re content is preferably equal to or less than 5 mass %.
  • the O component is usually treated as an impurity and an attempt is often made to reduce the O component.
  • the O component is an indispensable component to suppress the growth of the ⁇ phase fine crystals and facilitate the formation of the grain-boundary ⁇ ' phase particles.
  • the content of the O component is preferably equal to or more than 0.003 mass % and equal to or less than 0.05 mass %.
  • Residual components of the Ni-based alloy material are the Ni component and unavoidable impurities other than the O component.
  • unavoidable impurities are N (nitrogen), P (phosphorus), and S (sulfur).
  • master ingots (each 10 kg) were prepared by mixing, melting and casting raw materials. Melting was performed by means of a vacuum induction melting technique. Next, each of the obtained master ingots was re-molten and an Ni-based alloy powder was produced by means of a gas atomization technique while the oxygen partial pressure in the atomization atmosphere was controlled.
  • an average cooling rate in a temperature range from 1,100 to 600°C was 500°C/min or more in parts of the alloy powders.
  • the particles of the alloy powders observed to have been cooled at an average cooling rate of 500°C/min or more were judged as being ⁇ single-phase because the ⁇ ' phase was not detected in microstructure observation by SEM-EDX at a magnification of 1,000. Microstructure observations were not performed on the particles of the other alloy powders for which the average cooling rates were not measured in their production by gas atomizing.
  • each of the obtained Ni-based alloy powders was classified and sorted according into a particle size range within 25 to 150 ⁇ m to prepare Ni-based alloy precursor powders PP1 to PP8 and Ni-based alloy single-phase precursor powders PP9 and PP10.
  • the chemical compositions of the obtained powders PP1 to PP10 are shown in Table 1. TABLE 1 Chemical Compositions of Ni-based Alloy Precursor Powders PP1 to PP8 and Ni-based Alloy Single-phase Precursor Powders PP9 and PP10.
  • Precursor Powder / Single-phase Precursor Powder Chemical Composition (mass %) Cr Co Al Ti Nb Ta Fe Mo W Zr B C Hf Re O Ni PP1 11.5 15.7 4.4 - - - 6.5 - 0.03 0.015 0.015 0.5 - 0.010 Bal. PP2 13.0 20.0 3.4 3.7 0.9 2.4 - 3.8 2.1 0.05 0.020 0.050 - - 0.011 Bal. PP3 13.3 10.0 4.0 2.4 - 4.8 - 1.7 4.6 0.03 0.018 0.090 - - 0.011 Bal. PP4 15.6 14.6 2.6 5.1 - - - 3.0 1.2 0.03 0.030 0.008 - - 0.013 Bal.
  • Ni-based alloy precursor powders PP1 to PP8 and the Ni-based alloy single-phase precursor powders PP9 and PP10 obtained in Experimental 1 were subjected to a powder softening treatment under the heat treatment conditions (i.e., slow-cooling start temperature, and cooling rate during the slow-cooling process) indicated in Table 2, described later, thereby fabricating the Ni-based alloy softened powders according to Examples 1 to 11 and Comparative examples 1 to 12.
  • the slow-cooling end temperature was set to 950°C except for Comparative examples 1 and 12.
  • Comparative examples 1 and 12 were quenched from the slow-cooling start temperature to room temperature by gas cooling.
  • Ni-based alloy softened powders were subjected to microstructure observation (for the precipitation amount of the grain-boundary ⁇ ' phase) and Vickers hardness measurement at room temperature to evaluate molding processability.
  • the precipitation amount of the grain-boundary ⁇ ' phase of each softened powder was determined by electron microscope observation and image analysis (ImageJ).
  • the room temperature Vickers hardness measurement was performed on randomly drawn 10 particles of each softened powder with a micro Vickers hardness tester (Akashi Seisakusho, Ltd., model: MVK-E).
  • the room temperature Vickers hardness was measured for each of the 10 particles, and the average value of the 8 particles obtained after excluding the maximum and minimum values was regarded as the room temperature Vickers hardness of the softened powder.
  • a room temperature Vickers hardness of equal to or less than 370 Hv was judged as "Passed”
  • a room temperature Vickers hardness of more than 370 Hv was judged as "Failed”.
  • the precipitation amount of the grain-boundary ⁇ ' phase is less than 20 volume % (instead, coarsened intra-grain ⁇ ' phase particles were detected), and the room-temperature Vickers hardness is more than 370 Hv. As a result, the molding processability properties are failed.
  • the equilibrium amount of the ⁇ ' phase precipitation is less than 30 volume %.
  • This softened powder is not applicable to the high precipitation-strengthened Ni-based alloy material prescribed by the invention.
  • the precipitation amount of the ⁇ ' phase is absolutely small, and the forming/molding processability does not have particular problems from the past.
  • any material under test have the precipitation amount of the grain-boundary ⁇ ' phase of 20 volume % or more and the room-temperature Vickers hardness of 370 Hv or less. As a result, the molding processability properties are passed. This means that one of the advantageous effects of the invention is verified.
  • the molding processability properties thereof are passed. In other words, one of the advantageous effects of the invention is verified.
  • the softened powders according to Examples 10 and 11 respectively obtained by applying the high temperature and slow cooling heat treatment to the single-phase precursor powders PP9 and PP10, each also has the grain-boundary ⁇ ' phase precipitation amount of 20 volume % or more and the Vickers hardness of 370 Hv or less. As a result, the molding processability properties thereof are passed. In other words, one of the advantageous effects of the invention is also verified.
  • the softened powders according to Comparative Examples 9 to 12 each formed of the single-phase precursor powder PP9 or PP10 but obtained with the slow-cooling start temperature or the cooling rate in the softening treatment failing to meet the invention, each has the grain-boundary ⁇ ' phase precipitation amount of less than 20 volume % and the Vickers hardness of more than 370 Hv. As a result, the molding processability properties thereof are failed.

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4001445A1 (fr) * 2020-11-18 2022-05-25 Siemens Energy Global GmbH & Co. KG Superalliage a base de nickel ayant une résistance à l'oxydation élevée et une bonne aptitude au traitement
WO2022238073A1 (fr) * 2021-05-11 2022-11-17 Siemens Energy Global GmbH & Co. KG Alliage, poudre, procédé et composant

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112281099A (zh) * 2020-10-13 2021-01-29 江苏联捷冶金设备有限公司 钨钴合金沉没辊及其制备方法
JP2023032514A (ja) * 2021-08-27 2023-03-09 国立研究開発法人物質・材料研究機構 ニッケル基超合金及びその粉末、並びにニッケル基超合金造形体の製造方法
CN115233074A (zh) * 2022-07-12 2022-10-25 北京科技大学 一种燃机动叶片用钴镍基高温合金及其制备方法
CN116043066B (zh) * 2022-12-21 2024-05-03 东方电气集团东方汽轮机有限公司 一种低扩散性活化辅助剂及其应用、修复剂及其制备、合金修复方法

Family Cites Families (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5061324A (en) * 1990-04-02 1991-10-29 General Electric Company Thermomechanical processing for fatigue-resistant nickel based superalloys
US5649280A (en) 1996-01-02 1997-07-15 General Electric Company Method for controlling grain size in Ni-base superalloys
US5759305A (en) 1996-02-07 1998-06-02 General Electric Company Grain size control in nickel base superalloys
US8992699B2 (en) * 2009-05-29 2015-03-31 General Electric Company Nickel-base superalloys and components formed thereof
US20100329876A1 (en) * 2009-06-30 2010-12-30 General Electric Company Nickel-base superalloys and components formed thereof
EP2591135B1 (fr) 2010-07-09 2015-09-09 General Electric Company Alliage à base de nickel, son traitement et les composants formés à partir dudit alliage
US10487384B2 (en) * 2013-07-17 2019-11-26 Mitsubishi Hitachi Power Systems, Ltd. Ni-based alloy product and method for producing same, and Ni-based alloy member and method for producing same
EP2949768B1 (fr) * 2014-05-28 2019-07-17 Ansaldo Energia IP UK Limited Précipitation gamma prime renforcée par un superalliage à base de nickel destinée à être utilisée dans un processus de fabrication d'additif à base de poudre
JP5869624B2 (ja) * 2014-06-18 2016-02-24 三菱日立パワーシステムズ株式会社 Ｎｉ基合金軟化材及びＮｉ基合金部材の製造方法
EP3183372B1 (fr) * 2014-08-18 2018-11-28 General Electric Company Superalliages améliorés par l'ajout de zirconium
EP3278901B1 (fr) * 2015-03-30 2020-07-22 Hitachi Metals, Ltd. Procédé de fabrication d'un superalliage à base de ni et résistant à la chaleur
CN113122789B (zh) * 2016-11-16 2022-07-08 三菱重工业株式会社 镍基合金模具和该模具的修补方法
JP6809169B2 (ja) * 2016-11-28 2021-01-06 大同特殊鋼株式会社 Ｎｉ基超合金素材の製造方法
JP6931545B2 (ja) * 2017-03-29 2021-09-08 三菱重工業株式会社 Ｎｉ基合金積層造形体の熱処理方法、Ｎｉ基合金積層造形体の製造方法、積層造形体用Ｎｉ基合金粉末、およびＮｉ基合金積層造形体
WO2018216067A1 (fr) * 2017-05-22 2018-11-29 川崎重工業株式会社 Composant à haute température et procédé de production associé
CN108396269B (zh) * 2018-03-02 2019-11-08 河北工业大学 一种增强多晶Ni3Al基高温合金变形稳定性的热处理方法

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP4001445A1 (fr) * 2020-11-18 2022-05-25 Siemens Energy Global GmbH & Co. KG Superalliage a base de nickel ayant une résistance à l'oxydation élevée et une bonne aptitude au traitement
WO2022106134A1 (fr) * 2020-11-18 2022-05-27 Siemens Energy Global GmbH & Co. KG Superalliage à base de nickel présentant une haute résistance à l'oxydation, une haute résistance à la corrosion et une bonne aptitude au traitement
WO2022238073A1 (fr) * 2021-05-11 2022-11-17 Siemens Energy Global GmbH & Co. KG Alliage, poudre, procédé et composant

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