EP3653322A1 - Gesinterte materialien aus austenitstahlpulver und turbinenelemente - Google Patents

Gesinterte materialien aus austenitstahlpulver und turbinenelemente Download PDF

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Publication number
EP3653322A1
EP3653322A1 EP19209339.1A EP19209339A EP3653322A1 EP 3653322 A1 EP3653322 A1 EP 3653322A1 EP 19209339 A EP19209339 A EP 19209339A EP 3653322 A1 EP3653322 A1 EP 3653322A1
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EP
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Prior art keywords
steel powder
austenite steel
sintered material
practical
austenite
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.)
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Application number
EP19209339.1A
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English (en)
French (fr)
Inventor
Takashi Shibayama
Shinya Imano
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Mitsubishi Heavy Industries Ltd
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Mitsubishi Hitachi Power Systems Ltd
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Publication of EP3653322A1 publication Critical patent/EP3653322A1/de
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    • 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
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
    • 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
    • B22F5/009—Manufacture of workpieces or articles from metallic powder characterised by the special shape of the product of turbine components other than turbine blades
    • 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
    • C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C30/00—Alloys containing less than 50% by weight of each constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/006—Making ferrous alloys compositions used for making ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/15—Nickel or cobalt
    • 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
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/20—Refractory metals
    • B22F2301/205—Titanium, zirconium or hafnium
    • 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
    • B22F2301/00—Metallic composition of the powder or its coating
    • B22F2301/35—Iron
    • 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
    • B22F2304/00—Physical aspects of the powder
    • B22F2304/10—Micron size particles, i.e. above 1 micrometer up to 500 micrometer
    • 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

Definitions

  • the present invention relates to sintered materials of austenite steel powder and turbine members.
  • Ni-based alloy which is higher than the ferritic steels in durable temperature would become a candidate for an alloy which is applicable to the high-temperature members.
  • the Ni-based alloy contains Al and Ti as precipitation strengthening elements and exhibits an excellent strength at high temperatures by generating a ⁇ ' phase which would become a stable phase at the high temperatures.
  • active elements Al and Ti
  • the above-described Japanese Unexamined Patent Application Publication No. 2017-88963 proposes a composition of the austenite steel which reduces macrosegregations in a large-sized casting.
  • manufacturing of a metal mold which is used for the casting comparatively takes much time and labor.
  • a process cost is increased. Therefore, in a case where it becomes possible to obtain the turbine members not by casting but by sintering, it becomes possible to further increase manufacturability of the turbine members.
  • the present invention has been made in view of the above-described circumstances and aims to provide sintered materials of austenite steel powder each having a strength which is equivalent to or in excess of the strength of the Ni-based alloy and insusceptible to oxygen and turbine members each being composed of each sintered material of austinite steel powder.
  • a sintered material of austenite steel powder which contains 25 to 50% Ni, 12 to 25% Cr, 3 to 6% Nb, 0.001 to 0.05% B, not more than 1.6% Ti, not more than 6% W, not more than 4.8% Mo, and not more than 0.5% Zr in percentage by mass, with a balance made up of Fe and unavoidable impurities.
  • a sintered material of austenite steel powder which contains 30 to 45% Ni, 12 to 20% Cr, 3 to 5% Nb, 0.001 to 0.02% B, 0.3 to 1.3% Ti, not more than 5.5% W, not more than 2% Mo, and not more than 0.3% Zr in percentage by mass, with a balance made up of Fe and unavoidable impurities.
  • a sintered material of austenite steel powder which contains 30 to 40% Ni, 15 to 20% Cr, 3.5 to 4.5% Nb, 0.001 to 0.02% B, 0.5 to not more than 1.1% Ti, not more than 5.5% W, and not more than 0.3% Zr in percentage by mass, with a balance made up of Fe and unavoidable impurities.
  • a turbine member which uses the sintered material of austenite steel powder.
  • the sintered materials of austenite steel powder each having the strength which is equivalent to or in excess of the strength of the Ni-based alloy and insusceptible to oxygen and the turbine members each being composed of each sintered material of austinite steel powder.
  • FIG. 1A is a schematic diagram illustrating one example of a structure of a sintered material of austinite steel powder according to one practical example of the present invention
  • FIG. 1B is a photograph of one example of a structure of a sintered material of austinite steel powder according to one practical example of the present invention which is observed using an SEM (Scanning Electron Microscope).
  • the sintered material of the austenite steel powder according to the practical example of the present invention has an austenite steel powder crystal 1, a crystal grain boundary 2 which is present at a boundary between mutually adjacent austenite steel powder crystal grains, and a Laves phase 3 which precipitates on the crystal grain boundary 3.
  • an average grain diameter of the austenite steel powder crystal 1 be 10 to 300 ⁇ m. In a case where the average grain diameter is smaller than 10 ⁇ m, there is a fear that a creep strength would not become sufficient. In a case where the average grain diameter is larger than 300 ⁇ m, there is a fear that tensile strength and fatigue strength would not become sufficient. In addition, a grain boundary coverage of the Laves phase 3 changes with changing the total number of the grain boundaries, and there is a fear that the strengths (the creep strength, the tensile strength, the fatigue strength and so forth) would be lowered.
  • FIG. 2 is a schematic diagram illustrating one example of the structure of the cast material of austinite steel powder which is disclosed in Japanese Unexamined Patent Application Publication No. 2017-88963 . As illustrated in FIG.
  • the cast material of austenite steel powder has an austenite steel powder crystal 4, a crystal grain boundary 5 which is present at a boundary between the mutually adjacent austenite steel powder crystals, and a Laves phase 6 which precipitates on the crystal grain boundary 5.
  • the number of the crystal grain boundaries is small and the grain diameters and shapes of the crystals are not homogeneous.
  • the cast structure becomes larger than the structure of the sintered material in the micro segregation. It is thought that the micro segregation is increased as the member concerned becomes large, and there is a fear that a defect which is caused by the micro segregation would become liable to occur and the strengths would become liable to be reduced.
  • a homogeneous structure is formed not depending on the size of the member concerned and therefore the micro segregation becomes difficult to occur.
  • FIG. 3 is a schematic diagram illustrating one example of the structure of the related art Ni-based alloy forged material (Alloy 718).
  • the Ni-based alloy forged material has an Ni-based alloy crystal 7, a prior particle boundary (PPB) 8 which is present at a boundary between the mutually adjacent Ni-based alloy crystals 7, and a delta phase 9 which precipitates on the prior particle boundary (PPB) 8.
  • PPB prior particle boundary
  • the structure of the sintered material of austenite steel powder according to one practical example of the present invention is clearly distinguished from the structures of the related art austenite cast material and the Ni-based alloy forged material.
  • Ni is added as an austenite phase stabilization element.
  • Ni generates an intermetallic compound (a ⁇ phase, Ni 3 Nb) together with Nb which will be described later and contributes to intragranular strengthening by precipitating into grains.
  • an additive amount of Ni is preferably 25 to 50% (at least 25% and not more than 50%), more preferably 30 to 45%, and still more preferably 30 to 40%.
  • Cr is an element which improves oxidation resistance and steam oxidation resistance. It is possible to obtain sufficient oxidation resistance by adding Cr by 12% or more by taking an operating temperature of a steam turbine into consideration. Further, addition of Cr in excess of 25% leads to precipitation of intermetallic compounds such as a ⁇ phase and so forth and induces reductions in high temperature ductility and toughness.
  • an additive amount of Cr is preferably 12 to 25%, more preferably 12 to 20%, and still more preferably 15 to 20%.
  • Nb is added for stabilization of a Laves phase (Fe 2 Nb) and the ⁇ phase (Ni 3 Nb).
  • the Laves phase 6 precipitates mainly on the grain boundary 2 and contributes to grain boundary strengthening.
  • the ⁇ phase precipitates mainly into the grains and contributes to the intragranular strengthening. It is possible to obtain a sufficient high temperature creep strength by adding Nb by 3% or more. When adding Nb in excess of 6%, there is the possibility that harmful phases such as the ⁇ phase and so forth would become liable to precipitate.
  • an additive amount of Nb is preferably 3 to 6%, more preferably 3 to 5%, and still more preferably 3.5 to 4.5%.
  • B contributes to precipitation of the Laves phase on the grain boundary.
  • B is not added, precipitation of the Laves phase on the grain boundary becomes difficult and the creep strength and creep ductility are reduced.
  • the effect of grain boundary precipitation is obtained by addition of 0.001% or more of boron.
  • an additive amount of B is preferably 0.001 to 0.05% and more preferably 0.001 to 0.02%.
  • Ti is an element which contributes to intragranular precipitation strengthening of phases such as a ⁇ " phase, the ⁇ phase and so forth. It becomes possible to greatly reduce initial-stage creep deformation by appropriately adding Ti. However, excessive addition of Ti adversely affects mechanical properties of the member concerned under the influence of oxidation in manufacturing.
  • an additive amount of Ti is preferably not more than 1.6%, more preferably 0.3 to 1.3%, and still more preferably 0.5 to 1.1%.
  • W contributes to stabilization of the Laves phase in addition to contribution to solid solution strengthening.
  • a precipitation amount of the Laves phase which precipitates on the grain boundary is increased owing to addition of W, and W is able to contribute to improvement of breaking strength and ductility in long-term creep properties.
  • an additive amount of W is preferably not more than 6%, more preferably 5.3 to 6%, and still more preferably about 5.5%.
  • Mo contributes to stabilization of the Laves phase in addition to contribution to the solid solution strengthening.
  • the precipitation amount of the Laves phase which precipitates on the grain boundary is increased owing to addition of Mo, and Mo is able to contribute to improvement of the breaking strength and the ductility in the long-term creep properties.
  • an additive amount of Mo is preferably 0 to 4.8% and more preferably 0 to not more than 2%.
  • Zr contributes to precipitation of the ⁇ " phase (Ni 3 Nb) in addition to contribution to precipitation of the Laves phase on the grain boundary similarly to B. Addition of Zr is particularly effective in a short time or at a low temperature (less than 750°C, desirably not more than 700°C). However, the ⁇ " phase is a metastable phase and therefore changes to the ⁇ phase when maintained at a high temperature (in particular, 750°C or more) for a long time. Accordingly, Zr may not be added. When an additive amount of Zr is too large, the stability of the ⁇ phase is improved and the ⁇ " phase changes to the ⁇ phase early. In addition, weldability is worsened. When taking these matters into consideration, an additive amount of Zr is preferably 0 to 0.5% and more preferably 0 to not more than 0.3%.
  • the sintered material of austenite steel powder according to the practical example of the present invention contains Nb and Ti as main strengthening elements and does not contain Al as the strengthening element. Therefore, the sintered material of austinite steel powder is insusceptible to oxidation and so forth with oxygen and is able to improve the strengths (the creep strength, the tensile strength, the fatigue strength and so forth).
  • the sintered material has the forged structure, and it is possible to control with ease strength properties of the sintered material coping with a required strength of a product concerned by controlling the crystal grain diameter by heat treatment and so forth.
  • the sintered material makes it possible to manufacture even complicated shape products at a high yield.
  • Sintering may be performed by a hot-pressing method under an anisotropic pressure or a metal-powder injection molding method (MIM), in place of the HIP.
  • MIM metal-powder injection molding method
  • solution heat treatment a heat treatment temperature: 1100 to 1300°C
  • aging heat treatment the heat treatment temperature: not more than 1000°C
  • FIG. 4 is a schematic diagram illustrating one example of a turbine valve casing to which the sintered material of austinite steel powder according to one practical example of the present invention is applied.
  • FIG. 5 is a schematic diagram illustrating one example of a turbine disc to which the sintered material of austinite steel powder according to one practical example of the present invention is applied.
  • the sintered material of the austenite steel power according to one practical example of the present invention has the excellent strengths and therefore is preferable for a turbine valve casing 10 and a turbine disc 11.
  • Sintered materials according to practical examples 1 to 3 and comparative examples 1 and 2 are produced and evaluated. Compositions of the practical examples 1 to 3 and the comparative examples 1 and 2 are indicated on Table 1 which will be described later. Master ingots or raw materials having the compositions which are indicated in Table 1 are prepared, and alloy powder which is not more than 250 ⁇ m in grain diameter is produced by the gas atomizing method. The obtained alloy powder is sintered by the HIP (the sintering temperature: 1160 C, the isotropic pressure: 100 MPa) and the sintered materials of the practical examples 1 to 3 and the comparative examples 1 and 2 are produced.
  • the comparative example 1 has a composition which is out of range of the present invention in the amount of Cr and the comparative example 2 has a composition which is out of range of the present invention in the amount of Ni.
  • Alloy (INCONEL) 718 (the forged material) which is the Ni-based alloy is prepared as a comparative example 3
  • Alloy (INCONEL) 625 (the cast material) which is the Ni-based alloy is prepared as a comparative example 4 and these alloys are evaluated.
  • Compositions of the comparative example 3 and the comparative example 4 are also indicated on Table 1 together with other examples.
  • "INCONEL” is a registered trademark of Huntington Alloys Corporation.
  • 0.2% proof stress and creep durable temperature ratios of the practical examples 1 to 3 and the comparative examples 1 to 4 are evaluated.
  • the 0.2% proof stress are evaluated on the basis of JIS G 0567 and creep tests are performed on the basis of JIS Z 22761.
  • FIG. 6 is a graph illustrating one example of the 0.2% proof stress (with the comparative example 4 being set as the standard) of the practical examples 1 to 3 and the comparative examples 1 to 4.
  • both the sintered materials of the practical examples 1 and 3 indicate values which are higher than values of the comparative examples 1, 2, and 4 and indicate the 0.2% proof stress which are equivalent to or in excess of the 0.2% proof stress of the related art comparative example 3 (Alloy 718).
  • FIG. 7 is a graph illustrating one example of the creep durable temperature ratios (with the comparative example 3 being set as the standard) of the practical examples 1 to 3 and the comparative examples 1 to 4.
  • both the sintered materials of the practical examples 1 and 2 indicate values which are higher than values of the comparative examples 1 to 3 and indicate the 0.2% proof stress which are equivalent to or in excess of the 0.2% proof stress of the related art comparative example 4 (Alloy 625).
  • the creep durable temperature ratio of the practical example 2 is larger than the creep durable temperature ratios of the comparative examples 2 to 4, and it may be said that the practical example 2 is superior to the comparative examples 2 to 4 when making a decision by comprehensively taking both the 0.2% proof stress and the creep durable temperature ratio into account.
  • the creep durable temperature ratio of the practical example 3 is slightly lower than the creep durable temperature ratio of the comparative example 4
  • the 0.2% proof stress of the practical example 3 is greatly larger than the 0.2% proof stress of the comparative example 4, and it may be said that the practical example 3 is superior to the comparative example 4 when making a decision by comprehensively taking both the 0.2% proof stress and the creep durable temperature ratio into account.
  • FIG. 8 is a graph illustrating one example of the 0.2% proof stress and the creep durable temperature ratios of the practical examples 1 and 3 and the comparative examples 1, 3, and 4.
  • the practical examples 1 and 3 indicate values which are greatly lager than values of the comparative example 1 in both the 0.2% proof stress and the creep durable temperature ratio.
  • the values of the practical examples 1 and 3 are larger than a value of the comparative example 4 (Alloy 625) in the 0.2% proof stress and reach the level which is equivalent to the level of the comparative example 3 (Alloy 718).
  • the values of the practical examples 1 and 3 are larger than the value of the comparative example 3 (Alloy 718) in the creep durable temperature ratio.
  • the practical example 1 attains the level which is equivale to the level of the comparative example 4 (Alloy 625).
  • the 0.2% proof stress and the creep durable temperature are in a trade-off relation, that is, exhibit a behavior that when the 0.2% proof stress is increased, the creep durable temperature is deceased and when the creep durable temperature is increased, the 0.2% proof stress is decreased. Since both the practical example 1 and the practical example 3 are located at upper right positions above a straight line connecting the comparative example 3 with the comparative example 4, it may be said that the practical examples 1 and 3 are superior to the comparative example 3 and the comparative example 4 when making a decision by comprehensively taking both the 0.2% proof stress and the creep durable temperature ratio into account.
  • the sintered materials of the austenite steel powder each having the strength which is equivalent to or in excess of the strength of the Ni-based alloy and insusceptible to oxygen and the turbine members each being composed of each of the above-described sintered materials.
  • the present invention is not limited to the aforementioned practical examples and various modified examples are included.
  • the aforementioned practical examples have been described in detail in order to comprehensibly describe the present invention and are not necessarily limited to those which possess all the above-described configurations.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Powder Metallurgy (AREA)
  • Turbine Rotor Nozzle Sealing (AREA)
EP19209339.1A 2018-11-19 2019-11-15 Gesinterte materialien aus austenitstahlpulver und turbinenelemente Withdrawn EP3653322A1 (de)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP2018216639A JP7112317B2 (ja) 2018-11-19 2018-11-19 オーステナイト鋼焼結材およびタービン部材

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US (1) US20200157664A1 (de)
EP (1) EP3653322A1 (de)
JP (1) JP7112317B2 (de)
KR (1) KR102467393B1 (de)
CN (1) CN112585288A (de)
SG (1) SG11202100355UA (de)
WO (1) WO2020105496A1 (de)

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JP2023120710A (ja) * 2022-02-18 2023-08-30 三菱重工業株式会社 Ｆｅ－Ｎｉ－Ｃｒ系合金製造物

Citations (2)

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Publication number Priority date Publication date Assignee Title
CN105543747A (zh) * 2015-12-21 2016-05-04 西北工业大学 一种保留有Laves相的增材制造镍基高温合金的制备方法
JP2017088963A (ja) 2015-11-11 2017-05-25 三菱日立パワーシステムズ株式会社 オーステナイト鋼およびそれを用いたオーステナイト鋼鋳造品

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