WO2020195049A1 - Procédé de production d'un alliage super résistant à la chaleur à base de ni et alliage super résistant à la chaleur à base de ni - Google Patents

Procédé de production d'un alliage super résistant à la chaleur à base de ni et alliage super résistant à la chaleur à base de ni Download PDF

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WO2020195049A1
WO2020195049A1 PCT/JP2020/001725 JP2020001725W WO2020195049A1 WO 2020195049 A1 WO2020195049 A1 WO 2020195049A1 JP 2020001725 W JP2020001725 W JP 2020001725W WO 2020195049 A1 WO2020195049 A1 WO 2020195049A1
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resistant alloy
heat
less
heat treatment
plastic working
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PCT/JP2020/001725
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Japanese (ja)
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悠輔 巽
韓　剛
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日立金属株式会社
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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
    • 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
    • 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

Definitions

  • the present invention relates to a method for producing a Ni-based superheat-resistant alloy and, specifically, a Ni-based superheated alloy having a component composition in which the equilibrium precipitation amount of the gamma prime phase at 700 ° C. is 35 mol% or more. It relates to a method for producing a heat-resistant alloy and a Ni-based super heat-resistant alloy.
  • Ni-based super heat-resistant alloys such as Inconel (registered trademark) 718 alloy are often used.
  • heat-resistant parts having a high heat-resistant temperature are required.
  • the gamma prime (hereinafter, also referred to as “ ⁇ '”) phase which is a precipitation strengthening phase of an intermetallic compound having Ni 3 Al as a main composition. It is most effective to increase the amount of.
  • the Ni-based superheat-resistant alloy further contains the ⁇ 'forming elements Al, Ti, and Nb, so that the high-temperature strength of the Ni-based superheat-resistant alloy can be further improved.
  • a Ni-based super heat resistant alloy having a larger amount of ⁇ 'phase will be required.
  • Ni-based superheat-resistant alloys are difficult to process because the deformation resistance of hot processing increases as the ⁇ 'phase increases.
  • the amount of the ⁇ 'phase is 35 to 40 mol% or more, the processability is particularly lowered.
  • alloys such as Inconel (registered trademark) 713C alloy, IN939, IN100, and Mar-M247 have a particularly large number of ⁇ 'phases, which makes plastic working impossible, and are usually cast as cast alloys (as-cast). Used in.
  • Patent Document 1 As a proposal for improving the hot plastic workability of such a Ni-based superheat-resistant alloy, in Patent Document 1, a Ni-based superheat-resistant alloy ingot having a composition having a ⁇ 'molar ratio of 40 mol% or more is processed at a processing rate of 5%. A manufacturing method is described in which cold working is performed at a temperature of less than 30% and then heat treatment is performed at a temperature exceeding the ⁇ 'solid solution temperature. In this method, a recrystallization rate of 90% or more, which enables hot working to be applied to a Ni-based superheat-resistant alloy, is obtained by combining a cold working step and a heat treatment step.
  • Ni-based superheat-resistant alloy having a large amount of ⁇ 'phase
  • a fine wire of Ni-based super heat-resistant alloy is required as a modeling material in that case.
  • This thin wire can also be used by processing it into a component shape such as a spring.
  • the wire diameter (diameter) of the thin wire of the Ni-based superheat-resistant alloy is, for example, as thin as 5 mm or less and further 3 mm or less.
  • a thin wire for example, it is efficient to prepare a "wire rod" having a wire diameter of 10 mm or less as an intermediate product and perform plastic working on the wire rod to produce it. If this intermediate product, "wire rod", can also be obtained by plastic working, fine wires of Ni-based superheat-resistant alloy can be efficiently produced.
  • a method for producing such a fine wire of a super heat-resistant alloy a method has been proposed in which a cast wire having a wire diameter of 5 mm or more is used as a starting material, a bundle of these cast wires is hot-extruded, and then separated. Patent Document 2).
  • Patent Document 1 is effective for Ni-based superheat-resistant alloys to which hot working is applied.
  • the method of Patent Document 2 is effective for producing fine wires in a limited component composition, but can be applied only to the component composition, and the amount of ⁇ 'phase is "35 mol% or more" described later.
  • the method of Patent Document 2 has a problem that the process is complicated and the manufacturing cost is high.
  • in producing thin wires and wire rods there is a problem that if cracks occur in the middle of the process, the processing rate is limited and plastic working cannot be performed to a predetermined wire diameter.
  • a method for producing a Ni-based superheat resistant alloy This method (A) A temperature of 900 ° C. or higher with respect to a material having a carbon content of 0.05 to 0.25% by mass and a component composition in which the equilibrium precipitation amount of the gamma prime phase at 700 ° C. is 35 mol% or more.
  • the process of producing the first processed material by cooling after performing plastic working in (B) It includes a step of heating the first processed material to a temperature of 900 ° C. or higher to perform heat treatment to prepare the first heat-treated material.
  • the first heat-treated material includes a step of plastically working at a temperature of 500 ° C. or lower to produce a second processed material.
  • the second processed material further includes a step of performing a heat treatment at a temperature of 900 ° C. or higher.
  • the Ni-based superheat-resistant alloy is in mass%.
  • C 0.05-0.25%, Cr: 8.0-25.0%, Al: 0.5-8.0%, Ti: 0.4-7.0%, Co: 0-28.0%, Mo: 0-8.0%, W: 0 to 15.0%, Nb: 0-4.0%, Ta: 0-5.0%, Fe: 0 to 10.0%, V: 0-1.2%, Hf: 0-3.0%, B: 0 to 0.300%, Zr: 0 to 0.300% It is preferable that the balance is composed of Ni and impurities.
  • a Ni-based superheat resistant alloy is provided.
  • This alloy is for cold plastic working and It has a component composition having a carbon content of 0.05 to 0.25% by mass and an equilibrium precipitation amount of the gamma prime phase at 700 ° C. of 35 mol% or more.
  • the area ratio of M 23 C 6 is 4.0 area% or less, and the average particle size of the maximum diameter of the crystal grains is 1.4 to 100 ⁇ m.
  • the hardness of the Ni-based superheat-resistant alloy is preferably 460 HV or less.
  • the Ni-based superheat-resistant alloy is in mass%.
  • C 0.05-0.25%, Cr: 8.0-25.0%, Al: 0.5-8.0%, Ti: 0.4-7.0%, Co: 0-28.0%, Mo: 0-8.0%, W: 0 to 15.0%, Nb: 0-4.0%, Ta: 0-5.0%, Fe: 0 to 10.0%, V: 0-1.2%, Hf: 0-3.0%, B: 0 to 0.300%, Zr: 0 to 0.300% It is preferable that the balance is composed of Ni and impurities.
  • the cross-sectional microstructure of the material 3 (heat treatment temperature 1050 ° C.) in Example 1, the EPMA mapping diagram of Cr and Nb, and the EBSD image.
  • the cross-sectional microstructure of the material 4 (heat treatment temperature 1100 ° C.) in Example 1, the EPMA mapping diagram of Cr and Nb, and the EBSD image.
  • Cross-sectional microstructure of material 5 (heat treatment temperature 1150 ° C.) in Example 1, EPMA mapping diagram of Cr and Nb, and EBSD image.
  • the cross-sectional microstructure of the material 6 (heat treatment temperature 1200 ° C.) in Example 1, the EPMA mapping diagram of Cr and Nb, and the EBSD image.
  • FIG. 7 is a diagram showing the relationship between the heat treatment temperature and the number density of carbides when the first heat-treated material (material) is produced by heat-treating the first processed material in Example 1.
  • the present invention provides a new method capable of producing a Ni-based superheat-resistant alloy having excellent plastic workability and a Ni-based superheat-resistant alloy by a new approach different from the conventional hot plastic working.
  • the present inventor has studied the plastic workability of a Ni-based superheat resistant alloy having a large amount of ⁇ 'phase. As a result, it was found that it is possible to perform cold plastic working on a Ni-based superheat-resistant alloy that has been heat-treated by heating again after hot plastic working. At that time, it was found that nanocrystal grains were generated in the structure of the Ni-based superheat-resistant alloy by cold plastic working at a processing rate of 30% or more. It is presumed that the formation of these nanocrystal grains contributes to the dramatic improvement in the plastic workability of the Ni-based superheat-resistant alloy.
  • the method for producing a Ni-based superheat resistant alloy having a component composition in which the equilibrium precipitation amount of the gamma prime phase at 700 ° C. is 35 mol% or more is (A) A temperature of 900 ° C. or higher with respect to a material having a carbon content of 0.05 to 0.25 mass% and a component composition in which the equilibrium precipitation amount of the gamma prime phase at 700 ° C. is 35 mol% or more.
  • the process of producing the first processed material by cooling after performing plastic processing in (B) It includes a step of heating the first processed material to a temperature of 900 ° C. or higher to perform heat treatment to prepare the first heat-treated material.
  • the first heat-treated material is used as a material, and this material is subjected to plastic working at a temperature of 500 ° C. or lower to produce a second processed material.
  • the Ni-based superheat-resistant alloy targeted by the present invention is a component having a carbon content of 0.05 to 0.25% by mass and an equilibrium precipitation amount of the gamma prime ( ⁇ ') phase at 700 ° C. of 35 mol% or more.
  • ⁇ ' the amount of the ⁇ 'phase of the Ni-based superheat resistant alloy can be expressed by a numerical index such as "volume fraction" or "area ratio" of the ⁇ 'phase.
  • the amount of the ⁇ 'phase is represented by a numerical index of “ ⁇ 'molar rate”.
  • the ⁇ 'molar ratio is a stable equilibrium precipitation amount of the gamma prime phase in which a Ni-based superheat resistant alloy can be precipitated in a thermodynamic equilibrium state.
  • the value of the equilibrium precipitation amount of the gamma prime phase expressed in "molar ratio" is determined by the component composition of the Ni-based superheat resistant alloy.
  • the value of mol% of this equilibrium precipitation amount can be obtained by analysis by thermodynamic equilibrium calculation. In the analysis by thermodynamic equilibrium calculation, it can be obtained accurately and easily by using various thermodynamic equilibrium calculation software.
  • the ⁇ 'molar ratio of the Ni-based superheat-resistant alloy is defined as the “equilibrium precipitation amount at 700 ° C.”.
  • the high temperature strength of the Ni-based superheat resistant alloy can be evaluated by the equilibrium precipitation amount of the gamma prime phase in the structure, and the larger the high temperature strength, the more difficult the hot plastic working.
  • the equilibrium precipitation amount of the gamma prime phase in the structure is generally about 700 ° C. or lower, the temperature dependence becomes small and becomes almost constant, so the value at "700 ° C.” is used as a reference.
  • the ⁇ 'molar ratio of the Ni-based superheat resistant alloy is larger.
  • increasing the ⁇ 'molar ratio greatly contributes to the improvement of the cold plastic workability of the Ni-based superheat resistant alloy.
  • nanocrystal grains are most likely to be generated from the phase interface between the austenite phase (gamma ( ⁇ ) phase), which is a matrix of Ni-based superheat-resistant alloys, and the gamma prime phase.
  • FIG. 1 shows an example of an EBSD image of a cross-sectional microstructure produced by cold plastic working of a wire rod in the manufacturing method of the present invention.
  • the EBSD measurement conditions are as follows: Using the EBSD measurement system "OIM Version 5.3.1 (manufactured by TSL Solution)" attached to the scanning electron microscope "ULTRA55 (manufactured by Zeiss)", magnification: 10000 times, scanning Step: 0.01 ⁇ m, and the definition of crystal grains was defined as grain boundaries with an orientation difference of 15 ° or more.
  • the maximum diameter (maximum length) of the nanocrystal grains (enclosed portion) confirmed in the EBSD image in FIG. 1 is as small as about 25 nm.
  • a component composition in which the equilibrium precipitation amount of the gamma prime phase at 700 ° C. is 40 mol% or more is more preferable.
  • the equilibrium precipitation amount of the gamma prime phase is more preferably 50 mol% or more, and even more preferably 60 mol% or more.
  • a particularly preferable equilibrium precipitation amount of the gamma prime phase is 63 mol% or more, more preferably 66 mol% or more, and even more preferably 68 mol% or more.
  • the upper limit of the equilibrium precipitation amount of the gamma prime phase at 700 ° C. is not particularly limited, but is practically about 75 mol%.
  • the composition contains 0 to 0.300%, Zr: 0 to 0.300%, and the balance is composed of Ni and impurities.
  • each component having a preferable composition of the Ni-based superheat-resistant alloy of the present invention will be described (the unit of the component composition is "mass%").
  • C is contained as an element that enhances the castability of a Ni-based superheat resistant alloy.
  • Ni-based superheat-resistant alloys having a large amount of ⁇ 'phase are usually used as cast parts because plastic working is difficult, and a certain amount of C is added.
  • This added C remains as a carbide in the cast structure, and a part of it is formed as a coarse eutectic carbide.
  • coarse carbides serve as a crack starting point and a crack growth path when the Ni-based superheat-resistant alloy is plastically processed, especially when the Ni-based superheat-resistant alloy is plastically processed at room temperature. It has an adverse effect on sexuality.
  • the present invention in which a Ni-based superheat-resistant alloy having a large amount of ⁇ 'phase is produced by plastic working, not as a cast part, in the Ni-based superheat-resistant alloy. It is preferable to reduce C.
  • the C content is 0.25% or less. It is preferably 0.20% or less. More preferably, it is 0.15% or less.
  • C is also an element that enhances the strength of heat-resistant parts, and it is preferable that C is contained in consideration of producing or repairing such heat-resistant parts. According to the method for producing a Ni-based superheat-resistant alloy of the present invention, plastic working is possible even with an alloy having a high C content due to the effect of the nanocrystal grains described above.
  • C is assumed to be contained in an amount of 0.05% or more. It is preferably 0.06% or more, more preferably 0.07% or more, still more preferably 0.1% or more. Furthermore, C may be contained in an amount of more than 0.1%.
  • Chromium (Cr) Cr is an element that improves oxidation resistance and corrosion resistance. However, if Cr is excessively contained, an embrittled phase such as a ⁇ (sigma) phase is formed, which reduces the strength and hot workability at the time of material preparation. Therefore, Cr is preferably set to, for example, 8.0 to 25.0%. More preferably, it is 8.0 to 22.0%. The preferred lower limit is 9.0%, more preferably 9.5%. More preferably, it is 10.0%. The upper limit is preferably 18.0%, more preferably 16.0%. More preferably, it is 14.0%. Particularly preferably, it is 12.5%.
  • Mo Molybdenum
  • Mo contributes to the solid solution strengthening of the matrix and has the effect of improving the high temperature strength.
  • Mo is preferably 0 to 8.0% (addition-free (unavoidable impurity level) may be used). More preferably, it is 2.0 to 7.0%.
  • a further preferred lower limit is 2.5%, more preferably 3.0%. More preferably, it is 3.5%.
  • the upper limit is more preferably 6.0%, more preferably 5.0%.
  • Aluminum (Al) Al is an element that forms a ⁇ '(Ni 3 Al) phase, which is a strengthening phase, and improves high-temperature strength. However, excessive addition reduces hot workability during material preparation and causes material defects such as cracks during processing. Therefore, Al is preferably 0.5 to 8.0%. More preferably, it is 2.0 to 8.0%. A further preferred lower limit is 2.5%, more preferably 3.0%. It is even more preferably 4.0% and even more preferably 4.5%. Particularly preferably, it is 5.1%. Further, the upper limit is more preferably 7.5%, and more preferably 7.0%. More preferably, it is 6.5%.
  • the reduced Al content when the Cr content is reduced in order to ensure hot workability at the time of material preparation, the reduced Al content can be allowed. Then, for example, when the upper limit of Cr is set to 13.5%, the lower limit of the Al content is preferably set to 3.5%.
  • Ti Titanium (Ti) Like Al, Ti is an element that forms a ⁇ 'phase and strengthens the ⁇ 'phase by solid solution to increase high-temperature strength. However, excessive addition causes the ⁇ 'phase to become unstable at high temperatures, leading to coarsening at high temperatures, forming a harmful ⁇ (eta) phase, and impairing hot workability during material preparation. Therefore, Ti is preferably 0.4 to 7.0%, for example. Considering the balance with other ⁇ 'forming elements and Ni matrix, the preferable lower limit of Ti is 0.6%, more preferably 0.7%. More preferably, it is 0.8%. The upper limit is preferably 6.5%, more preferably 6.0%. It is more preferably 4.0%, and particularly preferably 2.0%.
  • Co Cobalt (Co) Co improves the stability of the structure and makes it possible to maintain the hot workability at the time of material preparation even if a large amount of Ti, which is a reinforcing element, is contained.
  • Co is one of the arbitrary elements that can be contained in the range of 28.0% or less, for example, by combining with other elements.
  • the preferable lower limit when adding Co is preferably 8.0%. More preferably, it is 10.0%.
  • the preferable upper limit of Co is 18.0%. More preferably, it is 16.0%. If Co may be added-free (the level of unavoidable impurities in the raw material) depending on the balance with the ⁇ 'forming element and the Ni matrix, the lower limit of Co is set to 0%.
  • W Tungsten
  • the upper limit is set to 15.0%.
  • the preferred upper limit is 13.0%, more preferably 11.0%, and even more preferably 9.0%.
  • the lower limit of W is preferably 1.0%.
  • the lower limit of W can be set to 3.0%, 5.0%, 7.0%.
  • W is preferably added in an amount of 0.8% or more. If W can be set to a non-addition level (a level of unavoidable impurities in the raw material) by sufficiently adding Mo, the lower limit of W is set to 0%.
  • Niobium (Nb) Like Al and Ti, Nb is one of the selective elements that forms the ⁇ 'phase and strengthens the ⁇ 'phase by solid solution to increase the high temperature strength. However, excessive addition of Nb forms a harmful delta phase, impairing hot workability during material preparation. Therefore, the upper limit of Nb is, for example, 4.0%. The preferred upper limit is 3.5%, more preferably 2.5%. In order to more reliably exert the effect of Nb, the lower limit of Nb is preferably 1.0%. It is preferably 2.0%. When Nb may be set to a non-addition level (unavoidable impurity level) by adding another ⁇ 'forming element, the lower limit of Nb is set to 0%.
  • Ta Tantalum (Ta) Like Al and Ti, Ta is one of the selective elements that forms the ⁇ 'phase and strengthens the ⁇ 'phase by solid solution to increase the high temperature strength. However, excessive addition of Ta causes the ⁇ 'phase to become unstable at high temperatures, leading to coarsening at high temperatures and forming a harmful ⁇ (eta) phase, which improves hot workability during material preparation. To spoil. Therefore, Ta is set to 5.0% or less, for example. It is preferably 4.0% or less, more preferably 3.0% or less, still more preferably 2.5% or less. In order to more reliably exert the effect of Ta, the lower limit of Ta is preferably 0.3%. Preferably, the lower limit of Ta can be 0.8%, 1.5%, 2.0%. If Ta may be an additive-free level (unavoidable impurity level) due to the addition of ⁇ 'forming elements such as Ti and Nb and the balance with the matrix, the lower limit of Ta is set to 0%.
  • Iron (Fe) Fe is one of the selective elements used as a substitute for expensive Ni and Co, and is effective in reducing the alloy cost. To obtain this effect, it is advisable to decide whether or not to add in combination with other elements. However, if Fe is excessively contained, an embrittled phase such as a ⁇ (sigma) phase is formed, which reduces the strength and hot workability at the time of material preparation. Therefore, the upper limit of Fe is, for example, 10.0%. The preferred upper limit is 9.0%, more preferably 8.0%. On the other hand, when Fe may be added-free level (unavoidable impurity level) depending on the balance with the ⁇ 'forming element and Ni matrix, the lower limit of Fe is set to 0%.
  • Vanadium (V) V is one of the selective elements useful for strengthening the solid solution of the matrix and strengthening the grain boundaries by forming carbides.
  • the upper limit of V is, for example, 1.2%.
  • the preferred upper limit is 1.0%, more preferably 0.8%.
  • the lower limit of V is preferably 0.5%. If V may be an additive-free level (unavoidable impurity level) due to the balance with other alloying elements in the alloy, the lower limit of V is set to 0%.
  • Hafnium (Hf) Hf is one of the selective elements useful for improving the oxidation resistance of alloys and strengthening grain boundaries by forming carbides.
  • the upper limit of Hf is, for example, 3.0%, preferably 2.0%, and more preferably 1.5%.
  • the lower limit of Hf may be set to 0.1%.
  • the lower limit of Hf can be 0.5%, 0.7%, 1.0%.
  • Hf may be added-free level (unavoidable impurity level) depending on the balance with other alloying elements in the alloy, the lower limit of Hf is set to 0%.
  • B B is an element that improves grain boundary strength and improves creep strength and ductility.
  • B has a large effect of lowering the melting point, and when a coarse boride is formed, the hot workability at the time of material preparation is hindered. Therefore, for example, it does not exceed 0.300%. It is good to control it like this.
  • the preferred upper limit is 0.200%, more preferably 0.100%. It is more preferably 0.050%, and particularly preferably 0.020%. In order to obtain the above effect, the content is preferably at least 0.001%. A more preferable lower limit is 0.003%, and even more preferably 0.005%. Particularly preferably, it is 0.010%. If B may be added-free level (unavoidable impurity level) depending on the balance with other alloying elements in the alloy, the lower limit of B is set to 0%.
  • the upper limit of Zr is, for example, 0.300%.
  • the preferred upper limit is 0.250%, more preferably 0.200%. It is more preferably 0.100%, and particularly preferably 0.050%.
  • the content is preferably at least 0.001%.
  • a more preferable lower limit is 0.005%, and even more preferably 0.010%.
  • Ni but it may contain unavoidable impurities.
  • the method of producing the first processed material to be subjected to the heat treatment described later is not particularly limited.
  • the first processed material can be obtained by a melting method in which molten metal is poured into a mold to produce an ingot. Then, for the production of the ingot, for example, vacuum melting may be applied by combining conventional methods such as vacuum arc remelting and electroslag remelting.
  • the first processed material may be obtained by a powder metallurgy method.
  • the above-mentioned ingot or alloy ingot material produced by the powder metallurgy method is subjected to hot working such as hot forging, hot rolling, and hot extrusion, and then cooled to form a predetermined shape.
  • it may be finished as a processed material in the shape of a bar material.
  • the processing temperature (processing start temperature) in hot processing shall be 900 ° C. or higher.
  • the temperature is preferably 950 ° C. or higher, more preferably 1000 ° C. or higher, and even more preferably 1050 ° C. or higher. And it is realistic that the temperature is 1250 ° C or lower at the highest.
  • heat treatment such as soaking can be performed between these operations.
  • soaking for example, holding at 1100 ° C. to 1280 ° C. for 5 to 60 hours
  • soaking may be performed to eliminate the elemental segregation of the ingot.
  • soaking may be performed after finishing the shape of a material (billet) to be subjected to hot extrusion.
  • the processed material after cooling can be machined (for example, cutting, polishing, grinding, etc. for dimensional adjustment and various maintenance), if necessary.
  • the conditions for hot extrusion are preferably an extrusion temperature (heating temperature of the material) of 1050 ° C. to 1200 ° C., an extrusion ratio of 4 to 20, and an extrusion speed (stem speed) of 5 to 80 mm / s.
  • the cross-sectional diameter of the extruded material is, for example, 10 mm or more or more than 20 mm. And, for example, it is 200 mm or less.
  • the cross-sectional diameter of the bar may be, for example, 150 mm or less, 100 mm or less, 50 mm or less, 30 mm or less, 10 mm or less. Keeping the cross-sectional diameter of the bar small is that the number of plastic workings (number of passes) can be reduced when making wire rods or thin wires with a smaller cross-sectional diameter by cold plastic working, which will be described later. preferable.
  • a first heat treatment material (referred to as “material”) having the component composition described above is prepared.
  • the Ni-based superheat-resistant alloy obtained by subjecting this material to strong processing for example, processing having a processing rate of 30% or more
  • the plastic working of (c) described later can be further processed. become. Therefore, cold working can be performed up to a larger working rate without performing heat treatment during plastic working.
  • the Ni-based superheat-resistant alloy targeted by the present invention contains 0.05 to 0.25% by mass of carbon.
  • Various carbides typified by MC and M 23 C 6 are formed in the structure of the material produced by subjecting the material having this composition to hot working such as hot forging, hot rolling, and hot extrusion. There is. Then, coarse carbide 2 is precipitated in the structure of the material 1 (FIG. 2).
  • the carbides are crushed by plastic working to become fine carbides 4, but the fine carbides are present in the processed structure as a carbide aggregate in which the fine carbides are connected in the extending direction of the structure.
  • Material defects 5 are formed between the fine carbides. If plastic working is further performed as it is, the defects 5 between the fine carbides 4 may spread and combine with the adjacent defects 5 to become the starting point of cracking. Therefore, by adjusting the morphology of the carbides in the structure before the cold plastic working is performed, it is possible to suppress the occurrence of defects 5 in the cold plastic working. For example, in the cross-sectional structure in the stretching direction, the defect rate can be 0.5 area% or less. Therefore, it is possible to suppress the occurrence of cracks starting from material defects.
  • the temperature of the material (referred to as "first processed material") that has been once cooled after the hot working is applied to 900 ° C. or higher.
  • the first heat-treated material is obtained by heating and heat-treating the material.
  • the reason why the morphology of the charcoal in the material structure is adjusted by this heat treatment and the occurrence of cracks during the plastic working is suppressed is that the first processed material (extruded material) before the cold plastic working is shown in FIG.
  • the relationship between the temperature of the heat treatment applied and the cold plastic workability surface reduction rate
  • Coarse MC is formed in the structure of the first processed material produced by hot processing at the above processing temperature. Then, a "composite carbide" formed by contacting the MC and the M 23 C 6 is formed. When plastic working is performed on such a structure, it is considered that M 23 C 6 and MC are separated at the interface and cause material defects. Therefore, by heating the first processed material to a heat treatment temperature of 900 ° C. or higher, most of the MC reacts with the gamma phase and changes its form to M 23 C 6 , especially at the position of the surface layer described above. The proportion of complex carbides is reduced.
  • the above-mentioned composite carbide is separated at the interface between the MC and M 23 C 6 like the above-mentioned first processed material.
  • the material being plastically worked tends to be cracked due to carbides, and the plastic workability tends to be lower than that of the stage 1 material.
  • the crystal grain size of the first heat-treated material after the heat treatment grows from that of the first processed material, and the plastic workability of the first heat-treated material is the first. Can be superior to that of processed materials.
  • the first heat-treated material according to the present invention has an area ratio of M 23 C 6 of 4.0 area% or less, 3.0 area% or less, or 2 in its cross-sectional structure. It is less than 0.0 area%. Preferably, for example, it is 1.5 area% or less, 1.0 area% or less, 0.7 area% or less, 0.5 area% or less. And more preferably, it is 0.3 area% or less, 0.2 area% or less, and 0.1 area% or less (including the case of 0 area%). Further, the first heat-treated material according to the present invention preferably has a number density of M 23 C 6 of 10.0 ⁇ 10-2 / ⁇ m 2 or less or 7.0 ⁇ in its cross-sectional structure.
  • the first heat-treated material according to the present invention preferably has an MC area ratio of 12.0 area% or less or 10.0 area% or less in its cross-sectional structure. And, for example, it is 8.0 area% or less, 6.0 area% or less, 5.0 area% or less. Further, for example, it is preferably 0.1 area% or more, 1.0 area% or more, and 2.0 area% or more. More preferably, for example, it is 2.5 area% or more, 3.1 area% or more, 3.2 area% or more, and 3.5 area% or more. And more preferably, it is 3.8 area% or more, 4.2 area% or more, and 4.5 area% or more.
  • the first heat-treated material according to the present invention preferably has a cross-sectional structure in which the number density of MCs is, for example, 5.0 ⁇ 10-2 / ⁇ m 2 or less, or 3.0 ⁇ 10-2.
  • Pieces / ⁇ m 2 or less 2.5 ⁇ 10-2 pieces / ⁇ m 2 or less. More preferably, for example, it is 2.0 ⁇ 10-2 pieces / ⁇ m 2 or less, 1.7 ⁇ 10-2 pieces / ⁇ m 2 or less, and 1.5 ⁇ 10-2 pieces / ⁇ m 2 or less.
  • 0.1 ⁇ 10 -2 pieces / ⁇ m 2 or more 0.5 ⁇ 10 -2 pieces / ⁇ m 2 or more, 1.0 ⁇ 10 -2 pieces / ⁇ m 2 or more.
  • the upper limit of the heat treatment temperature is not particularly limited, but is about 1250 ° C.
  • the heat treatment temperature is preferably a temperature exceeding 1150 ° C.
  • the heat treatment time can be, for example, 30 minutes or more, 45 minutes or more, 60 minutes or more depending on the size and shape of the first processed material, and the upper limit is 180 minutes or less, 120 minutes or less, 90 minutes or less. It may be decided as appropriate.
  • the heat treatment is preferably carried out in a vacuum, a reducing atmosphere, an inert atmosphere such as Ar, in order to avoid surface oxidation, but may be carried out in an oxidizing atmosphere (for example, an atmospheric atmosphere). When the heat treatment is performed in an oxidizing atmosphere, an oxidation scale is formed on the surface.
  • the heat treatment time is preferably completed in a short time, for example, 150 minutes or less, 100 minutes or less, 80 minutes or less.
  • the crystal grain size of the structure of the first heat-treated material (the average grain size of the maximum diameter of the crystal grains described later) can be set to 100 ⁇ m or less. It is preferably 80 ⁇ m or less, more preferably 60 ⁇ m or less, still more preferably 40 ⁇ m or less, still more preferably 20 ⁇ m or less.
  • the refinement of crystal grains is effective for the production of nanocrystal grains.
  • the crystal grains generated by recrystallization have less distortion in the grains, and the grain boundaries also increase by making the crystal grains finer. Processing strain is evenly applied to the entire structure.
  • the crystal grain size of the structure of the first heat-treated material can be made 1.4 ⁇ m or more. By growing the crystal grains, this acts on the adjustment of the distribution form of the carbides described above, and the plastic workability of the first heat-treated material is improved. It is preferably 1.5 ⁇ m or more, more preferably 1.8 ⁇ m or more.
  • the crystal grain size of the first heat treatment material grows to, for example, 2.0 ⁇ m or more, 3.0 ⁇ m or more, 4.0 ⁇ m or more, 5.0 ⁇ m or more.
  • the heat treatment temperature is a temperature exceeding 1150 ° C. or a temperature of 1200 ° C. or higher, it grows to a value of 7.0 ⁇ m or higher or 9.0 ⁇ m or higher.
  • the hardness of the first heat-treated material is not limited. Therefore, the cooling after the above heat treatment may be rapid cooling, air cooling, air cooling, furnace cooling, or the like.
  • the hardness of the first heat-treated material can be, for example, 460 HV or less or 450 HV or less. More preferably, it is 430 HV or less. It is more preferably 400 HV or less, and even more preferably 380 HV or less.
  • the lower limit of the hardness of the first heat-treated material is not particularly limited, but is realistically about 250 HV. Then, the hardness of the first heat-treated material can be set to 300 HV or more. The hardness of the first heat-treated material can be measured in cross section thereof.
  • (C) Step of Producing Second Processed Material cold plastic working is performed on the above material (first heat-treated material). Since the above-mentioned material is excellent in plastic workability and is also excellent in plastic workability during plastic working, it is possible to perform a plurality of times of cold plastic working in which the cumulative work rate from the material is 40% or more.
  • the present invention produces a Ni-based superheat resistant alloy by "cold" plastic working, as opposed to conventional "hot” plastic working.
  • a cumulative working rate of 40% or more can be obtained by cold plastic working, and the alloy is processed by hot plastic working.
  • the plastic working temperature in the present invention is preferably "500 ° C. or lower". It is more preferably 300 ° C. or lower, still more preferably 100 ° C. or lower, and even more preferably 50 ° C. or lower (for example, room temperature).
  • the method for producing a Ni-based superheat-resistant alloy of the present invention can be applied to the production of various shapes. Although it is suitable for the wire rod form, it can also be applied to a plate material, a strip material, and the like. Therefore, the Ni-based superheat-resistant alloy produced by the production method of the present invention has an intermediate product shape of a wire material, a sheet material, and a strip material, and also has a wire material. It may be the final product shape of a product), a sheet product, or a strip product. Regarding the relationship between the dimensions of the plate material (thin plate) and the strip material (thin strip), the wire diameter (diameter) of the wire rod (thin wire) can be read as the plate thickness or the strip thickness.
  • the hot-extruded material of the Ni-based superheat-resistant alloy is a bar material
  • the bar material processing for compressing the cross section can be performed.
  • the processing rate is expressed by the surface reduction rate when the bar is swaged or the die is drawn.
  • the surface reduction rate is the relationship between the cross-sectional area A 0 of the bar material before plastic working and the cross-sectional area A 1 of the wire rod or thin wire after plastic working. [(A 0- A 1 ) / A 0 ] x 100 (%) (1) It is calculated by the formula of.
  • the processing rate is expressed as a rolling reduction rate.
  • the cumulative working rate indicates the working rate of the final work piece with respect to the material when plastic working is performed a plurality of times or over a plurality of passes.
  • the cumulative working rate from the above-mentioned cold plastic working material is increased to 40% or more.
  • the plastic working at this working rate is not completed by one plastic working, but can be completed by dividing into a plurality of plastic working. No heat treatment is performed during multiple plastic workings.
  • the heat treatment referred to here is a heat treatment in a high temperature region where recovery or recrystallization occurs, and is, for example, a heat treatment for heating to a temperature exceeding 500 ° C.
  • heat treatment is not required between the cold working passes, and a plurality of cold strong working can be continuously performed to increase the cumulative working rate (cumulative surface reduction rate).
  • the formation of nanocrystal grains can be observed in the structure.
  • the cumulative working rate should be 40% or more.
  • the cumulative processing rate is preferably 45% or more, more preferably 50% or more, still more preferably 55% or more.
  • the upper limit of the cumulative processing rate is not particularly limited, but can be, for example, about 70%. Further, it can be about 80% and about 90%. It can exceed 90%.
  • plastic working is performed up to the target dimensions (final product dimensions).
  • the hardness of the material of the final product size can be 500 HV or more.
  • the processing rate (surface reduction rate) by one plastic working (pass) is preferably 30% at maximum. More preferably, it can be up to 28%.
  • pass used in the present specification, in the above-mentioned types of plastic working such as swaging, die wire drawing, and rolling, when plastic working is performed by one (or a pair of) dies or rolls, "1" is used. It can be called a "pass”.
  • 1 pass refers to the above-mentioned one-time "plastic working”.
  • the material of the Ni-based super heat-resistant alloy is a bar
  • plastic working that compresses the cross-sectional area of the bar from the peripheral surface of the bar toward the axis is effective.
  • a plastic working method in which pressure is evenly applied to the entire circumference of the bar to be plastic working is advantageous.
  • a specific example of this is swaging.
  • the swaging process is preferable for the formation of nanocrystal grains because the peripheral surface of the bar is forged while rotating a plurality of dies surrounding the entire circumference of the bar.
  • other plastic working such as cassette roller die drawing and hole type die drawing can also be applied.
  • the alloy obtained by the above-mentioned cold plastic working can be used as the final product shape.
  • it can be a "thin line", a "thin plate", or a "thin band”.
  • the thin wire has a wire diameter (diameter) of 5 mm or less, 4 mm or less, 3 mm or less, and finally 2 mm or less and 1 mm or less.
  • the thin plate and the thin band have a thickness of, for example, 5 mm or less, 4 mm or less, 3 mm or less, and finally 2 mm or less and 1 mm or less.
  • the thin wire, the thin plate, and the thin band are longer in length, for example, 50 times or more, 100 times or more, and 300 times or more with respect to the above wire diameter and thickness.
  • the alloy in this case is, for example, a linear structure in which the ⁇ phase and the ⁇ 'phase in the structure extend in the stretching direction.
  • the hardness of the alloy is 500 HV or more.
  • processing defects are present in the alloy.
  • the defect rate is a processing defect exceeding 0.5 area%.
  • it is 1.0 area% or less. The existence of such processing defects does not cause any problem in that no further plastic working is performed.
  • a desired equiaxed crystal structure can be obtained by performing heat treatment at a temperature of 900 ° C. or higher (for example, holding at a temperature of 900 ° C. to 1200 ° C. for 30 minutes to 3 hours).
  • the hardness can be adjusted to less than 500 HV, 450 HV or less, and 420 HV or less. And, for example, the hardness is 300 HV or more or 350 HV or more. This makes it easy to bend or cut the final product into a form suitable for the transportation form and usage form.
  • the processing defect can be repaired by this heat treatment, and for example, the defect rate can be reduced to 0.5 area% or less in the cross-sectional structure including the central axis in the length direction (that is, the plastic working direction) of the alloy. Then, combined with the effect of the heat treatment performed in the state of the material before plastic working, the above defect rate can be further reduced to 0.4 area% or less, 0.3 area% or less, and 0.2 area% or less.
  • This heat treatment can be performed when it is desired to reduce processing defects in the usage form of the Ni-based superheat resistant alloy.
  • the crystal grains in the equiaxed crystal structure are grown by performing the above heat treatment.
  • the grain size of the crystal grains may reach the maximum wire diameter. Then, if the effect of suppressing the coarsening of the crystal grains (pinning effect) effectively functions by the carbide aggregates connected in the stretching direction, the growth of the crystal grains is suppressed.
  • the size of the crystal grains after the heat treatment is the average particle size in the cross-sectional structure, for example, 100 ⁇ m or less, 75 ⁇ m or less, 50 ⁇ m or less, 25 ⁇ m or less, 10 ⁇ m or less.
  • the final heat treatment is preferably carried out in an inert atmosphere such as vacuum, reducing atmosphere or Ar in order to avoid surface oxidation, but may be carried out in an oxidizing atmosphere (for example, atmospheric atmosphere).
  • an oxidation scale is formed on the surface. If it may interfere with the quality of the product, the formed oxide scale may be removed mechanically or chemically, for example by polishing or grinding. In the case of wire rod production, it is preferable to remove the scale by using centerless polishing.
  • the surface of the final product can be mechanically or chemically finished by, for example, polishing or grinding.
  • Ni-based super heat-resistant alloy according to the present invention has been described above. According to the present invention, since plastic working of a Ni-based superheat resistant alloy having a large cumulative working rate (for example, 40% or more) can be performed at a temperature of 500 ° C. or lower, it is complicated to repeat hot working and heat treatment. Strong cold plastic working is possible without the need for various manufacturing processes, and heat treatment between plastic working can be omitted. Therefore, the simplification of the process can be achieved and the manufacturing cost can be reduced. Further, if necessary, a product having a defect rate of 1.0 area% or less and few processing defects, particularly a wire rod, can be obtained. This effect is particularly remarkable for Ni-based superheat-resistant alloys having a large carbon content in which processing defects are likely to occur.
  • a defect rate for example, 40% or more
  • (A) Step of Producing First Processed Material The molten metal prepared by vacuum melting was cast to prepare an ingot A of a columnar Ni-based superheat resistant alloy having a diameter of 100 mm and a mass of 10 kg.
  • the component composition of ingot A is shown in Table 1 (mass%).
  • Table 1 also shows the " ⁇ 'molar rate" of the above ingot A. This value was calculated using commercially available thermodynamic equilibrium calculation software "JMatPro (Version 8.0.1, a product of Center Software Ltd.)". The content of each element listed in Table 1 was input to this thermodynamic equilibrium calculation software to obtain the above " ⁇ 'molar ratio" (%).
  • the ingot A having this composition is heat-treated at a holding temperature of 1200 ° C. and a holding time of 8 hours, cooled in a furnace, and then a cylindrical material having a length of 150 mm and a diameter of 60 mm is collected in a direction parallel to the length of the ingot A. did.
  • This cylindrical material was sealed in SUS304 capsules and subjected to hot extrusion.
  • the conditions for hot extrusion were an extrusion temperature of 1100 ° C., an extrusion ratio of 10 (including capsules), and an extrusion stem speed of 15 mm / s. Hot extrusion was performed, the mixture was cooled to room temperature, and then the capsule material was removed to obtain an extruded material (first processed material) having a diameter of 27 mm.
  • Materials 1 to 7 were cut in half parallel to the axial direction, and the microstructure (crystal grain size, carbide morphology) and hardness of the cut surface were evaluated.
  • the cross-sectional microstructures of the cut surfaces as observed by scanning electron microscopes (SEM images) of materials 1 to 7 are shown in the order of FIGS. 4 to 10.
  • the magnification of the cross-sectional microstructure can be basically 2000 times.
  • the crystal grain size is large, the magnification can be reduced in order to confirm a larger number of crystal grains.
  • the crystal grain size by EBSD described later exceeds 8 ⁇ m, the magnification is 1000 times. (Materials 6 and 7).
  • the observation location was a position within a distance of D / 4 (D is the diameter of the extruded material) from the surface of the material toward the axis on the above-mentioned cut surface.
  • D is the diameter of the extruded material
  • Various carbide Each microstructure (MC, M 23 C 6, etc.) where it was observed (dispersion in the figure), the microstructure of the material 6, 7 of the heat treatment temperature is 1200 ° C., M 23 C No. 6 was substantially not confirmed (0.1 ⁇ 10-2 pieces / ⁇ m 2 or less).
  • the hardness was evaluated at a position within a distance of D / 2 from the surface of the material toward the axis (that is, the position of the axis) on the above-mentioned cut surface.
  • the distribution form of MC is a mapping diagram of Nb, which is a metal element that composes it, and that of M 23 C 6 is It can also be confirmed in the Cr mapping diagram.
  • the Nb mapping diagram and the Cr mapping diagram are shown in FIGS. 4 to 10.
  • Cr mapping diagram of FIGS. 9 (material 6) and 10 (material 7) Cr is evenly distributed over the entire surface (that is, Cr is solid-solved in the base), and Cr is unevenly distributed. (Ie, no carbides of Cr) were found. Then, the mapping diagram of FIGS.
  • 4 to 10 is set as one field of view (50 ⁇ m ⁇ 65 ⁇ m at 2000 times magnification, 100 ⁇ m ⁇ 130 ⁇ m at 1000 times magnification), and the area ratio and number density of carbides confirmed in this one field of view are shown in this one field of view. (That is, 100 ⁇ m ⁇ 130 ⁇ m at a magnification of 2000 times, 200 ⁇ m ⁇ 260 ⁇ m at a magnification of 1000 times), and the average value of these four fields of view is the value according to the present invention. It was determined as the carbide form of the heat treatment material of 1.
  • the EBSD measurement conditions are as follows: Magnification: 2000 using the EBSD measurement system "Aztec Version 3.2 (Oxford Instruments)" attached to the above scanning electron microscope (JIB-4700F (JEOL Ltd.)). Double (1000 times for materials 6 and 7), scan step: 0.1 ⁇ m, and the definition of crystal grains was defined as grain boundaries with an orientation difference of 15 ° or more. The EBSD images at this time are also shown in FIGS. 4 to 10.
  • the grains excluding those of the MC carbide confirmed by the above EPMA are defined as crystal grains, and for these crystal grains, the maximum diameter (maximum length) of each crystal grain is used. ) And the number of crystals, the crystal grain size distribution was confirmed, and the average diameter of the maximum diameter of the crystal grains was determined. Then, the average diameter of the maximum diameters of the crystal grains obtained in the EBSD image of this one field of view is obtained in the same manner as in the case of the above-mentioned carbide form in another three fields of view vertically and horizontally adjacent to this one field of view. The average value of the values for the four fields of view was determined as the crystal grain size of the first heat-treated material according to the present invention.
  • FIGS. 11 and 11 show the relationship between the heat treatment temperature and the carbide morphology (area ratio, number density), crystal grain size and hardness, except for the material 7 (air-cooled). 12, FIG. 13 and FIG. 14 are shown in this order.
  • the area ratio and number density of MC and the area ratio and number density of M 23 C 6 are reversed between 1100 ° C. and 1150 ° C., and the MC However, the area ratio and the number density are high.
  • stage 1 the relationship between the temperature of the heat treatment applied to the extruded material before the cold plastic working and the cold plastic working (surface reduction rate) is shown in FIG. From FIG. 3, by heat-treating the extruded material, the workability of the material was dramatically improved (stage 1). Then, although the workability tends to decrease once when the heat treatment temperature exceeds 1000 ° C. (stage 2), the initial workability is maintained and the heat treatment temperature rises again when the heat treatment temperature exceeds 1150 ° C. The workability was further improved (stage 3).
  • Ni-based superheat-resistant alloy As described above, it has been shown that a thin wire of a Ni-based superheat-resistant alloy can be produced by cold plastic working according to the examples.
  • the Ni-based superheat-resistant alloy produced by the production method of the present invention can be processed into a wire rod or the like having an arbitrary wire diameter by plastic working in the cold.
  • this embodiment was performed on the production of wire rods, it can also be applied to the production of other shapes such as plate materials.

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Abstract

L'invention concerne : un procédé de production d'un alliage super résistant à la chaleur à base de Ni présentant une composition constitutive telle que la quantité de précipitation à l'équilibre d'une phase gamma-prime à 700°C est de 35 % en mole ou plus; et un alliage super résistant à la chaleur à base de Ni. Ce procédé comprend : (a) une étape de production d'un premier matériau traité par soumission d'un matériau, dans lequel la teneur en carbone est de 0,05-0,25 % en masse et qui présente une composition constitutive telle que la quantité de précipitation à l'équilibre d'une phase gamma-prime à 700°C est de 35 % en mole ou plus, à un travail plastique à une température de 900°C ou plus, puis par refroidissement de celui-ci; et (b) une étape de production d'un premier matériau traité thermiquement par mise en oeuvre d'un traitement thermique par chauffage du premier matériau traité à une température de 900°C ou plus. Ce procédé comprend en outre (c) une étape de production d'un deuxième matériau traité par soumission du premier matériau traité thermiquement à un travail plastique à une température de 500°C ou moins. La présente invention concerne également un alliage super résistant à la chaleur à base de Ni qui est destiné au travail plastique à froid, qui présente la composition constitutive susmentionnée et qui présente une structure en coupe transversale dans laquelle le rapport surfacique de M23C6 est de 4,0 % en surface et le diamètre moyen de particule du diamètre maximum des grains cristallins est de 1,4-100 µm.
PCT/JP2020/001725 2019-03-26 2020-01-20 Procédé de production d'un alliage super résistant à la chaleur à base de ni et alliage super résistant à la chaleur à base de ni WO2020195049A1 (fr)

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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
CN113584370A (zh) * 2021-07-30 2021-11-02 北京北冶功能材料有限公司 一种低密度高强度高熵高温合金及其制备方法
CN113604706A (zh) * 2021-07-30 2021-11-05 北京北冶功能材料有限公司 一种低密度低膨胀高熵高温合金及其制备方法
CN114752817A (zh) * 2022-04-08 2022-07-15 南京工程学院 一种高温合金模具材料及其制备方法和应用
KR102684607B1 (ko) * 2021-04-06 2024-07-11 다이도 토쿠슈코 카부시키가이샤 내열 합금 부재, 이것에 이용하는 소재 및 이들의 제조 방법

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JP2017514998A (ja) * 2014-03-14 2017-06-08 オウベル・アンド・デュヴァル 析出硬化ニッケル合金、前記合金でできた部品、及びその製造方法
WO2018155446A1 (fr) * 2017-02-21 2018-08-30 日立金属株式会社 Alliage super-résistant à la chaleur à base de ni et son procédé de fabrication
WO2019004176A1 (fr) * 2017-06-30 2019-01-03 日立金属株式会社 Procédé de fabrication de fil de superalliage résistant à la chaleur à base de ni, et fil de superalliage résistant à la chaleur à base de ni

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JP2014070230A (ja) * 2012-09-27 2014-04-21 Hitachi Metals Ltd Ｎｉ基超耐熱合金の製造方法
JP2017514998A (ja) * 2014-03-14 2017-06-08 オウベル・アンド・デュヴァル 析出硬化ニッケル合金、前記合金でできた部品、及びその製造方法
WO2018155446A1 (fr) * 2017-02-21 2018-08-30 日立金属株式会社 Alliage super-résistant à la chaleur à base de ni et son procédé de fabrication
WO2019004176A1 (fr) * 2017-06-30 2019-01-03 日立金属株式会社 Procédé de fabrication de fil de superalliage résistant à la chaleur à base de ni, et fil de superalliage résistant à la chaleur à base de ni

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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
KR102684607B1 (ko) * 2021-04-06 2024-07-11 다이도 토쿠슈코 카부시키가이샤 내열 합금 부재, 이것에 이용하는 소재 및 이들의 제조 방법
CN113584370A (zh) * 2021-07-30 2021-11-02 北京北冶功能材料有限公司 一种低密度高强度高熵高温合金及其制备方法
CN113604706A (zh) * 2021-07-30 2021-11-05 北京北冶功能材料有限公司 一种低密度低膨胀高熵高温合金及其制备方法
CN114752817A (zh) * 2022-04-08 2022-07-15 南京工程学院 一种高温合金模具材料及其制备方法和应用
CN114752817B (zh) * 2022-04-08 2022-09-23 南京工程学院 一种高温合金模具材料及其制备方法和应用

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