[go: up one dir, main page]

WO2024162379A1 - Nickel-based superalloy, nickel-based superalloy powder, and method for manufacturing molded body - Google Patents

Nickel-based superalloy, nickel-based superalloy powder, and method for manufacturing molded body Download PDF

Info

Publication number
WO2024162379A1
WO2024162379A1 PCT/JP2024/003011 JP2024003011W WO2024162379A1 WO 2024162379 A1 WO2024162379 A1 WO 2024162379A1 JP 2024003011 W JP2024003011 W JP 2024003011W WO 2024162379 A1 WO2024162379 A1 WO 2024162379A1
Authority
WO
WIPO (PCT)
Prior art keywords
nickel
based superalloy
shaped body
powder
content
Prior art date
Application number
PCT/JP2024/003011
Other languages
French (fr)
Japanese (ja)
Inventor
誠 東
真也 日比野
利茂 藤光
直人 ▲高▼梨
具教 北嶋
誠 渡邊
雅彦 出村
貴由 中野
Original Assignee
川崎重工業株式会社
国立研究開発法人物質・材料研究機構
国立大学法人大阪大学
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 川崎重工業株式会社, 国立研究開発法人物質・材料研究機構, 国立大学法人大阪大学 filed Critical 川崎重工業株式会社
Publication of WO2024162379A1 publication Critical patent/WO2024162379A1/en

Links

Images

Classifications

    • 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
    • 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
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/20—Direct sintering or melting
    • B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
    • 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
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/30—Process control
    • B22F10/34—Process control of powder characteristics, e.g. density, oxidation or flowability
    • 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
    • B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
    • B22F10/60—Treatment of workpieces or articles after build-up
    • B22F10/64—Treatment of workpieces or articles after build-up by thermal means
    • 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
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y10/00—Processes of additive manufacturing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B33—ADDITIVE MANUFACTURING TECHNOLOGY
    • B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
    • B33Y70/00—Materials specially adapted for additive manufacturing
    • 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
    • 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
    • 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

Definitions

  • This disclosure relates to nickel-based superalloys and nickel-based superalloy powders, as well as to methods for manufacturing shaped bodies using the nickel-based superalloy powders.
  • Nickel-based superalloys are known to have excellent strength and oxidation resistance at high temperatures. For this reason, they are used in components that are subjected to high stress in high-temperature, oxidizing environments, such as aircraft engines and turbines used in thermal power plants.
  • IN738LC IN is an abbreviation for Inconel (registered trademark)
  • Inconel registered trademark
  • the additive manufacturing method is a method of manufacturing shaped objects by repeatedly spreading powder to form layers and irradiating the layers with energy rays to melt and solidify at least a portion of the layers.
  • the inventors invented a nickel-based superalloy that can precipitate a gamma-' phase at a volume fraction similar to that of IN738LC and that generates fewer cracks during rapid melting and rapid solidification processes such as welding and additive manufacturing (Patent Application No. 2021-138686).
  • a nickel-based superalloy has excellent high-temperature strength because it precipitates a gamma-' phase at a volume fraction similar to that of IN738LC through heat treatment.
  • this nickel-based superalloy has inferior ductility at high temperatures compared to IN738LC, and it is therefore desirable to improve the ductility at high temperatures.
  • the present disclosure therefore aims to provide a nickel-based superalloy with good ductility at high temperatures. It also aims to provide a nickel-based superalloy powder composed of particles of the nickel-based superalloy, and to provide a method for manufacturing a shaped body using the nickel-based superalloy powder.
  • the present disclosure provides a nickel-base superalloy containing, by mass percentage, 4.8% to 5.1% Al, 1.4% to 1.7% Ti, 14.2% to 19.2% Cr, 4.5% to 12.4% Co, 0.7% to 1.5% Ta, 2.8% to 5.3% W, 4.1% or less Mo, 0.02% to 0.15% C, 0.002% to 0.02% B, and 0.06% Zr, and having a boron equivalent Z defined by the following formula of 0.007 to 0.018.
  • Z X+10.811/91.224 ⁇ Y
  • Y content by mass percentage
  • the present disclosure provides a nickel-base superalloy powder composed of particles of the above-mentioned nickel-base superalloy.
  • the present disclosure provides a method for producing a shaped body, which comprises repeatedly spreading the nickel-based superalloy powder to form a layer and irradiating the layer with energy rays to melt and solidify at least a portion of the layer, thereby producing a shaped body.
  • the present disclosure provides a nickel-based superalloy having good ductility at high temperatures, a nickel-based superalloy powder composed of particles of the nickel-based superalloy, and a method for manufacturing a shaped body using the nickel-based superalloy powder.
  • FIG. 1 is a schematic diagram of an additive manufacturing apparatus.
  • FIG. 2 is a diagram showing the shape of a test piece.
  • 1 is a graph showing the relationship between boron equivalent and breaking elongation in Example 1 and Comparative Examples 1 to 5.
  • 1 is a graph showing the relationship between boron equivalent and amount of cracks in Example 1 and Comparative Examples 1 to 5.
  • 1 is a graph showing the relationship between boron equivalent and 0.2% proof stress in Example 1 and Comparative Examples 1, 2, 4, and 5.
  • 1 is a graph showing the relationship between boron equivalent and tensile strength in Example 1 and Comparative Examples 1-5.
  • Nickel-based superalloy contains, as essential components other than Ni, the following mass percentages: 4.8% to 5.1% Al, 1.4% to 1.7% Ti, 14.2% to 19.2% Cr, 4.5% to 12.4% Co, 0.7% to 1.5% Ta, 2.8% to 5.3% W, 0.02% to 0.15% C, and 0.002% to 0.02% B.
  • mass percentages 4.8% to 5.1% Al, 1.4% to 1.7% Ti, 14.2% to 19.2% Cr, 4.5% to 12.4% Co, 0.7% to 1.5% Ta, 2.8% to 5.3% W, 0.02% to 0.15% C, and 0.002% to 0.02% B.
  • “%” means “mass%”.
  • the nickel-based superalloy may also contain at least one of 4.1% or less Mo and 0.06% or less Zr as other optional components.
  • the balance of the nickel-based superalloy other than the above-mentioned components is Ni and unavoidable impurities.
  • the unavoidable impurities include Si, Mn, P, S, Cu, Nb, Fe, O, N, etc.
  • the boron equivalent Z defined by the following formula (1) is 0.007 or more and 0.018 or less.
  • Z X+10.811/91.224 ⁇ Y...(1)
  • Y Zr content by mass percentage
  • Al has the effect of forming the ⁇ ' phase, and the volume fraction of the ⁇ ' phase increases as the Al content increases. Therefore, by setting the Al content to 4.8% or more and 5.8% or less, the volume fraction of the ⁇ ' phase can be kept within a specified range.
  • Ti Like Al, Ti also has the effect of forming the ⁇ ' phase in nickel-based superalloys having the above-mentioned composition. Therefore, by making the Ti content 1.4% or more, the volume fraction of the ⁇ ' phase can be increased.
  • Ti has the effect of widening the solidification brittle temperature range (BTR), albeit slightly. Therefore, by making the Ti content 1.7% or less, it is possible to prevent the BTR from becoming too wide.
  • the BTR is the difference between the liquidus temperature and solidus temperature during rapid solidification, and the narrower the BTR, the fewer cracks that occur during the rapid melting and rapid solidification process.
  • Cr has the effect of improving oxidation resistance and solid solution strengthening of the nickel solid solution phase. Therefore, by making the Cr content 14.2% or more, the nickel-based superalloy can be made to have excellent oxidation resistance and mechanical strength.
  • Cr has the effect of reducing, albeit slightly, the volume fraction of the ⁇ ' phase and the effect of widening the BTR. Therefore, by making the Cr content 19.2% or less, it is possible to increase the volume fraction of the ⁇ ' phase while preventing the BTR from becoming too wide.
  • Co has a solid solution strengthening effect on the nickel solid solution phase in nickel-based superalloys having the above-mentioned composition. Therefore, by making the Co content 4.5% or more, the mechanical strength of the nickel-based superalloy can be made sufficient.
  • Co has the effect of reducing the volume fraction of the ⁇ ' phase, albeit slightly, and the effect of widening the BTR. Therefore, by making the Co content 12.4% or less, it is possible to increase the volume fraction of the ⁇ ' phase while preventing the BTR from becoming too wide.
  • Ta has a solid solution strengthening effect on the ⁇ ' phase in nickel-based superalloys having the above-mentioned composition, and the volume fraction of the ⁇ ' phase increases as the Ta content increases. Therefore, by setting the Ta content to 0.7% or more and 1.5% or less, the volume fraction of the ⁇ ' phase can be kept within a specified range.
  • W has a solid solution strengthening effect on the nickel solid solution phase in nickel-based superalloys having the above-mentioned composition. For this reason, by making the W content 2.8% or more, the nickel-based superalloy can be made to have excellent mechanical strength.
  • W has the effect of increasing the volume fraction of the ⁇ ' phase and, although it is small, widening the BTR. For this reason, by making the W content 5.3% or less, it is possible to keep the volume fraction of the ⁇ ' phase within a specified range while preventing the BTR from becoming too wide.
  • C has the effect of narrowing the BTR in nickel-based superalloys having the above-mentioned composition. For this reason, by making the C content 0.024% or more, a nickel-based superalloy with a narrow BTR and suppressed crack generation during rapid solidification can be obtained.
  • C can react with other metal elements to form carbides at grain boundaries, which can cause a decrease in corrosion resistance and toughness. For this reason, by making the C content 0.15% or less, it is possible to suppress the formation of carbides at grain boundaries.
  • B has the effect of increasing the ductility at high temperatures in nickel-based superalloys having the above-mentioned composition. Therefore, by making the B content 0.002% or more, a nickel-based superalloy with improved ductility at high temperatures can be obtained. On the other hand, B has the effect of widening the BTR. Therefore, by making the B content 0.02% or less, the occurrence of cracks can be suppressed.
  • the B content is 0.004% or more and 0.012% or less.
  • Mo has a solid solution strengthening effect on the nickel solid solution phase in nickel-based superalloys having the above-mentioned composition. Therefore, by including Mo in a nickel-based superalloy, the nickel-based superalloy can have excellent mechanical strength.
  • Mo has the effect of increasing the volume fraction of the ⁇ ' phase. Therefore, by keeping the Mo content at 4.1% or less, the volume fraction of the ⁇ ' phase can be kept within a specified range.
  • Zr has the effect of widening the BTR in nickel-based superalloys having the above-mentioned composition. Therefore, by making the Zr content 0.06% or less, it is possible to prevent the BTR from becoming too wide. In addition, since Zr also has the effect of increasing ductility at high temperatures, it is preferable that the Zr content be 0.02% or more.
  • the fact that the nickel-base superalloy has the above-mentioned composition can be confirmed by any of the following methods: energy dispersive X-ray spectroscopy (EDX), wavelength dispersive X-ray spectroscopy (WDS), X-ray fluorescence spectroscopy (XRF), inductively coupled plasma (ICP) optical emission spectroscopy, combustion infrared absorption spectroscopy, heating and fusion infrared absorption spectroscopy, or wet chemical analysis.
  • energy dispersive X-ray spectroscopy EDX
  • WDS wavelength dispersive X-ray spectroscopy
  • XRF X-ray fluorescence spectroscopy
  • ICP inductively coupled plasma
  • a nickel-based superalloy powder according to another aspect of the present disclosure is composed of particles of a nickel-based superalloy having the above-mentioned composition.
  • the nickel-based superalloy powder is applied to an additive manufacturing method, the occurrence of cracks in a shaped body can be suppressed.
  • the particle size of the nickel-based superalloy powder and the shape of the particles constituting the powder are not particularly limited.
  • the particle size can be, for example, one that passes through a sieve with a nominal mesh size of 106 ⁇ m as specified in JIS Z 8801 (2019), and preferably one that passes through a sieve with a nominal mesh size of 75 ⁇ m, 63 ⁇ m, or 53 ⁇ m.
  • the lower limit of the particle size can be 1 ⁇ m or more, and preferably 5 ⁇ m or more, 15 ⁇ m or more, or 25 ⁇ m or more.
  • the shape of the particles can be, for example, spherical.
  • the method for producing the nickel-based superalloy powder is not particularly limited, and any method that can produce powder of a specified particle size and shape can be appropriately selected from among known methods for producing metal powders.
  • One example is the gas atomization method, in which high-pressure gas is sprayed onto molten metal to cool it and obtain metal particles.
  • the gas atomization method has the advantage of obtaining spherical particles while suppressing oxidation of the metal.
  • the obtained nickel-based superalloy powder may be used directly to produce a shaped body, or it may be used to produce a shaped body after being divided into spheres using a sieve or the like to make the particle size uniform.
  • a method for producing a shaped body according to still another aspect of the present disclosure is a method for producing a shaped body 7 by repeatedly spreading the above-mentioned nickel-based superalloy powder 3 to form a layer 5 and irradiating the layer 5 with an energy ray 6 to melt and solidify at least a portion of the layer 5.
  • a shaped body 7 with few cracks can be obtained.
  • the manufacturing method is carried out using, for example, an additive manufacturing device 1 as shown in FIG. 1.
  • the additive manufacturing device used in the manufacturing method is not limited to this, and may be appropriately selected from known additive manufacturing devices for metals.
  • the additive manufacturing device 1 includes a storage tank 31 that stores nickel-based superalloy powder 3, a modeling chamber 32 adjacent to the storage tank 31, and a collector 33 located on the opposite side of the modeling chamber 32 from the storage tank 31.
  • the additive manufacturing device 1 also includes a supply piston 21 that forms the bottom of the storage tank 31, a modeling piston 22 that forms the bottom of the modeling chamber 32, and a recovery piston 23 that forms the bottom of the collector 33.
  • the additive manufacturing device 1 further includes a recoater 4 that moves from above the storage tank 31 to above the collector 33, and an energy ray emission device that emits energy rays 6 above the modeling chamber 32.
  • the supply piston 21 rises, and the nickel-based superalloy powder 3 in the storage tank 31 is pushed up to a predetermined height.
  • the recoater 4 moves, and the pushed-up nickel-based superalloy powder 3 is supplied to the manufacturing chamber 32 and spread out on a flat surface to form a layer 5.
  • the excess nickel-based superalloy powder 3 falls into the collector 33.
  • the layer 5 is then irradiated with energy rays 6 in a predetermined pattern, which melts and solidifies at least a portion of the layer 5. This forms a specific cross section in the shaped body 7. This process is repeated to stack the specific cross sections and produce the shaped body 7.
  • the energy beam 6 is irradiated onto the layer 5 in a predetermined pattern while the energy beam 6 is scanned over the surface of the layer 5 at a predetermined pitch and a predetermined speed.
  • the energy beam 6 is a laser or an electron beam.
  • the manufactured shaped body 7 may be heat treated. Examples of heat treatments that may be performed on the shaped body 7 include solution treatment and aging treatment. The solution treatment and aging treatment are performed in this order. The solution treatment and aging treatment may be performed separately using different heat treatment devices, or may be performed consecutively using the same heat treatment device. Furthermore, the shaped body 7 may be subjected to HIP (Hot Isostatic Pressing) treatment as a heat treatment prior to the solution treatment.
  • HIP Hot Isostatic Pressing
  • the shaped body 7 may be held at a temperature of 1100°C to 1250°C for 1 hour to 5 hours, and then cooled to 900°C or less. It is preferable that the cooling at this time be performed in a relatively short time (rapid cooling). Also, as an aging effect, the solution-treated shaped body 7 may be held at a temperature of 800°C to 900°C for 12 hours to 48 hours, and then cooled to room temperature. It is also preferable that the cooling at this time be performed in a relatively short time (rapid cooling).
  • the heat treatment atmosphere is not particularly limited.
  • the heat treatment atmosphere may be vacuum, argon, or air.
  • cooling may be water cooling, air cooling, oil cooling, or gas fan cooling.
  • Example 1 A nickel-based superalloy powder was prepared with an alloy composition of 5% Al, 1.6% Ti, 17.5% Cr, 8.6% Co, 1% Ta, 4% W, 1.9% Mo, 0.06% C, 0.05% B, 0.07% Zr, and the balance being Ni and unavoidable impurities.
  • the nickel-based superalloy powder was loaded into an additive manufacturing device (M290, manufactured by EOS), and a first object was manufactured under the conditions of a laser output of 210 W, a scanning speed of 1200 mm/s, a scanning pitch of 60 ⁇ m, and a layer thickness of 40 ⁇ m.
  • a second object was manufactured by changing the laser output to 270 W, the scanning speed to 1000 mm/s, and the scanning pitch to 70 ⁇ m.
  • the shape of the first object was a rectangular parallelepiped with a width of 60 mm, a depth of 10 mm, and a height (in the layering direction) of 10 mm
  • the shape of the second object was a rectangular parallelepiped with a width of 6 mm, a depth of 5 mm, and a height (in the layering direction) of 4.5 mm.
  • the second shaped body was not subjected to heat treatment, while the first shaped body was subjected to heat treatment as follows. First, the first shaped body was placed in a heat treatment furnace, and as a solution treatment, the shaped body was held at 1170°C for 2 hours while the atmosphere in the heat treatment furnace was argon at 50 Pa to 70 Pa, and then rapidly cooled to room temperature by gas fan cooling with 400 kPa argon. Next, as an aging treatment, the shaped body was held at 840°C for 24 hours while the atmosphere in the heat treatment furnace was argon at 50 Pa to 70 Pa, and then rapidly cooled to room temperature by gas fan cooling with 400 kPa argon.
  • Example 1 A first heat-treated shaped body and a second unheat-treated shaped body were obtained in the same manner as in Example 1, except that a nickel-based superalloy powder was used that had an alloy composition of 5% Al, 1.6% Ti, 17.5% Cr, 8.6% Co, 1% Ta, 4% W, 1.9% Mo, 0.06% C, 0.04% Zr, and the balance being Ni and unavoidable impurities.
  • Example 2 A commercially available IN738LC-P powder was used as the nickel-based superalloy powder, and a first heat-treated shaped body and a second unheat-treated shaped body were obtained in the same manner as in Example 1, except for the following heat treatment.
  • HIP treatment was performed before solution treatment as a heat treatment.
  • the atmosphere in the heat treatment furnace was 104 MPa argon, and the molded body was held at 1204°C for 4 hours, after which it was slowly cooled to room temperature.
  • solution treatment after HIP treatment the molded body was held at 1204°C for 2 hours with the atmosphere in the heat treatment furnace at 50 Pa to 70 Pa argon, and then it was rapidly cooled to room temperature by gas fan cooling with 400 kPa argon.
  • aging treatment after solution treatment the molded body was held at 843°C for 24 hours with the atmosphere in the heat treatment furnace at 50 Pa to 70 Pa argon, and then it was rapidly cooled to room temperature by gas fan cooling with 400 kPa argon.
  • Comparative Example 3 A heat-treated first shaped body and an unheat-treated second shaped body were obtained in the same manner as in Comparative Example 2, except that a commercially available IN738LC-T1 powder was used as the nickel-based superalloy powder and the shape of the first shaped body was a rectangular parallelepiped with a width of 50 mm, a depth of 6 mm, and a height (in the stacking direction) of 6 mm.
  • Comparative Example 4 A heat-treated first shaped body and an unheat-treated second shaped body were obtained in the same manner as in Comparative Example 2, except that a commercially available IN738LC-T2 powder was used as the nickel-based superalloy powder.
  • Comparative Example 5 A heat-treated first shaped body and an unheat-treated second shaped body were obtained in the same manner as in Comparative Example 2, except that a commercially available IN738LC-T4 powder was used as the nickel-based superalloy powder.
  • Table 1 shows the compositions recorded on the mill sheets of the nickel-based superalloy powders used in Example 1 and Comparative Examples 1-5.
  • the boron equivalent was calculated from the B content and Zr content in Table 1 according to the above formula (1). The results of the boron equivalent calculations are shown in Table 2. Table 2 also includes the results of the tensile test and the crack volume observations described below.
  • FIG. 4 shows the relationship between the boron equivalent and the amount of cracks in Examples 1-5.
  • Example 1 in which the boron equivalent is 0.007 or more and 0.018 or less, not only is the occurrence of cracks suppressed, but the ductility at high temperatures is also good.
  • the high-temperature strength is high.
  • the present disclosure provides a nickel-base superalloy containing, by mass percentage, 4.8% to 5.1% Al, 1.4% to 1.7% Ti, 14.2% to 19.2% Cr, 4.5% to 12.4% Co, 0.7% to 1.5% Ta, 2.8% to 5.3% W, 4.1% or less Mo, 0.02% to 0.15% C, 0.002% to 0.02% B, and 0.06% Zr, and having a boron equivalent Z defined by the following formula of 0.007 to 0.018.
  • Z X+10.811/91.224 ⁇ Y
  • Y content by mass percentage
  • the above configuration provides a nickel-based superalloy that has excellent high-temperature strength and good ductility at high temperatures.
  • the present disclosure provides, from another aspect, a nickel-base superalloy powder composed of particles of the above-mentioned nickel-base superalloy.
  • the present disclosure provides a method for producing a shaped body, which comprises repeatedly spreading the nickel-based superalloy powder to form a layer and irradiating the layer with energy rays to melt and solidify at least a portion of the layer, thereby producing a shaped body.
  • the manufactured shaped body may be held at a temperature of 1100°C or higher and 1250°C or lower for 1 hour or longer and 5 hours or shorter, then cooled to 900°C or lower, and then held at a temperature of 800°C or higher and 900°C or lower for 12 hours or longer and 48 hours or shorter, and then cooled to room temperature.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Plasma & Fusion (AREA)
  • Automation & Control Theory (AREA)
  • Powder Metallurgy (AREA)

Abstract

A nickel-based superalloy according to an embodiment contains, by mass percentage, 4.8% to 5.1% Al, 1.4% to 1.7% Ti, 14.2% to 19.2% Cr, 4.5% to 12.4% Co, 0.7% to 1.5% Ta, 2.8% to 5.3% W, 4.1% or less Mo, 0.02% to 0.15% C, 0.002% to 0.02% B, and 0.06% or less Zr. Additionally, in the nickel-based superalloy, a boron equivalent amount Z defined by the equation below is 0.007 to 0.018.　Z = X + 10.811 / 91.224 × Y, X: Content of B by mass percentage, Y: Content of Zr by mass percentage

Description

ニッケル基超合金、ニッケル基超合金粉末および造形体の製造方法Nickel-based superalloy, nickel-based superalloy powder and method for producing shaped body
　本開示は、ニッケル基超合金およびニッケル基超合金粉末に関するとともに、前記ニッケル基超合金粉末を用いた造形体の製造方法に関する。 This disclosure relates to nickel-based superalloys and nickel-based superalloy powders, as well as to methods for manufacturing shaped bodies using the nickel-based superalloy powders.
　ニッケル基超合金は、高温で優れた強度と耐酸化性を有することが知られている。このため、航空機のエンジンや火力発電所で使用されるタービン等の、高温・酸化性環境下で高応力が負荷される部材に使用されている。中でもＩＮ７３８ＬＣ（ＩＮはインコネル（登録商標）の略である）は、γ’相の析出強化により、優れた高温強度を有する合金として知られている。 Nickel-based superalloys are known to have excellent strength and oxidation resistance at high temperatures. For this reason, they are used in components that are subjected to high stress in high-temperature, oxidizing environments, such as aircraft engines and turbines used in thermal power plants. Among them, IN738LC (IN is an abbreviation for Inconel (registered trademark)) is known as an alloy with excellent high-temperature strength due to precipitation strengthening of the γ' phase.
　しかし、ＩＮ７３８ＬＣは、溶接時に微小割れを生じやすいため、溶接が極めて困難であることが知られている。また、積層造形法で造形体を製造する際にも、ＩＮ７３８ＬＣの粉末を用いた場合には造形体中に微小割れが生じることが報告されている。特許文献１参照。なお、積層造形法は、粉末を敷き詰めて層を形成することと、前記層にエネルギー線を照射して前記層の少なくとも一部を溶融および凝固させることを繰り返して造形体を製造する方法である。 However, IN738LC is known to be extremely difficult to weld because it is prone to microcracks when welded. It has also been reported that when IN738LC powder is used to manufacture shaped objects using additive manufacturing, microcracks occur in the shaped object. See Patent Document 1. The additive manufacturing method is a method of manufacturing shaped objects by repeatedly spreading powder to form layers and irradiating the layers with energy rays to melt and solidify at least a portion of the layers.
特開２０１５－２２４３９４号公報JP 2015-224394 A
　本発明者らは、本件出願に先立って、ＩＮ７３８ＬＣと同程度の体積割合のγ’相を析出可能で、溶接や積層造形法等の急速溶融急速凝固プロセスで発生するクラックが少ないニッケル基超合金を発明した（特願２０２１－１３８６８６）。このようなニッケル基超合金は、熱処理によりＩＮ７３８ＬＣと同程度の体積割合のγ’相を析出するので、優れた高温強度を有する。ただし、このニッケル基超合金はＩＮ７３８ＬＣに比べて高温での延性が劣るため、高温での延性を改善することが望まれる。 Prior to filing this application, the inventors invented a nickel-based superalloy that can precipitate a gamma-' phase at a volume fraction similar to that of IN738LC and that generates fewer cracks during rapid melting and rapid solidification processes such as welding and additive manufacturing (Patent Application No. 2021-138686). Such a nickel-based superalloy has excellent high-temperature strength because it precipitates a gamma-' phase at a volume fraction similar to that of IN738LC through heat treatment. However, this nickel-based superalloy has inferior ductility at high temperatures compared to IN738LC, and it is therefore desirable to improve the ductility at high temperatures.
　そこで、本開示は、高温での延性が良好なニッケル基超合金を提供することを目的とする。また、本開示は、前記ニッケル基超合金の粒子で構成されたニッケル基超合金粉末を提供するとともに、前記ニッケル基超合金粉末を用いた造形体の製造方法を提供することも目的とする。 The present disclosure therefore aims to provide a nickel-based superalloy with good ductility at high temperatures. It also aims to provide a nickel-based superalloy powder composed of particles of the nickel-based superalloy, and to provide a method for manufacturing a shaped body using the nickel-based superalloy powder.
　本開示は、一つの側面から、質量百分率で、４．８％以上５．１％以下のＡｌ、１．４％以上１．７％以下のＴｉ、１４．２％以上１９．２％以下のＣｒ、４．５％以上１２．４％以下のＣｏ、０．７％以上１．５％以下のＴａ、２．８％以上５．３％以下のＷ、４．１％以下のＭｏ、０．０２％以上０．１５％以下のＣ、０．００２％以上０．０２％以下のＢ、０．０６％以下のＺｒを含有し、以下の式で規定されるホウ素当量Ｚが０．００７以上０．０１８以下である、ニッケル基超合金を提供する。
　Ｚ＝Ｘ＋１０．８１１／９１．２２４×Ｙ
　　　Ｘ：質量百分率でのＢの含有率
　　　Ｙ：質量百分率でのＺｒの含有率 According to one aspect, the present disclosure provides a nickel-base superalloy containing, by mass percentage, 4.8% to 5.1% Al, 1.4% to 1.7% Ti, 14.2% to 19.2% Cr, 4.5% to 12.4% Co, 0.7% to 1.5% Ta, 2.8% to 5.3% W, 4.1% or less Mo, 0.02% to 0.15% C, 0.002% to 0.02% B, and 0.06% Zr, and having a boron equivalent Z defined by the following formula of 0.007 to 0.018.
Z=X+10.811/91.224×Y
X: B content by mass percentage Y: Zr content by mass percentage
　また、本開示は、別の側面から、上記のニッケル基超合金の粒子で構成される、ニッケル基超合金粉末を提供する。 In another aspect, the present disclosure provides a nickel-base superalloy powder composed of particles of the above-mentioned nickel-base superalloy.
　さらに、本開示は、さらに別の側面から、上記のニッケル基超合金粉末を敷き詰めて層を形成することと、前記層にエネルギー線を照射して前記層の少なくとも一部を溶融および凝固させることを繰り返して造形体を製造する、造形体の製造方法を提供する。 Furthermore, from another aspect, the present disclosure provides a method for producing a shaped body, which comprises repeatedly spreading the nickel-based superalloy powder to form a layer and irradiating the layer with energy rays to melt and solidify at least a portion of the layer, thereby producing a shaped body.
　本開示によれば、高温での延性が良好なニッケル基超合金、前記ニッケル基超合金の粒子で構成されたニッケル基超合金粉末および前記ニッケル基超合金粉末を用いた造形体の製造方法が提供される。 The present disclosure provides a nickel-based superalloy having good ductility at high temperatures, a nickel-based superalloy powder composed of particles of the nickel-based superalloy, and a method for manufacturing a shaped body using the nickel-based superalloy powder.
積層造形装置の模式図である。FIG. 1 is a schematic diagram of an additive manufacturing apparatus. 試験片の形状を示す図である。FIG. 2 is a diagram showing the shape of a test piece. 実施例１および比較例１－５におけるホウ素当量と破断伸びとの関係を示すグラフである。1 is a graph showing the relationship between boron equivalent and breaking elongation in Example 1 and Comparative Examples 1 to 5. 実施例１および比較例１－５におけるホウ素当量とクラック量との関係を示すグラフである。1 is a graph showing the relationship between boron equivalent and amount of cracks in Example 1 and Comparative Examples 1 to 5. 実施例１および比較例１，２，４，５におけるホウ素当量と０．２％耐力との関係を示すグラフである。1 is a graph showing the relationship between boron equivalent and 0.2% proof stress in Example 1 and Comparative Examples 1, 2, 4, and 5. 実施例１および比較例１－５におけるホウ素当量と引張強度との関係を示すグラフである。1 is a graph showing the relationship between boron equivalent and tensile strength in Example 1 and Comparative Examples 1-5.
　［ニッケル基超合金］
　本開示の一つの側面に係るニッケル基超合金は、Ｎｉ以外の必須成分として、質量百分率で、４．８％以上５．１％以下のＡｌ、１．４％以上１．７％以下のＴｉ、１４．２％以上１９．２％以下のＣｒ、４．５％以上１２．４％以下のＣｏ、０．７％以上１．５％以下のＴａ、２．８％以上５．３％以下のＷ、０．０２％以上０．１５％以下のＣ、０．００２％以上０．０２％以下のＢを含有する。なお、以下の説明では、「％」は「質量％」を意味する。 [Nickel-based superalloy]
The nickel-based superalloy according to one aspect of the present disclosure contains, as essential components other than Ni, the following mass percentages: 4.8% to 5.1% Al, 1.4% to 1.7% Ti, 14.2% to 19.2% Cr, 4.5% to 12.4% Co, 0.7% to 1.5% Ta, 2.8% to 5.3% W, 0.02% to 0.15% C, and 0.002% to 0.02% B. In the following description, "%" means "mass%".
　また、前記ニッケル基超合金は、その他の選択的成分として、４．１％以下のＭｏ、０．０６％以下のＺｒの少なくとも１つを含有してもよい。ニッケル基超合金の上述した成分以外の残部は、Ｎｉおよび不可避的不純物である。不可避的不純物には、Ｓｉ、Ｍｎ、Ｐ、Ｓ、Ｃｕ、Ｎｂ、Ｆｅ、Ｏ、Ｎなどが含まれる。 The nickel-based superalloy may also contain at least one of 4.1% or less Mo and 0.06% or less Zr as other optional components. The balance of the nickel-based superalloy other than the above-mentioned components is Ni and unavoidable impurities. The unavoidable impurities include Si, Mn, P, S, Cu, Nb, Fe, O, N, etc.
　さらに、前記ニッケル基超合金では、以下の式（１）で規定されるホウ素当量Ｚが０．００７以上０．０１８以下である。
　Ｚ＝Ｘ＋１０．８１１／９１．２２４×Ｙ　・・・（１）
　　　Ｘ：質量百分率でのＢの含有率
　　　Ｙ：質量百分率でのＺｒの含有率 Furthermore, in the nickel-base superalloy, the boron equivalent Z defined by the following formula (1) is 0.007 or more and 0.018 or less.
Z=X+10.811/91.224×Y...(1)
X: B content by mass percentage Y: Zr content by mass percentage
　Ａｌは、上述の組成を有するニッケル基超合金において、γ’相の形成作用を有し、Ａｌの含有量の増加に伴いγ’相の体積割合も増加する。このため、Ａｌの含有率を４．８％以上５．８％以下とすることで、γ’相の体積割合を所定の範囲内とすることができる。 In nickel-based superalloys having the above-mentioned composition, Al has the effect of forming the γ' phase, and the volume fraction of the γ' phase increases as the Al content increases. Therefore, by setting the Al content to 4.8% or more and 5.8% or less, the volume fraction of the γ' phase can be kept within a specified range.
　ＴｉもＡｌと同様に、上述の組成を有するニッケル基超合金において、γ’相の形成作用を有する。このため、Ｔｉの含有率を１．４％以上とすることで、γ’相の体積割合を高めることができる。他方、Ｔｉは、僅かではあるものの凝固脆性温度域（Brittle Temperature Range、以下、ＢＴＲ）を広げる作用を有する。このため、Ｔｉの含有率を１．７％以下とすることで、ＢＴＲが広くなりすぎることを防止できる。ＢＴＲは急冷凝固時の液相線温度と固相線温度との差であり、ＢＴＲが狭いほど急速溶融急速凝固プロセスで発生するクラックが少なくなる。 Like Al, Ti also has the effect of forming the γ' phase in nickel-based superalloys having the above-mentioned composition. Therefore, by making the Ti content 1.4% or more, the volume fraction of the γ' phase can be increased. On the other hand, Ti has the effect of widening the solidification brittle temperature range (BTR), albeit slightly. Therefore, by making the Ti content 1.7% or less, it is possible to prevent the BTR from becoming too wide. The BTR is the difference between the liquidus temperature and solidus temperature during rapid solidification, and the narrower the BTR, the fewer cracks that occur during the rapid melting and rapid solidification process.
　Ｃｒは、上述の組成を有するニッケル基超合金において、耐酸化性を向上させる作用、およびニッケル固溶体相の固溶強化作用を有する。このため、Ｃｒの含有率を１４．２％以上とすることで、ニッケル基超合金を耐酸化性および機械的強度に優れるものとすることができる。他方、Ｃｒは、僅かではあるもののγ’相の体積割合を低減する作用、およびＢＴＲを広げる作用を有する。このため、Ｃｒの含有率を１９．２％以下とすることで、γ’相の体積割合を高めつつ、ＢＴＲが広くなりすぎることを防止できる。 In nickel-based superalloys having the above-mentioned composition, Cr has the effect of improving oxidation resistance and solid solution strengthening of the nickel solid solution phase. Therefore, by making the Cr content 14.2% or more, the nickel-based superalloy can be made to have excellent oxidation resistance and mechanical strength. On the other hand, Cr has the effect of reducing, albeit slightly, the volume fraction of the γ' phase and the effect of widening the BTR. Therefore, by making the Cr content 19.2% or less, it is possible to increase the volume fraction of the γ' phase while preventing the BTR from becoming too wide.
　Ｃｏは、上述の組成を有するニッケル基超合金において、ニッケル固溶体相の固溶強化作用を有する。このため、Ｃｏの含有率を４．５％以上とすることで、ニッケル基超合金の機械的強度を十分なものとすることができる。他方、Ｃｏは、Ｃｒと同様に僅かではあるもののγ’相の体積割合を低減する作用、およびＢＴＲを広げる作用を有する。このため、Ｃｏの含有率を１２．４％以下とすることで、γ’相の体積割合を高めつつ、ＢＴＲが広くなりすぎることを防止できる。 Co has a solid solution strengthening effect on the nickel solid solution phase in nickel-based superalloys having the above-mentioned composition. Therefore, by making the Co content 4.5% or more, the mechanical strength of the nickel-based superalloy can be made sufficient. On the other hand, like Cr, Co has the effect of reducing the volume fraction of the γ' phase, albeit slightly, and the effect of widening the BTR. Therefore, by making the Co content 12.4% or less, it is possible to increase the volume fraction of the γ' phase while preventing the BTR from becoming too wide.
　Ｔａは、上述の組成を有するニッケル基超合金において、γ’相の固溶強化作用を有し、Ｔａの含有量の増加に伴いγ’相の体積割合も増加する。このため、Ｔａの含有率を０．７％以上１．５％以下とすることで、γ’相の体積割合を所定の範囲内とすることができる。 Ta has a solid solution strengthening effect on the γ' phase in nickel-based superalloys having the above-mentioned composition, and the volume fraction of the γ' phase increases as the Ta content increases. Therefore, by setting the Ta content to 0.7% or more and 1.5% or less, the volume fraction of the γ' phase can be kept within a specified range.
　Ｗは、上述の組成を有するニッケル基超合金において、ニッケル固溶体相の固溶強化作用を有する。このため、Ｗの含有率を２．８％以上とすることで、ニッケル基超合金を機械的強度に優れるものとすることができる。他方、Ｗはγ’相の体積割合を高める作用、および僅かではあるもののＢＴＲを広げる作用を有する。このため、Ｗの含有率を５．３％以下とすることで、γ’相の体積割合を所定の範囲内としつつ、ＢＴＲが広くなりすぎることを防止できる。 W has a solid solution strengthening effect on the nickel solid solution phase in nickel-based superalloys having the above-mentioned composition. For this reason, by making the W content 2.8% or more, the nickel-based superalloy can be made to have excellent mechanical strength. On the other hand, W has the effect of increasing the volume fraction of the γ' phase and, although it is small, widening the BTR. For this reason, by making the W content 5.3% or less, it is possible to keep the volume fraction of the γ' phase within a specified range while preventing the BTR from becoming too wide.
　Ｃは、上述の組成を有するニッケル基超合金において、ＢＴＲを狭める作用を有する。このため、Ｃの含有率を０．０２４％以上とすることで、ＢＴＲが狭く、急冷凝固時のクラックの発生が抑制されたニッケル基超合金が得られる。他方、Ｃは、他の金属元素と反応して粒界に炭化物を生成し、耐食性および靭性の低下を引き起こすことがある。このため、Ｃの含有率を０．１５％以下とすることで、粒界での炭化物の生成を抑制することができる。 C has the effect of narrowing the BTR in nickel-based superalloys having the above-mentioned composition. For this reason, by making the C content 0.024% or more, a nickel-based superalloy with a narrow BTR and suppressed crack generation during rapid solidification can be obtained. On the other hand, C can react with other metal elements to form carbides at grain boundaries, which can cause a decrease in corrosion resistance and toughness. For this reason, by making the C content 0.15% or less, it is possible to suppress the formation of carbides at grain boundaries.
　Ｂは、上述の組成を有するニッケル基超合金において、高温での延性を高める作用を有する。このため、Ｂの含有率を０．００２％以上とすることで、高温での延性が改善されたニッケル基超合金が得られる。他方、Ｂは、ＢＴＲを広げる作用を有する。このため、Ｂの含有率を０．０２％以下とすることで、クラックの発生を抑制することができる。好ましくは、Ｂの含有率は０．００４％以上０．０１２％以下である。 B has the effect of increasing the ductility at high temperatures in nickel-based superalloys having the above-mentioned composition. Therefore, by making the B content 0.002% or more, a nickel-based superalloy with improved ductility at high temperatures can be obtained. On the other hand, B has the effect of widening the BTR. Therefore, by making the B content 0.02% or less, the occurrence of cracks can be suppressed. Preferably, the B content is 0.004% or more and 0.012% or less.
　Ｍｏは、上述の組成を有するニッケル基超合金において、ニッケル固溶体相の固溶強化作用を有する。このため、ニッケル基超合金がＭｏを含有することで、ニッケル基超合金を機械的強度に優れるものとすることができる。他方、Ｍｏはγ’相の体積割合を高める作用を有する。このため、Ｍｏの含有率を４．１％以下とすることで、γ’相の体積割合を所定の範囲内とすることができる。 Mo has a solid solution strengthening effect on the nickel solid solution phase in nickel-based superalloys having the above-mentioned composition. Therefore, by including Mo in a nickel-based superalloy, the nickel-based superalloy can have excellent mechanical strength. On the other hand, Mo has the effect of increasing the volume fraction of the γ' phase. Therefore, by keeping the Mo content at 4.1% or less, the volume fraction of the γ' phase can be kept within a specified range.
　Ｚｒは、上述の組成を有するニッケル基超合金において、ＢＴＲを広げる作用を有する。このため、Ｚｒの含有率を０．０６％以下とすることで、ＢＴＲが広くなりすぎることを防止できる。また、Ｚｒは高温での延性を高める作用も有するため、Ｚｒの含有率は０．０２％以上であることが好ましい。 Zr has the effect of widening the BTR in nickel-based superalloys having the above-mentioned composition. Therefore, by making the Zr content 0.06% or less, it is possible to prevent the BTR from becoming too wide. In addition, since Zr also has the effect of increasing ductility at high temperatures, it is preferable that the Zr content be 0.02% or more.
　ニッケル基超合金が上述の組成を有することは、エネルギー分散型エックス線分光（ＥＤＸ）法、波長分散型エックス線分光（ＷＤＳ）法、蛍光エックス線分析法（ＸＲＦ）、高周波誘導結合プラズマ（ＩＣＰ）発光分光分析法、燃焼赤外線吸収法、加熱融解赤外線吸収法、または湿式化学分析法のいずれかにより確認することができる。 The fact that the nickel-base superalloy has the above-mentioned composition can be confirmed by any of the following methods: energy dispersive X-ray spectroscopy (EDX), wavelength dispersive X-ray spectroscopy (WDS), X-ray fluorescence spectroscopy (XRF), inductively coupled plasma (ICP) optical emission spectroscopy, combustion infrared absorption spectroscopy, heating and fusion infrared absorption spectroscopy, or wet chemical analysis.
　［ニッケル基超合金粉末］
　本開示の別の側面に係るニッケル基超合金粉末は、上述の組成を有するニッケル基超合金の粒子で構成される。当該ニッケル基超合金粉末は、積層造形法に適用した際に、造形体中のクラックの発生を抑制できる。 [Nickel-based superalloy powder]
A nickel-based superalloy powder according to another aspect of the present disclosure is composed of particles of a nickel-based superalloy having the above-mentioned composition. When the nickel-based superalloy powder is applied to an additive manufacturing method, the occurrence of cracks in a shaped body can be suppressed.
　前記ニッケル基超合金粉末の粒径および当該粉末を構成する粒子の形状は特に限定されない。粒径については、例えば、ＪＩＳ　Ｚ　８８０１（２０１９）で規定される、公称目開き１０６μｍの篩を通過するものとすることができ、公称目開き７５μｍ、６３μｍまたは５３μｍの篩を通過するものとすることが好ましい。粒径の下限については、１μｍ以上とすることができ、５μｍ以上、１５μｍ以上または２５μｍ以上とすることが好ましい。また、粒子の形状については、例えば、球形とすることができる。 The particle size of the nickel-based superalloy powder and the shape of the particles constituting the powder are not particularly limited. The particle size can be, for example, one that passes through a sieve with a nominal mesh size of 106 μm as specified in JIS Z 8801 (2019), and preferably one that passes through a sieve with a nominal mesh size of 75 μm, 63 μm, or 53 μm. The lower limit of the particle size can be 1 μm or more, and preferably 5 μm or more, 15 μm or more, or 25 μm or more. The shape of the particles can be, for example, spherical.
　前記ニッケル基超合金粉末の製造方法は特に限定されず、公知の金属粉末の製法の中から所定の粒径および粒子形状の粉末が得られるものを適宜選択すればよい。一例として、溶融金属に高圧のガスを吹き付けて冷却し、金属粒子を得るガスアトマイズ法が挙げられる。ガスアトマイズ法は、金属の酸化を抑制しつつ、球形の粒子が得られる利点を有する。得られたニッケル基超合金粉末は、そのまま造形体の製造に供してもよく、篩等により分球して粒度を揃えた後、造形体の製造に供してもよい。 The method for producing the nickel-based superalloy powder is not particularly limited, and any method that can produce powder of a specified particle size and shape can be appropriately selected from among known methods for producing metal powders. One example is the gas atomization method, in which high-pressure gas is sprayed onto molten metal to cool it and obtain metal particles. The gas atomization method has the advantage of obtaining spherical particles while suppressing oxidation of the metal. The obtained nickel-based superalloy powder may be used directly to produce a shaped body, or it may be used to produce a shaped body after being divided into spheres using a sieve or the like to make the particle size uniform.
　［造形体の製造方法］
　本開示のさらに別の側面に係る造形体の製造方法は、図１に示すように、上述のニッケル基超合金粉末３を敷き詰めて層５を形成することと、層５にエネルギー線６を照射して層５の少なくとも一部を溶融および凝固させることを繰り返して造形体７を製造する方法である。この製造方法により、クラックの少ない造形体７を得ることができる。 [Method of manufacturing a shaped body]
1, a method for producing a shaped body according to still another aspect of the present disclosure is a method for producing a shaped body 7 by repeatedly spreading the above-mentioned nickel-based superalloy powder 3 to form a layer 5 and irradiating the layer 5 with an energy ray 6 to melt and solidify at least a portion of the layer 5. By this production method, a shaped body 7 with few cracks can be obtained.
　前記製造方法は、例えば図１に示すような積層造形装置１を用いて行われる。なお、前記製造方法で用いられる積層造形装置はこれに限られず、公知の金属用積層造形装置から適宜選択すればよい。 The manufacturing method is carried out using, for example, an additive manufacturing device 1 as shown in FIG. 1. Note that the additive manufacturing device used in the manufacturing method is not limited to this, and may be appropriately selected from known additive manufacturing devices for metals.
　積層造形装置１は、ニッケル基超合金粉末３を貯留する貯留槽３１と、貯留槽３１に隣接する造形室３２と、造形室３２を挟んで貯留槽３１と反対側に位置するコレクター３３を含む。また、積層造形装置１は、貯留槽３１の底を構成する供給ピストン２１と、造形室３２の底を構成する造形ピストン２２と、コレクター３３の底を構成する回収ピストン２３を含む。さらに、積層造形装置１は、貯留槽３１の上方からコレクター３３の上方まで移動するリコータ４と、造形室３２の上方でエネルギー線６を放射するエネルギー線放射装置を含む。 The additive manufacturing device 1 includes a storage tank 31 that stores nickel-based superalloy powder 3, a modeling chamber 32 adjacent to the storage tank 31, and a collector 33 located on the opposite side of the modeling chamber 32 from the storage tank 31. The additive manufacturing device 1 also includes a supply piston 21 that forms the bottom of the storage tank 31, a modeling piston 22 that forms the bottom of the modeling chamber 32, and a recovery piston 23 that forms the bottom of the collector 33. The additive manufacturing device 1 further includes a recoater 4 that moves from above the storage tank 31 to above the collector 33, and an energy ray emission device that emits energy rays 6 above the modeling chamber 32.
　積層造形装置１では、まず供給ピストン２１が上昇し、貯留槽３１内のニッケル基超合金粉末３が所定の高さだけ押し上げられる。ついで、リコータ４の移動によって、押し上げられたニッケル基超合金粉末３が造形室３２へと供給されるとともに、平面上に敷き詰められて層５が形成される。余剰のニッケル基超合金粉末３はリコータ４の移動に伴ってコレクター３３に落下する。その後、層５に所定のパターンでエネルギー線６が照射され、これにより層５の少なくとも一部が溶融および凝固する。これにより、造形体７中の特定断面が形成される。この工程が繰り返されることにより特定断面が積み重ねられて造形体７が製造される。 In the additive manufacturing device 1, first the supply piston 21 rises, and the nickel-based superalloy powder 3 in the storage tank 31 is pushed up to a predetermined height. Next, the recoater 4 moves, and the pushed-up nickel-based superalloy powder 3 is supplied to the manufacturing chamber 32 and spread out on a flat surface to form a layer 5. As the recoater 4 moves, the excess nickel-based superalloy powder 3 falls into the collector 33. The layer 5 is then irradiated with energy rays 6 in a predetermined pattern, which melts and solidifies at least a portion of the layer 5. This forms a specific cross section in the shaped body 7. This process is repeated to stack the specific cross sections and produce the shaped body 7.
　層５への所定のパターンでのエネルギー線６の照射は、エネルギー線６が層５の表面上に所定のピッチおよび所定の速度で走査されながら行われる。例えば、エネルギー線６はレーザまたは電子ビームである。 The energy beam 6 is irradiated onto the layer 5 in a predetermined pattern while the energy beam 6 is scanned over the surface of the layer 5 at a predetermined pitch and a predetermined speed. For example, the energy beam 6 is a laser or an electron beam.
　製造された造形体７は熱処理されてもよい。造形体７に行う熱処理としては、溶体化処理および時効処理が挙げられる。溶体化処理および時効処理はこの順に行われる。溶体化処理と時効処理とは、異なる熱処理装置を用いて別々に行ってもよく、同一の熱処理装置を用いて連続的に行ってもよい。また、溶体化処理の前に造形体７に熱処理としてＨＩＰ（Hot Isostatic Pressing）処理を施してもよい。 The manufactured shaped body 7 may be heat treated. Examples of heat treatments that may be performed on the shaped body 7 include solution treatment and aging treatment. The solution treatment and aging treatment are performed in this order. The solution treatment and aging treatment may be performed separately using different heat treatment devices, or may be performed consecutively using the same heat treatment device. Furthermore, the shaped body 7 may be subjected to HIP (Hot Isostatic Pressing) treatment as a heat treatment prior to the solution treatment.
　例えば、溶体化処理として、造形体７を１１００℃以上１２５０℃以下の温度にて１時間以上５時間以下の時間保持した後に９００℃以下まで冷却してもよい。このときの冷却は、比較的に短時間で行われることが好ましい（急冷）。また、時効効果として、溶体化処理された造形体７を８００℃以上９００℃以下の温度にて１２時間以上４８時間以下の時間保持した後に室温まで冷却してもよい。このときの冷却も、比較的に短時間で行われることが好ましい（急冷）。 For example, as a solution treatment, the shaped body 7 may be held at a temperature of 1100°C to 1250°C for 1 hour to 5 hours, and then cooled to 900°C or less. It is preferable that the cooling at this time be performed in a relatively short time (rapid cooling). Also, as an aging effect, the solution-treated shaped body 7 may be held at a temperature of 800°C to 900°C for 12 hours to 48 hours, and then cooled to room temperature. It is also preferable that the cooling at this time be performed in a relatively short time (rapid cooling).
　溶体化処理および時効処理のいずれについても、熱処理雰囲気は特に限定されない。例えば、熱処理雰囲気は、真空、アルゴン、空気のいずれであってもよい。また、冷却（急冷）は、水冷、空冷、油冷、ガスファン冷却のいずれであってもよい。 For both solution treatment and aging treatment, the heat treatment atmosphere is not particularly limited. For example, the heat treatment atmosphere may be vacuum, argon, or air. In addition, cooling (quenching) may be water cooling, air cooling, oil cooling, or gas fan cooling.
　以下、本開示を実施例により説明するが、本開示は以下の実施例に限定されるものではない。 The present disclosure will be explained below using examples, but the present disclosure is not limited to the following examples.
　［実施例１］
　合金組成が、Ａｌ：５％、Ｔｉ：１．６％、Ｃｒ：１７．５％、Ｃｏ：８．６％、Ｔａ：１％、Ｗ：４％、Ｍｏ：１．９％、Ｃ：０．０６％、Ｂ：０．０５％、Ｚｒ：０．０７％、残部：Ｎｉおよび不可避的不純物となるように調製されたニッケル基超合金粉末を準備した。粒子径分布は、ｄ１０＝２４．８８μｍ、ｄ５０＝３７．４２μｍ、ｄ９０＝５６．３２μｍであった。 [Example 1]
A nickel-based superalloy powder was prepared with an alloy composition of 5% Al, 1.6% Ti, 17.5% Cr, 8.6% Co, 1% Ta, 4% W, 1.9% Mo, 0.06% C, 0.05% B, 0.07% Zr, and the balance being Ni and unavoidable impurities. The particle size distribution was d10=24.88 μm, d50=37.42 μm, and d90=56.32 μm.
　上記のニッケル基超合金粉末を、積層造形装置（ＥＯＳ社製、Ｍ２９０）に装填し、レーザ出力２１０Ｗ、走査速度１２００ｍｍ／ｓ、走査ピッチ６０μｍ、積層厚４０μｍの条件で第１の造形体を製造した。また、レーザ出力を２７０Ｗ、走査速度を１０００ｍｍ／ｓ、走査ピッチを７０μｍに変更して第２の造形体を製造した。第１の造形体の形状は幅６０ｍｍ、奥行き１０ｍｍ、高さ（積層方向）１０ｍｍの直方体状とし、第２の造形体の形状は、幅６ｍｍ、奥行き５ｍｍ、高さ（積層方向）４．５ｍｍの直方体状とした。 The nickel-based superalloy powder was loaded into an additive manufacturing device (M290, manufactured by EOS), and a first object was manufactured under the conditions of a laser output of 210 W, a scanning speed of 1200 mm/s, a scanning pitch of 60 μm, and a layer thickness of 40 μm. A second object was manufactured by changing the laser output to 270 W, the scanning speed to 1000 mm/s, and the scanning pitch to 70 μm. The shape of the first object was a rectangular parallelepiped with a width of 60 mm, a depth of 10 mm, and a height (in the layering direction) of 10 mm, and the shape of the second object was a rectangular parallelepiped with a width of 6 mm, a depth of 5 mm, and a height (in the layering direction) of 4.5 mm.
　第２の造形体には熱処理を施さず、第１の造形体には以下のように熱処理を施した。まず、第１の造形体を熱処理炉内に配置し、溶体化処理として、熱処理炉内の雰囲気を５０Ｐａ以上７０Ｐａ以下のアルゴンとしたまま造形体を１１７０℃で２時間保持した後、４００ｋＰａのアルゴンによるガスファン冷却で室温まで急冷した。ついで、時効処理として、熱処理炉内の雰囲気を５０Ｐａ以上７０Ｐａ以下のアルゴンとしたまま造形体を８４０℃で２４時間保持した後、４００ｋＰａのアルゴンによるガスファン冷却で室温まで急冷した。 The second shaped body was not subjected to heat treatment, while the first shaped body was subjected to heat treatment as follows. First, the first shaped body was placed in a heat treatment furnace, and as a solution treatment, the shaped body was held at 1170°C for 2 hours while the atmosphere in the heat treatment furnace was argon at 50 Pa to 70 Pa, and then rapidly cooled to room temperature by gas fan cooling with 400 kPa argon. Next, as an aging treatment, the shaped body was held at 840°C for 24 hours while the atmosphere in the heat treatment furnace was argon at 50 Pa to 70 Pa, and then rapidly cooled to room temperature by gas fan cooling with 400 kPa argon.
　［比較例１］
　合金組成が、Ａｌ：５％、Ｔｉ：１．６％、Ｃｒ：１７．５％、Ｃｏ：８．６％、Ｔａ：１％、Ｗ：４％、Ｍｏ：１．９％、Ｃ：０．０６％、Ｚｒ：０．０４％、残部：Ｎｉおよび不可避的不純物となるように調製されたニッケル基超合金粉末を用いた以外は、実施例１と同様にして熱処理された第１の造形体と未熱処理の第２の造形体を得た。ニッケル基超合金粉末の粒子径分布は、ｄ１０＝２７．８７μｍ、ｄ５０＝４３．９３μｍ、ｄ９０＝６６．６８μｍであった。 [Comparative Example 1]
A first heat-treated shaped body and a second unheat-treated shaped body were obtained in the same manner as in Example 1, except that a nickel-based superalloy powder was used that had an alloy composition of 5% Al, 1.6% Ti, 17.5% Cr, 8.6% Co, 1% Ta, 4% W, 1.9% Mo, 0.06% C, 0.04% Zr, and the balance being Ni and unavoidable impurities. The particle size distribution of the nickel-based superalloy powder was d10=27.87 μm, d50=43.93 μm, and d90=66.68 μm.
　［比較例２］
　ニッケル基超合金粉末として市販のＩＮ７３８ＬＣ－Ｐ粉末を用いるとともに下記の熱処理以外は実施例１と同様にして熱処理された第１の造形体と未熱処理の第２の造形体を得た。ニッケル基超合金粉末の粒子径分布は、ｄ１０＝２４．８６μｍ、ｄ５０＝３３．５４μｍ、ｄ９０＝４８．０４μｍであった。 [Comparative Example 2]
A commercially available IN738LC-P powder was used as the nickel-based superalloy powder, and a first heat-treated shaped body and a second unheat-treated shaped body were obtained in the same manner as in Example 1, except for the following heat treatment. The particle size distribution of the nickel-based superalloy powder was d10 = 24.86 μm, d50 = 33.54 μm, and d90 = 48.04 μm.
　熱処理として、溶体化処理の前に、ＨＩＰ処理を行った。ＨＩＰ処理では、熱処理炉内の雰囲気を１０４ＭＰａのアルゴンとした上で、造形体を１２０４℃で４時間保持した後に室温までゆっくり冷却した。ＨＩＰ処理後の溶体化処理では、熱処理炉内の雰囲気を５０Ｐａ以上７０Ｐａ以下のアルゴンとしたまま造形体を１２０４℃で２時間保持した後、４００ｋＰａのアルゴンによるガスファン冷却で室温まで急冷した。溶体化処理後の時効処理では、熱処理炉内の雰囲気を５０Ｐａ以上７０Ｐａ以下のアルゴンとしたまま造形体を８４３℃で２４時間保持した後、４００ｋＰａのアルゴンによるガスファン冷却で室温まで急冷した。 HIP treatment was performed before solution treatment as a heat treatment. In HIP treatment, the atmosphere in the heat treatment furnace was 104 MPa argon, and the molded body was held at 1204°C for 4 hours, after which it was slowly cooled to room temperature. In solution treatment after HIP treatment, the molded body was held at 1204°C for 2 hours with the atmosphere in the heat treatment furnace at 50 Pa to 70 Pa argon, and then it was rapidly cooled to room temperature by gas fan cooling with 400 kPa argon. In aging treatment after solution treatment, the molded body was held at 843°C for 24 hours with the atmosphere in the heat treatment furnace at 50 Pa to 70 Pa argon, and then it was rapidly cooled to room temperature by gas fan cooling with 400 kPa argon.
　［比較例３］
　ニッケル基超合金粉末として市販のＩＮ７３８ＬＣ－Ｔ１粉末を用いたことと、第１の造形体の形状を幅５０ｍｍ、奥行き６ｍｍ、高さ（積層方向）６ｍｍの直方体状としたこと以外は比較例２と同様にして熱処理された第１の造形体と未熱処理の第２の造形体を得た。ニッケル基超合金粉末の粒子径分布は、ｄ１０＝２６．５７μｍ、ｄ５０＝４３．９３μｍ、ｄ９０＝６６．８０μｍであった。 [Comparative Example 3]
A heat-treated first shaped body and an unheat-treated second shaped body were obtained in the same manner as in Comparative Example 2, except that a commercially available IN738LC-T1 powder was used as the nickel-based superalloy powder and the shape of the first shaped body was a rectangular parallelepiped with a width of 50 mm, a depth of 6 mm, and a height (in the stacking direction) of 6 mm. The particle size distribution of the nickel-based superalloy powder was d10 = 26.57 μm, d50 = 43.93 μm, and d90 = 66.80 μm.
　［比較例４］
　ニッケル基超合金粉末として市販のＩＮ７３８ＬＣ－Ｔ２粉末を用いた以外は比較例２と同様にして熱処理された第１の造形体と未熱処理の第２の造形体を得た。ニッケル基超合金粉末の粒子径分布は、ｄ１０＝２９．６６μｍ、ｄ５０＝４４．９０μｍ、ｄ９０＝６６．６６μｍであった。 [Comparative Example 4]
A heat-treated first shaped body and an unheat-treated second shaped body were obtained in the same manner as in Comparative Example 2, except that a commercially available IN738LC-T2 powder was used as the nickel-based superalloy powder. The particle size distribution of the nickel-based superalloy powder was d10 = 29.66 μm, d50 = 44.90 μm, and d90 = 66.66 μm.
　［比較例５］
　ニッケル基超合金粉末として市販のＩＮ７３８ＬＣ－Ｔ４粉末を用いた以外は比較例２と同様にして熱処理された第１の造形体と未熱処理の第２の造形体を得た。ニッケル基超合金粉末の粒子径分布は、ｄ１０＝２５．９６μｍ、ｄ５０＝４１．６４μｍ、ｄ９０＝６３．２６μｍであった。 [Comparative Example 5]
A heat-treated first shaped body and an unheat-treated second shaped body were obtained in the same manner as in Comparative Example 2, except that a commercially available IN738LC-T4 powder was used as the nickel-based superalloy powder. The particle size distribution of the nickel-based superalloy powder was d10 = 25.96 μm, d50 = 41.64 μm, and d90 = 63.26 μm.
　［組成］
　実施例１および比較例１－５で用いたニッケル基超合金粉末のミルシートに記載された組成を表１に示す。 [composition]
Table 1 shows the compositions recorded on the mill sheets of the nickel-based superalloy powders used in Example 1 and Comparative Examples 1-5.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
　また、表１中のＢ含有率およびＺｒ含有率から、上記の式（１）に従ってホウ素当量を計算した。ホウ素当量の計算結果を表２に示す。なお、表２中には、後述する引張試験の結果およびクラック量観察の結果も含まれる。 The boron equivalent was calculated from the B content and Zr content in Table 1 according to the above formula (1). The results of the boron equivalent calculations are shown in Table 2. Table 2 also includes the results of the tensile test and the crack volume observations described below.
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000002
　［引張試験］
　実施例１および比較例１－５の熱処理された第１の造形体から、図２に示すような棒状の試験片を削り出し、この試験片に対してＡＳＴＭ（American Society for Testing and Materials）　Ｅ２１に従って引張試験を行い、７６０℃での０．２％耐力、引張強度および破断伸びを測定した。引張試験の結果を表２に示す。また、図３に実施例１および比較例１－５のホウ素当量と破断伸びとの関係を示す。 [Tensile test]
From the heat-treated first shaped bodies of Example 1 and Comparative Examples 1-5, rod-shaped test pieces as shown in Fig. 2 were cut out, and tensile tests were performed on these test pieces in accordance with ASTM (American Society for Testing and Materials) E21 to measure the 0.2% proof stress, tensile strength, and breaking elongation at 760°C. The results of the tensile tests are shown in Table 2. Also, Fig. 3 shows the relationship between the boron equivalent and the breaking elongation of Example 1 and Comparative Examples 1-5.
　［クラック量観察］
　実施例１および比較例１－５の未熱処理の第２の造形体を幅方向の中心線に沿って切断し、その断面を光学顕微鏡（ＯＭ）（オリンパス製、ＧＸ５３）にて撮影した。そのＯＭ像に対して画像解析により二値化処理を行った後、２０ピクセル（１ピクセルの幅は０．９２６μｍとなる解像度で撮像）以上の面積を有する黒色部分をクラックとして抽出した。ついで、クラックとして抽出した各部分のフェレー径を測定し、各クラックの長さとした。最後に、各クラックの長さの合計（μｍ）を、ＯＭ像を得た領域の面積（ｍｍ2）で割った商を、単位面積あたりのクラック量（ｍｍ／ｍｍ2）とした。クラック量観察の結果を表２に示す。また、図４に実施例１－５のホウ素当量とクラック量との関係を示す。 [Observation of crack volume]
The unheated second molded bodies of Example 1 and Comparative Example 1-5 were cut along the center line in the width direction, and the cross sections were photographed with an optical microscope (OM) (Olympus, GX53). After binarization processing was performed on the OM images by image analysis, black parts having an area of 20 pixels or more (imaged at a resolution where the width of 1 pixel is 0.926 μm) were extracted as cracks. Next, the Feret diameter of each part extracted as a crack was measured and used as the length of each crack. Finally, the quotient obtained by dividing the total length of each crack (μm) by the area (mm 2 ) of the region where the OM image was obtained was used as the amount of cracks per unit area (mm/mm 2 ). The results of the crack amount observation are shown in Table 2. In addition, FIG. 4 shows the relationship between the boron equivalent and the amount of cracks in Examples 1-5.
　図３および図４から、ホウ素当量が０．００７以上０．０１８以下の実施例１では、クラックの発生が抑制されるだけでなく、高温での延性が良好であることが分かる。その他にも、図５および図６に示す上記の引張試験の結果から、ホウ素当量が０．００７以上０．０１８以下の実施例１では、高温強度が高いことが分かる。 From Figures 3 and 4, it can be seen that in Example 1, in which the boron equivalent is 0.007 or more and 0.018 or less, not only is the occurrence of cracks suppressed, but the ductility at high temperatures is also good. In addition, from the results of the tensile test shown in Figures 5 and 6, it can be seen that in Example 1, in which the boron equivalent is 0.007 or more and 0.018 or less, the high-temperature strength is high.
　＜まとめ＞
　第１の態様として、本開示は、一つの側面から、質量百分率で、４．８％以上５．１％以下のＡｌ、１．４％以上１．７％以下のＴｉ、１４．２％以上１９．２％以下のＣｒ、４．５％以上１２．４％以下のＣｏ、０．７％以上１．５％以下のＴａ、２．８％以上５．３％以下のＷ、４．１％以下のＭｏ、０．０２％以上０．１５％以下のＣ、０．００２％以上０．０２％以下のＢ、０．０６％以下のＺｒを含有し、以下の式で規定されるホウ素当量Ｚが０．００７以上０．０１８以下である、ニッケル基超合金を提供する。
　Ｚ＝Ｘ＋１０．８１１／９１．２２４×Ｙ
　　　Ｘ：質量百分率でのＢの含有率
　　　Ｙ：質量百分率でのＺｒの含有率 <Summary>
As a first aspect, the present disclosure provides a nickel-base superalloy containing, by mass percentage, 4.8% to 5.1% Al, 1.4% to 1.7% Ti, 14.2% to 19.2% Cr, 4.5% to 12.4% Co, 0.7% to 1.5% Ta, 2.8% to 5.3% W, 4.1% or less Mo, 0.02% to 0.15% C, 0.002% to 0.02% B, and 0.06% Zr, and having a boron equivalent Z defined by the following formula of 0.007 to 0.018.
Z=X+10.811/91.224×Y
X: B content by mass percentage Y: Zr content by mass percentage
　上記の構成によれば、優れた高温強度を有するとともに高温での延性が良好なニッケル基超合金が提供される。 The above configuration provides a nickel-based superalloy that has excellent high-temperature strength and good ductility at high temperatures.
　第２の態様として、本開示は、別の側面から、上記のニッケル基超合金の粒子で構成される、ニッケル基超合金粉末を提供する。 In a second aspect, the present disclosure provides, from another aspect, a nickel-base superalloy powder composed of particles of the above-mentioned nickel-base superalloy.
　第３の態様として、本開示は、さらに別の側面から、上記のニッケル基超合金粉末を敷き詰めて層を形成することと、前記層にエネルギー線を照射して前記層の少なくとも一部を溶融および凝固させることを繰り返して造形体を製造する、造形体の製造方法を提供する。 In a third aspect, the present disclosure provides a method for producing a shaped body, which comprises repeatedly spreading the nickel-based superalloy powder to form a layer and irradiating the layer with energy rays to melt and solidify at least a portion of the layer, thereby producing a shaped body.
　第４の態様として、第３の態様において、例えば、製造された前記造形体を、１１００℃以上１２５０℃以下の温度にて１時間以上５時間以下の時間保持した後に９００℃以下まで冷却し、ついで８００℃以上９００℃以下の温度にて１２時間以上４８時間以下の時間保持した後に室温まで冷却してもよい。 As a fourth embodiment, in the third embodiment, for example, the manufactured shaped body may be held at a temperature of 1100°C or higher and 1250°C or lower for 1 hour or longer and 5 hours or shorter, then cooled to 900°C or lower, and then held at a temperature of 800°C or higher and 900°C or lower for 12 hours or longer and 48 hours or shorter, and then cooled to room temperature.
　１　　積層造形装置
　３　　ニッケル基超合金粉末
　５　　層
　６　　エネルギー線
　７　　造形体
  1 Additive manufacturing device 3 Nickel-based superalloy powder 5 Layer 6 Energy beam 7 Model

Claims (4)

  1. 　質量百分率で、４．８％以上５．１％以下のＡｌ、１．４％以上１．７％以下のＴｉ、１４．２％以上１９．２％以下のＣｒ、４．５％以上１２．４％以下のＣｏ、０．７％以上１．５％以下のＴａ、２．８％以上５．３％以下のＷ、４．１％以下のＭｏ、０．０２％以上０．１５％以下のＣ、０．００２％以上０．０２％以下のＢ、０．０６％以下のＺｒを含有し、
    　以下の式で規定されるホウ素当量Ｚが０．００７以上０．０１８以下である、ニッケル基超合金。
    　Ｚ＝Ｘ＋１０．８１１／９１．２２４×Ｙ
    　　　Ｘ：質量百分率でのＢの含有率
    　　　Ｙ：質量百分率でのＺｒの含有率     The alloy contains, by mass percentage, 4.8% to 5.1% Al, 1.4% to 1.7% Ti, 14.2% to 19.2% Cr, 4.5% to 12.4% Co, 0.7% to 1.5% Ta, 2.8% to 5.3% W, 4.1% Mo, 0.02% to 0.15% C, 0.002% to 0.02% B, and 0.06% Zr.
    A nickel-based superalloy having a boron equivalent Z defined by the following formula of 0.007 or more and 0.018 or less.
    Z=X+10.811/91.224×Y
    X: B content by mass percentage Y: Zr content by mass percentage
  2. 　請求項１に記載のニッケル基超合金の粒子で構成される、ニッケル基超合金粉末。 A nickel-based superalloy powder comprising particles of the nickel-based superalloy according to claim 1.
  3. 　請求項２に記載のニッケル基超合金粉末を敷き詰めて層を形成することと、前記層にエネルギー線を照射して前記層の少なくとも一部を溶融および凝固させることを繰り返して造形体を製造する、造形体の製造方法。 A method for manufacturing a shaped body, comprising repeatedly spreading the nickel-based superalloy powder according to claim 2 to form a layer, and irradiating the layer with energy rays to melt and solidify at least a portion of the layer, thereby manufacturing the shaped body.
  4. 　製造された前記造形体を、１１００℃以上１２５０℃以下の温度にて１時間以上５時間以下の時間保持した後に９００℃以下まで冷却し、ついで８００℃以上９００℃以下の温度にて１２時間以上４８時間以下の時間保持した後に室温まで冷却する、請求項３に記載の造形体の製造方法。
          The method for producing a shaped body according to claim 3, wherein the produced shaped body is held at a temperature of 1100°C or higher and 1250°C or lower for 1 hour or higher and 5 hours or lower, then cooled to 900°C or lower, and then held at a temperature of 800°C or higher and 900°C or lower for 12 hours or higher and 48 hours or lower, before being cooled to room temperature.
PCT/JP2024/003011 2023-02-03 2024-01-31 Nickel-based superalloy, nickel-based superalloy powder, and method for manufacturing molded body WO2024162379A1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2023-015398 2023-02-03
JP2023015398A JP2024110677A (en) 2023-02-03 2023-02-03 Nickel-based superalloy, nickel-based superalloy powder and method for producing shaped body

Publications (1)

Publication Number Publication Date
WO2024162379A1 true WO2024162379A1 (en) 2024-08-08

Family

ID=92146737

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2024/003011 WO2024162379A1 (en) 2023-02-03 2024-01-31 Nickel-based superalloy, nickel-based superalloy powder, and method for manufacturing molded body

Country Status (2)

Country Link
JP (1) JP2024110677A (en)
WO (1) WO2024162379A1 (en)

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2017036485A (en) * 2015-08-12 2017-02-16 山陽特殊製鋼株式会社 Ni-based superalloy powder for additive manufacturing
JP2017529453A (en) * 2014-07-21 2017-10-05 ヌオーヴォ ピニォーネ ソチエタ レスポンサビリタ リミタータＮｕｏｖｏ Ｐｉｇｎｏｎｅ Ｓ．Ｒ．Ｌ． Method for manufacturing machine components by additive manufacturing
WO2018216514A1 (en) * 2017-05-22 2018-11-29 川崎重工業株式会社 High temperature component and method for producing same
JP2019035144A (en) * 2017-08-10 2019-03-07 三菱日立パワーシステムズ株式会社 Method for producing Ni-based alloy member

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2017529453A (en) * 2014-07-21 2017-10-05 ヌオーヴォ ピニォーネ ソチエタ レスポンサビリタ リミタータＮｕｏｖｏ Ｐｉｇｎｏｎｅ Ｓ．Ｒ．Ｌ． Method for manufacturing machine components by additive manufacturing
JP2017036485A (en) * 2015-08-12 2017-02-16 山陽特殊製鋼株式会社 Ni-based superalloy powder for additive manufacturing
WO2018216514A1 (en) * 2017-05-22 2018-11-29 川崎重工業株式会社 High temperature component and method for producing same
JP2019035144A (en) * 2017-08-10 2019-03-07 三菱日立パワーシステムズ株式会社 Method for producing Ni-based alloy member

Also Published As

Publication number Publication date
JP2024110677A (en) 2024-08-16

Similar Documents

Publication Publication Date Title
KR102722473B1 (en) Aluminum alloy parts manufacturing process
AU2015294055B2 (en) Method for manufacturing machine components by additive manufacturing
US12152291B2 (en) Process for manufacturing an aluminum-chromium alloy part with superimposed successive solid metals layer
CN112805105B (en) Method for manufacturing aluminum alloy parts
JP6499546B2 (en) Ni-based superalloy powder for additive manufacturing
US12037661B2 (en) Process for manufacturing an aluminum alloy part
CN113862543A (en) Method for manufacturing alloy member
US12134127B2 (en) Composite member
CN113412172B (en) Method for manufacturing aluminum alloy parts
US20230191488A1 (en) Method for producing an aluminium alloy part
CN115551659A (en) Method for preparing aluminum alloy parts
US20240227023A1 (en) Method for producing an aluminum alloy part implementing an additive manufacturing technique with preheating
JP7689847B2 (en) Manufacturing method of molded objects using Fe-based alloy powder
JP7103548B2 (en) Ni—Cr—Mo alloy member, Ni—Cr—Mo alloy powder, and composite member
WO2024162379A1 (en) Nickel-based superalloy, nickel-based superalloy powder, and method for manufacturing molded body
JP7685546B2 (en) Nickel-based superalloy, nickel-based superalloy powder and method for producing shaped body
WO2022054803A1 (en) Ni-BASED ALLOY POWDER AND METHOD FOR MANUFACTURING LAMINATION MOLDED ARTICLE USING SAID Ni-BASED ALLOY POWDER
WO2019074059A1 (en) Titanium-based alloy member, method for producing titanium-based alloy member, and product in which titanium-based alloy member is used
WO2023027054A1 (en) Nickel-based superalloy and powder thereof, and nickel-based superalloy molded article manufacturing method
JP7677529B2 (en) Ni-Cr alloy member made of laminated body, manufacturing method of Ni-Cr alloy member, and product using Ni-Cr alloy member
JP7670237B2 (en) Alloys, alloy powders, alloy components, and composite components
WO2023074613A1 (en) Ni alloy powder suited to additive manufacturing and additively manufactured article obtained using same
WO2025053148A1 (en) Ni-based alloy powder for additive manufacturing and method for manufacturing ni-based alloy molding
JP2024156538A (en) Copper alloy powder, laminated object using same, and copper alloy molded object made of laminated object
WO2023095805A1 (en) Composite material, manufacturing method for composite material, and mold

Legal Events

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

Ref document number: 24750328

Country of ref document: EP

Kind code of ref document: A1