WO2018092204A1 - ニッケル基合金高温部材の製造方法 - Google Patents
ニッケル基合金高温部材の製造方法 Download PDFInfo
- Publication number
- WO2018092204A1 WO2018092204A1 PCT/JP2016/083931 JP2016083931W WO2018092204A1 WO 2018092204 A1 WO2018092204 A1 WO 2018092204A1 JP 2016083931 W JP2016083931 W JP 2016083931W WO 2018092204 A1 WO2018092204 A1 WO 2018092204A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- phase
- temperature
- forging
- mold
- hot
- Prior art date
Links
Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/02—Preliminary treatment of metal stock without particular shaping, e.g. salvaging segregated zones, forging or pressing in the rough
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
- B21K3/00—Making engine or like machine parts not covered by sub-groups of B21K1/00; Making propellers or the like
- B21K3/04—Making engine or like machine parts not covered by sub-groups of B21K1/00; Making propellers or the like blades, e.g. for turbines; Upsetting of blade roots
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
Definitions
- the present invention relates to a technique for manufacturing a high-temperature member such as a member for a steam turbine, and particularly relates to a method for manufacturing a high-temperature member made of a nickel-based alloy having a higher high-temperature strength than heat-resistant steel.
- the main steam temperature is 600 ° C (about 600-620 ° C), and the power transmission efficiency is about 42%.
- A-USC advanced super supercritical
- Heat-resistant steel eg, ferritic heat-resistant steel, austenitic heat-resistant steel
- high-temperature members eg, turbine blades
- high-temperature components of the 700 ° C class A-USC power plant must be able to maintain the necessary and sufficient mechanical properties (for example, creep strength) at the main steam temperature.
- nickel (Ni) based alloys with excellent strength is assumed.
- High temperature components of power plants are often manufactured by hot die forging to ensure the necessary mechanical properties.
- hot die forging from the viewpoint of shape accuracy, it is important to increase the difference in deformation resistance between the mold and the forged material (the forged material is easy to deform and the die is difficult to deform). is there.
- the forging material is taken out immediately. A method of performing a forging press with an unheated mold is performed.
- Ni-based alloys particularly, ⁇ 'phase precipitation strengthened Ni-based alloys
- the contact surface of the forged material is caused by the contact between the mold and the forged material.
- a rapid temperature drop occurs, and the ⁇ ′ phase begins to precipitate due to the temperature drop of the forged material, and the forged material hardens rapidly.
- the deformation resistance of the material to be forged is rapidly increased and the ductility is lowered, so that there is a problem that the forging yield is lowered and the mold is damaged.
- Patent Document 1 Japanese Patent Laid-Open No. 2-133133
- the stress applied to the impression surface of the mold by the hydraulic press is the deformation resistance value of the mold material.
- a hot precision die forging method is disclosed in which forging is performed while a constant pressure within a range not exceeding 1 is continuously applied from the start of pressurization to the end of pressurization.
- Patent Document 2 Japanese Unexamined Patent Application Publication No. 2015-193045
- a third step of hot forging the forging material and the heating device includes a lower heating section divided in a facing direction of the lower mold and the upper mold.
- An upper heating unit, and the first step is performed in a state where the lower heating unit and the upper heating unit are in contact with each other in the opposing direction, and the second step is performed by the lower heating unit and the upper heating unit.
- a method for producing a forged product is disclosed, which is performed in a state of being separated in the facing direction.
- Patent Documents 1 and 2 in hot die forging technology for difficult-to-work metals such as Ni-base heat-resistant alloys and titanium (Ti) alloys, it becomes possible to reduce the size of forging equipment and simplify the manufacturing procedure. It is said that the cost of forged metal forged products can be reduced.
- Patent Documents 1 and 2 describe that a Ni-based alloy is used as a material for a hot forging die.
- Patent Documents 1 and 2 it is not considered that hot die forging of such a high-strength, high heat-resistant Ni-based alloy material is assumed, and a die that can withstand the hot die forging. There is not enough explanation about. In other words, if the techniques of Patent Documents 1 and 2 are applied as they are to a high-temperature member for a 700 ° C A-USC power plant, it is difficult to ensure a sufficient deformation resistance difference between the mold and the forged material. Therefore, there is a concern that the forging yield may be reduced and the mold may be damaged (resulting in an increase in manufacturing cost of the high temperature member).
- a mold made of a refractory metal such as tungsten (W) is a material that has a high material cost and a high mold manufacturing cost and is difficult to repair. Therefore, the use of a refractory metal mold increases the cost. There is a problem of inviting.
- a mold made of a heat-resistant ceramic material has a weak point in the mold life because the impact resistance of the ceramic material is low, and there is a problem that the use of a ceramic material mold also increases the cost.
- the present invention has been made in view of the above problems, and its purpose is to significantly increase the manufacturing cost even for a high-temperature member made of a Ni-based alloy that is superior in high-temperature strength and heat resistance to heat-resistant steel. It is an object of the present invention to provide a method that enables stable production without incurring any problems.
- One aspect of the present invention is a method for producing a high-temperature member made of a Ni-based alloy, A melting / casting process for melting and casting the Ni-based alloy material to form a workpiece; and A hot die forging step of forming a forged molded material by performing hot die forging using a predetermined die for the workpiece; A solution treatment and an aging treatment step of forming a precipitation strengthening molding material by performing a solution treatment and an aging treatment on the forged molding material,
- the predetermined mold has a composition in which a ⁇ ′ (gamma prime) phase of 10% by volume or more is precipitated at 1050 ° C. with respect to a ⁇ (gamma) phase serving as a parent phase. The temperature is higher than 1050 ° C.
- the hot die forging step uses a heating device, and a die / workpiece material co-heating element step for heating to the forging temperature together with the work piece sandwiched between the molds, It comprises a hot forging element process in which the die heated to a forging temperature and the workpiece are taken out from the heating device to a room temperature environment and immediately hot forged using a press device.
- the present invention provides a method for producing a high temperature Ni-base alloy member.
- the ⁇ ′ phase precipitation ratio and the solid solution temperature of Ni-base alloys and Ni-base superalloys can be values obtained by thermodynamic calculation from the composition of the alloys.
- the present invention can add the following improvements and changes to the above-described Ni-based alloy high temperature member manufacturing method.
- the composition of the strong precipitation strengthened Ni-base superalloy is 10 mass% to 25 mass% Cr (chromium), more than 0 mass% to 30 mass% Co (cobalt), 1 mass% to 6 mass%
- the forging temperature is 900 ° C. or higher and 20 ° C. or lower than the solid solution temperature of the ⁇ ′ phase in the strong precipitation strengthened Ni-base superalloy.
- the mold has a tensile strength at 900 ° C. of 450 MPa or more.
- a preform forming step for forming a preform in which ⁇ 'phase crystal grains (intergranular ⁇ ' phase crystal grains) are precipitated between the ⁇ phase crystal grains The preform is reheated to the hot working temperature to reduce the ⁇ ′ phase crystal grains (intragranular ⁇ ′ phase crystal grains) in the ⁇ phase crystal grains, and then to 100 ° C. up to 500 ° C.
- the hot die forging step is performed on the softened preform.
- a method that enables stable production without causing a significant increase in production cost even for a high-temperature member made of a Ni-based alloy that is superior in high-temperature strength and heat resistance to heat-resistant steel. Can do. As a result, it is possible to provide a high-temperature member made of a Ni-based alloy having excellent high-temperature strength and heat resistance at a low cost.
- the temperature of the mold is usually set lower than the temperature of the material to be forged. This is considered to ensure that the deformation resistance of the mold during forging is larger than that of the material to be forged.
- a mold having a deformation resistance larger than the deformation resistance of the material to be forged at the hot forging temperature of the material to be forged is within an industrially acceptable cost range (so-called low cost). It is thought that it was difficult to prepare.
- a mold having a deformation resistance larger than the deformation resistance of the forged material at the hot forging temperature of the forged material can be prepared at low cost, the forged material and the mold are It becomes possible to perform hot die forging in a temperature state, and in hot die forging to Ni-based alloy materials with excellent high-temperature strength and heat resistance, it can contribute to yield improvement and cost reduction compared to conventional technology.
- the present inventors examined a technique for preparing a die having a higher high-temperature strength than a conventional die for hot die forging at a low cost.
- As a basic direction for increasing the high-temperature strength it is conceivable to increase the amount of the ⁇ ′ phase that is precipitated in the ⁇ phase that is the parent phase in the precipitation-strengthened Ni-based alloy.
- Ni-base alloys in which ⁇ ' phase is precipitated by 30% by volume or more have conventionally been too hard to work. There is a problem that it is extremely bad, and it has been considered difficult to prepare a die for hot die forging at low cost using the strong precipitation strengthened Ni-base superalloy.
- the present inventors returned to the mechanism of increasing the strength by ⁇ 'phase precipitation to investigate and examine the technical problem.
- the precipitation form of the ⁇ 'phase in the intermediate material is controlled (a part of the ⁇ ' phase grains that normally precipitate in the ⁇ phase grains is converted into ⁇ 'phase grains that precipitate between the ⁇ phase grains) It has been found that the workability is dramatically improved even with a strong precipitation strengthened Ni-base superalloy member.
- Ni-base superalloy members strengthened by precipitation by aging treatment can be easily re-softened by controlling the precipitation ratio of intergranular ⁇ 'phase grains to 10% by volume or more. .
- FIG. 1 is a flowchart showing an example of steps of a method for producing a Ni-based alloy high temperature member according to the present invention.
- a melting / casting step (S1) is performed in which a Ni-based alloy material is melted and cast to form a workpiece.
- the melting method and the casting method There is no particular limitation on the melting method and the casting method, and conventional methods for Ni-based alloy materials can be used.
- a softening step (S2) is performed in which the workpiece is preformed and softened to form a softened preform.
- this step is not an essential step, for example, this step is preferably performed in the case of a workpiece made of a heat-resistant Ni-based alloy whose solid solution temperature of the ⁇ ′ phase is higher than 1000 ° C. Specific processes and mechanisms of the softening process will be described later.
- a hot die forging step (S3) for forming a forged molded material by performing hot die forging on a workpiece (or softened preform) using a predetermined die.
- the hot die forging step S3 includes a mold / workpiece material co-heating elementary step (S3a) and a hot forging elementary step (S3b).
- the present invention has the greatest feature in this hot die forging step S3.
- the predetermined mold has a composition in which a ⁇ ′ phase of 10% by volume or more is precipitated at 1050 ° C. with respect to the ⁇ phase as a parent phase, and the solid solution temperature of the ⁇ ′ phase is higher than 1050 ° C. and 1250 ° C.
- a die made of a strong precipitation strengthened Ni-base superalloy is used.
- the ⁇ 'phase has two types, an intragranular ⁇ ' phase crystal grain that precipitates in the crystal grains of the ⁇ phase of the parent phase, and an intergranular ⁇ 'phase crystal grain that precipitates between the crystal grains of the ⁇ phase. It is important to have the following precipitation form.
- the strong precipitation-strengthened Ni-base superalloy is 10-25% Cr, more than 0%, 30% or less Co, 1-6% Al, 2.5-7% Ti, Ti and Nb in mass%.
- Total with Ta is 3-9%, Mo less than 4%, W less than 4%, Zr less than 0.08%, Fe less than 10%, B less than 0.03%, C less than 0.1%, less than 2%
- a composition containing Hf and 5% or less of Re, with the balance being Ni and inevitable impurities can be suitably used.
- the mold / workpiece material co-heating element step S3a is an element process using a heating device to heat the work piece to the forging temperature in a state of being sandwiched between the molds.
- a heating apparatus There is no special limitation in a heating apparatus, For example, a conventional heating furnace can be used.
- the lower limit of the forging temperature but 900 ° C. or higher is preferable because it is a hot forging of a Ni-based alloy.
- the upper limit of the forging temperature is preferably 20 ° C. or lower than the solid solution temperature of the ⁇ ′ phase in the mold alloy. From the viewpoint of preventing seizure between the mold and the workpiece, it is preferable to interpose an inorganic release material between the mold and the workpiece.
- the hot forging element process S3b is a process in which the die heated to the forging temperature and the workpiece are taken out from the heating device to a room temperature environment and immediately hot forged using a press device.
- This elementary process S3b has the advantage that the temperature of the workpiece is unlikely to decrease because the workpiece and the mold sandwiching the workpiece are in an isothermal state and the heat capacity of the mold is added. Therefore, a special mechanism (for example, a heating mechanism) is not required for the press device, and a conventional press device can be used.
- the mold / work material co-heating element process S3a and The hot forging element process S3b may be repeated.
- the hot die forging step S3 of the present invention can be performed using a conventional heating device and a conventional press device without using a hot forging device equipped with a special mechanism. Therefore, there exists an advantage which can suppress apparatus cost (namely, manufacturing cost).
- a solution treatment and an aging treatment step (S4) for forming a precipitation-strengthened molding material by performing a solution treatment and an aging treatment on the forged molding material are performed.
- the solution treatment and the aging treatment There is no particular limitation on the solution treatment and the aging treatment, and the conventional solution treatment / aging treatment may be performed so as to satisfy the characteristics required for the high temperature member to be produced.
- a finishing step (S5) is performed in which the precipitation-strengthened molding material is finished to form a desired high-temperature member.
- a conventional finishing process for example, surface finishing
- the present invention has a great feature in that a die made of a strong precipitation strengthened Ni-base superalloy can be prepared at low cost.
- die used by this invention is demonstrated.
- FIG. 2 is a flowchart showing a process example of a method for manufacturing a strong precipitation strengthened Ni-base superalloy mold used in the present invention.
- a melting / casting step (S1 ') is performed in which a material of strong precipitation strengthened Ni-base superalloy is melted and cast to form an ingot.
- the melting method and the casting method There is no particular limitation on the melting method and the casting method, and conventional methods for Ni-based alloy materials can be used.
- the strong precipitation-strengthened Ni-base superalloy is 10 to 25% Cr, more than 0% to 30% Co, 1 to 6% Al, 2.5 to 7% Ti, Ti, as described above. 3 to 9%, Mo less than 4%, W less than 4%, Zr less than 0.08%, Fe less than 10%, B less than 0.03%, C less than 0.1%, 2
- a composition containing not more than% Hf and not more than 5% Re, with the balance being Ni and inevitable impurities, can be suitably used.
- FIG. 3 is a schematic diagram showing changes in the softening process and the microstructure.
- the softening step S2 ' includes a preformed body forming element process (S2a') and a softening preformed body forming element process (S2b ').
- the softening step S2 'performed here is substantially the same as the softening step S2 in the method for manufacturing a high temperature member.
- the preformed body forming element step S2a ′ is performed at a temperature not lower than 1000 ° C. and lower than the solid solution temperature of the ⁇ ′ phase in the Ni-base superalloy of the ingot (that is, the temperature at which the ⁇ ′ phase exists).
- ⁇ 'phase crystal grains intergranular ⁇ ' phase crystal grains precipitated between the ⁇ phase crystal grains that are the parent phase of the Ni-base superalloy. It is.
- the precipitation ratio of intergranular ⁇ ′ phase crystal grains is preferably 10% by volume or more, and more preferably 20% by volume or more.
- the hot working method is not particularly limited, and a conventional method (for example, hot forging) can be used. Moreover, you may perform a homogenization process with respect to an ingot before hot processing as needed.
- the mechanism of ⁇ ′ phase precipitation strengthening in Ni-based alloys is that the interface between the ⁇ phase crystal grains of the parent phase and the ⁇ ′ phase crystal grains of the precipitate is highly consistent (so-called This is considered to be mainly due to the formation of the matching interface.
- the ⁇ phase crystal grains and the intergranular ⁇ ′ phase crystal grains formed an interface with low consistency (so-called non-matching interface) and contributed little to precipitation strengthening. From these facts, the present inventors, even in the case of a strong precipitation strengthened Ni-base superalloy, will dramatically improve the workability of the alloy by converting the intragranular ⁇ 'phase grains to intergranular ⁇ ' phase grains. I got the knowledge that it improved.
- the softening preformed body forming element step S2b ′ is reheated to the above hot working temperature with respect to the above preformed body to dissolve and reduce the intragranular ⁇ ′ phase crystal grains, and then to 100 ° C. up to 500 ° C.
- This is an elementary process for forming a softened preform by performing a softening heat treatment to grow intergranular ⁇ ′ phase crystal grains by slow cooling at a cooling rate of ° C./h or less.
- the cooling rate to 500 ° C is more preferably 50 ° C / h or less, and further preferably 10 ° C / h or less.
- the meaning of the annealing end temperature of 500 ° C is the temperature at which the absolute temperature becomes sufficiently low and the rearrangement of atoms in the Ni-based alloy (ie, crystallization of another phase) becomes substantially difficult. It is.
- a mold forming step (S6) is performed to form a softened mold having a desired shape by performing a molding process on the softened preform.
- the softened preform has high workability, low-cost cold processing and warm processing (for example, press processing, cutting processing) can be performed. It can be suitably used.
- FIG. 4 is a schematic diagram showing the process of the partial solution treatment / aging process and the change in the microstructure.
- the partial solution treatment of the present invention is a heat treatment for raising the temperature to a temperature equivalent to the previous hot working temperature. Since the temperature is lower than the solid solution temperature of the ⁇ 'phase, the precipitation amount of the ⁇ ' phase (here, intergranular ⁇ 'phase crystal grains) is reduced, but all of the intergranular ⁇ ' phase crystal grains are dissolved. It will not disappear. Further, the partial solution treatment is preferably controlled so that the precipitation ratio of the intergranular ⁇ ′ phase crystal grains is 10% by volume or more and 1/2 or less of the total ⁇ ′ phase before the partial solution treatment. . For example, it is preferable to control the temperature of the partial solution treatment to be not less than the recrystallization temperature of the ⁇ phase and not more than 20 ° C. below the solid solution temperature of the ⁇ ′ phase.
- an aging treatment for precipitating intragranular ⁇ ′ phase grains is performed.
- a conventional aging treatment for example, 700 to 900 ° C.
- a finishing step (S5 ') is performed in which the precipitation strengthening mold is finished to form a desired mold.
- a conventional finishing process for example, surface finishing
- the mold used in the present invention can be manufactured without using a manufacturing apparatus equipped with a special mechanism, despite being made of a strong precipitation-strengthened Ni-base superalloy.
- a mold having a large deformation resistance at the hot forging temperature can be prepared at low cost, it can contribute to the reduction of the manufacturing cost of the high temperature member.
- the softened heat treatment (see the right side of FIG. 3) of the softened preformed body forming element step S2b ′ in the mold manufacturing method is performed on the damaged mold.
- the intragranular ⁇ ′ phase crystal grains precipitated in the partial solution treatment / aging treatment step S7 in the mold manufacturing method can be dissolved and reduced to grow intergranular ⁇ ′ phase crystal grains. This is exactly equivalent to the state of the softened preform in the mold manufacturing method.
- the mold used in the present invention is in a state in which intergranular ⁇ ′ phase crystal grains remain. Therefore, it is not necessary to perform the preformed body forming element step S2a ′ in the mold manufacturing method, and only by performing the softening heat treatment of the softened preformed body forming element process S2b ′, the state of the softened preform can be obtained. it can.
- the shape correction is performed on the damaged mold subjected to the softening heat treatment by performing a molding process (for example, a press process or a cutting process) similar to the mold molding step S6 in the mold manufacturing method.
- a molding process for example, a press process or a cutting process
- the mold used in the present invention is made of a strong precipitation-strengthened Ni-base superalloy, the damaged mold can be repaired and reused by a very simple method. This feature contributes to further reduction in the manufacturing cost of the high temperature member.
- Example 1 (Production, testing and evaluation of hot die forging die) A die for hot die forging was produced along the flow shown in FIG. First, alloy materials (alloys 1 to 6) having the composition shown in Table 1 were prepared, and the melting / casting step S1 ′ was performed. 100 kg of each alloy material was melted and cast by vacuum induction heating melting method to produce an ingot.
- the solid solution temperature of the ⁇ ′ phase of each alloy and the amount of precipitation of the ⁇ ′ phase at 1050 ° C. were calculated based on thermodynamic calculations.
- Alloy 1 is an Fe-based alloy and not a precipitation strengthening type alloy, the solid solution temperature of the ⁇ ′ phase and the precipitation amount of the ⁇ ′ phase at 1050 ° C. are not calculated.
- Alloy 2 is a ⁇ ′ phase precipitation strengthened Ni-based alloy, but the solid solution temperature of the ⁇ ′ phase is about 800 ° C., and the precipitation amount of the ⁇ ′ phase at 1050 ° C. is 0% by volume.
- Alloy 3 is a ⁇ ′ phase precipitation strengthened Ni-base superalloy, and the solid solution temperature of the ⁇ ′ phase is about 1100 ° C., and the precipitation amount of the ⁇ ′ phase at 1050 ° C. is 10% by volume or more.
- Alloys 4 to 6 are also ⁇ ′ phase precipitation strengthened Ni-base superalloys.
- the solid solution temperature of the ⁇ ′ phase is about 1150 ° C., and the precipitation amount of the ⁇ ′ phase at 1050 ° C. is 10% by volume or more.
- the ingots of alloys 1 and 2 were homogenized and then subjected to a preformed body forming element step S2a ′ for hot forging at 1050 ° C. to prepare a preformed body.
- the ingot of alloy 3 was homogenized and then subjected to a preformed body forming element step S2a ′ for hot forging at 1070 ° C. to prepare a preformed body.
- the ingots of alloys 4 to 5 were homogenized and then subjected to a preformed body forming element step S2a ′ for hot forging at 1100 ° C. to prepare a preformed body.
- each preform is reheated to the previous hot forging temperature, held for 1 hour, gradually cooled to 500 ° C. at a cooling rate of 10 ° C./h, and then softened preform formed by water cooling Elementary process S2b ′ was performed to produce a softened preform.
- the precipitation form of the ⁇ ′ phase was observed with respect to each test specimen for microstructure evaluation using a scanning electron microscope.
- the softened preform of Alloy 1 was not a precipitation strengthened alloy, and no precipitation of ⁇ 'phase was observed.
- the softened preform of alloy 2 only the intragranular ⁇ ′ phase was observed (no intergranular ⁇ ′ phase was observed).
- the softened preforms of Alloys 3 to 5 only the intergranular ⁇ 'phase was observed (no intragranular ⁇ ' phase was observed).
- a soft mold was produced by performing a mold forming step S6 by cutting the softened preforms of the alloys 1 to 5. For the ingot of alloy 6, cutting was attempted after cutting to a predetermined size. However, since cutting was difficult, a die was formed by electric discharge machining.
- a test piece for a tensile test was separately prepared in the same procedure as described above, and 900 ° C. using a high temperature tensile test apparatus.
- a tensile test at As a result the tensile strength of the test pieces of Alloys 1 and 2 was less than 300 MPa, but the tensile strength of the test pieces of Alloys 3 to 6 was 450 MPa or more.
- Example 2 (Preparation of Ni-based alloy high temperature member) Using the hot die forging die prepared in Experiment 1, a high temperature member made of a Ni-based alloy was produced along the flow shown in FIG. First, an alloy material having the composition shown in Table 2 was prepared, and the melting / casting step S1 was performed. An alloy material 100 kg was melted and cast by a vacuum induction heating melting method to produce a workpiece.
- a specimen for a tensile test was taken from a part of the workpiece, and a tensile test at 900 ° C. was performed using a high-temperature tensile test apparatus.
- the tensile strength of the test piece of the workpiece was about 300 MPa.
- a hot die forging step S3 was performed on the work material by performing hot die forging using each die prepared in Experiment 1 to form a forged material.
- a mold / workpiece co-heating element step S3a was performed in which the work piece was heated to 1000 ° C. with the work piece sandwiched between the molds.
- a hot forging element process S3b was performed in which the mold heated to 1000 ° C. and the workpiece were taken out from the heating device to a room temperature environment and immediately subjected to hot forging using a pressing device (pressure of 4000 tons). .
- the metal mold of alloy 3 was heated to 1070 ° C. and held for 1 hour, subjected to softening heat treatment by cooling to 500 ° C. at a cooling rate of 10 ° C./h, followed by water cooling.
- the molds of alloys 4 to 6 were heated to 1100 ° C. and held for 1 hour, subjected to softening heat treatment by cooling to 500 ° C. at a cooling rate of 10 ° C./h, followed by water cooling.
- the molds of alloys 3 to 4 were obtained by performing the partial solution / aging treatment step S7 of the present invention in the solution treatment / aging treatment at the time of producing the reinforced mold.
- the molds of alloys 5 to 6 are obtained by performing the conventional solution treatment and aging treatment in which the temperature is raised to a temperature higher than the solid solution temperature of the ⁇ ′ phase in the solution treatment. It is considered that almost no grains were precipitated. As a result, it is considered that good repairability could not be obtained even after softening heat treatment. In other words, it was confirmed that the presence of intergranular ⁇ ′ phase crystal grains is important in order to ensure good mold repairability.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Forging (AREA)
Abstract
Description
加熱した被成形材を、該被成形材の加熱温度と略同温度に加熱した金型を用い、液圧プレスにより、金型のインプレッション面に負荷される応力が該金型材料の変形抵抗値を超えない範囲内の一定の加圧力を、加圧開始時点より加圧終了までの間、継続して加えながら鍛造することを特徴とする熱間精密型鍛造方法が、開示されている。
下型と前記下型に対向して配置された上型とを、前記下型および上型の周囲に配置された加熱装置により加熱する第1の工程と、加熱された前記下型に鍛造素材を載置する第2の工程と、前記鍛造素材を熱間鍛造する第3の工程とを有し、前記加熱装置は、前記下型と上型の対向方向に分割された下側加熱部と上側加熱部を有し、前記第1の工程は前記下側加熱部と上側加熱部が前記対向方向に当接した状態で行い、前記第2の工程は前記下側加熱部と上側加熱部が前記対向方向に離間した状態で行うことを特徴とする鍛造製品の製造方法が、開示されている。
前記Ni基合金の素材を溶解・鋳造して被加工材を形成する溶解・鋳造工程と、
前記被加工材に対して所定の金型を用いて熱間型鍛造を行って鍛造成型材を形成する熱間型鍛造工程と、
前記鍛造成型材に対して溶体化処理および時効処理を行って析出強化成型材を形成する溶体化・時効処理工程と、を有し、
前記所定の金型は、1050℃において、母相となるγ(ガンマ)相に対して10体積%以上のγ’(ガンマ プライム)相が析出する組成を有し、前記γ’相の固溶温度が1050℃超1250℃未満であり、前記γ’相は前記γ相の結晶粒内に析出する粒内γ’相結晶粒と該γ相の結晶粒間に析出する粒間γ’相結晶粒との二種類の析出形態を有する強析出強化Ni基超合金からなる金型であり、
前記熱間型鍛造工程は、加熱装置を用いて、前記被加工材を前記金型に挟み込んだ状態で共に鍛造温度まで加熱する金型・被加工材共加熱素工程と、
鍛造温度まで加熱した前記金型と前記被加工材とを前記加熱装置から室温環境に取り出して直ちにプレス装置を用いて熱間鍛造を行う熱間鍛造素工程とからなる、
ことを特徴とするNi基合金高温部材の製造方法を提供するものである。
なお、本発明において、Ni基合金やNi基超合金のγ’相の析出割合や固溶温度は、該合金の組成から熱力学計算によって求められる値を利用できるものとする。
(i)前記強析出強化Ni基超合金の組成は、10質量%以上25質量%以下のCr(クロム)、0質量%超30質量%以下のCo(コバルト)、1質量%以上6質量%以下のAl(アルミニウム)、2.5質量%以上7質量%以下のTi、TiとNb(ニオブ)とTa(タンタル)との総和が3質量%以上9質量%以下、4質量%以下のMo(モリブデン)、4質量%以下のW、0.08質量%以下のZr(ジルコニウム)、10質量%以下のFe、0.03質量%以下のB(ホウ素)、0.1質量%以下のC(炭素)、2質量%以下のHf(ハフニウム)および5質量%以下のRe(レニウム)を含有し、残部がNiおよび不可避不純物からなる。
(ii)前記鍛造温度が、900℃以上かつ前記強析出強化Ni基超合金における前記γ’相の固溶温度より20℃低い温度以下である。
(iii)前記金型は、900℃における引張強さが450 MPa以上である。
(iv)前記溶解・鋳造工程と前記熱間型鍛造工程との間に、前記被加工材を軟化させる軟化工程を更に有し、
前記軟化工程は、前記被加工材に対して1000℃以上かつ該被加工材の前記Ni基合金におけるγ’相の固溶温度未満の温度で熱間加工を行って前記Ni基合金の母相となるγ相の結晶粒間にγ’相結晶粒(粒間γ’相結晶粒)が析出した予備成型体を形成する予備成型体形成素工程と、
前記予備成型体に対して前記熱間加工の温度まで再加熱してγ相の結晶粒内のγ’相結晶粒(粒内γ’相結晶粒)を減少させた後、500℃まで100℃/h以下の冷却速度で徐冷して前記粒間γ’相結晶粒を成長させた軟化予備成型体を形成する軟化予備成型体形成素工程とからなり、
前記熱間型鍛造工程は、前記軟化予備成型体に対して行う。
特許文献1~2に記載されているように、従来の熱間型鍛造方法では、通常、金型の温度が被鍛造材の温度よりも低く設定される。これは、鍛造中の金型の変形抵抗が被鍛造材のそれよりも大きい状態を確保するためと考えられる。言い換えると、従来技術においては、被鍛造材の熱間鍛造温度で該被鍛造材の変形抵抗よりも大きい変形抵抗を有する金型を、工業的に許容できるコストの範囲内(いわゆる低コスト)で用意することが困難であったと考えられる。
図1は、本発明に係るNi基合金高温部材の製造方法の工程例を示すフロー図である。図1に示したように、まず、Ni基合金の素材を溶解・鋳造して被加工材を形成する溶解・鋳造工程(S1)を行う。溶解方法および鋳造方法に特段の限定はなく、Ni基合金材に対する従前の方法を利用できる。
前述したように、本発明は、強析出強化Ni基超合金からなる金型を低コストで用意できることに、大きな特徴がある。以下、本発明で用いる金型の製造方法について説明する。
本発明に係る高温部材の製造方法によって、熱間型鍛造用の金型に変形などの損傷が生じた場合、以下のような方法で補修を実施できる。言い換えると、本発明で用いる金型は、容易に補修が可能という優れた特徴を有する。
(熱間型鍛造用金型の作製および試験・評価)
図2に示したフローに沿って熱間型鍛造用の金型を作製した。まず、表1に示す組成を有する合金素材(合金1~6)を用意し、溶解・鋳造工程S1’を行った。各合金素材100 kgずつを真空誘導加熱溶解法により溶解し鋳造して、鋳塊を作製した。
(Ni基合金高温部材の作製)
実験1で用意した熱間型鍛造用金型を用い、図1に示したフローに沿ってNi基合金からなる高温部材を作製した。まず、表2に示す組成を有する合金素材を用意し、溶解・鋳造工程S1を行った。合金素材100 kgを真空誘導加熱溶解法により溶解し鋳造して、被加工材を作製した。
(熱間型鍛造用金型の補修性の評価)
実験2において良好な熱間型鍛造が可能であった合金3~6の金型に対し、補修性(補修が可能であるか否か)を評価した。まず、実験2で用いた合金3~6の金型に対して、実験1における軟化予備成型体形成素工程S2b’の軟化熱処理を施した。
Claims (5)
- Ni基合金からなる高温部材の製造方法であって、
前記Ni基合金の素材を溶解・鋳造して被加工材を形成する溶解・鋳造工程と、
前記被加工材に対して所定の金型を用いて熱間型鍛造を行って鍛造成型材を形成する熱間型鍛造工程と、
前記鍛造成型材に対して溶体化処理および時効処理を行って析出強化成型材を形成する溶体化・時効処理工程と、を有し、
前記所定の金型は、1050℃において、母相となるγ相に対して10体積%以上のγ’相が析出する組成を有し、前記γ’相の固溶温度が1050℃超1250℃未満であり、前記γ’相は前記γ相の結晶粒内に析出する粒内γ’相結晶粒と該γ相の結晶粒間に析出する粒間γ’相結晶粒との二種類の析出形態を有する強析出強化Ni基超合金からなる金型であり、
前記熱間型鍛造工程は、加熱装置を用いて、前記被加工材を前記金型に挟み込んだ状態で共に鍛造温度まで加熱する金型・被加工材共加熱素工程と、
鍛造温度まで加熱した前記金型と前記被加工材とを前記加熱装置から室温環境に取り出して直ちにプレス装置を用いて熱間鍛造を行う熱間鍛造素工程とからなる、
ことを特徴とするNi基合金高温部材の製造方法。 - 請求項1に記載のNi基合金高温部材の製造方法において、
前記強析出強化Ni基超合金の組成は、質量%で、10~25%のCr、0%超30%以下のCo、1~6%のAl、2.5~7%のTi、TiとNbとTaとの総和が3~9%、4%以下のMo、4%以下のW、0.08%以下のZr、10%以下のFe、0.03%以下のB、0.1%以下のC、2%以下のHfおよび5%以下のReを含有し、残部がNiおよび不可避不純物からなることを特徴とするNi基合金高温部材の製造方法。 - 請求項1又は請求項2に記載のNi基合金高温部材の製造方法において、
前記鍛造温度が、900℃以上かつ前記強析出強化Ni基超合金における前記γ’相の固溶温度より20℃低い温度以下であることを特徴とするNi基合金高温部材の製造方法。 - 請求項1乃至請求項3のいずれか一項に記載のNi基合金高温部材の製造方法において、
前記金型は、900℃における引張強さが450 MPa以上であることを特徴とするNi基合金高温部材の製造方法。 - 請求項1乃至請求項4のいずれか一項に記載のNi基合金高温部材の製造方法において、
前記溶解・鋳造工程と前記熱間型鍛造工程との間に、前記被加工材を予備成型・軟化させる軟化工程を更に有し、
前記軟化工程は、前記被加工材に対して1000℃以上かつ該被加工材の前記Ni基合金におけるγ’相の固溶温度未満の温度で熱間加工を行って前記Ni基合金の母相となるγ相の結晶粒間にγ’相結晶粒(粒間γ’相結晶粒)が析出した予備成型体を形成する予備成型体形成素工程と、
前記予備成型体に対して前記熱間加工の温度まで再加熱してγ相の結晶粒内のγ’相結晶粒(粒内γ’相結晶粒)を減少させた後、500℃まで100℃/h以下の冷却速度で徐冷して前記粒間γ’相結晶粒を成長させた軟化予備成型体を形成する軟化予備成型体形成素工程とからなり、
前記熱間型鍛造工程は、前記軟化予備成型体に対して行う、
ことを特徴とするNi基合金高温部材の製造方法。
Priority Applications (11)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/JP2016/083931 WO2018092204A1 (ja) | 2016-11-16 | 2016-11-16 | ニッケル基合金高温部材の製造方法 |
CN202110414229.XA CN113122789B (zh) | 2016-11-16 | 2016-11-16 | 镍基合金模具和该模具的修补方法 |
EP16921781.7A EP3543369B8 (en) | 2016-11-16 | 2016-11-16 | Method for producing nickel-based alloy high temperature material |
US16/348,774 US11021780B2 (en) | 2016-11-16 | 2016-11-16 | Method for manufacturing nickel-based alloy high-temperature component |
JP2018550910A JP6727323B2 (ja) | 2016-11-16 | 2016-11-16 | ニッケル基合金高温部材の製造方法 |
KR1020207022510A KR102150341B1 (ko) | 2016-11-16 | 2016-11-16 | 니켈기 합금 금형 및 상기 금형의 보수 방법 |
CN201680090850.2A CN109963961B (zh) | 2016-11-16 | 2016-11-16 | 镍基合金高温构件的制造方法 |
RU2019114230A RU2710701C9 (ru) | 2016-11-16 | 2016-11-16 | Способ изготовления высокотемпературного элемента конструкции из сплава на основе никеля |
KR1020197013652A KR102143369B1 (ko) | 2016-11-16 | 2016-11-16 | 니켈기 합금 고온 부재의 제조 방법 |
TW106136628A TWI674934B (zh) | 2016-11-16 | 2017-10-25 | 鎳基合金高溫構件的製造方法 |
US17/239,616 US11401597B2 (en) | 2016-11-16 | 2021-04-25 | Method for manufacturing nickel-based alloy high-temperature component |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PCT/JP2016/083931 WO2018092204A1 (ja) | 2016-11-16 | 2016-11-16 | ニッケル基合金高温部材の製造方法 |
Related Child Applications (2)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US16/348,774 A-371-Of-International US11021780B2 (en) | 2016-11-16 | 2016-11-16 | Method for manufacturing nickel-based alloy high-temperature component |
US17/239,616 Continuation US11401597B2 (en) | 2016-11-16 | 2021-04-25 | Method for manufacturing nickel-based alloy high-temperature component |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2018092204A1 true WO2018092204A1 (ja) | 2018-05-24 |
Family
ID=62145446
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2016/083931 WO2018092204A1 (ja) | 2016-11-16 | 2016-11-16 | ニッケル基合金高温部材の製造方法 |
Country Status (8)
Country | Link |
---|---|
US (2) | US11021780B2 (ja) |
EP (1) | EP3543369B8 (ja) |
JP (1) | JP6727323B2 (ja) |
KR (2) | KR102150341B1 (ja) |
CN (2) | CN109963961B (ja) |
RU (1) | RU2710701C9 (ja) |
TW (1) | TWI674934B (ja) |
WO (1) | WO2018092204A1 (ja) |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN111629852A (zh) * | 2018-11-30 | 2020-09-04 | 三菱日立电力系统株式会社 | Ni基合金软化粉末和该软化粉末的制造方法 |
KR20210022599A (ko) * | 2018-10-29 | 2021-03-03 | 리버디 엔지니어링 리미티드 | 고 감마 프라임 니켈계 초합금 및 터빈 엔진 부품의 제조방법 |
CN112513301A (zh) * | 2018-07-31 | 2021-03-16 | 赛峰集团 | 通过粉末成型制造零件的镍基超合金 |
CN113930697A (zh) * | 2021-09-23 | 2022-01-14 | 鞍钢集团北京研究院有限公司 | 一种750-850℃级变形高温合金的热处理方法 |
CN115233125A (zh) * | 2022-07-25 | 2022-10-25 | 华能国际电力股份有限公司 | 一种厚壁高温合金部件的热处理方法 |
US11634792B2 (en) | 2017-07-28 | 2023-04-25 | Alloyed Limited | Nickel-based alloy |
WO2023243146A1 (ja) * | 2022-06-17 | 2023-12-21 | 三菱重工業株式会社 | Ni基合金部材の製造方法 |
Families Citing this family (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN110484841B (zh) * | 2019-09-29 | 2020-09-29 | 北京钢研高纳科技股份有限公司 | 一种gh4780合金锻件的热处理方法 |
CN111060553B (zh) * | 2019-12-05 | 2022-04-08 | 北京钢研高纳科技股份有限公司 | 确定gh4738合金锻造温度的方法、该合金锻件及其锻造方法和应用 |
US11384414B2 (en) * | 2020-02-07 | 2022-07-12 | General Electric Company | Nickel-based superalloys |
AU2021233462B2 (en) | 2020-03-13 | 2024-05-23 | Proterial, Ltd. | Method for manufacturing hot-forged member |
JP2021172852A (ja) * | 2020-04-24 | 2021-11-01 | 三菱パワー株式会社 | Ni基合金補修部材および該補修部材の製造方法 |
CN111519069B (zh) * | 2020-05-08 | 2021-11-30 | 中国华能集团有限公司 | 一种高强镍钴基高温合金及其制备工艺 |
CN111394621A (zh) * | 2020-05-08 | 2020-07-10 | 中国华能集团有限公司 | 一种可形成复合耐蚀层的变形高温合金及其制备工艺 |
CN111549313B (zh) * | 2020-06-24 | 2022-05-03 | 合肥学院 | 一种高温诱导钛锆基合金表面耐磨扩散层的制备方法 |
CN111745114B (zh) * | 2020-06-30 | 2022-03-15 | 中国航发动力股份有限公司 | 一种gh4163环形锻件胎模锻造方法 |
US11951528B2 (en) * | 2020-08-20 | 2024-04-09 | Rolls-Royce Corporation | Controlled microstructure for superalloy components |
CN113234963B (zh) * | 2021-05-19 | 2021-12-17 | 沈阳航空航天大学 | 室温以及低温环境用镍铬基超合金及其制备方法 |
CN113430406B (zh) * | 2021-05-21 | 2022-01-14 | 中国科学院金属研究所 | 一种沉淀强化CoCrNiAlNb多主元合金及其制备方法 |
CN114700451B (zh) * | 2022-03-28 | 2023-11-03 | 江西宝顺昌特种合金制造有限公司 | 一种Waspaloy镍基合金的锻造生产工艺 |
CN114682718B (zh) * | 2022-03-30 | 2023-10-20 | 江西宝顺昌特种合金制造有限公司 | 一种hb-2合金锻件及其制备方法 |
CN115287427B (zh) * | 2022-07-19 | 2023-11-10 | 西安聚能高温合金材料科技有限公司 | 一种Fe-Ni-Co基高温合金GH907合金棒材制备方法 |
CN115572930B (zh) * | 2022-11-09 | 2023-08-29 | 江苏美特林科特殊合金股份有限公司 | 一种提高镍基铸造合金综合性能的热处理方法 |
Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60116740A (ja) * | 1983-11-30 | 1985-06-24 | Daido Steel Co Ltd | 鍛造用金敷 |
JPH02133133A (ja) | 1988-11-09 | 1990-05-22 | Kobe Steel Ltd | 熱間精密型鍛造方法 |
JPH0441641A (ja) * | 1990-06-07 | 1992-02-12 | Kobe Steel Ltd | 金型用ニッケル基超耐熱合金 |
JPH0885838A (ja) * | 1994-07-19 | 1996-04-02 | Hitachi Metals Ltd | Ni基超耐熱合金 |
US20040221927A1 (en) * | 2002-07-19 | 2004-11-11 | Raymond Edward Lee | Isothermal forging of nickel-base superalloys in air |
WO2015008343A1 (ja) * | 2013-07-17 | 2015-01-22 | 三菱日立パワーシステムズ株式会社 | Ni基合金製品とその製造方法、およびNi基合金部材とその製造方法 |
JP2015193045A (ja) | 2014-03-28 | 2015-11-05 | 日立金属株式会社 | 鍛造装置および鍛造製品の製造方法 |
WO2016152982A1 (ja) * | 2015-03-25 | 2016-09-29 | 日立金属株式会社 | Ni基超耐熱合金の製造方法 |
Family Cites Families (19)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4740354A (en) * | 1985-04-17 | 1988-04-26 | Hitachi, Metals Ltd. | Nickel-base alloys for high-temperature forging dies usable in atmosphere |
US4769087A (en) * | 1986-06-02 | 1988-09-06 | United Technologies Corporation | Nickel base superalloy articles and method for making |
US5547523A (en) * | 1995-01-03 | 1996-08-20 | General Electric Company | Retained strain forging of ni-base superalloys |
US5759305A (en) | 1996-02-07 | 1998-06-02 | General Electric Company | Grain size control in nickel base superalloys |
EP1666618B2 (en) | 2000-10-04 | 2015-06-03 | General Electric Company | Ni based superalloy and its use as gas turbine disks, shafts and impellers |
US6932877B2 (en) * | 2002-10-31 | 2005-08-23 | General Electric Company | Quasi-isothermal forging of a nickel-base superalloy |
CN1587649A (zh) | 2004-07-28 | 2005-03-02 | 斯奈克玛马达公司 | 用于涡轮发动机的中空叶片的制造方法 |
US20090060714A1 (en) | 2007-08-30 | 2009-03-05 | General Electric Company | Multi-part cast turbine engine component having an internal cooling channel and method of forming a multi-part cast turbine engine component |
JP5235383B2 (ja) | 2007-11-07 | 2013-07-10 | 株式会社日立製作所 | Ni基単結晶合金及び鋳物 |
ES2534043T3 (es) | 2008-10-02 | 2015-04-16 | Nippon Steel & Sumitomo Metal Corporation | Aleación basada en el níquel resistente al calor |
US20110076180A1 (en) | 2009-09-30 | 2011-03-31 | General Electric Company | Nickel-Based Superalloys and Articles |
US20120006452A1 (en) | 2010-07-12 | 2012-01-12 | Rolls-Royce Plc | Method of improving the mechanical properties of a component |
JP2012092378A (ja) * | 2010-10-26 | 2012-05-17 | Toshiba Corp | 蒸気タービンの鍛造用Ni基合金および蒸気タービンの鍛造部品 |
JP5767080B2 (ja) | 2011-06-21 | 2015-08-19 | 三菱日立パワーシステムズ株式会社 | 耐熱合金部材及びその製造方法、耐熱合金部材の補修方法 |
JP5146576B1 (ja) | 2011-08-09 | 2013-02-20 | 新日鐵住金株式会社 | Ni基耐熱合金 |
EP2778241B1 (en) * | 2011-12-15 | 2017-08-30 | National Institute for Materials Science | Heat-resistant nickel-based superalloy |
CA2874304C (en) | 2012-06-07 | 2017-08-01 | Nippon Steel & Sumitomo Metal Corporation | Ni-based alloy |
JP6398277B2 (ja) * | 2014-04-14 | 2018-10-03 | 新日鐵住金株式会社 | Ni基耐熱合金溶接継手の製造方法 |
JP5869624B2 (ja) | 2014-06-18 | 2016-02-24 | 三菱日立パワーシステムズ株式会社 | Ni基合金軟化材及びNi基合金部材の製造方法 |
-
2016
- 2016-11-16 JP JP2018550910A patent/JP6727323B2/ja active Active
- 2016-11-16 WO PCT/JP2016/083931 patent/WO2018092204A1/ja unknown
- 2016-11-16 CN CN201680090850.2A patent/CN109963961B/zh active Active
- 2016-11-16 US US16/348,774 patent/US11021780B2/en active Active
- 2016-11-16 KR KR1020207022510A patent/KR102150341B1/ko active IP Right Grant
- 2016-11-16 CN CN202110414229.XA patent/CN113122789B/zh active Active
- 2016-11-16 KR KR1020197013652A patent/KR102143369B1/ko active IP Right Grant
- 2016-11-16 RU RU2019114230A patent/RU2710701C9/ru active
- 2016-11-16 EP EP16921781.7A patent/EP3543369B8/en active Active
-
2017
- 2017-10-25 TW TW106136628A patent/TWI674934B/zh active
-
2021
- 2021-04-25 US US17/239,616 patent/US11401597B2/en active Active
Patent Citations (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60116740A (ja) * | 1983-11-30 | 1985-06-24 | Daido Steel Co Ltd | 鍛造用金敷 |
JPH02133133A (ja) | 1988-11-09 | 1990-05-22 | Kobe Steel Ltd | 熱間精密型鍛造方法 |
JPH0441641A (ja) * | 1990-06-07 | 1992-02-12 | Kobe Steel Ltd | 金型用ニッケル基超耐熱合金 |
JPH0885838A (ja) * | 1994-07-19 | 1996-04-02 | Hitachi Metals Ltd | Ni基超耐熱合金 |
US20040221927A1 (en) * | 2002-07-19 | 2004-11-11 | Raymond Edward Lee | Isothermal forging of nickel-base superalloys in air |
WO2015008343A1 (ja) * | 2013-07-17 | 2015-01-22 | 三菱日立パワーシステムズ株式会社 | Ni基合金製品とその製造方法、およびNi基合金部材とその製造方法 |
JP2015193045A (ja) | 2014-03-28 | 2015-11-05 | 日立金属株式会社 | 鍛造装置および鍛造製品の製造方法 |
WO2016152982A1 (ja) * | 2015-03-25 | 2016-09-29 | 日立金属株式会社 | Ni基超耐熱合金の製造方法 |
Non-Patent Citations (1)
Title |
---|
See also references of EP3543369A4 |
Cited By (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US11634792B2 (en) | 2017-07-28 | 2023-04-25 | Alloyed Limited | Nickel-based alloy |
CN112513301A (zh) * | 2018-07-31 | 2021-03-16 | 赛峰集团 | 通过粉末成型制造零件的镍基超合金 |
KR20210022599A (ko) * | 2018-10-29 | 2021-03-03 | 리버디 엔지니어링 리미티드 | 고 감마 프라임 니켈계 초합금 및 터빈 엔진 부품의 제조방법 |
KR102228130B1 (ko) | 2018-10-29 | 2021-03-16 | 리버디 엔지니어링 리미티드 | 고 감마 프라임 니켈계 초합금 및 터빈 엔진 부품의 제조방법 |
CN111629852A (zh) * | 2018-11-30 | 2020-09-04 | 三菱日立电力系统株式会社 | Ni基合金软化粉末和该软化粉末的制造方法 |
KR20210024119A (ko) * | 2018-11-30 | 2021-03-04 | 미츠비시 파워 가부시키가이샤 | Ni기 합금 연화 분말 및 해당 연화 분말의 제조 방법 |
KR102443966B1 (ko) * | 2018-11-30 | 2022-09-19 | 미츠비시 파워 가부시키가이샤 | Ni기 합금 연화 분말 및 해당 연화 분말의 제조 방법 |
CN111629852B (zh) * | 2018-11-30 | 2023-03-31 | 三菱重工业株式会社 | Ni基合金软化粉末和该软化粉末的制造方法 |
CN113930697A (zh) * | 2021-09-23 | 2022-01-14 | 鞍钢集团北京研究院有限公司 | 一种750-850℃级变形高温合金的热处理方法 |
CN113930697B (zh) * | 2021-09-23 | 2022-09-27 | 鞍钢集团北京研究院有限公司 | 一种750-850℃级变形高温合金的热处理方法 |
WO2023243146A1 (ja) * | 2022-06-17 | 2023-12-21 | 三菱重工業株式会社 | Ni基合金部材の製造方法 |
CN115233125A (zh) * | 2022-07-25 | 2022-10-25 | 华能国际电力股份有限公司 | 一种厚壁高温合金部件的热处理方法 |
Also Published As
Publication number | Publication date |
---|---|
CN113122789B (zh) | 2022-07-08 |
JP6727323B2 (ja) | 2020-07-22 |
KR20190071743A (ko) | 2019-06-24 |
CN113122789A (zh) | 2021-07-16 |
CN109963961A (zh) | 2019-07-02 |
RU2710701C1 (ru) | 2020-01-09 |
KR20200096684A (ko) | 2020-08-12 |
US11401597B2 (en) | 2022-08-02 |
KR102150341B1 (ko) | 2020-09-01 |
KR102143369B1 (ko) | 2020-08-12 |
TW201819065A (zh) | 2018-06-01 |
US11021780B2 (en) | 2021-06-01 |
EP3543369A1 (en) | 2019-09-25 |
EP3543369B1 (en) | 2022-06-15 |
RU2710701C9 (ru) | 2020-04-06 |
CN109963961B (zh) | 2021-04-09 |
EP3543369A4 (en) | 2020-04-29 |
US20200056275A1 (en) | 2020-02-20 |
EP3543369B8 (en) | 2022-08-03 |
TWI674934B (zh) | 2019-10-21 |
US20210246538A1 (en) | 2021-08-12 |
JPWO2018092204A1 (ja) | 2019-10-10 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US11401597B2 (en) | Method for manufacturing nickel-based alloy high-temperature component | |
KR102078922B1 (ko) | Ni기 합금 부재의 제조 방법 | |
US20200048750A1 (en) | Ni-Based Alloy Product and Method for Producing Same, and Ni-Based Alloy Member and Method for Producing Same | |
JP6252704B2 (ja) | Ni基超耐熱合金の製造方法 | |
JP6150192B2 (ja) | Ni基超耐熱合金の製造方法 | |
JP5652730B1 (ja) | Ni基超耐熱合金及びその製造方法 | |
KR20190073344A (ko) | Ni기 단조 합금재 및 그것을 사용한 터빈 고온 부재 | |
JP6120200B2 (ja) | Ni基超耐熱合金およびそれを用いたタービンディスク | |
AU2014358718A1 (en) | Nickel-based alloy, method and use | |
JP6931112B2 (ja) | ニッケル基合金金型および該金型の補修方法 | |
JP6185347B2 (ja) | Ni基超耐熱合金の分塊用中間素材及びその製造方法、Ni基超耐熱合金の製造方法 | |
RU2694098C1 (ru) | Способ получения полуфабрикатов из высокопрочных никелевых сплавов |
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: 16921781 Country of ref document: EP Kind code of ref document: A1 |
|
ENP | Entry into the national phase |
Ref document number: 2018550910 Country of ref document: JP Kind code of ref document: A |
|
ENP | Entry into the national phase |
Ref document number: 20197013652 Country of ref document: KR Kind code of ref document: A |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
ENP | Entry into the national phase |
Ref document number: 2016921781 Country of ref document: EP Effective date: 20190617 |