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WO2018061540A1 - Procédé de moulage par extrusion à chaud pour alliage à base de ni très résistant à la chaleur et procédé de production d'un matériau d'extrusion d'alliage à base de ni très résistant à la chaleur - Google Patents

Procédé de moulage par extrusion à chaud pour alliage à base de ni très résistant à la chaleur et procédé de production d'un matériau d'extrusion d'alliage à base de ni très résistant à la chaleur Download PDF

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Publication number
WO2018061540A1
WO2018061540A1 PCT/JP2017/030079 JP2017030079W WO2018061540A1 WO 2018061540 A1 WO2018061540 A1 WO 2018061540A1 JP 2017030079 W JP2017030079 W JP 2017030079W WO 2018061540 A1 WO2018061540 A1 WO 2018061540A1
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WIPO (PCT)
Prior art keywords
billet
container
hot
less
base superalloy
Prior art date
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Ceased
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PCT/JP2017/030079
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English (en)
Japanese (ja)
Inventor
レミ 向瀬
韓　剛
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Proterial Ltd
Original Assignee
Hitachi Metals Ltd
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Filing date
Publication date
Application filed by Hitachi Metals Ltd filed Critical Hitachi Metals Ltd
Priority to JP2018541993A priority Critical patent/JP6631896B2/ja
Priority to EP17855498.6A priority patent/EP3520916A4/fr
Priority to CN201780060171.5A priority patent/CN109789458A/zh
Priority to US16/337,775 priority patent/US20200030863A1/en
Publication of WO2018061540A1 publication Critical patent/WO2018061540A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/002—Extruding materials of special alloys so far as the composition of the alloy requires or permits special extruding methods of sequences
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/02—Making uncoated products
    • B21C23/04—Making uncoated products by direct extrusion
    • B21C23/08—Making wire, rods or tubes
    • 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%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • C22C19/03—Alloys based on nickel or cobalt based on nickel
    • C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
    • C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
    • C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • 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
    • B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES, PROFILES OR LIKE SEMI-MANUFACTURED PRODUCTS OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
    • B21C23/00—Extruding metal; Impact extrusion
    • B21C23/32—Lubrication of metal being extruded or of dies, or the like, e.g. physical state of lubricant, location where lubricant is applied

Definitions

  • the present invention relates to a hot extrusion molding method of a precipitation strengthening type Ni-base superalloy and a method of manufacturing a Ni-base superalloy extruded material.
  • FIG. 2 is a schematic diagram illustrating an example of a cross-sectional structure of the extrusion molding apparatus.
  • the billet 1 heated to the hot working temperature is inserted into the container 2.
  • a compressive force is applied to the billet 1 inserted into the container 2 by the stem 4 via the dummy block 3.
  • the billet 1 is extruded from the hole of the die 5 installed in the container 2 and formed into an extruded material 6 having a hole-shaped cross section of the die 5.
  • Direct Extrusion is a press machine that applies a compressive force to the billet from one end of the container into which the billet is inserted, and extrudes the billet from the hole of the die installed on the other end of the container.
  • This is the simplest and most basic extrusion method.
  • lubrication between the billet and the container is important. Therefore, conventionally, when inserting a billet heated to a hot working temperature into a container, a “lubricant-enclosed direct extrusion” is proposed in which a glass lubricant is applied to the peripheral surface of the billet and then inserted (patent document). 1).
  • Patent Document 2 For the purpose of improving the lubricity between the billet and the die, “glass lubrication extrusion” in which a lubricating glass pad is mounted between the billet and the die has been proposed (Patent Document 2).
  • JP-A-6-269844 Japanese Patent Laid-Open No. 7-136710
  • An object of the present invention is to provide a method for hot extrusion of a precipitation-strengthened Ni-base superalloy and a method for producing a Ni-base superalloy extruded material.
  • the present invention heats a billet to a hot working temperature, inserts the billet heated to the hot working temperature into a container, applies a compressive force to the billet inserted into the container, and inserts a hole in a die installed in the container.
  • a hot extrusion molding method in which a billet is extruded and molded from The hot extrusion molding method is based on direct extrusion in which a compressive force is applied to the billet from one end side of the container into which the billet is inserted, and the billet is extruded from a hole of a die installed on the other end side of the container.
  • the above hot extrusion molding method is based on glass lubrication extrusion in which a glass pad for lubrication is mounted between a die and a billet.
  • the billet has a component composition of a precipitation-strengthened Ni-base superalloy having an equilibrium precipitation amount of gamma prime at 700 ° C.
  • the inner diameter D C (mm) of the container is preferably 60 to 180 mm, or the inner diameter D C ′ (mm) of the container is preferably 60 to 180 mm.
  • the hot working temperature is preferably 1150 to 1180 ° C.
  • the present invention also includes a first step of heating the billet of the Ni-base superalloy to a hot working temperature; A billet heated to the above hot working temperature is inserted into a container, a compressive force is applied to the billet from one end side of the container, the billet is extruded from a hole of a die installed on the other end side of the container, and Ni base A second step of obtaining a super heat-resistant alloy extruded material,
  • the billet of the Ni-base superalloy described above has a component composition of a precipitation-strengthened Ni-base superalloy having an equilibrium precipitation amount of gamma prime at 700 ° C.
  • the hot working temperature is preferably 1150 to 1180 ° C.
  • the hot extrusion molding method of the present invention applies a compressive force to the billet from one end side of the container into which the billet is inserted, and extrudes the billet from the hole of the die installed on the other end side of the container. Is due to.
  • the hot extrusion molding method of the present invention is based on “glass lubrication extrusion” in which a lubricating glass pad is mounted between a die and a billet.
  • FIG. 2 is a cross-sectional structure of an extrusion molding apparatus showing an example of an apparatus for performing direct extrusion molding by glass lubrication. In FIG.
  • the billet 1 inserted into the container 2 is pushed out from a hole of a die 5 provided on the other end side of the container 2 with a compressive force applied from one end side of the container 2.
  • a lubricating glass pad 7 is mounted between the die 5 and the billet 1 when the billet 1 is inserted into the container 2.
  • the die 5 in FIG. 2 includes a die holder (not shown). Strictly speaking, when the cross-sectional structure of the extrusion molding apparatus is in the state shown in FIG.
  • the lubricating glass pad 7 has already been provided. It is melted.
  • the molten lubricating glass pad 7 is sufficiently infiltrated between the billet 1 and the container 2.
  • the molten glass pad 7 for lubrication is firmly adhered to the surface of the extruded material 6 extruded from the hole of the die 5.
  • generally known materials can be used as the lubricating glass pad 7.
  • the lubricating glass pad 7 is formed by solidifying various glass materials with a binder.
  • the shape has a “disk shape” that fits between the die 5 and the billet 1 (hence, also called a glass disk).
  • a “hole” corresponding to the position and diameter of the hole of the die 5 is opened at the center of the disk shape.
  • a plurality of such glass pads for lubrication 7 can be used in piles depending on the case. Since the billet is made of a precipitation-strengthened Ni-base superalloy, for the present invention in which the extrusion is performed at a high temperature, such a lubricating glass pad can be quickly melted and the molten lubricating pad It is effective in increasing the flow rate of the glass pad (ie, improving the lubricity between the billet and the container).
  • the billet may be an ingot obtained by casting a molten metal, or a material obtained by subjecting the ingot to a lump processing, machining, heat treatment, or the like, if necessary.
  • the sintering raw material obtained by the powder metallurgy method can also be used.
  • the billet has a component composition of a precipitation-strengthened Ni-base superalloy having an equilibrium precipitation amount of gamma prime at 700 ° C. of 40 mol% or more. is there.
  • Precipitation-strengthened Ni-base superalloys have a microstructure that consists exclusively of a gamma phase in which alloy components are dissolved in a Ni base and precipitation strengthening of intermetallic compounds typically represented by [Ni 3 (TiAl)]. It is composed of a gamma prime phase that is a phase.
  • the hot working of such a Ni-base superalloy is generally performed from the solid solution temperature (gamma prime solvus temperature) at which the above-mentioned gamma prime phase is in solution to the solidus temperature of this Ni-base superalloy.
  • the temperature range for example, 900 ° C. to 1200 ° C.
  • this hot working is also hot extrusion molding with a high working ratio, for example, the extruded material after molding is divided, and thus hot working of precipitation-strengthened Ni-base superalloy is difficult. there were.
  • the gamma prime phase in a Ni-base superalloy is reduced as the temperature of the alloy itself (that is, hot working temperature) increases. It is possible that the hot workability of the heat resistant alloy can be improved somewhat.
  • the above-mentioned alloy having many gamma prime phases specifically, a Ni-based superalloy having a component composition in which the equilibrium precipitation amount of gamma prime at 700 ° C. is 40 mol% or more. Is a Ni-based superalloy that is particularly difficult to hot work because the gamma prime phase does not disappear even when it is heated to a temperature near the melting point.
  • the hot extrusion molding method of the present invention such a Ni-base superalloy that is difficult to hot work is used as a billet, and this is “extruded”.
  • the hot extrusion molding method of the present invention enables extrusion of a Ni-base superalloy having a large amount of gamma prime and is difficult to hot-work. Is expensive.
  • the billet extruded in the present invention has an equilibrium precipitation amount of gamma prime at 700 ° C. of preferably 50 mol% or more. More preferably, it is 60 mol% or more. It is not particularly necessary to set an upper limit for this value. However, about 75 mol% is realistic.
  • the equilibrium precipitation amount of gamma prime of the precipitation strengthened Ni-base superalloy is the amount of precipitation of gamma prime that is stable in a thermodynamic equilibrium state.
  • the value which expressed the equilibrium precipitation amount of this gamma prime in "mol%” is a value which can be decided by the component composition which precipitation strengthening type Ni-base superalloy has.
  • the value of “mol%” of the equilibrium precipitation amount can be obtained by analysis by thermodynamic equilibrium calculation. In the case of analysis by thermodynamic equilibrium calculation, it can be obtained accurately and easily by using various thermodynamic equilibrium calculation software.
  • Ni-base superalloys include Alloy 713C and UDIMET 720 (UDIMET is a registered trademark of Special Metals Corporation).
  • C has an effect of increasing the strength of the grain boundary of the Ni-base superalloy. Moreover, there exists an effect which improves the castability of Ni-base superalloy.
  • the C content is preferably 0.001 to 0.25%. More preferably, it is 0.10% or less, More preferably, it is 0.05% or less. Particularly preferably, the content is 0.02% or less. Further, it is more preferably 0.003% or more, further preferably 0.005% or more. Particularly preferably, it is 0.008% or more.
  • Cr is an element that improves oxidation resistance and corrosion resistance. However, when Cr is excessively contained, an embrittlement phase such as a ⁇ phase is formed, and the strength and hot workability are lowered. Therefore, the Cr content is preferably 8.0 to 22.0%. More preferably, it is 9.0% or more, More preferably, it is 9.5% or more. Particularly preferably, it is 10.0% or more. Further, it is more preferably 18.0% or less, and further preferably 16.0% or less. Particularly preferably, it is 14.0% or less.
  • Mo contributes to the solid solution strengthening of the matrix and has the effect of improving the high temperature strength.
  • Mo content is preferably 2.0 to 7.0%. More preferably, it is 2.5% or more, More preferably, it is 3.0% or more. Particularly preferably, it is 3.5% or more. Further, it is more preferably 6.0% or less, and still more preferably 5.5% or less. Particularly preferably, it is 5.0% or less.
  • Al is an element that improves the high-temperature strength by forming gamma prime.
  • the content of Al is preferably set to 2.0 to 8.0%. More preferably, it is 2.5% or more, More preferably, it is 3.5% or more. Particularly preferably, it is 4.5% or more. Further, it is more preferably 7.5% or less, and still more preferably 7.0% or less. Particularly preferably, it is 6.5% or less.
  • Ti like Al, is an element that forms a gamma prime and enhances the high temperature strength by solid solution strengthening of the gamma prime.
  • the Ti content is preferably 0.4 to 7.0%. More preferably, it is 0.45% or more, More preferably, it is 0.5% or more. Further, it is more preferably 5.0% or less, and further preferably 3.0% or less. Especially preferably, it is 1.0% or less.
  • Ni but naturally unavoidable impurities may be included. And in this basic component composition, the following element seed
  • Co is one of the selective elements that improves the stability of the structure and makes it possible to maintain hot workability even when containing a large amount of Ti as a strengthening element.
  • the Co content is preferably 28.0% or less. More preferably, it is 18.0% or less, More preferably, it is 16.0% or less. Particularly preferably, it is 13.0% or less.
  • the minimum of Co shall be 0%.
  • Co can be made into less than 1.0%.
  • content of Co when acquiring said effect by content of Co, it is preferable that content of Co shall be 1.0% or more. More preferably, it is 3.0% or more, More preferably, it is 8.0% or more. Particularly preferably, it is 10.0% or more.
  • W is one of the selective elements that contribute to the solid solution strengthening of the matrix.
  • W is one of the selective elements that contribute to the solid solution strengthening of the matrix.
  • the W content is preferably 6.0% or less. More preferably, it is 5.5% or less, More preferably, it is 5.0% or less. Particularly preferably, it is 4.5% or less.
  • W is good also as an additive-free level (inevitable impurity level of a raw material)
  • the minimum of W shall be 0%.
  • W can be made into less than 1.0%, and also can be made into less than 0.8%.
  • content of W when acquiring said effect by content of W, it is preferable that content of W shall be 1.0% or more. And by containing W and Mo in a composite, it is effective for exhibiting the above-mentioned solid solution strengthening.
  • the content of W in a case where it is combined with Mo is preferably 0.8% or more.
  • Nb like Al and Ti, is a selective element that forms a gamma prime and enhances the high-temperature strength by solid-solution strengthening the gamma prime.
  • an excessive content of Nb forms a harmful ⁇ (delta) phase and degrades hot workability. Therefore, even when Nb is contained, the Nb content is preferably 4.0% or less. More preferably, it is 3.5% or less, More preferably, it is 3.0% or less. Particularly preferably, it is 2.5% or less.
  • the minimum of Nb shall be 0%. And Nb can be made into less than 0.5%.
  • content of Nb when acquiring said effect by content of Nb, it is preferable that content of Nb shall be 0.5% or more. More preferably, it is 1.0% or more, More preferably, it is 1.5% or more. Particularly preferably, it is 2.0% or more.
  • Ta like Al and Ti, is one of the selective elements that form gamma prime and enhance the high temperature strength by solid solution strengthening of gamma prime.
  • excessive addition of Ta causes the gamma prime phase to become unstable at a high temperature and cause coarsening at a high temperature, and forms a harmful ⁇ (eta) phase, thereby degrading hot workability. Therefore, even if it contains Ta, the content of Ta is preferably 3.0% or less. More preferably, it is 2.5% or less, More preferably, it is 2.0% or less. Particularly preferably, it is 1.5% or less.
  • the minimum of Ta is made into 0%. And Ta can be made into less than 0.3%.
  • content of Ta shall be 0.3% or more. More preferably, it is 0.5% or more, More preferably, it is 0.7% or more. Particularly preferably, it is 1.0% or more.
  • Fe is one of the selective elements that can be contained as an alternative to expensive Ni and Co and is effective in reducing alloy costs.
  • an embrittlement phase such as a ⁇ phase is formed, and the strength and hot workability are lowered. Therefore, even if it contains Fe, the content of Fe is preferably 10.0% or less. More preferably, it is 8.0% or less, More preferably, it is 6.0% or less. Particularly preferably, it is 3.0% or less.
  • the minimum of Fe shall be 0%. And Fe can be made into less than 0.1%.
  • content of Fe substituted with content of Ni or Co shall be 0.1% or more, for example. More preferably, it is 0.4% or more, More preferably, it is 0.6% or more. Especially preferably, it is 0.8% or more.
  • V is one of the selective elements useful for strengthening the solid solution of the matrix and strengthening the grain boundaries by forming carbides.
  • the V content is preferably 1.2% or less. More preferably, it is 1.0% or less, More preferably, it is 0.8% or less. Particularly preferably, it is 0.7% or less.
  • V an additive-free level (inevitable impurity level of a raw material)
  • the minimum of V is made into 0%.
  • V can be made into less than 0.1%.
  • content of V shall be 0.1% or more. More preferably, it is 0.2% or more, More preferably, it is 0.3% or more. Particularly preferably, it is 0.5% or more.
  • Hf is one of the selective elements useful for improving the oxidation resistance of alloys and strengthening grain boundaries by forming carbides.
  • excessive addition of Hf leads to the production of oxides and high temperature unstable phases in the production process, which adversely affects manufacturability and high temperature dynamic performance. Therefore, even if it contains Hf, the content of Hf is preferably 1.0% or less. More preferably, it is 0.7% or less, More preferably, it is 0.5% or less. Particularly preferably, it is 0.3% or less.
  • Hf is good also as an additive-free level (inevitable impurity level of a raw material)
  • the minimum of Hf shall be 0%.
  • Hf can be less than 0.02%.
  • content of Hf when acquiring said effect by content of Hf, it is preferable that content of Hf shall be 0.02% or more. More preferably, it is 0.05% or more, More preferably, it is 0.1% or more. Particularly preferably, it is 0.15% or more.
  • B is one of the selective elements that can improve the grain boundary strength and improve the creep strength and ductility.
  • B content is preferably 0.300% or less. More preferably, it is 0.100% or less, More preferably, it is 0.050% or less. Particularly preferably, it is 0.020% or less.
  • B is good also as an additive-free level (inevitable impurity level of a raw material)
  • the minimum of B shall be 0%.
  • B can be made into less than 0.001%.
  • content of B when acquiring said effect by content of B, it is preferable that content of B shall be 0.001% or more. More preferably, it is 0.003% or more, More preferably, it is 0.005% or more. Particularly preferably, it is 0.007% or more.
  • Zr is one of the selective elements that has the effect of improving the grain boundary strength.
  • the Zr content is preferably set to 0.30% or less. More preferably, it is 0.25% or less, More preferably, it is 0.20% or less. Particularly preferably, it is 0.15% or less.
  • Zr is an additive-free level (inevitable impurity level of a raw material)
  • the minimum of Zr is made into 0%.
  • Zr can be made into less than 0.001%.
  • content of Zr when acquiring said effect by content of Zr, it is preferable that content of Zr shall be 0.001% or more. More preferably, it is 0.005% or more, More preferably, it is 0.01% or more. Particularly preferably, it is 0.03% or more.
  • the precipitation-strengthened Ni-base superalloy has poor “wetability” with respect to the molten glass pad as compared with general stainless steel and the like. Therefore, in the case of hot extrusion molding in which the billet is a precipitation-strengthened Ni-base superalloy, in order to sufficiently infiltrate the molten glass pad between the billet and the container, conditions for the extrusion molding, etc. Review is important. And in order to fully infiltrate the molten glass pad and to fully exert the effect of the infiltration of the molten glass pad, the billet and the container directly related to the ease of infiltration of the glass pad The present inventors have found that the optimization of the “clearance” between the two is effective.
  • FIG. 1 shows the difference between the outer diameter D B (mm) of the billet and the inner diameter D C (mm) of the billet in the hot extrusion molding of the billet made of the precipitation-strengthened Ni-base superalloy.
  • FIG. At this time, the part where the thickness of the lubricating film is obtained is the part where the thickness of the lubricating film is minimum in this billet.
  • the billet 1 is an elasto-plastic body
  • the container 2 and the dummy block 3 are rigid bodies
  • the lubricating glass pad 7 is a rigid plastic body. It was obtained by calculation by analysis. At this time, since the operation in the extrusion direction is directly set in the dummy block 3, the stem 4 is not expressed in the analysis model. In the above calculation, the finite element analysis software “FORGE Nxt ver1.0” manufactured by TRANSVALOR was used, and the calculation was performed on the assumption that the lubricating glass pad 7 was completely melted by contact with the billet 1 in advance. .
  • the relationship between the outer diameter D B (mm) of the billet when inserted into the container and the inner diameter D C (mm) of the container is “(D C ⁇ D B ): 2 to 8 mm”. Adjust as follows. In the range of 2 to 8 mm, for example, this can be further adjusted in the range of 2 to 4 mm, or can be adjusted in the range of 4 to 8 mm.
  • the value of (D C ⁇ D B ) can be handled as an integer. For example, it can be a value obtained by rounding off decimals.
  • the container of an extrusion molding apparatus is cylindrical, for example, is cylindrical. Accordingly, the billet has a columnar shape, for example, a columnar shape. In such a case, the value of (D C ⁇ D B ) can be adjusted at the parallel portion of the interval formed by the inner peripheral surface of the container and the outer peripheral surface of the billet.
  • the adjustment of the value of (D C ⁇ D B ) can be performed by adjusting the outer diameter of the billet, for example. And the adjustment of the outer diameter of this billet can be adjusted, for example, by the outer diameter of the billet before insertion into the container (that is, before heating to the hot working temperature). Adjustment of the outer diameter of the billet is based on the billet component composition and heating conditions by counting the thermal expansion amount of the billet when heated to the hot working temperature and the thermal expansion of the container when heated to the preheating temperature. Accordingly, it can be performed by machining such as turning.
  • the relationship between the outer diameter D B ′ (mm) of the billet before heating to the hot working temperature and the inner diameter D C ′ (mm) of the container before heating to the preheating temperature is (D C '-D B '): It can be adjusted to be 3 to 9 mm. In the range of 3 to 9 mm, for example, this can be further adjusted in the range of 3 to 5 mm, or can be adjusted in the range of 5 to 9 mm.
  • the value of (D C ′ ⁇ D B ′) can be adjusted at a parallel portion of the interval formed by the inner peripheral surface of the container and the outer peripheral surface of the billet.
  • the inner diameter D C (mm) of the container is preferably 180 mm or less. And it is more preferable to make this small, for example, 160 mm or less, 140 mm or less, 120 mm or less, and 100 mm or less.
  • the inner diameter D C (mm) of the container is preferably 60 mm or more. And it is more preferable to enlarge this to 70 mm or more and 80 mm or more, for example.
  • the inner diameter D C of the container instead of to a value above the inner diameter D C 'of before the container is heated to a preheat temperature is preferably not greater than 180 mm. And it is more preferable to make this small, for example, 160 mm or less, 140 mm or less, 120 mm or less, and 100 mm or less. Further, it is preferably not less than 60mm inner diameter D C 'of the container. And it is more preferable to enlarge this to 70 mm or more and 80 mm or more, for example.
  • the temperature is preferably “1150 to 1180 ° C.”. More preferably, it is 1170 degrees C or less.
  • This extrusion molding at a high temperature contributes to maintaining the hot workability of the billet made of a precipitation-strengthened Ni-base superalloy.
  • the extrusion molding at this high temperature promotes rapid melting of the above-described lubricating glass pad, and increases the flow rate of the molten lubricating glass pad, thereby improving the lubricity between the billet and the container. It is effective to improve.
  • a glass lubricant may be applied to the peripheral surface of the billet when the billet heated to the hot working temperature is inserted into the container.
  • the diameter of the cross section of the produced extruded material is, for example, 10 to 130 mm. And the diameter of the cross section of this extrusion material may be 100 mm or less, may be 60 mm or less, and may be 30 mm or less.
  • the extrusion ratio (the cross-sectional area of the billet / the cross-sectional area of the extruded material) at the time of extrusion molding may be 70 or less, for example. And this extrusion ratio may be 40 or less, or 30 or less. Furthermore, it may be 20 or less, or 10 or less. Further, it may be 2 or more, 4 or more, or 6 or more.
  • the extruded material thus obtained has, for example, a bar shape or a wire shape. Further, these rods and wires have, for example, a solid state. Then, by using such an extruded material as a starting material, further hot working and cold working are performed on this, for example, to produce a thin wire having a cross-sectional diameter of 1 to 6 mm, further 4 mm or less, 3 mm or less, etc. It is also possible to do.
  • the billet may be in a form in which a molded body (that is, a precipitation strengthened Ni-base superalloy) is contained in a container.
  • the precipitation strengthening type Ni base is adjusted by adjusting to the value of (D C -D B ) described above or by adjusting to the value of (D C '-D B ') described above. Hot extrusion molding of super heat-resistant alloy is possible.
  • An ingot was obtained by casting a molten metal having a predetermined composition prepared by vacuum melting. The ingot was then machined to produce cylindrical billets A to E having a predetermined diameter and corresponding to Alloy 713C having a length of 105 mm.
  • the diameters (D B ′) of billets A to E were billet A: 83 mm, billet B: 82 mm, billet C: 80 mm, billet D: 76 mm, billet E: 72 mm.
  • Table 1 shows the component compositions of billets A to E (ie, ingots). Note that Co, W, Ta, V, and Hf are impurity elements, so Co ⁇ 28.0%, W ⁇ 6.0%, Ta ⁇ 3.0%, V ⁇ 1.2%, and Hf ⁇ 1.
  • the amount of gamma-prime equilibrium precipitation of billets A to E at 700 ° C. was determined using thermodynamic equilibrium calculation software “JMatPro (Version 8.0.1, manufactured by Sente Software Ltd.)”. As a result of inputting the contents of each element listed in Table 1 into this thermodynamic equilibrium calculation software, the above-described equilibrium precipitation amount of billets A to E was “70 mol%”. The gamma prime solvus temperature of billets A to E was “1180 ° C.”.
  • Billets A to E were heated to the hot working temperature (first step). Then, the heated billets A to E are inserted into a cylindrical container (manufactured by JIS-SKD61, inner diameter (D C ′) before preheating: 85 mm) of the extrusion molding apparatus shown in FIG. Hot extrusion was performed to produce a solid extruded material (second step). In the hot extrusion molding described above, the billets A to E are heated to a hot working temperature of 1150 ° C. before the billets A to E are inserted into the container, and the container is also heated to a preheating temperature of 500 ° C., respectively. .
  • the distance between the inner peripheral surface of the billet and the outer peripheral surfaces of the billets A to E when the billets A to E are inserted into the container is “1 mm” for the billet A and “ It was “4 mm” for billet C, “8 mm” for billet D, and “12 mm” for billet E.
  • FIG. 3 shows the appearance of an extruded material obtained from billet D (clearance: 8 mm) by the above hot extrusion molding.
  • FIG. 4 shows the appearance of the extruded material obtained from billet E (clearance: 12 mm). 3 and 4, the right side is the tip of the extruded material (the die was located on the left side).
  • the deposit observed on the surface of the extruded material is a solidified molten glass pad for lubrication.
  • a lubricating glass pad adhered from the front end to the rear end of the extruded material. The surface of the extruded material was free from cracks and no noticeable wrinkles were observed, indicating a good surface condition.

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  • 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)
  • Extrusion Of Metal (AREA)

Abstract

L'invention concerne : un procédé de moulage par extrusion à chaud pour un alliage à base de Ni très résistant à la chaleur de type renforcé par précipitation; et un procédé de production d'un matériau d'extrusion d'alliage à base de Ni très résistant à la chaleur. Le procédé de moulage par extrusion à chaud est destiné à un alliage à base de Ni très résistant à la chaleur. Dans ce procédé : une billette prèsente une composition de composants pour un alliage à base de Ni très résistant à la chaleur de type renforcé par précipitation dont la quantité de précipitation d'équilibre de phase gamma prime est de 40% en moles ou supérieure, à 700°C; un tampon en verre de lubrification est placé entre une matrice et la billette; et un réglage est effectué de sorte que la relation entre le diamètre externe DB (mm) de la billette au moment de son insertion dans un récipient et le diamètre interne DC (mm) du récipient satisfasse la condition (DC-DB): 2-8 mm, ou un réglage est effectué de sorte que la relation entre le diamètre externe DB' (mm) de la billette avant d'être chauffée à une température de traitement à chaud et le diamètre interne DC' (mm) du récipient avant d'être chauffé à une température de préchauffage satisfasse la condition (DC'-DB'): 3-9 mm Le procédé de production d'un matériau d'extrusion d'alliage à base de Ni très résistant à la chaleur selon l'invention est réalisé par la mise en oeuvre dudit procédé de moulage par extrusion à chaud.
PCT/JP2017/030079 2016-09-29 2017-08-23 Procédé de moulage par extrusion à chaud pour alliage à base de ni très résistant à la chaleur et procédé de production d'un matériau d'extrusion d'alliage à base de ni très résistant à la chaleur Ceased WO2018061540A1 (fr)

Priority Applications (4)

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JP2018541993A JP6631896B2 (ja) 2016-09-29 2017-08-23 Ｎｉ基超耐熱合金の熱間押出成形方法およびＮｉ基超耐熱合金押出材の製造方法
EP17855498.6A EP3520916A4 (fr) 2016-09-29 2017-08-23 Procédé de moulage par extrusion à chaud pour alliage à base de ni très résistant à la chaleur et procédé de production d'un matériau d'extrusion d'alliage à base de ni très résistant à la chaleur
CN201780060171.5A CN109789458A (zh) 2016-09-29 2017-08-23 Ni基超耐热合金的热挤出成型方法及Ni基超耐热合金挤出材的制造方法
US16/337,775 US20200030863A1 (en) 2016-09-29 2017-08-23 HOT EXTRUSION-MOLDING METHOD FOR Ni-BASED SUPER HEAT-RESISTANT ALLOY AND PRODUCTION METHOD FOR Ni-BASED SUPER HEAT-RESISTANT ALLOY EXTRUSION MATERIAL

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JP2016190801 2016-09-29
JP2016-190801 2016-09-29

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CN109789458A (zh) 2019-05-21
US20200030863A1 (en) 2020-01-30
JP6631896B2 (ja) 2020-01-15
EP3520916A1 (fr) 2019-08-07
JPWO2018061540A1 (ja) 2019-04-11

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