CN109789458A - The hot extrusion forming method and Ni base superalloy of Ni base superalloy squeeze out the manufacturing method of material - Google Patents
The hot extrusion forming method and Ni base superalloy of Ni base superalloy squeeze out the manufacturing method of material Download PDFInfo
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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 OR PROFILES, 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
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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 OR PROFILES, 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, bars, tubes
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/055—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 20% but less than 30%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—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%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/057—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being less 10%
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- 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
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- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
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- 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
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Abstract
The present invention provides the hot extrusion forming method of the Ni base superalloy of precipitation strength type and the manufacturing method of Ni base superalloy extrusion material.A kind of hot extrusion forming method of Ni base superalloy, wherein, blank have the Ni base superalloy for the precipitation strength type that the Equilibrium Precipitation amount of the γ ' phase at 700 DEG C is 40 moles of % or more at being grouped as, the outer diameter D of blank when installing lubrication glass isolator between mold and blank, and ingot-containing tube will be inserted intoB(mm) with the internal diameter D of ingot-containing tubeC(mm) relationship is adjusted to (DC‑DB): 2~8mm or the outer diameter D that will warm up the blank before hot processing temperatureB' (mm) and the internal diameter D of ingot-containing tube that is heated to before preheating temperatureC' relationship of (mm) is adjusted to (DC’‑DB'): 3~9mm.In addition, the manufacturing method that Ni base superalloy squeezes out material is carried out using above-mentioned hot extrusion forming method.
Description
Technical field
The present invention relates to the hot extrusion forming method of the Ni base superalloy of precipitation strength type and Ni base superalloy
Squeeze out the manufacturing method of material.
Background technique
Extrusion molding is that following hot extrusion forms: by blank heating to hot processing temperature, will warm up the hot-working temperature
The blank of degree is inserted into ingot-containing tube, applies compressing force to the blank for being inserted into the ingot-containing tube, from the mold for being set to ingot-containing tube
Blank is squeezed out, is formed by hole.Fig. 2 is the schematic diagram for showing an example of cross section structure of extrusion molding apparatus.In Fig. 2, firstly, will
The blank 1 for being heated to hot processing temperature is inserted into ingot-containing tube 2.Then, to the blank 1 for being inserted into the ingot-containing tube 2, across hot pressing pad
Piece 3 assigns compressing force by bar 4.Then, blank 1 is squeezed out from the hole for the mold 5 for being set to ingot-containing tube 2 as a result, is shaped to have
The extrusion material 6 in the hole shape section of mold 5.
Among various extruding forming methods, from the one end of the ingot-containing tube inserted with blank to blank apply compressing force and from
Be set to the hole of the mold of the another side of ingot-containing tube by be for " directly extruding " that blank squeezes out press structure it is simple
Most basic extruding forming method.In the case where directly extruding, it is important that the lubrication between blank and ingot-containing tube.Therefore,
In the past, proposing will warm up when the blank of hot processing temperature is inserted into ingot-containing tube after the circumferential surface coated glass lubricant of blank
" lubricant sealing directly extrudes " (patent document 1) of insertion.In addition, for the mesh for improving the lubricity between blank and mold
, propose " glass lubrication extrusion " (patent document 2) that lubrication glass isolator is installed between blank and mold.
Existing technical literature
Patent document
Patent document 1: Japanese Unexamined Patent Publication 6-269844 bulletin
Patent document 2: Japanese Unexamined Patent Publication 7-136710 bulletin
Summary of the invention
Problems to be solved by the invention
In recent years, the requirement for coping with repairing, the three-dimensional appearance of various heat-resistant parts, needs the gold of " Ni base superalloy "
Belong to line.Moreover, in Ni base superalloy, the especially having excellent high-temperature strength of the Ni base superalloy of " precipitation strength type ",
Hot-workability with this particularly at the Ni base superalloy being grouped as is poor, and the metal wire based on extrusion molding is very
Difficult.
The object of the present invention is to provide the hot extrusion forming methods and Ni base of the Ni base superalloy of precipitation strength type
The manufacturing method of superalloy extrusion material.
The solution to the problem
The present invention is a kind of hot extrusion forming method of Ni base superalloy, wherein by blank heating to hot-working temperature
Degree, the blank that will warm up the hot processing temperature are inserted into ingot-containing tube, apply compressing force to the blank for being inserted into the ingot-containing tube, from
And squeezed out from the hole for the mold for being set to ingot-containing tube by blank, molding,
Above-mentioned hot extrusion forming method is using the following method directly extruded: from one of the ingot-containing tube inserted with blank
End side applies compressing force to blank, squeezes out blank from the hole of the mold for the another side for being set to ingot-containing tube,
Above-mentioned hot extrusion forming method utilizes the glass lubrication for being equipped with lubrication glass isolator between mold and blank to squeeze
Out,
Above-mentioned blank has the precipitation strength type that the Equilibrium Precipitation amount of the γ ' phase at 700 DEG C is 40 moles of % or more
Ni base superalloy at being grouped as,
The outer diameter D of blank when will be inserted into ingot-containing tubeB(mm) with the internal diameter D of ingot-containing tubeC(mm) relationship is adjusted to (DC-
DB): 2~8mm or the outer diameter D that will warm up the blank before hot processing temperatureB' (mm) and the ingot-containing tube that is heated to before preheating temperature
Internal diameter DC' relationship of (mm) is adjusted to (DC’-DB'): 3~9mm.
At this point, it is preferred that the internal diameter D of above-mentioned ingot-containing tubeCIt (mm) is the 60~180mm or internal diameter D of above-mentioned ingot-containing tubeC' (mm) be
60~180mm.In addition, above-mentioned hot processing temperature is preferably 1150~1180 DEG C.
In addition, the present invention is the manufacturing method that a kind of Ni base superalloy squeezes out material, include
1st process, by the blank heating of Ni base superalloy to hot processing temperature；With
2nd process, the blank that will warm up above-mentioned hot processing temperature are inserted into ingot-containing tube, from the one end pair of the ingot-containing tube
Blank applies compressing force, squeezes out blank from the hole of the mold for the another side for being set to the ingot-containing tube, it is super heat-resisting to obtain Ni base
The extrusion material of alloy,
It is 40 moles of % or more that the blank of above-mentioned Ni base superalloy, which has the Equilibrium Precipitation amount of the γ ' phase at 700 DEG C,
Precipitation strength type Ni base superalloy at being grouped as,
Blank when installing lubrication glass isolator between above-mentioned mold and blank, and above-mentioned ingot-containing tube will be inserted into
Outer diameter DB(mm) with the internal diameter D of ingot-containing tubeC(mm) relationship is adjusted to (DC-DB): 2~8mm will warm up above-mentioned hot-working
The outer diameter D of blank before temperatureB' (mm) and the internal diameter D of ingot-containing tube that is heated to before preheating temperatureC' relationship of (mm) is adjusted to
(DC’-DB'): thus 3~9mm carries out above-mentioned 2nd process.
At this point, it is preferred that by the internal diameter D of above-mentioned ingot-containing tubeC(mm) it is adjusted to 60~180mm or by the internal diameter of above-mentioned ingot-containing tube
DC' (mm) be adjusted to 60~180mm.Additionally, it is preferred that above-mentioned hot processing temperature is set as 1150~1180 DEG C.
The effect of invention
According to the present invention, it can be achieved that the hot extrusion of the Ni base superalloy of precipitation strength type forms.
Detailed description of the invention
Fig. 1 be show by simulate it is finding out, utilize blank when being inserted into ingot-containing tube in the directly extruding of glass lubrication
Outer diameter DB(mm) with the internal diameter D of ingot-containing tubeC(mm) difference " DC-DB(mm) " between the blank and ingot-containing tube and in extrusion molding
It is formed by the figure of an example of the result of the relationship of " thickness (mm) of lubricating film ".
Fig. 2 is cutting for the extrusion molding apparatus of an example for showing the device for carrying out the direct extrusion molding using glass lubrication
The schematic diagram of face structure.
Fig. 3 is the photograph instead of attached drawing for showing an example of the surface state of the extrusion material of method production of example through the invention
Piece.
Fig. 4 is the photograph instead of attached drawing for showing an example of surface state of the extrusion material made by comparing the method for example
Piece.
Specific embodiment
(1) hot extrusion forming method of the invention using following " directly extruding " method: from inserted with blank
The one end of ingot-containing tube applies compressing force to blank, squeezes out blank from the hole of the mold for the another side for being set to ingot-containing tube.
Moreover, hot extrusion forming method of the invention between mold and blank using lubrication glass isolator is equipped with, " glass moistens
The method of sliding extrusion ".
Fig. 2 is cutting for the extrusion molding apparatus of an example for showing the device for carrying out the direct extrusion molding using glass lubrication
Face structure.In Fig. 2, the blank 1 for being inserted into ingot-containing tube 2 is applied compressing force from the one end of ingot-containing tube 2, from being set to ingot-containing tube
The hole of the mold 5 of 2 another side squeezes out.Moreover, blank 1 is inserted into ingot-containing tube 2 in the case where glass lubrication squeezes out
When, lubrication glass isolator 7 is installed between mold 5 and blank 1.At this point, being provided with mold in ingot-containing tube 2 by mold holder
In the case where 5, the mold 5 of Fig. 2 includes mold holder (not shown).Moreover, strictly, the section of extrusion molding apparatus is tied
When structure is in the state of Fig. 2 (that is, when blank 1 is squeezed out to a certain degree from the hole of mold 5), above-mentioned lubrication with glass isolator 7
Melting.Moreover, in the case where the present invention, the lubrication of the melting also can sufficiently be infiltrated with glass isolator 7 to blank 1 and ingot-containing tube 2 it
Between.Moreover, the lubrication glass isolator 7 for being attached with above-mentioned melting can be solidified on the surface of the extrusion material 6 squeezed out from the hole of mold 5.
In the present invention, commonly known glass isolator is can be used in above-mentioned lubrication glass isolator 7.Such as lubrication glass isolator 7
For with binder by various glass material curing moldings winner.In addition, for example, having and being substantially fitted to for its shape
" disk shape " (therefore, also referred to as glass plate) between mold 5 and blank 1.Moreover, for example, the disk shape central portion
It is provided with " hole " corresponding with the position in the hole of mold 5, diameter.It according to circumstances, can also be by such lubrication glass isolator more than 7
Overlapping is opened to use.Since blank is formed by the Ni base superalloy of precipitation strength type, for carrying out it by high temperature
For the present invention of extrusion molding, such lubrication melts it rapidly and is being improved the lubrication glass of melting with glass isolator
Flowing velocity (that is, improving the lubricity between blank and ingot-containing tube) aspect of pad is effective.
It should be noted that blank can be used ingot casting obtained from casting melt, implement as needed to the ingot casting
Cogging processing, machining, heat treatment etc. and winner.In addition, also can be used and obtained by powder metallurgic method as above-mentioned ingot casting
The sintering raw material arrived.
(2) in hot extrusion forming method of the invention, Equilibrium Precipitation amount of the above-mentioned blank with the γ ' phase at 700 DEG C is
The Ni base superalloy of the precipitation strength type of 40 moles of % or more at being grouped as.
For the Ni base superalloy of precipitation strength type, tissue is mainly solid-solution in made of Ni substrate as alloying component
γ phase and as by [Ni3(TiAl)] γ ' of the precipitation strength phase of the intermetallic compound typically indicated is mutually constituted.In this way
Ni base superalloy the solid solubility temperature (γ ' phase solid solubility temperature) that is usually mutually dissolved in above-mentioned γ ' of hot-working to the Ni base
Temperature region (such as 900 DEG C~1200 DEG C) between the solidus temperature of superalloy carries out.When the hot-working, if above-mentioned
γ ' phase is more, then deformation drag is got higher, so that the hot-workability as Ni base superalloy entirety reduces.Moreover, if the heat adds
Work is also to process than high hot extrusion molding, then such as being broken extrusion material after molding, thus the Ni base of precipitation strength type
The hot-working of superalloy is difficult.
Generally, due to the γ ' in Ni base superalloy mutually with the temperature (that is, hot processing temperature) of its alloy itself
Rise and reduce, therefore by improving hot processing temperature, it is possible to how much can improve the hot-workability of Ni base superalloy.
But even if improving hot processing temperature, for more than above-mentioned γ ' phase alloy, specifically with the flat of the γ ' phase at 700 DEG C
The amount of precipitation that weighs be 40 moles of % or more at the Ni base superalloy being grouped as, even if it is heated near fusing point
Temperature, γ ' will not mutually disappear, therefore to be particularly difficult to carry out hot worked Ni base superalloy.Moreover, of the invention
In hot extrusion forming method, hot worked Ni base superalloy can be difficult to as blank using this, it " be extruded into
Type ".
Hot extrusion forming method of the invention can be realized γ ' phase is more, be difficult to hot worked Ni base superalloy squeeze
It forms out, the Ni base superalloy more more than γ ' phase, application value is higher.From this viewpoint, it is extruded into the present invention
The Equilibrium Precipitation amount of γ ' phase at above-mentioned 700 DEG C of the blank of type is preferably 50 moles of % or more.More preferably 60 moles of % with
On.It should be noted that especially not needing to be arranged the upper limit of the value.But 75 moles of % or so are real.
The Equilibrium Precipitation amount of the γ ' phase of precipitation strength type Ni base superalloy refers to stable under thermodynamic equilibrium state
The amount of precipitation of γ ' phase.Moreover, with " mole % " indicate the Equilibrium Precipitation amount of the γ ' phase value be can be by precipitation strength type
Ni base superalloy have at the value for being grouped as decision.The value of " mole % " of the Equilibrium Precipitation amount can be by based on heat
The parsing that mechanical balance calculates is found out.Moreover, in the case where the parsing based on calculation of thermodynamic equilibrium, by using various heat
Mechanical balance software for calculation, can precision it is good and easily find out.
Moreover, the Equilibrium Precipitation amount as the γ ' phase at above-mentioned 700 DEG C is the precipitation strength type of " 40 moles of % or more "
Ni base superalloy, for example, can enumerate in terms of quality % C:0.001~0.25%, Cr:8.0~22.0%, Mo:2.0~
7.0%, Al:2.0~8.0%, Ti:0.4~7.0%, surplus are the basic at being grouped as (hereinafter, for " matter of Ni and impurity
The such statement of % " is measured, " % " is abbreviated as).In addition, it is above-mentioned it is basic at being grouped as in, as needed can also be containing being selected from
Co:28.0% or less, W:6.0% or less, Nb:4.0% or less, Ta:3.0% or less, Fe:10.0% or less, V:1.2% with
Under, the one kind or two or more element material in Hf:1.0% or less, B:0.300% or less, Zr:0.30% or less.As this
The Ni base superalloy of sample, such as (UDIMET is Special Metals Corporation by Alloy713C, UDIMET720
Registered trademark) be representative.
For the mentioned component composition exemplified, the effect of each element is illustrated.
<C:0.001~0.25%>
C has the effect of improving the intensity of the crystal boundary of Ni base superalloy.Ni base superalloy is improved in addition, having
Castability effect.But if the content of C is more, coarse eutectic can be precipitated in the final solidification portion of the ingot casting in casting
Carbide.Moreover, the coarse carbide increases the reduction of hot-workability when can make extrusion molding.Therefore, the content of C is preferably set
It is 0.001~0.25%.It is more preferably set as 0.10% or less, is further preferably set as 0.05% or less.Particularly preferably it is set as
0.02% or less.In addition, being more preferably set as 0.003% or more, being further preferably set as 0.005% or more.Particularly preferably it is set as
0.008% or more.
<Cr:8.0~22.0%>
Cr is the element for improving oxidative resistance, corrosion resistance.But if excessively containing Cr, the equal embrittlement of σ will form
Phase reduces intensity, hot-workability.Therefore, the content of Cr is preferably set to 8.0~22.0%.More preferably 9.0% or more, into
One step is preferably 9.5% or more.Particularly preferably 10.0% or more.In addition, more preferably 18.0% or less, further preferably
16.0% or less.Particularly preferably 14.0% or less.
<Mo:2.0~7.0%>
Mo has the effect of facilitating the solution strengthening of matrix, improves elevated temperature strength.But it if Mo is excessive, will form
Intermetallic compound phase is to damage elevated temperature strength.Therefore, the content of Mo is preferably set to 2.0~7.0%.More preferably 2.5%
It above, is more preferably 3.0% or more.Particularly preferably 3.5% or more.In addition, more preferably 6.0% or less, further
Preferably 5.5% or less.Particularly preferably 5.0% or less.
<Al:2.0~8.0%>
Al is to form γ ' mutually thus the element for improving elevated temperature strength.But excessively containing for Al can be such that hot-workability drops
The reason of low, as faults in material such as crackles in extrusion molding.Therefore, the content of Al is preferably set to 2.0~8.0%.It is more excellent
It is selected as 2.5% or more, further preferably 3.5% or more.Particularly preferably 4.5% or more.In addition, more preferably 7.5% with
Under, further preferably 7.0% or less.Particularly preferably 6.5% or less.
<Ti:0.4~7.0%>
Ti is the element to form γ ' phase, the solution strengthening of γ ' phase is improved to elevated temperature strength in the same manner as Al.But if mistake
Degree contains Ti, then will form harmful η (eta) phase, to damage hot-workability.Therefore, the content of Ti be preferably set to 0.4~
7.0%.It more preferably 0.45% or more, is more preferably 0.5% or more.In addition, more preferably 5.0% or less, further
Preferably 3.0% or less.Particularly preferably 1.0% or less.
Surplus in addition to the element illustrated in above uses Ni, certainly also may include inevitable impurity.Moreover, should
It is basic also to contain element material below at can according to need in being grouped as.
<Co:28.0% or less>
Co is the stability for improving tissue, and the choosing of hot-workability can be maintained containing a large amount of Ti as intensified element
One of selecting property element.On the other hand, due to Co valuableness, cost increase.Therefore, even if Co's contains containing in the case where Co
Amount is it is also preferred that be set as 28.0% or less.It more preferably 18.0% or less, is more preferably 16.0% or less.Particularly preferably
13.0% or less.Moreover, in the case where Co can be set as to no added grade (the inevitable impurity levels of raw material), it will
The lower limit of Co is set as 0%.Furthermore, it is possible to be set as Co less than 1.0%.
It should be noted that obtaining by containing in the case where Co bring said effect, the content of Co is preferably set to 1.0%
More than.It more preferably 3.0% or more, is more preferably 8.0% or more.Particularly preferably 10.0% or more.
<W:6.0% or less>
W is to facilitate one of selective element of solution strengthening of matrix in the same manner as Mo.On the other hand, if W is excessive,
It will form harmful intermetallic compound phase, so that elevated temperature strength deteriorates.Therefore, even if containing in the case where W, the content of W
It is preferably set to 6.0% or less.It more preferably 5.5% or less, is more preferably 5.0% or less.Particularly preferably 4.5% with
Under.Moreover, the lower limit of W is set in the case where W can be set as to no added grade (the inevitable impurity levels of raw material)
It is 0%.Furthermore, it is possible to be set as W less than 1.0%, and then can be set to less than 0.8%.
It should be noted that obtain by containing in the case where W bring said effect, the content of W be preferably set to 1.0% with
On.Moreover, by compound containing W and Mo, thus effective to the performance of above-mentioned solution strengthening.With Mo compound containing containing W sometimes
Amount is preferably set to 0.8% or more.
<Nb:4.0% or less>
Nb is the selective element to form γ ' phase, the solution strengthening of γ ' phase is improved to elevated temperature strength in the same manner as Al, Ti
One of.But excessive the containing of Nb will form harmful δ (delta) phase, deteriorate hot-workability.Therefore, even if containing Nb
In the case where, the content of Nb is it is also preferred that be set as 4.0% or less.It more preferably 3.5% or less, is more preferably 3.0% or less.
Particularly preferably 2.5% or less.Moreover, Nb can be set as to no added grade (the inevitable impurity levels of raw material)
In the case of, the lower limit of Nb is set as 0%.Furthermore, it is possible to be set as Nb less than 0.5%.
It should be noted that obtaining by containing in the case where Nb bring said effect, the content of Nb is preferably set to 0.5%
More than.It more preferably 1.0% or more, is more preferably 1.5% or more.Particularly preferably 2.0% or more.
<Ta:3.0% or less>
Ta is the selective element to form γ ' phase, the solution strengthening of γ ' phase is improved to elevated temperature strength in the same manner as Al, Ti
One of.But the excessive addition of Ta makes γ ' mutually become the unstable coarsening so as to cause under high temperature at high temperature, and
Harmful η (eta) phase is formed, hot-workability is deteriorated.Therefore, even if the content of Ta is it is also preferred that be set as containing in the case where Ta
3.0% or less.It more preferably 2.5% or less, is more preferably 2.0% or less.Particularly preferably 1.5% or less.Moreover,
In the case that Ta can be set as to no added grade (the inevitable impurity levels of raw material), the lower limit of Ta is set as 0%.And
And Ta can be set as less than 0.3%.
It should be noted that obtaining by containing in the case where Ta bring said effect, the content of Ta is preferably set to 0.3%
More than.It more preferably 0.5% or more, is more preferably 0.7% or more.Particularly preferably 1.0% or more.
<Fe:10.0% or less>
Fe is that can replace expensive Ni, Co and contain, to one of reduction effective as selective element of cost of alloy.
But if excessively containing Fe, the equal brittle phase of σ will form to make intensity, hot-workability reduce.Therefore, even if containing
In the case where Fe, the content of Fe is it is also preferred that be set as 10.0% or less.More preferably 8.0% or less, be more preferably 6.0% with
Under.Particularly preferably 3.0% or less.Moreover, Fe can be set as to no added grade (inevitable impurity of raw material etc.
Grade) in the case where, the lower limit of Fe is set as 0%.Furthermore, it is possible to be set as Fe less than 0.1%.
It should be noted that in the case where obtaining by containing Fe bring said effect, instead of the Fe of the content of Ni, Co
Content be for example preferably set to 0.1% or more.It more preferably 0.4% or more, is more preferably 0.6% or more.Particularly preferably
It is 0.8% or more.
<V:1.2% or less>
V is useful one of the selective element of solution strengthening, the brought intercrystalline strengthening of carbide generation to matrix.But
It is that the excessive addition of V will lead to the generation of the unstable phase of high temperature in manufacturing process, gives manufacturing and mechanical behavior under high temperature band
Carry out adverse effect.Therefore, even if the content of V is it is also preferred that be set as 1.2% or less containing in the case where V.More preferably 1.0% with
Under, further preferably 0.8% or less.Particularly preferably 0.7% or less.Moreover, (former V can be set as to no added grade
The inevitable impurity levels of material) in the case where, the lower limit of V is set as 0%.Furthermore, it is possible to be set as V less than 0.1%.
It should be noted that obtain by containing in the case where V bring said effect, the content of V be preferably set to 0.1% with
On.It more preferably 0.2% or more, is more preferably 0.3% or more.Particularly preferably 0.5% or more.
<Hf:1.0% or less>
Hf be the oxidative resistance of alloy is improved, selective element that intercrystalline strengthening brought by carbide generates is useful it
One.But the oxide that the excessive addition of Hf will lead to manufacturing process generates, the generation of the unstable phase of high temperature, gives manufacturing
And mechanical behavior under high temperature brings adverse effect.Therefore, even if containing in the case where Hf, the content of Hf it is also preferred that be set as 1.0% with
Under.It more preferably 0.7% or less, is more preferably 0.5% or less.Particularly preferably 0.3% or less.Moreover, that can incite somebody to action
In the case that Hf is set as no added grade (the inevitable impurity levels of raw material), the lower limit of Hf is set as 0%.Moreover, can
Being set as Hf less than 0.02%.
It should be noted that obtaining by containing in the case where Hf bring said effect, the content of Hf is preferably set to
0.02% or more.It more preferably 0.05% or more, is more preferably 0.1% or more.Especially excellent is to select 0.15% or more.
<B:0.300% or less>
B is that one of can be improved grain-boundary strength, improve creep strength, the selective element of ductility.On the other hand, the mistake of B
The addition of degree can make the fusing point of alloy reduce to bring adverse effect to elevated temperature strength, hot-workability.Therefore, even if containing B
In the case where, the content of B is preferably also 0.300% or less.More preferably 0.100% or less, be more preferably 0.050% with
Under.Particularly preferably 0.020% or less.Moreover, B can be set as to no added grade (inevitable impurity of raw material etc.
Grade) in the case where, the lower limit of B is set as 0%.Furthermore, it is possible to be set as B less than 0.001%.
It should be noted that obtaining by containing in the case where B bring said effect, the content of B is preferably set to 0.001%
More than.It more preferably 0.003% or more, is more preferably 0.005% or more.Particularly preferably 0.007% or more.
<Zr:0.30% or less>
Zr is one of the selective element improve with grain-boundary strength in the same manner as B.But if excessively contain
Zr then will lead to the reduction of the fusing point of alloy, so that elevated temperature strength, hot-workability deteriorate.Therefore, even if the case where containing Zr
Under, the content of Zr is it is also preferred that be set as 0.30% or less.It more preferably 0.25% or less, is more preferably 0.20% or less.It is special
It You Xuanwei 0.15% or less.Moreover, Zr can be set as to no added grade (the inevitable impurity levels of raw material)
In the case of, the lower limit of Zr is set as 0%.Furthermore, it is possible to be set as Zr less than 0.001%.
It should be noted that obtaining by containing in the case where Zr bring said effect, the content of Zr is preferably set to
0.001% or more.It more preferably 0.005% or more, is more preferably 0.01% or more.Particularly preferably 0.03% or more.
(3) in hot extrusion forming method of the invention, the outer diameter D of blank when will be inserted into ingot-containing tubeB(mm) with contain ingot
The internal diameter D of cylinderC(mm) relationship is adjusted to (DC-DB): 2~8mm.
Hot extrusion molding particularly is carried out at " the Ni base superalloy of precipitation strength type " being grouped as to above-mentioned
When, the above-mentioned " outer diameter D of blank when being inserted into ingot-containing tubeB(mm) " with " the internal diameter D of ingot-containing tubeC(mm) " have between optimal
Numerical relation.In order to which the fracture ground of the interruption, extrusion material that do not squeeze out is continuously super heat-resisting to the Ni base of above-mentioned precipitation strength type
Alloy carries out hot extrusion molding and makes its completion, it is important that adjustment is mounted on " lubrication glass isolator " between mold and blank
Effect.Lubrication is heated when the blank that will warm up hot processing temperature is inserted into ingot-containing tube with glass isolator and is melted.Moreover,
In extrusion molding, the glass isolator of the melting can improve the lubricity between blank and mold.At this time, if it is possible to make the melting
Glass isolator also sufficiently infiltration between blank and ingot-containing tube, then " lubricating film " can be formed between blank and ingot-containing tube,
The lubricity between blank and ingot-containing tube can be made also to be improved.But compared with common stainless steel etc., precipitation strength type
Ni base superalloy it is poor to " wetability " of the glass isolator of above-mentioned melting.Therefore, in blank by the Ni base of precipitation strength type
In the molding situation of hot extrusion that superalloy is formed, in order to infiltrate the glass isolator of above-mentioned melting sufficiently to blank and contain ingot
Between cylinder, it is important that restudy the correlated condition etc. of its extrusion molding.Then, the present inventor has found out following content: for
Infiltrate the glass isolator of melting sufficiently so that the infiltration bring function and effect of the glass isolator of the melting are given full play to, with the glass
The optimization in " gap " between the easness of the infiltration of glass pad directly related blank and ingot-containing tube is effective.
Fig. 1 is to show by simulating the heat found out in the blank formed by the Ni base superalloy of above-mentioned precipitation strength type
In extrusion molding, the outer diameter D of blankB(mm) with the internal diameter D of ingot-containing tubeC(mm) difference is " DC-DB(mm) " with, be extruded into
The figure of an example of the result of the relationship of " thickness (mm) of lubricating film " is formed by between blank and ingot-containing tube in type.This
When, the position for finding out the thickness of above-mentioned lubricating film is the smallest position of thickness of lubricating film in the blank.Fig. 1's the result is that
Blank 1 is set as elasticoplastic body, ingot-containing tube 2 and hot pressing gasket 3 are set as rigid body, lubrication glass isolator 7 is set as rigid-plastic material,
As obtained from two-dimensional axis target model is computed the finite element analysis of heat and Coupling Deformation.At this point, due to heat
Pressure pad piece 3 is set to the movement for directly extruding direction, therefore non-indication rod 4 in analytic modell analytical model.In above-mentioned calculating, use
The finite element analysis software " FORGENxtver1.0 " of TRANSVALOR corporation, lubrication glass isolator 7 presuppose to pass through
It melts with the contact of blank 1, is thus calculated completely.
According to the result of Fig. 1 it is found that by reducing above-mentioned gap (that is, " DC-DB(mm) " value), so as to squeeze out
The lubricating film of adequate thickness is formed between blank and ingot-containing tube in molding.For example, knowing by the way that above-mentioned gap to be set as
" 8mm or less " is capable of forming the lubricating film that thickness is more than the degree of " 0.05mm ".It is thought that because the glass isolator of melting
Flowing velocity becomes faster.Thereby, it is possible to improve the lubricity between blank and ingot-containing tube.
In addition, if above-mentioned gap becomes larger, diameter of the easy inner wall towards ingot-containing tube of the blank in extrusion molding along blank
To deformation.Moreover, the gap of blank and ingot-containing tube in the position that the blank radially substantially deforms, extrusion molding locally becomes
Narrow (occlusion), so that the flowing of the glass isolator of melting interdict etc., the smoothly flowing of glass isolator that melts is obstructed.It is tied
Fruit has extrusion material fracture after molding etc. that cannot complete extrusion molding if generating significant crackle on the surface of blank
Worry.
But exceedingly reducing above-mentioned gap is not good method.Firstly, having the glass of melting if above-mentioned gap is too small
What the flowing of glass pad such as was interdicted at the glass isolator of meltings smoothly flows the worry being obstructed.Moreover, as this as a result, for example,
In the case of figure 1, using gap be " about 4mm " when as boundary, hereafter, have as gap reduces, the thickness of lubricating film also becomes smaller
Tendency.Then it is believed that in Fig. 1, when gap is such as left and right " 1mm ", even if the thickness of lubricating film is maintained
The left and right " 0.05mm ", actually the thickness of its lubricating film also partly can be thinned or interrupt.
Moreover, if above-mentioned gap is too small, there is following worry: in the preparation stage of extrusion molding, will warm up heat
When the blank of processing temperature is inserted into ingot-containing tube, blank is contacted with the inner wall of ingot-containing tube, thus the blank before extrusion molding starts
Temperature be greatly reduced.Moreover, especially in the case where the Ni base superalloy of precipitation strength type, with common stainless steel
Etc. comparing, relative to the rising high sensitivity for the deformation drag that temperature reduces, if the temperature of blank reduces, the deformation resistance of blank
Power can increase the degree reduced to temperature or more, so that the completion to extrusion molding brings obstacle.
Therefore, in the present invention, the outer diameter D of blank when will be inserted into ingot-containing tubeB(mm) with the internal diameter D of ingot-containing tubeC(mm)
Relationship is adjusted to " (DC-DB): 2~8mm ".Moreover, in the range of above-mentioned 2~8mm, for example, can by it further 2~
The range of 4mm is adjusted or is adjusted in the range of 4~8mm.It should (DC-DB) value handled in the form of integer.
For example, can be using to value obtained from rounding up after decimal point.
In addition, the ingot-containing tube of usually extrusion molding apparatus is tubular, it is for example, cylindric.Moreover, corresponding to which, blank
It is for example, cylindric for column.In this case, above-mentioned (DC-DB) value can pass through the inner peripheral surface and base of the ingot-containing tube
The formed parallel section being spaced of the outer peripheral surface of material is adjusted.
Above-mentioned (DC-DB) the adjustment of value can for example be carried out by the adjustment of the outer diameter of blank.Moreover, the blank
The adjustment of outer diameter can for example be carried out by being inserted into the outer diameter of (that is, before being heated to hot processing temperature) blank before ingot-containing tube
Adjustment.Adjustment for the outer diameter of the blank can calculate the thermal expansion amount of blank when being heated to hot processing temperature, be heated to
The thermal expansion etc. of ingot-containing tube when preheating temperature, according to blank at be grouped as, heating condition, by the machinings such as rotary cut come
It carries out.Moreover, for example, the outer diameter D of the blank before above-mentioned hot processing temperature can be will warm upB' (mm) be heated to it is above-mentioned pre-
The internal diameter D of ingot-containing tube before hot temperatureC' relationship of (mm) is adjusted to (DC’-DB'): 3~9mm.Moreover, above-mentioned 3~9mm's
In range, for example, it can be further adjusted in the range of 3~5mm or be adjusted in the range of 5~9mm.
Above-mentioned (DC’-DB') value can be parallel with interval formed by the outer peripheral surface of blank by the inner peripheral surface of ingot-containing tube
Part is adjusted.
It should be noted that at this point, if the internal diameter of ingot-containing tube is excessive, according to the internal diameter of ingot-containing tube, in order to remain above-mentioned
Gap, it is necessary to make the big blank of outer diameter.The treatability that the big blank of production outer diameter will lead to blank reduces very much.In turn, will
When being heated to the blank of hot processing temperature and being inserted into ingot-containing tube, if the processing of blank spends the time, the temperature of blank can drop
It is low.Therefore, the internal diameter D of ingot-containing tubeC(mm) it is preferably set to 180mm or less.Moreover, more preferably make its as low as such as 160mm or less,
140mm or less, 120mm or less, 100mm or less.
In addition, conversely, the diameter of blank must be reduced if the internal diameter of ingot-containing tube is too small.If the diameter of blank becomes smaller,
The cooling velocity of the blank of heating itself will increase.Moreover, when the blank that will warm up hot processing temperature is inserted into ingot-containing tube
Deng the temperature of blank can be greatly reduced.Therefore, the internal diameter D of ingot-containing tubeC(mm) it is preferably set to 60mm or more.Moreover, more preferably making
It is greatly to such as 70mm or more, 80mm or more.
Further it is preferred that will warm up the internal diameter D of the ingot-containing tube before preheating temperatureC' 180mm or less is set as to replace
By the internal diameter D of ingot-containing tubeCReplace with above-mentioned value.Moreover, more preferably making its as low as such as 160mm or less, 140mm or less, 120mm
Below, 100mm or less.Additionally, it is preferred that by the internal diameter D of above-mentioned ingot-containing tubeC' it is set as 60mm or more.In turn, more preferably make it greatly extremely
Such as 70mm or more, 80mm or more.
In the case where the present invention, to having, " the Equilibrium Precipitation amount of the γ ' phase at 700 DEG C is the precipitation of 40 moles of % or more
The Ni base superalloy of enhanced type at being grouped as " hot processing temperature of blank when carrying out hot extrusion molding be preferably set to
" 1150~1180 DEG C ".More preferably 1170 DEG C or less.Extrusion molding under the high temperature helps to maintain by precipitation strength type
The hot-workability for the blank that Ni base superalloy is formed.Moreover, the extrusion molding under the high temperature can promote above-mentioned lubrication glass
The Flashmelt of glass pad, and improve the flowing velocity of the lubrication glass isolator of the melting, thus to improve blank and ingot-containing tube it
Between lubricity it is effective.
It, can be in the week of blank when will warm up the blank of hot processing temperature and being inserted into ingot-containing tube in the case where the present invention
Face coated glass lubricant.
In the case where the present invention, it is believed that the diameter in the section of the extrusion material of production is, for example, 10~130mm.Moreover,
The diameter in the section of the extrusion material can be 100mm or less, can be 60mm or less or 30mm or less.It in addition can be with
Think, in the case where the present invention, the extrusion ratio (sectional area of blank/extrusion material sectional area) when extrusion molding be, for example, 70 with
Under.Moreover, the extrusion ratio can be 40 or less or 30 or less.And then it can be 20 or less, can also be 10 or less.
Furthermore it is possible to be 2 or more, can be 4 or more or 6 or more.
The extrusion material such as form with bar, wire rod obtained in this way.In addition, these bars, wire rod are for example with reality
The form of the heart.Moreover, carrying out further hot-working, cold working to it, thus using such extrusion material as starting material
The diameter that such as section can be made is 1~6mm and then is the such lametta of 4mm or less, 3mm or less.
In the case where the present invention, above-mentioned blank can also be made and be accommodated with molded body in a reservoir (that is, precipitation strength
The Ni base superalloy of type) form.Moreover, in this case, by adjusting for above-mentioned (DC-DB) value or be adjusted to
(the D statedC’-DB') value, also can be realized the Ni base superalloy of precipitation strength type hot extrusion molding.
Embodiment
To by casting as defined in vacuum dissolution preparation at the melt being grouped as, ingot casting is obtained.Then, to the casting
Ingot is machined, and the columned blank A for being equivalent to Alloy 713C with defined diameter, length 105mm is made
~E.Diameter (the D of blank A~EB') it is set as: blank A:83mm, blank B:82mm, blank C:80mm, blank D:76mm, blank
E:72mm.
By the shown in table 1 at being grouped as of blank A~E (i.e. ingot casting).It should be noted that since Co, W, Ta, V, Hf are miscellaneous
Prime element, therefore meet Co≤28.0%, W≤6.0%, Ta≤3.0%, V≤1.2%, Hf≤1.0%.
It is found out with thermodynamic balance calculation software " JMatPro (Version8.0.1, Sente Software Ltd. system) "
The Equilibrium Precipitation amount of γ ' phase of the blank A~E at 700 DEG C.It is inputted cited by table 1 into the thermodynamic balance calculation software
The content of each element and calculated, as a result the above-mentioned Equilibrium Precipitation amount of blank A~E be " 70 moles of % ".In addition, blank A
γ ' the phase solid solubility temperature of~E is " 1180 DEG C ".
[table 1]
(quality %)
※ includes impurity
Blank A~E is heated to hot processing temperature (the 1st process).Then, which is inserted into figure
Cylindric ingot-containing tube (the JIS-SKD61 system of 2 extrusion molding apparatus.Internal diameter (D before preheatingC'): 85mm), it is based on
The hot extrusion of the condition of table 2 forms, and makes solid extrusion material (the 2nd process).
In above-mentioned hot extrusion molding, before blank A~E is inserted into ingot-containing tube, blank A~E is heated to 1150 DEG C
Hot processing temperature, also, ingot-containing tube is also separately heated to 500 DEG C of preheating temperature.Then, respective temperature is heated at this
In the blank A~E and ingot-containing tube of state, about inner peripheral surface when blank A~E is inserted into ingot-containing tube, in the ingot-containing tube
The parallel section at interval formed by the outer peripheral surface with blank A~E, blank A~E outer diameter DB(mm) with the internal diameter D of ingot-containing tubeC
(mm) gap (DC-DB), blank A is " 1mm ", blank B is " 2mm ", blank C is " 4mm ", blank D is " 8mm ", blank E is
“12mm”。
[table 2]
Then, carried out hot extrusion molding, as a result blank B~D respectively in, live part can all be squeezed out to last
Until without squeeze out material (diameter in section about 27mm) fracture.
On the other hand, in the case where blank A, since above-mentioned gap is too small, when blank is inserted into ingot-containing tube, blank with
The inner wall of ingot-containing tube contacts, to need time (temperature of blank reduces), is difficult in terms of starting hot extrusion molding.Separately
Outside, in the case where blank E, it is believed that since above-mentioned gap is excessive, so that the smoothly flowing of the glass isolator of melting is hindered,
As a result, showing the sign for squeezing out material fracture of extrusion.Moreover, on the way having ceased hot extrusion molding.
Fig. 3 shows the appearance by above-mentioned hot extrusion molding by the obtained extrusion material of blank D (gap: 8mm).In addition,
Fig. 4 is shown by the appearance of the obtained extrusion material of blank E (gap: 12mm).Fig. 3, in 4, right side is the front end (mold for squeezing out material
Positioned at left side).The attachment that confirms of surface for squeezing out material be melting lubrication glass isolator it is concretionary.
On the surface of the extrusion material of Fig. 3, lubrication is attached to rear end from the front end of the extrusion material with glass isolator.Moreover,
The surface for squeezing out material does not have crackle, does not observe apparent defect yet, shows good surface state.Moreover, this is good
Surface state it is also the same in the extrusion material obtained by blank B (gap: 2mm), blank C (gap: 4mm).
On the other hand, on the surface of the extrusion material of Fig. 4, after lubrication is not attached to from the front end of the extrusion material with glass isolator
End.The many " necking down (constricted part) " before material reaches fracture is squeezed out moreover, producing on the surface for squeezing out material.
Description of symbols
1 blank
2 ingot-containing tubes
3 hot pressing gaskets
4 bars
5 molds (including mold holder)
6 squeeze out material
7 lubrications use glass isolator
Claims (10)
1. a kind of hot extrusion forming method of Ni base superalloy, wherein by blank heating to hot processing temperature, will warm up
The blank of the hot processing temperature is inserted into ingot-containing tube, applies compressing force to the blank for being inserted into the ingot-containing tube, thus
It squeezing out, forms from the hole for the mold for being set to the ingot-containing tube by the blank, the hot extrusion forming method is characterized in that,
The hot extrusion forming method is using the following method directly extruded: from one of the ingot-containing tube inserted with the blank
End side applies compressing force to the blank, squeezes the blank from the hole of the mold for the another side for being set to the ingot-containing tube
Out,
The hot extrusion forming method utilizes the glass for being equipped with lubrication glass isolator between the mold and the blank to moisten
It is sliding to squeeze out,
The blank has the Ni base for the precipitation strength type that the Equilibrium Precipitation amount of the γ ' phase at 700 DEG C is 40 moles of % or more super
Heat-resisting alloy at being grouped as,
The outer diameter D of blank when will be inserted into the ingot-containing tubeBWith the internal diameter D of the ingot-containing tubeCRelationship be adjusted to DC-
DB: 2~8mm, wherein DB、DCUnit be mm.
2. the hot extrusion forming method of Ni base superalloy according to claim 1, which is characterized in that the ingot-containing tube
Internal diameter DCFor 60~180mm, wherein DCUnit be mm.
3. a kind of hot extrusion forming method of Ni base superalloy, wherein by blank heating to hot processing temperature, will warm up
The blank of the hot processing temperature is inserted into ingot-containing tube, applies compressing force to blank described in the ingot-containing tube is inserted into, from setting
The blank is squeezed out in the hole of the mold of the ingot-containing tube, is formed, the hot extrusion forming method is characterized in that,
The hot extrusion forming method is using the following method directly extruded: from one of the ingot-containing tube inserted with the blank
End side applies compressing force to the blank, squeezes the blank from the hole of the mold for the another side for being set to the ingot-containing tube
Out,
The hot extrusion forming method utilizes the glass for being equipped with lubrication glass isolator between the mold and the blank to moisten
It is sliding to squeeze out,
The blank has the Ni base for the precipitation strength type that the Equilibrium Precipitation amount of the γ ' phase at 700 DEG C is 40 moles of % or more super
Heat-resisting alloy at being grouped as,
The outer diameter D of blank before will warm up the hot processing temperatureB' with the internal diameter D of ingot-containing tube that is heated to before preheating temperatureC’
Relationship be adjusted to DC’-DB': 3~9mm, wherein DB’、DC' unit be mm.
4. the hot extrusion forming method of Ni base superalloy according to claim 3, which is characterized in that the ingot-containing tube
Internal diameter DC' it is 60~180mm, wherein DC' unit be mm.
5. the hot extrusion forming method of Ni base superalloy according to any one of claims 1 to 4, feature exist
In the hot processing temperature is 1150~1180 DEG C.
6. a kind of Ni base superalloy squeeze out the manufacturing method of material comprising:
1st process, by the blank heating of Ni base superalloy to hot processing temperature；With
2nd process, the blank that will warm up the hot processing temperature are inserted into ingot-containing tube, from the one end of the ingot-containing tube to institute
It states blank and applies compressing force, the blank is squeezed out from the hole of the mold for the another side for being set to the ingot-containing tube, obtains Ni
The extrusion material of base superalloy,
The blank of the Ni base superalloy has the analysis that the Equilibrium Precipitation amount of the γ ' phase at 700 DEG C is 40 moles of % or more
Out the Ni base superalloy of enhanced type at being grouped as,
Base when installing lubrication glass isolator between the mold and the blank, and the ingot-containing tube will be inserted into
The outer diameter D of materialBWith the internal diameter D of the ingot-containing tubeCRelationship be adjusted to DC-DB: thus 2~8mm carries out the 2nd process,
In, DB、DCUnit be mm.
7. the manufacturing method that Ni base superalloy according to claim 6 squeezes out material, which is characterized in that by the Sheng ingot
The internal diameter D of cylinderCIt is adjusted to 60~180mm, wherein DCUnit be mm.
8. a kind of Ni base superalloy squeeze out the manufacturing method of material comprising:
1st process, by the blank heating of Ni base superalloy to hot processing temperature；With
2nd process, the blank that will warm up the hot processing temperature are inserted into ingot-containing tube, from the one end of the ingot-containing tube to institute
It states blank and applies compressing force, the blank is squeezed out from the hole of the mold for the another side for being set to the ingot-containing tube, obtains Ni
The extrusion material of base superalloy,
The blank of the Ni base superalloy has the analysis that the Equilibrium Precipitation amount of the γ ' phase at 700 DEG C is 40 moles of % or more
Out the Ni base superalloy of enhanced type at being grouped as,
Lubrication glass isolator is installed between the mold and the blank, and will warm up the institute before the hot processing temperature
State the outer diameter D of blankB' with the internal diameter D of the ingot-containing tube that is heated to before preheating temperatureC' relationship be adjusted to DC’-DB': 3~
Thus 9mm carries out the 2nd process, wherein DB’、DC' unit be mm.
9. the manufacturing method that Ni base superalloy according to claim 8 squeezes out material, which is characterized in that by the Sheng ingot
The internal diameter D of cylinderC' it is adjusted to 60~180mm, wherein DC' unit be mm.
10. the Ni base superalloy according to any one of claim 6~9 squeezes out the manufacturing method of material, feature exists
In the hot processing temperature is set as 1150~1180 DEG C.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2016190801 | 2016-09-29 | ||
| JP2016-190801 | 2016-09-29 | ||
| PCT/JP2017/030079 WO2018061540A1 (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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|---|---|
| CN109789458A true CN109789458A (en) | 2019-05-21 |
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Country Status (5)
| Country | Link |
|---|---|
| US (1) | US20200030863A1 (en) |
| EP (1) | EP3520916A4 (en) |
| JP (1) | JP6631896B2 (en) |
| CN (1) | CN109789458A (en) |
| WO (1) | WO2018061540A1 (en) |
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| WO2018061317A1 (en) * | 2016-09-30 | 2018-04-05 | 日立金属株式会社 | Method of manufacturing ni-based super heat resistant alloy extruded material, and ni-based super heat resistant alloy extruded material |
| JP6748951B2 (en) * | 2018-08-07 | 2020-09-02 | 日立金属株式会社 | Method for producing Ni-base superheat-resistant alloy and Ni-base superheat-resistant alloy |
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2017
- 2017-08-23 EP EP17855498.6A patent/EP3520916A4/en not_active Withdrawn
- 2017-08-23 JP JP2018541993A patent/JP6631896B2/en not_active Expired - Fee Related
- 2017-08-23 US US16/337,775 patent/US20200030863A1/en not_active Abandoned
- 2017-08-23 WO PCT/JP2017/030079 patent/WO2018061540A1/en unknown
- 2017-08-23 CN CN201780060171.5A patent/CN109789458A/en active Pending
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Also Published As
| Publication number | Publication date |
|---|---|
| WO2018061540A1 (en) | 2018-04-05 |
| US20200030863A1 (en) | 2020-01-30 |
| EP3520916A1 (en) | 2019-08-07 |
| EP3520916A4 (en) | 2020-05-27 |
| JP6631896B2 (en) | 2020-01-15 |
| JPWO2018061540A1 (en) | 2019-04-11 |
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Application publication date: 20190521 |