EP3608041A1 - Consolidation de pressage isostatique à chaud de pièces dérivées de poudre - Google Patents

Consolidation de pressage isostatique à chaud de pièces dérivées de poudre Download PDF

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Publication number
EP3608041A1
EP3608041A1 EP18275113.1A EP18275113A EP3608041A1 EP 3608041 A1 EP3608041 A1 EP 3608041A1 EP 18275113 A EP18275113 A EP 18275113A EP 3608041 A1 EP3608041 A1 EP 3608041A1
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Prior art keywords
pressure
minutes
metal
temperature
metal powder
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EP18275113.1A
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German (de)
English (en)
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BAE Systems PLC
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BAE Systems PLC
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Priority to EP18275113.1A priority Critical patent/EP3608041A1/fr
Priority to US17/261,431 priority patent/US11638956B2/en
Priority to EP19752545.4A priority patent/EP3833499A1/fr
Priority to GB1911290.3A priority patent/GB2577788B/en
Priority to PCT/GB2019/052211 priority patent/WO2020030906A1/fr
Publication of EP3608041A1 publication Critical patent/EP3608041A1/fr
Pending legal-status Critical Current

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/14—Both compacting and sintering simultaneously
    • B22F3/15—Hot isostatic pressing
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/045—Alloys based on refractory metals
    • C22C1/0458—Alloys based on titanium, zirconium or hafnium
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy

Definitions

  • the present invention generally relates to Hot Isostatic Pressing (HIP) of metal powder.
  • the invention has particular application in the aerospace industry and in the production of metal aircraft components.
  • Hot Isostatic Pressing is a process that can be used to densify powders, cast parts or sintered parts at high pressure and high temperatures. It is widely used in the manufacture of complex, metal parts in the aerospace industry and has become an alternative to conventional processes such as forging, casting and machining.
  • a HIP process will involve one high pressure/high temperature cycle, where the temperature and pressure are applied, held for a period of time, known as the soak period (determined by the properties of the material, design of the HIP system, desired characteristics of the formed material etc.) and then the pressure released to atmospheric pressure and the temperature returned to ambient/room temperature.
  • the soak period determined by the properties of the material, design of the HIP system, desired characteristics of the formed material etc.
  • HIP is generally utilised in two principle ways; as a primary production process or as a secondary production process.
  • HIP When used as a primary production process, HIP is used to produce the finished solid metal parts/components from metal powders.
  • Metal powder is placed into a container, known as a can, and is usually flushed with an inert gas, such as argon.
  • the can (and canned powder) is then evacuated and sealed from the external atmosphere. Pressure and heat are then applied such that the powder is compressed (compacted) and then fused into solid metal.
  • a high residual gas pressure will remain within any residual microscopic gas pores in the metal, which can increase further if the component is subjected to high temperatures in subsequent manufacturing processes or in operation.
  • An increase in the internal gas pressure within sealed pores can cause the pores to re-open and damage the integrity of the surrounding structure.
  • HIP When used as a secondary production process, HIP is used in combination with a primary production process such as casting or a powder metallurgy (PM) process (e.g. additive layer manufacturing (ALM) technologies) so as to consolidate and diffusion bond internal (i.e. non surface breaking) defects in the primary produced part.
  • PM powder metallurgy
  • ALM additive layer manufacturing
  • HIP processing of cast parts has been shown to successfully reduce such shrinkage porosity, thus improving the integrity of the casting.
  • SLM selective laser melting
  • a high power-density laser is used to melt and fuse metal powders together.
  • An inert gas usually argon gas in the case of titanium powder SLM, is used both as a purge gas to displace air from the powder, and as a gas stream to act as the medium for the carry-over of spatter caused by the laser interacting with the powder. It is also used to maintain an inert atmosphere inside the SLM chamber.
  • the use of SLM in the manufacturing of metal components in the aerospace industry may be limited by the potential for porosity within the components produced by SLM.
  • the present invention provides a method of forming a metal component from metal powder, the method comprising: (a) exposing the metal powder to an inert gas; (b) consolidating the metal powder into a solid metal; followed by (c) exposing the solid metal to a hot isostatic pressing process to form a metal component, wherein the hot isostatic pressing process comprises one initial compression cycle followed by at least one decompression and recompression cycle.
  • the method may further comprise, following step (c), (d) a final decompression to an intermediate pressure between the compression pressure of the recompression cycle (of step (c)) and atmospheric pressure or below.
  • Steps (a) and (b) may be part of a primary hot isostatic pressing method or an additive layer manufacturing method.
  • the additive layer manufacturing method may be selective laser melting.
  • the metal powder may be selected from the group consisting of nickel, cobalt, titanium, iron, aluminium and alloys thereof.
  • the metal powder may be a titanium alloy, for example an alpha, beta or alpha-beta titanium alloy.
  • Suitable titanium alloys include Ti-5Al-2.5Sn (alpha), Ti-8Al-1Mo-1V (alpha), Ti-6Al-4Sn-4Zr-0.7Nb-0.5Mo-0.4Si (alpha), Ti-6Al-2Sn-4Zr-2Mo (alpha-beta), Ti-6Al-4V (alpha-beta), Ti-6Al-6V-2Sn (alpha-beta), Ti-6Al-2Sn-4Zr-6Mo (alpha-beta), Ti-10V-2Fe-3Al (beta) and Ti-3Al-8V-6Cr-4Mo-4Zr (beta).
  • the metal is a titanium/aluminium/vanadium alloy.
  • the metal is an alpha-be
  • the inert gas is preferably soluble in the solid metal.
  • the inert gas is helium.
  • the inert gas is helium and the metal powder is an alpha, beta or alpha-beta titanium alloy.
  • the gas is a gas having 40-60% of the radius of the metal atom, for example titanium atoms. More preferably the gas is a gas that has a radius 50-60% of that of the metal, most preferably 55%.
  • Helium has an effective atomic radius that is 55% that of titanium and thus advantageously will enable a relatively high rate of diffusion of helium through titanium alloys.
  • the one initial compression cycle may comprise increasing the pressure to a first pressure between 100 to 300MPa (preferably 200 to 300MPa) and increasing the temperature to a first temperature between 500 to 1500°C. (preferably 800 to 1000°C).
  • the first pressure and first temperature may be held for a period of time ranging from 30 to 120 minutes (preferably 60 to 100 minutes).
  • the at least one decompression and recompression of step (c) may comprise reducing the first pressure to atmospheric pressure or below followed by increasing the pressure back to a second pressure, which second pressure is substantially the same (or the same) as the first pressure, and wherein the first temperature is maintained throughout the at least one decompression and recompression step.
  • the atmospheric pressure or below may be held for a period of time ranging from 5 to 120 minutes.
  • the decompressed state hold time i.e. the time that should be allowed for diffusion in the reduced pressure state
  • the second pressure may be held for a period of time ranging from 30 to 120 minutes or 30 to 100 minutes, for example 30 to 40 minutes or 60 to 100 minutes, for example 60 minutes.
  • the method may further comprise the step of (d) lowering the pressure to a third pressure which is between the first pressure and atmospheric pressure or below, and holding the third pressure for a period of time ranging from 30 to 120 minutes (preferably 50 to 70 minutes, for example 60 minutes), before lowering the third pressure to atmospheric pressure or below.
  • Primary hot isostatic pressing process may mean that the solid metal is formed from metal powder in a can in the usual known way.
  • Step (c) (or (c) and (d)) may then be considered a secondary hot isostatic pressing process.
  • the solid part could be removed from the can and placed back in the HIP chamber and subjected to a second hot isostatic pressing process.
  • the solid part may stay in the can, with the temperature maintained (i.e. not reduced to ambient/room temperature) and applying a second HIP process.
  • the HIP of steps (a) and (b) may be considered a distinct process from the HIP of step (c) or (c) and (d).
  • the method may be finalised, after step (c) or (d), by reducing the second, third or intermediate pressure to atmospheric pressure or below.
  • the first temperature may at the same time, be reduced down to ambient/room temperature and the method of the present invention finished to produce a metal component with reduced porosity (when compared to the solid metal used in step (b)).
  • step (c) or step (c) with step (d) of the method of the present invention reduces the porosity of the solid metal formed after step (b) to below 10%, below 5%, below 3%, below 2%, below 1%, preferably 0% porosity.
  • Percentage porosity may be considered (total volume of voids/ total volume) x100.
  • the porosity of the metal component is preferably below 10%, below 5%, below 3%, below 2%, below 1%, more preferably 0% porosity.
  • the metal component may be an aircraft component.
  • it may be an aircraft skin or stringer.
  • FIG. 1a shows a flow chart of a manufacturing process 100a including primary HIP formation and subsequent secondary HIP processing using, for example, a Quintus QIH286 HIP Press.
  • a HIP can is filled with metal powder, for example a titanium powder.
  • the metal powder inside the HIP can is flushed (purged) with an inert gas.
  • helium may be utilised with a titanium powder (such as a Ti-6AI-4V powder), however any gas soluble in the metal being used and which is non-deleterious, may be utilised.
  • the can is substantially evacuated of the inert gas and is then sealed. Inevitably a very small amount of the inert gas will remain in the powder grains.
  • step 104a the can is pressed in a HIP cycle to form the component.
  • the metallic powder will have fused and diffusion bonded to become a solid component, but defects, for example bubbles formed from residual helium that was not evacuated from the HIP can, may remain in the form of residual gas porosity.
  • step 104a At the end of step 104a the temperature is not reduced pending moving to the following step 105a.
  • the HIP cycle may be continued in a contiguous manner (i.e. whilst maintaining an elevated temperature and the component remains in the can) by applying a further HIP process in step 105a.
  • This is a modified/enhanced HIP process that has been developed to shrink the size of gas bubbles in the component, therefore reducing the porosity of the component.
  • Figure 1b shows a flow chart of a manufacturing process 100b including primary SLM processing (using for example a Renishaw REN AM 500Q) and subsequent secondary HIP processing.
  • primary SLM processing using for example a Renishaw REN AM 500Q
  • secondary HIP processing using for example a Renishaw REN AM 500Q
  • a metal powder for example, a titanium alloy is provided in a SLM chamber.
  • the metal powder (and SLM chamber) is purged with an inert gas.
  • helium may be utilised with a titanium powder (such as a Ti-6AI-4V powder), however any gas soluble in the metal being used and which is non-deleterious, may be utilised.
  • the soluble inert gas is used as the purge gas to purge the powder of any air, and as the gas stream to act as the medium for the carry-over of spatter caused due to the laser interacting with the powder in step 104b. It is also used to maintain an inert atmosphere inside the SLM chamber in which the steps of 101b-104b are carried out.
  • the metal powder is melted or fused together by the action of a high power-density laser. Inevitably a very small amount of the inert gas will remain in the powder grains.
  • step 104b the melted material is deposited in layers (e.g. on a base plate of a work piece). Subsequent layers are then built up upon each preceding layer.
  • the metal powder will have fused and diffusion bonded to become a solid component, but defects, for example bubbles formed from the helium, may remain in the form of residual gas porosity. The solid component is then removed from the SLM chamber.
  • the solid component is treated using a modified HIP process to significantly reduce the size of the trapped gas pores, thereby reducing the porosity of the component.
  • any surface breaking defects in SLM will most likely not be healed by the HIP process. If this is the case and on inspection these surface defects are present, the surface layer (and defects) may be removed by, for example, electrochemical machining.
  • FIG. 2 shows a typical HIP cycle for a titanium component, such as that performed at step 104a.
  • the HIP cycle begins with step 201 - an increase in pressure to approximately 200 MPa (and generally at least about 100 MPa) and increase in temperature to approximately 930°C over a period of time, such as about 10-20 minutes (for example 15 minutes).
  • the helium gas bubbles e.g. residual gas entrapment from the can flushing process
  • start to collapse point 202
  • the internal pressure of the helium gas bubble increases.
  • the pressure and temperature are then held for a soak period.
  • the soak period is a sufficient period of time for the bubble to continue to collapse as much as possible at this specific pressure and temperature, and for diffusion bonding to occur in the metal around the bubble.
  • the soak period is approximately 90-100 minutes (for example 90 minutes).
  • the pressure is released and brought back to around atmospheric pressure.
  • the temperature is also reduced down to room/ambient temperature.
  • Figure 3 which shows an example modified/enhanced HIP cycle, for example as is noted in 105a or 105b of Figures 1a or 1b , for shrinking residual helium gas bubbles (residual helium gas entrapment/porosity) in a previously manufactured titanium component (for example previously produced by HIP or SLM).
  • a previously manufactured titanium component for example previously produced by HIP or SLM.
  • the HIP cycle begins with step 301 - an increase in pressure to a first pressure and an increase in temperature to a first temperature over a first period of time. For example, about 200 MPa (and generally at least about 100 MPa), about 930°C and for about 10-20 minutes (for example 15 minutes).
  • a sufficiently high pressure and temperature are reached, in this case 200MPa and 930°C, the helium gas bubbles start to collapse and shrink (point 302).
  • the internal pressure of the helium gas bubble in turn increases.
  • the pressure and temperature are then held for a first soak period.
  • the first soak period is a sufficient period of time for the helium bubble to continue to collapse as much as possible at this pressure and temperature, and for newly interacting intimate surfaces to diffusion bond to each other.
  • the first soak period in Figure 3 is approximately 90-100 minutes, for example 90 minutes.
  • the first pressure is released and brought back to approximately atmospheric pressure or below, whilst maintaining the first temperature at the elevated level (point 304), e.g. 930°C.
  • This decompressed state is held for a period of time sufficient to allow some of the previously pressurised helium gas to diffuse into the metallic matrix (decompressed state hold time).
  • the isostatic pressure in the titanium is thus relieved by the decompression of the HIP chamber which thereby allows the pockets of pressurised helium gas to begin diffusion into the titanium (the diffusion being driven by the pressure gradient between the high helium gas pressure and the titanium).
  • the helium pressure in each gas bubble will in turn reduce as the diffusion process proceeds and so the rate of diffusion will progressively reduce as more diffusion occurs.
  • the decompressed state hold time should be sufficiently enough time for the diffusion process to substantially conclude.
  • the decompressed state hold time i.e. the time that should be allowed for diffusion in the reduced pressure state
  • the pressure is then once again increased (step 305) to a second pressure, which is substantially the same ( ⁇ 5% differential) as the original first elevated pressure, in this case 200MPa, and held again for a second soak period (step 306).
  • the second soak period is either the same time as the first soak period (e.g. 90-100 minutes) or shorter than the first soak period (e.g. approximately 30-40 minutes, for example 30 minutes). It will be appreciated that the choice of second soak period time will depend on a balance between maximising the diffusion bonding and bubble collapse, and also economic considerations.
  • the second soak period is 30-100 minutes and does not exceed 100 minutes.
  • the second pressure is then reduced (step 307), after the bubble has almost collapsed, to a third pressure which is an intermediate pressure between the first pressure (and the second pressure, which is substantially the same as the first pressure) and atmospheric pressure or below.
  • This intermediate pressure is a pressure that is able to facilitate diffusion bonding but does not facilitate further reduction in the size of any bubbles.
  • the third intermediate pressure is held for approximately 30-120 minutes, for example 60 minutes. In Figure 3 , the intermediate pressure is approximately 100MPa.
  • a lower, intermediate pressure ensures that the bubble does not continue to reduce in size during the diffusion bonding phase, but is held at a steady size and ensures that the diffusion bonding occurs in a steady state condition (the diffusion bonding can take place without further shrinkage).
  • the step 307 pressure reduction acts to arrest the bubble size and thus ensures steady state diffusion bonding. This ensures that the reduced-sized, arrested/stable bubble is surrounded by fully diffusion bonded material. Without this pressure reduction step 307, the material directly adjacent to the bubble may only be partially bonded (owing to the reduced time in intimate contact), thus potentially making it vulnerable to either partial peeling or cracking on release of the HIP pressure. Further, cracks may also develop in service.
  • the use of an intermediate pressure hold before the final reduction to atmospheric pressure or below thus advantageously avoids such problems.
  • the helium diffusion into the metallic matrix which occurs at step 304 when the HIP pressure is first removed allows the bubble to be further compressed in size when the HIP pressure is re-applied at step 305. Without the time period at step 304 with the HIP pressure removed there would be little or no opportunity for the helium to diffuse into the surrounding titanium metal.
  • Figure 3 illustrates one decompression and recompression cycle before the final (intermediate pressure) diffusion bond stage
  • Figure 4 illustrates two decompression and recompression cycles before the final (intermediate pressure) diffusion bond stage.
  • the final diffusion bonding step of the process may require a slightly longer period of time to ensure full diffusion bonding of the final collapsed gas bubble.
  • the process may be repeated as many times as necessary.
  • the use of the decompression and recompression cycle(s) and an intermediate pressure on helium produced titanium parts is particularly advantageous.
  • the HIP cycle begins with an increase in pressure to a first pressure and an increase in temperature to a first temperature over a first period of time. For example, about 200 MPa (and generally at least about 100 MPa), about 930°C and for about 10-20 minutes (for example 15 minutes). The pressure and temperature are then held for a first soak period.
  • the first soak period in Figure 4 is approximately 60-100 minutes, for example around 60-65 minutes.
  • the first pressure is released and brought back to approximately atmospheric pressure or below, whilst maintaining the first temperature at the elevated level, e.g. 930°C.
  • This first decompressed state is held for sufficiently enough time for the diffusion process to substantially conclude.
  • the first decompressed state hold time i.e. the time that should be allowed for diffusion in the reduced pressure state
  • the pressure is then once again increased to a second pressure, which is substantially the same ( ⁇ 5% differential) as the original first elevated pressure, in this case 200MPa, and held again for a second soak period.
  • the second soak period is either the same time as the first soak period (e.g. 60-65 minutes) or shorter than the first soak period (e.g. approximately 30-40 minutes, for example 30 minutes). It will be appreciated that the choice of second soak period time will depend on a balance between maximising the diffusion bonding and bubble collapse, and also economic considerations. Preferably the second soak period is 30-100 minutes and does not exceed 100 minutes.
  • the second pressure is released and brought back to approximately atmospheric pressure or below, whilst maintaining the first temperature at the elevated level, e.g. 930°C.
  • This second decompressed state is held for sufficiently enough time for the diffusion process to substantially conclude.
  • the second decompressed state hold time i.e. the time that should be allowed for diffusion in the reduced pressure state
  • the pressure is then once again increased to a third pressure, which is substantially the same ( ⁇ 5% differential) as the original first and/or second elevated pressure, in this case 200MPa, and held again for a third soak period.
  • the third soak period is either the same time as the first soak period and/or second soak period (e.g. 60-65 minutes) or shorter than the first and/or second soak period (e.g. approximately 15-30 minutes, for example 20 minutes). It will be appreciated that the choice of third soak period time will depend on a balance between maximising the diffusion bonding and bubble collapse, and also economic considerations.
  • the third soak period is 15-100 minutes and does not exceed 100 minutes.
  • the third soak period may be 15-60 minutes or 15-20 minutes.
  • the third pressure is then reduced, after the bubble has almost collapsed, to a fourth pressure which is an intermediate pressure between the first pressure (and the second and/or third pressure, which both may be substantially the same as the first pressure) and atmospheric pressure or below.
  • This intermediate pressure is a pressure that is able to facilitate diffusion bonding but does not facilitate further reduction in the size of any bubbles.
  • the fourth intermediate pressure is held for approximately 30-120 minutes, for example 60 to 70 minutes. In Figure 4 , the intermediate pressure is approximately 100MPa.
  • the intermediate pressure is then finally reduced to atmospheric pressure or below (e.g. approx. 0MPa), along with the first temperature reduced to room temperature.
  • helium is used since it is a sufficiently small gas atom that diffusion can occur into the titanium used in these examples. It will be apparent that other inert gases may also be used when the process is performed with other metals, provided there is -
  • the first pressure is about 200 MPa
  • the first temperature is about 930°C.
  • the second and/or third pressure is about 200 MPa
  • the intermediate pressure is about 100MPa.
  • the first, second, third and intermediate HIP pressures used are however dependant on the metal. They are all typically in the region of 100 MPa to 300MPa. If pressures below 100 MPa are used then process times would need to be increased accordingly.
  • the first temperature is again dependant on the metal used. In the case of titanium alloys, it should be above 800°C but should normally be less than the beta transus temperature (which is approximately 960°C for Ti-6AI-4V) if an alpha-beta microstructure is required. Higher temperatures can be used provided the microstructural effects are acceptable and the component does not distort.
EP18275113.1A 2018-08-07 2018-08-07 Consolidation de pressage isostatique à chaud de pièces dérivées de poudre Pending EP3608041A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
EP18275113.1A EP3608041A1 (fr) 2018-08-07 2018-08-07 Consolidation de pressage isostatique à chaud de pièces dérivées de poudre
US17/261,431 US11638956B2 (en) 2018-08-07 2019-08-07 Hot isostatic pressing consolidation of powder derived parts
EP19752545.4A EP3833499A1 (fr) 2018-08-07 2019-08-07 Consolidation par compression isostatique à chaud de pièces dérivées de poudre
GB1911290.3A GB2577788B (en) 2018-08-07 2019-08-07 Hot isostatic pressing consolidation of powder derived parts
PCT/GB2019/052211 WO2020030906A1 (fr) 2018-08-07 2019-08-07 Consolidation par compression isostatique à chaud de pièces dérivées de poudre

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EP18275113.1A EP3608041A1 (fr) 2018-08-07 2018-08-07 Consolidation de pressage isostatique à chaud de pièces dérivées de poudre

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EP3608041A1 true EP3608041A1 (fr) 2020-02-12

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Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0580081A1 (fr) * 1992-07-17 1994-01-26 Sumitomo Light Metal Industries Limited Produit preparé à partir d'un composé intermétallique du système Ti-Al ayant une résistance élevée à l'oxydation et à l'usure et procédé pour la fabrication de ce produit
US5397050A (en) * 1993-10-27 1995-03-14 Tosoh Smd, Inc. Method of bonding tungsten titanium sputter targets to titanium plates and target assemblies produced thereby
US5864744A (en) * 1995-06-19 1999-01-26 Commissariat A L'energie Atomique Reactive sintering method of forming intermetallic materials
WO2000015371A1 (fr) * 1998-09-17 2000-03-23 Flow Holdings Gmbh (Sagl) Limited Liability Company Procede et dispositif de compression isostatique a chaud
US6506227B1 (en) * 2001-04-11 2003-01-14 Bohler Edelstahl Gmbh Process for the powder metallurgical production of objects
US20030215539A1 (en) * 2002-05-15 2003-11-20 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd) Hot isostatic pressing apparatus
EP2340905A1 (fr) * 2009-12-16 2011-07-06 Rolls-Royce plc Procédé de fabrication d'un composant

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0580081A1 (fr) * 1992-07-17 1994-01-26 Sumitomo Light Metal Industries Limited Produit preparé à partir d'un composé intermétallique du système Ti-Al ayant une résistance élevée à l'oxydation et à l'usure et procédé pour la fabrication de ce produit
US5397050A (en) * 1993-10-27 1995-03-14 Tosoh Smd, Inc. Method of bonding tungsten titanium sputter targets to titanium plates and target assemblies produced thereby
US5864744A (en) * 1995-06-19 1999-01-26 Commissariat A L'energie Atomique Reactive sintering method of forming intermetallic materials
WO2000015371A1 (fr) * 1998-09-17 2000-03-23 Flow Holdings Gmbh (Sagl) Limited Liability Company Procede et dispositif de compression isostatique a chaud
US6506227B1 (en) * 2001-04-11 2003-01-14 Bohler Edelstahl Gmbh Process for the powder metallurgical production of objects
US20030215539A1 (en) * 2002-05-15 2003-11-20 Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd) Hot isostatic pressing apparatus
EP2340905A1 (fr) * 2009-12-16 2011-07-06 Rolls-Royce plc Procédé de fabrication d'un composant

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