WO2015058534A1 - 一种高温合金粉末的热等静压工艺 - Google Patents

一种高温合金粉末的热等静压工艺 Download PDF

Info

Publication number
WO2015058534A1
WO2015058534A1 PCT/CN2014/079806 CN2014079806W WO2015058534A1 WO 2015058534 A1 WO2015058534 A1 WO 2015058534A1 CN 2014079806 W CN2014079806 W CN 2014079806W WO 2015058534 A1 WO2015058534 A1 WO 2015058534A1
Authority
WO
WIPO (PCT)
Prior art keywords
temperature
isostatic pressing
hot isostatic
alloy
powder
Prior art date
Application number
PCT/CN2014/079806
Other languages
English (en)
French (fr)
Inventor
常立涛
崔玉友
孙文儒
杨锐
Original Assignee
中国科学院金属研究所
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 中国科学院金属研究所 filed Critical 中国科学院金属研究所
Priority to US15/029,900 priority Critical patent/US20160263655A1/en
Publication of WO2015058534A1 publication Critical patent/WO2015058534A1/zh

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B22F1/14—Treatment of metallic powder
    • B22F1/142—Thermal or thermo-mechanical treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • 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
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • 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
    • C22C1/0433—Nickel- or cobalt-based alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C16/00—Alloys based on zirconium
    • 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
    • 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
    • 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
    • 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
    • B22F9/00—Making metallic powder or suspensions thereof
    • B22F9/02—Making metallic powder or suspensions thereof using physical processes
    • B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
    • B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
    • B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
    • B22F2009/0824—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid
    • 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
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps

Definitions

  • the invention belongs to the field of powder metallurgy superalloys, and is specifically a hot isostatic pressing process of a high-temperature alloy powder, which is suitable for preparing a powder metallurgy superalloy component which is directly hot isostatically pressed.
  • Superalloys are the most used materials in aerospace engines.
  • the mechanical properties and temperature-bearing properties of superalloys depend greatly on the amount of strengthening elements in the alloy. Excessive addition of strengthening elements can increase the macroscopic and microsegregation of the alloy, deteriorate the microstructure uniformity and hot workability, or even heat process.
  • the preparation of the alloy powder by the rapid solidification technique can effectively suppress the segregation of elements formed during the solidification of the alloy, so that more strengthening elements can be added to the superalloy without lowering the uniformity of the structure.
  • the high-temperature alloy compacted by using the rapidly solidified powder as a raw material has uniform microstructure and excellent mechanical properties, and is widely used in hot end parts such as aerospace engine turbine disks.
  • the superalloy prepared by the powder metallurgy process also has its own disadvantages, that is, when the powder is consolidated by hot isostatic pressing, a precipitate such as carbide precipitates along the surface of the powder.
  • a precipitate such as carbide precipitates along the surface of the powder.
  • the preferential precipitation of these precipitates results in a lower ductility of the alloy, and the particle boundary of the powder is also a potential source of cracking of the alloy, which affects the reliability of the direct hot isostatically consolidated powder superalloy.
  • the powder blank is deformed by a large deformation amount by extrusion, blank forging, isothermal forging, etc. to change the morphology of the powder original grain boundary to change the precipitation phase distribution thereon;
  • the hot isostatically consolidated powder alloy billet is subjected to long-time high-temperature solution heat treatment to partially dissolve the precipitated phase;
  • An object of the present invention is to provide a hot isostatic pressing process for a superalloy powder which can be directly obtained by hot isostatic pressing to obtain a powder superalloy billet having excellent structural properties.
  • the hot isostatic pressing process conditions are such that the temperature of the hot isostatic pressing is higher than the initial melting temperature of the low melting point phase of the alloy powder, less than 15 ° C above the solidus line of the completely homogenized alloy, and the pressure is greater than or equal to 90 MPa,
  • the heat retention time in the furnace body to the temperature is greater than or equal to 20 minutes, less than or equal to 1 hour; (3) Step (2) After the heat preservation process is completed, the heating is stopped, and the powder wrap is cooled again after the furnace is cooled to the initial melting temperature of the low melting point phase of the alloy powder (generally cooled to below the initial melting temperature of the low melting point phase 10 ⁇ 20°0;
  • the time of re-insulation is greater than or equal to 2 hours to ensure that the low-melting phase formed during the cooling process can be completely dissolved during the heat preservation process.
  • the pressure during the heat preservation process is greater than or equal to 90 MPa, and the heating is stopped after the heat preservation process is completed.
  • the furnace was cooled to room temperature
  • the hot isostatic pressing process of the high-temperature alloy powder is suitable for hot isostatic pressing consolidation of a nickel-iron-based superalloy powder or a nickel-based superalloy powder.
  • the size of the powder obtained by sieving is preferably less than or equal to 105 ⁇ m ; and the size of the powder obtained by sieving is preferably less than or equal to 55 ⁇ m.
  • the hot isostatic pressing process of the high-temperature alloy powder, for GH4169 and its derived alloy powder, the initial melting temperature of the low melting point phase is the Laves phase melting temperature of GH4169 and its derived alloy; for other ⁇ ' phase strengthened nickel-base high temperature
  • the alloy powder, the initial melting temperature of the low melting point phase is the ⁇ / ⁇ ' eutectic temperature.
  • the hot isostatic pressing pressure preferably ranges from 120 to 150 MPa 0
  • the pressure in the heat preservation process is preferably in the range of
  • the hot isostatic pressing process of the high-temperature alloy powder in the step (2), when the temperature of the hot isostatic pressing is higher than the initial melting temperature of the low melting point phase of the alloy powder, and lower than the solid phase line of the completely homogenized alloy , the process can significantly reduce the number of precipitated phases on the boundary of the original particles; when the temperature of the hot isostatic pressing is higher than the solidus line of the completely homogenized alloy, less than 15 ° C above the solidus of the fully homogenized alloy, The process avoids the formation of raw grain boundaries.
  • the process of the present invention is divided into two steps.
  • the hot isostatic pressing temperature range of the first step is: higher than the initial melting temperature of the low melting point phase of the alloy powder and lower than the solid phase line of the completely homogenized alloy by 15 ° C, gas
  • the pressure should be greater than or equal to 90 MPa, and the hold time is greater than or equal to 20 minutes and less than or equal to 1 hour.
  • the heating is stopped to keep the material warmed down to the low melting point phase of the alloy, and the heat preservation process is the second step.
  • the holding time of the second step should be greater than or equal to 2 hours to ensure complete dissolution of the low melting point phase formed during the first step of cooling.
  • the alloy is cooled to room temperature with the furnace pressure.
  • the invention is used for hot isostatic pressing consolidation of rapidly solidified high-temperature alloy powder, and a near-net forming technique can be used to prepare a powder superalloy component with a complicated shape, thereby improving the utilization rate of the alloy material.
  • the invention can be realized on a conventional hot isostatic pressing machine, and the applicable range of the process is hot isostatic pressing and consolidation of nickel-iron-based superalloy powder and nickel-based superalloy powder.
  • the present invention is simple and practical, and can shorten the manufacturing process of the powder superalloy component, thereby reducing the manufacturing cost thereof.
  • Figure 1 (a) - Figure 1 (b) is the microstructure (metallographic photograph) of the powder metallurgy GH4169G alloy prepared by the system A of the present invention; wherein, Figure 1 (a) is magnified by X 100, Figure 1 (b) ) The magnification is X 200.
  • 2(a) to 2(b) are room temperature and 65 CTC tensile fractures (SEM images) of the powder metallurgy GH4169G alloy prepared by the system A of the present invention and heat treated; wherein, Fig. 2(a) is room temperature, Figure 2 (b) is 650 °C.
  • Figure 3 (a) - Figure 3 (b) is the microstructure (metallographic photograph) of the powder metallurgy GH4169G alloy prepared by the system B of the present invention; wherein, Figure 3 (a) is magnified by X 100, Figure 3 (b) ) The magnification is X 200.
  • FIG. 4(a) to 4(b) are room temperature and 65 CTC tensile fractures (SEM images) of the powder metallurgy GH4169G alloy prepared by the system B of the present invention; wherein, FIG. 4(a) is room temperature.
  • Figure 4 (b) is 650 °C.
  • FIG. 5(a) to 5(b) are the microstructure (metallographic photograph) of the ME3 alloy (nickel-based superalloy) prepared by the system C of the present invention; wherein, the magnification of Fig. 5(a) is X 100, The magnification of Fig. 5(b) is X 200.
  • Fig. 6(a) - Fig. 6(b) are the microstructure (metallographic photograph) of the ME3 alloy prepared by the system D of the present invention; wherein, Fig. 6(a) is magnified by X 100, and Fig. 6 (b) is enlarged The multiple is X 200.
  • the present invention is a hot isostatic pressing process which avoids the formation of primary particle boundaries during hot isostatic pressing of a superalloy powder or significantly reduces the number of precipitated phases on the boundaries of the original particles, as follows:
  • a superalloy powder by gas atomization and other methods, and obtain a powder having a size of less than or equal to 155 ⁇ m (preferably less than or equal to 105 ⁇ , preferably less than or equal to 55 ⁇ ) by sieving, and the powder is loaded into a low carbon steel. Or stainless steel wrap, high temperature degassing and sealing.
  • the use of fine powder is to reduce the amount of ceramic inclusions in the powder and reduce the amount of hollow powder; the use of carbon steel or stainless steel is because the material of the jacket is completely solid, has a certain strength and will not be used in the temperature range used in the present invention.
  • high temperature degassing is to remove the gas adsorbed on the surface of the powder to minimize the tendency of the alloy to form heat-induced pores in the subsequent heat treatment.
  • the temperature range of high temperature degassing is 180 ° C ⁇ 50 (TC .
  • the first part of the hot isostatic pressing process conditions is that the temperature is higher than the initial melting temperature of the low melting point phase of the alloy powder (eg: Inconel 718 series alloy (ie corresponding to the domestic grade GH4169 series alloy) Laves phase melting temperature, other
  • the ⁇ / ⁇ ' eutectic temperature of the ⁇ ' phase-enhanced nickel-base superalloy is lower than 15 °C above the solidus line of the fully homogenized alloy, and the pressure is greater than or equal to 90 MPa.
  • the holding time is greater than Or equal to 20 minutes, less than or equal to 1 hour.
  • the temperature selection of the first stage of the process conditions has two reasons in the temperature range in which the liquid phase is formed. The first is that the solubility of elements such as boron and boron in the alloy matrix increases at high temperatures, and precipitates such as carbides and borides are not easily found. The surface of the powder is precipitated. The second part is the partial melting of the surface position of the powder to lose the nucleation of the phase of the carbide and the position at which it can be attached. The third is the liquid phase formation, the powder melting, and the spherical shape of the powder disappears.
  • the holding time of the first step is greater than or equal to 20 minutes and less than or equal to 1 hour for the following reasons: First, in the temperature range of the first step selected in the present invention, the complete compaction of the powder compact takes at least 20 minutes. Second, if the holding time is too long, the grain size of the alloy compact will be too large, which will affect the mechanical properties.
  • the heating is stopped, and the powder wrap is kept warmed below the initial melting temperature of the low melting point phase of the alloy powder, and the heat preservation process is the second step.
  • the holding time of the second step should be greater than or equal to 2 hours to ensure that the low-melting substance formed during the cooling process after the first step can be completely dissolved during the heat preservation process, and the pressurization process may not be pressurized during the heat preservation process, preferably pressurization.
  • the pressure should be greater than or equal to 90 MPa.
  • the reason why the second step must be carried out is that during the first hot isostatic pressing process, a part of the liquid phase is formed inside the sheath, and these liquid phases form a Laves phase during the cooling process after the first step (Inconel 718 and its Derivatized alloys, ie GH4169 and its derived alloys) and ⁇ / ⁇ ' eutectic ( ⁇ '-reinforced nickel-based superalloys), Laves phase and ⁇ / ⁇ ' eutectic are inherently brittle, which is potential in alloy applications The source of the crack must be eliminated.
  • the method of eliminating the Laves phase and the ⁇ / ⁇ ' eutectic is to heat the alloy for a long time below the melting temperature of the Laves phase or the ⁇ / ⁇ ' eutectic.
  • the second step is preferably accomplished in the presence of external pressure because the presence of external pressure can avoid the creation of thermally induced pores in the alloy billet.
  • composition of the alloy is shown in Table 1:
  • the powder of the alloy is prepared by argon gas atomization, and the powder having a size of 105 ⁇ m or less is placed in a stainless steel sheath, and subjected to hot isostatic pressing after vacuum degassing.
  • the following process regime was selected for this alloy (A):
  • the first stage is heated and boosted with the furnace, 1245 ° C / 150 MPa / 0.5 hours, and then cooled with the furnace after completion;
  • the second stage of the insulation process 1110 ° C / 150 MPa / 4 hours, with the furnace cooled to room temperature.
  • the first isothermal temperature of the system is higher than the Laves phase melting temperature (116CTC) but lower than the alloy solidus temperature (126CTC).
  • the microstructure of the alloy prepared by this process is shown in Fig. 1(a) and Fig. 1(b). It can be seen that the alloy structure prepared by the process is uniform and fine, and the precipitated phase on the boundary of the original particles is very less.
  • the alloy prepared by the process is subjected to direct aging treatment to test its room temperature and 65 CTC tensile properties and
  • the room temperature and 65CTC tensile fracture morphology of the heat treated alloy are shown in Fig. 2(a) and Fig. 2(b). It can be seen that the fracture mode is the plastic dimple-dominated fracture, which indicates the powder during hot isostatic pressing. A good combination has been obtained.
  • the alloy used in this embodiment is the same as that of Embodiment 1, except that the temperature of the first stage of the present embodiment is above the solid phase line of the alloy, and more liquid phase is formed during the hot isostatic pressing process, thus the second The temperature of the stage is correspondingly increased to ensure that the Laves phase formed after the first stage of cooling can be sufficiently eliminated.
  • the powder of the alloy is prepared by argon gas atomization, and the powder having a size of 105 ⁇ or less is placed in a stainless steel sheath, and subjected to hot isostatic pressing after vacuum degassing.
  • the following process regime was selected for this alloy ( ⁇ ):
  • the first stage is heated and boosted with the furnace, 1265 ° C / 150 MPa / 0.5 hours, and then cooled with the furnace after completion;
  • the second stage of the insulation process 1140 ° C / 150 MPa / 4 hours, with the furnace cooled to room temperature.
  • the first isothermal temperature of the system is higher than the Laves phase melting temperature (116 CTC) and the alloy solidus temperature (1260 ° C).
  • the microstructure of the alloy prepared by this process is shown in Fig. 3(a) and Fig. 3(b), and it can be seen that the formation of the original particle boundary during the hot isostatic pressing process is completely avoided by the process, and the like is obtained.
  • the microstructure of the shaft is shown in Fig. 3(a) and Fig. 3(b), and it can be seen that the formation of the original particle boundary during the hot isostatic pressing process is completely avoided by the process, and the like is obtained.
  • the microstructure of the shaft is shown in Fig. 3(a) and Fig. 3(b), and it can be seen that the formation of the original particle boundary during the hot isostatic pressing process is completely avoided by the process, and the like is obtained.
  • the microstructure of the shaft is shown in Fig. 3(a) and Fig. 3(b), and it can be seen that the formation of the original particle boundary during the hot isostatic pressing process is completely avoided by the process, and the like is obtained.
  • the microstructure of the shaft is shown in
  • the alloy prepared by the process was subjected to direct aging treatment to test its room temperature and 65 CTC tensile properties and durability at 650 ° C / 760 MPa.
  • the results are shown in Table 2. It can be seen from the table that the tensile properties of the alloy at room temperature and 65 CTC have met the standards of the GH4169 alloy and are much higher than the K4169 alloy. However, since the grain size is slightly larger than that of Process A, the strength level is lower than that of Process A, and the alloy has excellent durability.
  • the room temperature and 65CTC tensile fracture morphology of the alloy after heat treatment are shown in Fig. 4(a) and Fig. 4(b). It can be seen that the tensile fracture mode of the alloy at room temperature and 65CTC is a complete plastic dimple fracture, which indicates that the alloy The powder obtained a good knot. 2.
  • composition of the alloy is shown in Table 3:
  • the powder of the alloy is prepared by argon gas atomization, and the powder having a size of 155 ⁇ or less is placed in a stainless steel sheath, and subjected to hot isostatic pressing after vacuum degassing.
  • the following process regime was selected for this alloy (C):
  • the first stage is heated and boosted with the furnace, 1245 ° C / 150 MPa / l hours, after the completion of the furnace cooling;
  • the second stage of the insulation process 1210 ° C / 150 MPa / 4 hours, with the furnace cooled to room temperature.
  • the first isothermal temperature of the system is higher than the melting temperature of ⁇ / ⁇ ' eutectic (122CTC) but lower than the solidus temperature of the alloy (1260 ⁇ 1265°C).
  • Fig. 5(a) and Fig. 5(b) The microstructure of the alloy prepared by this process is shown in Fig. 5(a) and Fig. 5(b). It can be seen that an alloy having an average grain size of 44 ⁇ m is prepared by the process, and can be observed in the alloy. Primitive particle boundaries, but few precipitated phases are densely precipitated.
  • the alloy prepared by the process is subjected to 1170 ° C / lh / air cooling + 845 ° C / 4 h / air cooling + 760 ° C / 8 h / air cooling heat treatment, the room temperature of the alloy after heat treatment and 76 CTC tensile properties and 76 CTC / 690 MPa long-term performance See Table 4 (Institution C hot isostatic alloy). As can be seen from the table, the alloy prepared by this process has excellent mechanical properties.
  • This embodiment uses the same alloy as in Example 3, the powder and powder degassing system of the same size, except that the first step of the system is completed near the solidus of the alloy, and the specific system (D) is:
  • the first stage is heated and boosted with the furnace, 1265 ° C / 150 MPa / l hours, after the completion of the furnace cooling;
  • the second stage of the insulation process 1210 ° C / 150 MPa / 4 hours, with the furnace cooled to room temperature.
  • the hot isostatic temperature of the first stage of the system is slightly higher than the alloy solidus temperature (1260 ⁇ 1265 °C).
  • the microstructure of the alloy prepared by this process is shown in Fig. 6(a) and Fig. 6(b), and it can be seen that the formation of the original particle boundary during the hot isostatic pressing process is completely avoided by the process, and the like is obtained.
  • the microstructure of the shaft is shown in Fig. 6(a) and Fig. 6(b), and it can be seen that the formation of the original particle boundary during the hot isostatic pressing process is completely avoided by the process, and the like is obtained.
  • the microstructure of the shaft is shown in Fig. 6(a) and Fig. 6(b), and it can be seen that the formation of the original particle boundary during the hot isostatic pressing process is completely avoided by the process, and the like is obtained.
  • the microstructure of the shaft is shown in Fig. 6(a) and Fig. 6(b), and it can be seen that the formation of the original particle boundary during the hot isostatic pressing process is completely avoided by the process, and the like is obtained.
  • the microstructure of the shaft is shown in
  • the process of the present invention can prevent the high temperature alloy powder from forming an original particle boundary during hot isostatic pressing or effectively reducing the number of precipitated phases on the boundary of the original particles, thereby obtaining a dense and equiaxed crystal.
  • An alloy with excellent mechanical properties which can shorten the manufacturing process of powder metallurgy superalloy billets or components. Thereby, the manufacturing cost thereof is lowered, and the process is suitable for hot isostatic pressing of high-temperature alloy powders of all systems.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Manufacturing & Machinery (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Powder Metallurgy (AREA)

Abstract

一种高温合金粉末的热等静压工艺，适用于制备直接热等静压成型的粉末冶金高温合金构件。第一步的热等静压温度应高于合金粉末的低熔点相的初熔温度且低于完全均匀化合金的固相线以上15°C，气体压力应大于或等于90MPa，时间大于或等于20分钟且小于或等于1个小时。第一步完成后进行第二步，停止加热使材料随炉冷却至合金低熔点相初熔温度以下保温，时间应大于或等于2小时，以保证第一步后冷却过程中形成的低熔点相完全溶解，第二步完成后合金随炉保压冷却至室温。采用所述热等静压工艺可以避免高温合金粉末在热等静压过程中形成原始颗粒边界或显著减少原始颗粒边界上析出相的数量，从而得到致密且显微组织为等轴晶的合金。

Description

一种高温合金粉末的热等静压工艺 技术领域
本发明属于粉末冶金高温合金领域， 具体为一种高温合金粉末的热等静压工艺， 适 用于制备直接热等静压成型的粉末冶金高温合金构件。
背景技术
高温合金是航空发动机上用量最大的材料，高温合金的力学性能及承温能力极大地 依赖于合金中强化元素的加入量。 过多地加入强化元素会使合金的宏观及微观偏析加 大， 组织均匀性及热加工性能恶化， 甚至不能热加工。 采用快速凝固技术制备合金粉末 可以有效地抑制合金凝固过程中的形成的元素偏析， 从而可以在不降低其组织均匀性的 情况下向高温合金中加入更多的强化元素。 以快速凝固的粉末为原料压实成型的高温合 金显微组织均匀、力学性能优异，在航空航天发动机涡轮盘等热端部件上有着广泛应用。 但用粉末冶金工艺制备的高温合金也有其自身的缺点， 即通过热等静压固结粉末时， 碳 化物等析出相会沿着粉末表面析出。 这些析出相的择优析出会使合金塑性较低， 同时粉 末的颗粒边界也是合金的潜在的裂纹源从而影响直接热等静压固结的粉末高温合金的 可靠性。
为了改善析出相沿粉末原始颗粒边界析出以提高粉末高温的可靠性，国内外的科研 人员发展了一系列的方法， 这主要包括：
1、 在粉末热等静压固结后， 采用挤压、 开坯锻造、 等温锻造等工艺对粉末坯料进 行大变形量的变形以改变粉末原始颗粒边界的形态以改变其上的析出相分布；
2、 将热等静压固结的粉末合金坯料进行长时间高温固溶热处理， 将析出相部分溶 解；
3、 通过添加其他元素， 如： Hf， 改善原始颗粒边界的相析出。
毫无疑问， 这些方法都增加了粉末高温合金的制造成本。
发明内容
本发明的目的在于提供一种高温合金粉末的热等静压工艺，可以直接通过热等静压 成型获得组织性能优异的粉末高温合金坯料。
本发明的技术方案是：
一种高温合金粉末的热等静压工艺， 具体工艺步骤如下：
( 1 ) 用气体雾化或其他方法制备高温合金粉末， 将粉末进行筛分以得到尺寸小于 或等于 155μηι的粉末， 将筛分出的粉末装入碳钢或不锈钢包套， 高温除气并封焊；
(2) 将 步骤 （1 ) 制备的粉末包套放入热等静压设备中， 以同时升温升压或先升 温后升压的方式达到预定条件后开始热等静压；
热等静压的工艺条件为， 热等静压的温度高于合金粉末的低熔点相的初熔温度， 低 于完全均匀化合金的固相线以上 15°C， 压力大于或等于 90 MPa， 炉体内到温后保温时 间大于或等于 20分钟， 小于或等于 1小时； (3 ) 步骤 （2) 保温过程完成后， 停止加热， 将粉末包套随炉冷却至合金粉末的 低熔点相的初熔温度以下再次进行保温 （一般冷却至低熔点相的初熔温度以下 10~20°0； 再次保温的时间大于或等于 2小时， 以保证冷却过程中形成的低熔点相能够 在保温过程中完全溶解， 保温过程中压力大于或等于 90 MPa, 保温过程完成后停止加 热随炉冷却至室温。
所述的高温合金粉末的热等静压工艺适用于镍铁基高温合金粉末或镍基高温合金 粉末的热等静压固结成型。
所述的高温合金粉末的热等静压工艺， 其步骤 （1 ) 中， 通过筛分得到的粉末尺寸 优选为小于或等于 105μηι; 通过筛分得到的粉末尺寸较佳为小于或等于 55μηι。
所述的高温合金粉末的热等静压工艺， 对于 GH4169及其衍生合金粉末， 低熔点相 的初熔温度为 GH4169及其衍生合金的 Laves相熔化温度； 对于其他 γ'相强化的镍基高 温合金粉末， 低熔点相的初熔温度为 γ/γ'共晶温度。
所述的高温合金粉末的热等静压工艺， 步骤 （2) 中， 热等静压的压力优选范围为 120-150 MPa0
所述的高温合金粉末的热等静压工艺， 步骤 （3 ) 中， 保温过程的压力优选范围为
120-150 MPa0
所述的高温合金粉末的热等静压工艺， 步骤 （2) 中， 当热等静压的温度高于合金 粉末的低熔点相的初熔温度， 低于完全均匀化合金的固相线时， 该工艺能够显著减少原 始颗粒边界上的析出相数量； 当热等静压的温度高于完全均匀化合金的固相线， 低于完 全均匀化合金的固相线以上 15°C时， 该工艺可避免原始颗粒边界形成。
本发明的优点及有益效果是：
1、 本发明工艺分二步， 第一步的热等静压温度范围是： 高于合金粉末的低熔点相 的初熔温度且低于完全均匀化合金的固相线以上 15°C，气体压力应大于或等于 90 MPa， 保持时间大于或等于 20分钟且小于或等于 1个小时。 第一步完成后停止加热使材料随 炉冷却至合金低熔点相初熔温度以下保温， 保温过程为第二步。 第二步的保持时间应大 于或等于 2小时， 以保证第一步后冷却过程中形成的低熔点相完全溶解， 第二步完成后 合金随炉保压冷却至室温。 本发明用于对快速凝固的高温合金粉末的热等静压固结成 型， 结合近净成形技术可以制备形状复杂的粉末高温合金构件， 从而提高合金材料的利 用率。
2、 本发明可以在传统的热等静压机上实现， 该工艺适用范围为镍铁基高温合金粉 末、 镍基高温合金粉末的热等静压固结成型。
3、 本发明简单实用， 可以缩短粉末高温合金构件的制造工序， 从而降低其制造成 本。
附图说明
图 1(a)-图 1(b)为利用本发明制度 A制备的粉末冶金 GH4169G合金的显微组织 （金 相照片)； 其中， 图 1(a)放大倍数为 X 100， 图 1(b)放大倍数为 X 200。 图 2(a)-图 2(b)为利用本发明制度 A制备的并经热处理的粉末冶金 GH4169G合金的 室温及 65CTC拉伸断口 (扫描电镜照片)； 其中， 图 2(a)为室温， 图 2(b)为 650°C。
图 3(a)-图 3(b)为利用本发明制度 B制备的粉末冶金 GH4169G合金的显微组织 （金 相照片） ； 其中， 图 3(a)放大倍数为 X 100， 图 3(b)放大倍数为 X 200。
图 4(a)-图 4(b)为利用本发明制度 B制备的并经热处理的粉末冶金 GH4169G合金的 室温及 65CTC拉伸断口 (扫描电镜照片)； 其中， 图 4(a)为室温， 图 4(b)为 650°C。
图 5(a)-图 5(b) 为利用本发明制度 C制备的 ME3合金（镍基高温合金）的显微组织 (金相照片)； 其中， 图 5(a)放大倍数为 X 100， 图 5(b)放大倍数为 X 200。
图 6(a)-图 6(b) 为利用本发明制度 D制备的 ME3合金的显微组织 （金相照片)； 其 中， 图 6(a)放大倍数为 X 100， 图 6(b)放大倍数为 X 200。
具体实施方式
本发明为可避免高温合金粉末在热等静压过程中形成原始颗粒边界或显著减少原 始颗粒边界上析出相数量的热等静压工艺， 具体如下：
1. 通过气体雾化及其他方法制备高温合金粉末， 通过筛分得到尺寸小于或等于 155μηι (较好为小于或等于 105μηι， 最好为小于或等于 55μηι) 的粉末， 将粉末装入低 碳钢或不锈钢包套， 高温除气后封焊。 使用细粉末是为了降低粉末中的陶瓷夹杂数量及 减少空心粉的数量； 使用碳钢或不锈钢包套是因为在本发明所用的温度范围内， 包套材 料为完全固态、 具有一定强度且不会与粉末发生反应； 高温除气是为了最大限度的除掉 粉末表面吸附的气体， 以降低合金在后续热处理过程中形成热诱导孔洞的倾向， 高温除 气的温度范围为 180°C~50(TC。
2. 将第一步制备的粉末包套放入热等静压设备中，以随炉升温升压或先升温再升压 的方式达到第一段的工艺条件并开始热等静压。 第一段热等静压的工艺条件为， 温度高 于合金粉末的低熔点相的初熔温度 （如： Inconel 718 系列合金 （即对应于国内牌号为 GH4169系列合金） 的 Laves相熔化温度， 其他 γ'相强化的镍基高温合金的 γ/γ'共晶温 度），低于完全均匀化合金的固相线以上 15°C，压力大于或等于 90 MPa，炉体内到温后， 保温时间大于或等于 20分钟， 小于或等于 1小时。 第一段工艺条件的温度选择在有适 量液相形成的温度范围内有两个原因，第一是高温下碳硼等元素在合金基体中溶解度升 高， 碳化物及硼化物等析出相不易在粉末表面析出， 第二是部分粉末表面位置的部分熔 化使碳化物等相的形核失去了可以依附的位置； 第三是液相形成、 粉末熔化， 粉末的球 形形态消失。 第一步的保温时间大于或等于 20分钟、 小于或等于 1小时是基于以下的 原因： 第一， 在本发明选择的第一步的温度范围内， 粉末压坯的完全压实至少需要 20 分钟； 第二， 保温时间过长将使合金压坯晶粒尺寸过大， 影响力学性能。
3. 热等静压第一步完成后，停止加热，将粉末包套随炉冷至合金粉末的低熔点相的 初熔温度以下保温， 保温过程即为第二步。 第二步的保持时间应大于或等于 2小时， 以 保证第一步后冷却过程中形成的低熔点物质能够在保温过程中完全溶解，保温过程中加 压不加压均可， 优选加压， 压力应大于或等于 90 MPa, 第二步完成后停止加热随炉冷 却至室温。 必须有第二步工艺的原因是， 在第一步热等静压过程中包套内部会产生部分 液相， 这些液相在第一步后的冷却过程中会形成 Laves相 （Inconel 718及其衍生合金， 即指 GH4169及其衍生合金） 和 γ/γ'共晶 （γ'强化的镍基高温合金）， Laves相和 γ/γ'共 晶本身具有脆性， 其在合金应用过程中是潜在的裂纹源头， 必须消除。 消除 Laves相和 γ/γ'共晶的方法是将合金在 Laves相或 γ/γ'共晶的熔化温度以下长时间保温。第二步最好 在有外界压力存在的条件下完成，这是因为外部压力的存在可以避免合金坯料中产生热 诱导孔洞。
下面结合附图及实施例对本发明进一步详细说明。
实施例 1
该合金的成分见表 1 :
表 1. GH4169G的合金成分 (wt.% )
Figure imgf000006_0001
本实施例采用氩气雾化制备该合金的粉末，将尺寸在 105微米以下的粉末装入不锈 钢包套中， 真空除气后做热等静压。 针对该合金选择了如下的工艺制度 （A):
第一阶段随炉升温升压， 1245°C/150 MPa /0.5小时， 完成后随炉冷却；
第二阶段保温过程， 1110°C/150 MPa/4小时， 随炉冷至室温。
该制度第一阶段的热等静压温度高于 Laves相熔化温度 （116CTC ) 但低于合金固相 线温度 （126CTC )
通过该工艺制备的合金的显微组织如图 1(a)和图 1(b)所示， 可以看出， 通过该工艺 制备的出的合金组织均匀细小， 且原始颗粒边界上的析出相很少。
对通过该工艺制备的合金进行直接时效处理后测试其室温及 65CTC拉伸性能和
65CTC/760 MPa持久性能， 结果见表 2 (工艺 A)。 从表中可以看出， 合金室温和 65CTC 的拉伸性能已经满足了 GH4169合金的标准， 并且远高于 K4169合金。合金持久性能非 常优异， 特别是 650°C/690 MPa 的持久寿命超过 700小时， 可以与变形 GH4169G合金 相媲美。
经热处理后的合金的室温及 65CTC拉伸断口形貌见图 2(a)和图 2(b), 可以看出， 断 裂方式为塑性韧窝主导的断裂， 这说明热等静压过程中粉末得到了良好的结合。
实施例 2
本实施例使用的合金与实施例 1相同， 不同之处在于， 本实施例的第一阶段的温度 在合金固相线以上，热等静压过程中会有更多液相形成，因而第二阶段的温度相应升高， 以保证第一阶段冷却后形成的 Laves相能被充分消除。
本实施例采用氩气雾化制备该合金的粉末， 将尺寸在 105μηι 以下的粉末装入不锈 钢包套中， 真空除气后做热等静压。 针对该合金选择了如下的工艺制度 （Β ):
第一阶段随炉升温升压， 1265°C/150 MPa/0.5小时， 完成后随炉冷却；
第二阶段保温过程， 1140°C/150 MPa/4小时， 随炉冷至室温。 该制度第一阶段的热等静压温度高于 Laves相熔化温度 （116CTC ) 和合金固相线温 度 （1260°C )。
通过该工艺制备的合金的显微组织如图 3(a)和图 3(b)所示， 可以看出， 通过该工艺 完全避免了热等静压过程中原始颗粒边界的形成， 得到了等轴的显微组织。
对通过该工艺制备的合金进行直接时效处理后测试其室温及 65CTC拉伸性能和 650°C/760 MPa持久性能， 结果见表 2。 从表中可以看出， 合金室温和 65CTC的拉伸性能 已经满足了 GH4169合金的标准， 并且远高于 K4169合金。 但由于晶粒尺寸比工艺 A 制备的稍微粗大， 因而强度水平低于工艺 A， 合金持久性能也非常优异。
经热处理后合金的室温及 65CTC拉伸断口形貌见图 4(a)和图 4(b), 可以看出合金室 温和 65CTC的拉伸断裂方式都是完全的塑性韧窝断裂， 这说明合金粉末得到了很好的结 表 2.经过热处理后的利用本发明制备的粉末冶金 GH4169G合金的力学性能
Figure imgf000007_0001
实施例 3
该合金的成分见表 3:
表 3. 镍钴基合金的成分 （wt.%)
Figure imgf000007_0002
本实施例采用氩气雾化制备该合金的粉末， 将尺寸在 155μηι 以下的粉末装入不锈 钢包套中， 真空除气后做热等静压。 针对该合金选择了如下的工艺制度 （C):
第一阶段随炉升温升压， 1245°C/150 MPa /l小时， 完成后随炉冷却; 第二阶段保温过程， 1210°C/150 MPa/4小时， 随炉冷至室温。
该制度第一阶段的热等静压温度高于 γ/γ'共晶的熔化温度 （122CTC ) 但低于合金固 相线温度 （1260〜1265°C )。
通过该工艺制备的合金的显微组织如图 5(a)和图 5(b)所示， 可以看出， 通过该工艺 制备的出了平均晶粒尺寸为 44μηι的合金， 合金中可观察到原始颗粒边界， 但其上很少 有析出相密集析出。
对通过该工艺制备的合金进行 1170°C/lh/空冷 +845°C/4h/空冷 +760°C/8h/空冷热处 理， 热处理后合金的室温及 76CTC拉伸性能和 76CTC/690 MPa持久性能见表 4 (制度 C 热等静压合金）。 从表中可以看出， 该工艺制备的合金具有优异的力学性能。
表 4 本发明 （制度 3) 制备的镍钴基高温合金的拉伸和持久性能
Figure imgf000008_0001
实施例 4
本实施例使用与实施例 3同样的合金， 同样尺寸的粉末和粉末除气制度， 不同之处 在于该制度的第一步在接近合金的固相线完成， 具体制度 （D) 为：
第一阶段随炉升温升压， 1265°C/150 MPa /l小时， 完成后随炉冷却；
第二阶段保温过程， 1210°C/150 MPa/4小时， 随炉冷至室温。
该制度第一阶段的热等静压温度略高于合金固相线温度 （1260〜1265°C )。
通过该工艺制备的合金的显微组织如图 6(a)和图 6(b)所示， 可以看出， 通过该工艺 完全避免了热等静压过程中原始颗粒边界的形成， 得到了等轴的显微组织。
这些实施例结果表明， 本发明工艺可以避免高温合金粉末在热等静压过程中形成原 始颗粒边界或有效较少原始颗粒边界上析出相的数量， 从而得到致密且显微组织为等轴 晶， 力学性能优异的合金， 该工艺可以缩短粉末冶金高温合金坯料或构件的制造工序。 从而， 降低其制造成本， 该工艺适合所有体系的高温合金粉末的热等静压成型。

Claims

权 利 要 求 书
1、 一种高温合金粉末的热等静压工艺， 其特征在于： 该工艺包括如下步骤：
( 1 ) 用气体雾化或其他方法制备高温合金粉末， 将粉末进行筛分以得到尺寸小于 或等于 155μηι的粉末， 将筛分出的粉末装入碳钢或不锈钢包套， 高温除气并封焊； (2)将步骤 （1 )制备的粉末包套放入热等静压设备中， 以同时升温升压或先升温 后升压的方式达到预定条件后开始热等静压；
热等静压的工艺条件为， 热等静压的温度高于合金粉末的低熔点相的初熔温度， 低 于完全均匀化合金的固相线以上 15°C， 压力大于或等于 90 MPa， 炉体内到温后保温时 间大于或等于 20分钟， 小于或等于 1小时；
(3 ) 步骤 （2)保温过程完成后， 停止加热， 将粉末包套随炉冷却至合金粉末的低 熔点相的初熔温度以下再次进行保温， 保温时间大于或等于 2小时， 以保证冷却过程中 形成的低熔点相能够在保温过程中完全溶解， 保温过程中压力大于或等于 90 MPa, 保 温过程完成后停止加热随炉冷却至室温。
2、 按照权利要求 1所述的高温合金粉末的热等静压工艺， 其特征在于： 该工艺适 用于镍铁基高温合金粉末或镍基高温合金粉末的热等静压固结成型。
3、 按照权利要求 1所述的高温合金粉末的热等静压工艺， 其特征在于： 步骤 （1 ) 中， 通过筛分得到的粉末尺寸为小于或等于 105μηι。
4、 按照权利要求 1所述的高温合金粉末的热等静压工艺， 其特征在于： 步骤 （1 ) 中， 通过筛分得到的粉末尺寸为小于或等于 55μηι。
5、按照权利要求 1所述的高温合金粉末的热等静压工艺，其特征在于：对于 GH4169 及其衍生合金粉末，低熔点相的初熔温度为 GH4169及其衍生合金的 Laves相初熔温度； 对于其他 γ'相强化的镍基高温合金粉末， 低熔点相的初熔温度为 γ/γ'共晶温度。
6、按照权利要求 1所述的温合金粉末的热等静压工艺， 其特征在于： 步骤（2)中， 热等静压的压力范围为 120~150 MPa。
7、 按照权利要求 1所述的高温合金粉末的热等静压工艺， 其特征在于： 步骤 （3 ) 中， 保温过程的压力范围为 120~150 MPa。
8、 按照权利要求 1所述的高温合金粉末的热等静压工艺， 其特征在于： 步骤 （2) 中， 当热等静压的温度高于合金粉末的低熔点相的初熔温度， 并低于完全均匀化合金的 固相线时， 该工艺能够减少原始颗粒边界上的析出相数量。
9、 按照权利要求 1所述的高温合金粉末的热等静压工艺， 其特征在于： 步骤 （2) 中， 当热等静压的温度高于完全均匀化合金的固相线， 低于完全均匀化合金的固相线以 上 15°C时， 该工艺能够消除原始颗粒边界。
PCT/CN2014/079806 2013-10-22 2014-06-13 一种高温合金粉末的热等静压工艺 WO2015058534A1 (zh)

Priority Applications (1)

Application Number Priority Date Filing Date Title
US15/029,900 US20160263655A1 (en) 2013-10-22 2014-06-13 Hot isostatic pressing process for superalloy powder

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CN201310506601.5 2013-10-22
CN201310506601.5A CN103551573B (zh) 2013-10-22 2013-10-22 可避免原始颗粒边界相析出的高温合金粉末热等静压工艺

Publications (1)

Publication Number Publication Date
WO2015058534A1 true WO2015058534A1 (zh) 2015-04-30

Family

ID=50006021

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/CN2014/079806 WO2015058534A1 (zh) 2013-10-22 2014-06-13 一种高温合金粉末的热等静压工艺

Country Status (3)

Country Link
US (1) US20160263655A1 (zh)
CN (1) CN103551573B (zh)
WO (1) WO2015058534A1 (zh)

Families Citing this family (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105274373A (zh) * 2014-06-06 2016-01-27 中国科学院金属研究所 一种γ″相强化的高温合金的粉末冶金制备工艺
CN106032554A (zh) * 2015-03-09 2016-10-19 中南大学 消除粉末冶金高温合金原始颗粒边界和孔洞缺陷的方法
CN105004587B (zh) * 2015-07-09 2017-11-21 中国航空工业集团公司北京航空材料研究院 一种镍基高温合金粉末快速熔凝试样的制备及试验方法
CN105603259A (zh) * 2016-04-11 2016-05-25 西安欧中材料科技有限公司 一种in718合金的粉末冶金方法
CN106378456B (zh) * 2016-11-16 2018-01-19 中国航空工业集团公司北京航空材料研究院 一种用于粉末高温合金构件的快速致密化方法
CN106623941B (zh) * 2016-11-16 2018-06-29 中国航空工业集团公司北京航空材料研究院 一种粉末高温合金构件阶段加热挤压控形方法
CN106868436B (zh) * 2017-01-18 2021-05-14 抚顺特殊钢股份有限公司 一种快径锻联合生产高温合金gh4169细晶棒材制造方法
GB201707895D0 (en) * 2017-05-17 2017-06-28 Rolls Royce Plc Heat treatment method
CN109226767A (zh) * 2018-07-27 2019-01-18 常州大学 制备铝合金中第二相粒子模拟材料的超高压高温合成方法
CN110607464B (zh) * 2019-08-21 2021-06-29 中国科学院金属研究所 一种Ti2AlNb合金粉末的热等静压工艺
CN110643857A (zh) * 2019-09-29 2020-01-03 西安欧中材料科技有限公司 一种无原始颗粒边界的镍基合金粉末及其制备方法
CN110666175B (zh) * 2019-10-31 2022-03-04 西安欧中材料科技有限公司 一种镍基高温合金粉末的热等静压成型方法
FR3105041B1 (fr) * 2019-12-18 2023-04-21 Commissariat Energie Atomique Procédé de fabrication par compression isostatique à chaud d’une pièce outil
CN111702182A (zh) * 2020-08-05 2020-09-25 矿冶科技集团有限公司 一种用于增材制造的低杂质含量合金粉末的制备方法
US11199154B1 (en) 2020-12-04 2021-12-14 Fca Us Llc Nested cylinder head
CN116833409A (zh) * 2021-11-29 2023-10-03 河冶科技股份有限公司 粉末冶金工艺制备沉淀硬化高速钢的方法
CN114672680B (zh) * 2022-03-07 2023-04-07 中南大学 一种增材制造镍基高温合金分步热等静压方法
CN114855047B (zh) * 2022-04-08 2022-11-18 大连理工大学 一种Laves相可控的CrxMoNbWTi难熔高熵合金及其制备方法
CN115846689B (zh) * 2022-11-15 2023-08-18 哈尔滨工业大学（威海） 一种激光粉末床熔融gh3230合金的固溶处理方法及gh3230合金
CN116460407A (zh) * 2023-04-21 2023-07-21 西安嘉业航空科技有限公司 铜合金与合金钢工件及其热等静压扩散连接方法
CN116809915A (zh) * 2023-07-03 2023-09-29 中国航发北京航空材料研究院 粉末高温合金痕量元素微区均匀标准物质的制备方法
CN118080856B (zh) * 2024-04-28 2024-06-21 合肥工业大学 一种铝基复合材料y形件原位成形方法

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62214102A (ja) * 1986-03-14 1987-09-19 Kobe Steel Ltd Ｎｉ基耐食合金焼結部分を有する構造物の製造方法
JPH10152704A (ja) * 1996-11-21 1998-06-09 Daido Steel Co Ltd 高融点金属間化合物粉末焼結体の製造方法
US20070092394A1 (en) * 2005-10-26 2007-04-26 General Electric Company Supersolvus hot isostatic pressing and ring rolling of hollow powder forms
CN102251131A (zh) * 2011-06-30 2011-11-23 北京科技大学 一种制备注射成形镍基ods合金的方法
CN102409276A (zh) * 2011-11-16 2012-04-11 钢铁研究总院 一种消除粉末冶金高温合金中原始颗粒边界的方法
CN102672174A (zh) * 2012-05-15 2012-09-19 华中科技大学 一种采用热等静压成型工艺制作整体环形机匣件的方法
CN103551273A (zh) * 2013-10-31 2014-02-05 扬州力士德机械制造有限公司 一种水帘水旋喷漆室

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61159539A (ja) * 1984-12-29 1986-07-19 Toshiba Corp 形状記憶合金の製造法
AT392929B (de) * 1989-03-06 1991-07-10 Boehler Gmbh Verfahren zur pulvermetallurgischen herstellung von werkstuecken oder werkzeugen
JP3673136B2 (ja) * 1999-04-01 2005-07-20 株式会社デンソー 高炭素−高合金系鋼の冷温間加工品の熱処理方法
FR2865671B1 (fr) * 2004-01-30 2007-03-16 Commissariat Energie Atomique Nanopoudre ceramique apte au frittage et son procede de synthese
CN102392147B (zh) * 2011-11-16 2012-11-14 钢铁研究总院 超细晶镍基粉末高温合金的制备方法
CN102676881A (zh) * 2012-06-12 2012-09-19 钢铁研究总院 消除原始颗粒边界的镍基粉末冶金高温合金

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62214102A (ja) * 1986-03-14 1987-09-19 Kobe Steel Ltd Ｎｉ基耐食合金焼結部分を有する構造物の製造方法
JPH10152704A (ja) * 1996-11-21 1998-06-09 Daido Steel Co Ltd 高融点金属間化合物粉末焼結体の製造方法
US20070092394A1 (en) * 2005-10-26 2007-04-26 General Electric Company Supersolvus hot isostatic pressing and ring rolling of hollow powder forms
CN102251131A (zh) * 2011-06-30 2011-11-23 北京科技大学 一种制备注射成形镍基ods合金的方法
CN102409276A (zh) * 2011-11-16 2012-04-11 钢铁研究总院 一种消除粉末冶金高温合金中原始颗粒边界的方法
CN102672174A (zh) * 2012-05-15 2012-09-19 华中科技大学 一种采用热等静压成型工艺制作整体环形机匣件的方法
CN103551273A (zh) * 2013-10-31 2014-02-05 扬州力士德机械制造有限公司 一种水帘水旋喷漆室

Also Published As

Publication number Publication date
CN103551573B (zh) 2015-06-17
US20160263655A1 (en) 2016-09-15
CN103551573A (zh) 2014-02-05

Similar Documents

Publication Publication Date Title
WO2015058534A1 (zh) 一种高温合金粉末的热等静压工艺
JP3074465B2 (ja) ニッケル基超合金鍛造用プリフォームの製造方法
US3920489A (en) Method of making superalloy bodies
WO2021031231A1 (zh) 一种Ti 2AlNb合金粉末的热等静压工艺
JP5652730B1 (ja) Ｎｉ基超耐熱合金及びその製造方法
CN112322933B (zh) 一种高性能近α高温钛合金及其粉末冶金制备方法
TW201908499A (zh) 高溫零件及其製造方法
CN103498065B (zh) 一种TiAl合金晶粒细化方法
CN103382536A (zh) 一种高强度且组织稳定的第四代单晶高温合金及制备方法
CN109897991B (zh) 一种高熵晶界修饰的纳米晶合金粉末及其制备方法
Zhou et al. Enhanced tensile properties in a Mg-6Gd-3Y-0.5 Zr alloy due to hot isostatic pressing (HIP)
CN108546863A (zh) 一种多主元高温合金及其制备方法
JP4994843B2 (ja) ニッケル含有合金、その製造方法、およびそれから得られる物品
CN112828289A (zh) 一种减少热裂的沉淀强化镍基高温合金激光粉床熔融成形方法
CN103436828A (zh) 一种大尺寸镁合金铸锭的均匀化热处理工艺
TW201103999A (en) Method for manufacturing nickel alloy target
Sheng et al. Influence of the substrate orientation on the isothermal solidification during TLP bonding single crystal superalloys
CN105274373A (zh) 一种γ″相强化的高温合金的粉末冶金制备工艺
US5015305A (en) High temperature hydrogenation of gamma titanium aluminide
CN115722671A (zh) 一种gh4099镍基合金构件及其粉末冶金成形工艺
CN104028734B (zh) 高铌钛铝合金低偏析及组织均匀细化的方法
JP6185347B2 (ja) Ｎｉ基超耐熱合金の分塊用中間素材及びその製造方法、Ｎｉ基超耐熱合金の製造方法
Xun et al. Ti2Ni and TiNi3 intermetallic compounds to prepare dense TiNi alloy with enhanced recovery property
CN116445763B (zh) 一种室温塑性钛铝铌系合金及其制备方法
CN113732281B (zh) 一种适用于3D打印的弹性医用β钛合金粉末及其制备方法和应用

Legal Events

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

Ref document number: 14855474

Country of ref document: EP

Kind code of ref document: A1

WWE Wipo information: entry into national phase

Ref document number: 15029900

Country of ref document: US

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 14855474

Country of ref document: EP

Kind code of ref document: A1