CN103551573A - Previous particle boundary precipitation preventable high-temperature alloy powder hot isostatic pressing process - Google Patents
Previous particle boundary precipitation preventable high-temperature alloy powder hot isostatic pressing process Download PDFInfo
- Publication number
- CN103551573A CN103551573A CN201310506601.5A CN201310506601A CN103551573A CN 103551573 A CN103551573 A CN 103551573A CN 201310506601 A CN201310506601 A CN 201310506601A CN 103551573 A CN103551573 A CN 103551573A
- Authority
- CN
- China
- Prior art keywords
- powder
- temperature
- alloy
- equal
- phase
- Prior art date
- Legal status (The legal status 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 status listed.)
- Granted
Links
Images
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
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
The invention belongs to the field of powder metallurgy high-temperature alloy field, particularly relates to a previous particle boundary precipitation preventable high-temperature alloy powder hot isostatic pressing process and is applicable to preparation of powder metallurgy high-temperature alloy members formed through hot isostatic pressing directly. The process comprises that step one, the hot isostatic pressing temperature is higher than the initial melting temperature of low-melting-point phases of alloy powder and lower than 15 DEG C above the solidus of complete homogenization of alloy, the gas pressure is larger than or equal to 90 MPa, and time is longer than or equal to 20 minutes and shorter than or equal to 2 hours; step two, heating is stopped to subject materials to furnace cooling till the temperature of the materials is below the initial melting temperature of the low-melting-point phases to perform thermal insulation for 2 hours or longer after the first step is completed, so that the low-melting-point phases formed during cooling after the first step can be dissolved completely; the alloy is subjected to pressure maintaining and cooling with furnace till the room temperature after the second step is completed. By means of the process, precipitated phase such as carbides can be prevented from precipitating out along the powder previous particle boundaries, and accordingly, the compact alloy with microscopic structures as equiaxed grains is obtained.
Description
Technical field
The invention belongs to powder metallurgy high-temperature alloy field, be specially a kind of superalloy powder heat and other static pressuring processes of avoiding the precipitated phases such as carbide to separate out along powder primary granule border, be applicable to prepare the powder metallurgy high-temperature alloy member of direct heat isostatic compaction.
Background technology
High temperature alloy is the material of consumption maximum in aero-engine, the mechanical property of high temperature alloy and hold the addition that warm ability greatly depends on intensified element in alloy.Add too much intensified element can make the macroscopic view of alloy and microsegregation strengthen, structural homogenity and hot-working character worsen, even can not hot-working.Adopt flash set technology to prepare the element segregation that alloy powder can suppress the formation in alloy graining process effectively, thereby can in the situation that not reducing its structural homogenity, in high temperature alloy, add more intensified element.High temperature alloy microscopic structure that the powder of rapid solidification of take is raw material compaction moulding is even, mechanical property is excellent, extensive application on the hot-end components such as Aero-Space engine turbine disk.But the high temperature alloy of preparing with powder metallurgical technique also has the shortcoming of himself, during by high temperature insostatic pressing (HIP) consolidated powder, the precipitated phases such as carbide can be separated out along powder surface.Preferentially separating out of these precipitated phases can make alloy plasticity lower, thereby the potential formation of crack that the granule boundary of while powder is also alloy affects the reliability of the fixed powder metallurgy superalloy of direct high temperature insostatic pressing (HIP).
In order to improve precipitated phase, separate out to improve the reliability of powder high temperature along powder primary granule border, scientific research personnel both domestic and external has been developed a series of method, and this mainly comprises:
1. after powder high temperature insostatic pressing (HIP) is fixed, the distortion that adopts the techniques such as extruding, cogging forging, isothermal forging powder blank to be carried out to aximal deformation value distributes with the precipitated phase changing on it to change the form on powder primary granule border;
2. the fixed powder metallurgy blank of high temperature insostatic pressing (HIP) is carried out to long-time high temperature solid solution heat treatment, precipitated phase is partly dissolved;
3. pass through to add other elements, as: Hf, improves separating out mutually of primary granule border.
Certainly, these methods have all increased the manufacturing cost of powder metallurgy superalloy.
Summary of the invention
The object of the present invention is to provide a kind of superalloy powder heat and other static pressuring processes of avoiding the precipitated phases such as carbide to separate out along powder primary granule border, can directly by hip moulding, obtain the powder metallurgy superalloy blank that structure property is good.
Technical scheme of the present invention is:
The superalloy powder heat and other static pressuring processes that the precipitated phases such as carbide are separated out along powder primary granule borderline phase, concrete technology step is as follows:
(1). with gas atomization or additive method, prepare superalloy powder, powder is sieved to obtain the powder that size is less than or equal to 155 microns, pack the powder sieving out into carbon steel or stainless steel jacket, high-temperature degassing soldering and sealing;
(2). powder jacket prepared by the first step is put into hot isostatic apparatus, with while increasing temperature and pressure or the mode of boosting afterwards of first heating up start high temperature insostatic pressing (HIP) after reaching predetermined condition;
The process conditions of first step high temperature insostatic pressing (HIP) are, the temperature of high temperature insostatic pressing (HIP) is higher than the initial melting temperature of the low melting point phase of alloy powder, lower than above 15 degrees Celsius of the solidus of complete homogenising alloy, pressure is more than or equal to 90MPa, in body of heater, to the rear temperature retention time of temperature, be more than or equal to 20 minutes, be less than or equal to 1 hour;
(3). after the first step completes, stop heating, the initial melting temperature that powder jacket is cooled to the furnace to the low melting point phase of alloy powder is incubated below, and insulating process is second step;
The retention time of second step is more than or equal to 2 hours, with the low melting point that guarantees to form in cooling procedure after the first step, can in insulating process, dissolve completely mutually, and pressure is more than or equal to 90MPa, stops heating and cool to room temperature with the furnace after second step completes.
The superalloy powder heat and other static pressuring processes that the precipitated phases such as the described carbide avoided are separated out along powder primary granule borderline phase, this technique is applicable to the fixed moulding of high temperature insostatic pressing (HIP) of ferronickel based high-temperature alloy powder or Ni-base Superalloy Powder.
The superalloy powder heat and other static pressuring processes that the precipitated phases such as the described carbide avoided are separated out along powder primary granule borderline phase, in step (1), obtains being preferably dimensioned to be by screening and is less than or equal to 105 microns.
The superalloy powder heat and other static pressuring processes that the precipitated phases such as the described carbide avoided are separated out along powder primary granule borderline phase, in step (1), obtains size by screening and is preferably and is less than or equal to 55 microns.
The superalloy powder heat and other static pressuring processes that the precipitated phases such as the described carbide avoided are separated out along powder primary granule borderline phase, for GH4169 and derivative alloy powder thereof, the initial melting temperature of low melting point phase is the Laves phase fusion temperature of GH4169 and derivative alloy thereof; The Ni-base Superalloy Powder of strengthening mutually for other γ ', the initial melting temperature of low melting point phase is γ/γ ' eutectic temperature.
The superalloy powder heat and other static pressuring processes that the precipitated phases such as the described carbide avoided are separated out along powder primary granule borderline phase, in step (2), the pressure preferable range of high temperature insostatic pressing (HIP) is 120～150MPa.
The superalloy powder heat and other static pressuring processes that the precipitated phases such as the described carbide avoided are separated out along powder primary granule borderline phase, in step (3), the pressure preferable range of insulating process is 120～150MPa.
Advantage of the present invention and beneficial effect are:
1, technique of the present invention is divided two steps, the hip temperature scope of the first step is: higher than the initial melting temperature of the low melting point phase of alloy powder and lower than above 15 degrees Celsius of the solidus of homogenising alloy completely, gas pressure should be more than or equal to 90MPa, and the retention time is more than or equal to 20 minutes and is less than or equal to 1 hour.After the first step completes, stop heating and make material cool to alloy low melting point phase initial melting temperature with the furnace to be incubated below, insulating process is second step.The retention time of second step should be more than or equal to 2 hours, with the low melting point that guarantees to form in cooling procedure after the first step, dissolves completely mutually, and after second step completes, alloy is cooled to room temperature with stove pressurize.The present invention, for to the fixed moulding of the high temperature insostatic pressing (HIP) of the superalloy powder of rapid solidification, can prepare complex-shaped powder metallurgy superalloy member in conjunction with near-net-shape technology, thereby improves the utilization rate of alloy material.
2, the present invention can realize on traditional hot isostatic press, and this technique scope of application is the fixed moulding of high temperature insostatic pressing (HIP) of ferronickel based high-temperature alloy powder, Ni-base Superalloy Powder.
3, the present invention is simple and practical, can shorten the manufacturing process of powder metallurgy superalloy member, thereby reduces its manufacturing cost.
Accompanying drawing explanation
Fig. 1 (a)-Fig. 1 (b) is for utilizing the microscopic structure (metallograph) of powder metallurgy GH4169G alloy prepared by system A of the present invention; Wherein, Fig. 1 (a) multiplication factor is that * 100, Fig. 1 (b) multiplication factor is * 200.
Fig. 2 (a)-Fig. 2 (b) is prepared by system A of the present invention and through room temperature and 650 ℃ of stretching fractures (stereoscan photograph) of heat treated powder metallurgy GH4169G alloy for utilizing; Wherein, Fig. 2 (a) is room temperature, and Fig. 2 (b) is 650 ℃.
Fig. 3 (a)-Fig. 3 (b) is for utilizing the microscopic structure (metallograph) of powder metallurgy GH4169G alloy prepared by system B of the present invention; Wherein, Fig. 3 (a) multiplication factor is that * 100, Fig. 3 (b) multiplication factor is * 200.
Fig. 4 (a)-Fig. 4 (b) is prepared by system B of the present invention and through room temperature and 650 ℃ of stretching fractures (stereoscan photograph) of heat treated powder metallurgy GH4169G alloy for utilizing; Wherein, Fig. 4 (a) is room temperature, and Fig. 4 (b) is 650 ℃.
The specific embodiment
The superalloy powder heat and other static pressuring processes of the present invention for avoiding the precipitated phases such as carbide to separate out along powder primary granule borderline phase, specific as follows:
By gas atomization and other party legal system thereof for superalloy powder, by screening, obtaining size is less than or equal to 155 microns and (is preferably less than or equal to 105 microns, be preferably and be less than or equal to 55 microns) powder, pack powder into low-carbon (LC) steel or stainless steel jacket, soldering and sealing after high-temperature degassing.Using fine powder is in order to reduce the ceramic inclusions quantity in powder and to reduce the quantity of hollow powder; Using carbon steel or stainless steel jacket is because in the present invention's temperature range used, sheath material for completely solid-state, there is some strength and can not react with powder; High-temperature degassing is in order to remove to greatest extent the gas of powder surface absorption, forms the tendency of thermal induction hole to reduce alloy in follow-up heat treatment process, and the temperature range of high-temperature degassing is 180 degrees Celsius to 500 degrees Celsius.
2. the powder jacket of being prepared by the first step is put into hot isostatic apparatus, with stove increasing temperature and pressure or the mode boost again that first heats up reach the process conditions of first paragraph and start high temperature insostatic pressing (HIP).The process conditions of first paragraph high temperature insostatic pressing (HIP) are, temperature is higher than initial melting temperature (as: the Laves phase fusion temperature of GH4169 series alloy of the low melting point phase of alloy powder, γ/γ ' eutectic temperature of the nickel base superalloy that other γ ' strengthen mutually), lower than above 15 degrees Celsius of the solidus of complete homogenising alloy, pressure is more than or equal to 90MPa, in body of heater, after temperature, temperature retention time is more than or equal to 20 minutes, is less than or equal to 1 hour.The temperature of first paragraph process conditions is chosen in the temperature range that appropriate liquid phase forms two reasons, the firstth, under high temperature, the element such as carbon solubility in alloy substrate raises, carbide etc. are difficult for separating out at powder surface mutually, and the secondth, the partial melting of part powder surface position makes the forming core of the phases such as carbide lose the position that can depend on.The temperature retention time of the first step is more than or equal to 20 minutes, is less than or equal to 1 hour is the reason based on following: the first, and in the temperature range of the first step of selecting in the present invention, the completely densified of powder compact at least needs 20 minutes; The second, the long alloy pressed compact crystallite dimension that will make of temperature retention time is excessive, affects the mechanical properties.
3. after the high temperature insostatic pressing (HIP) first step completes, stop heating, the initial melting temperature that powder jacket is chilled to the low melting point phase of alloy powder with stove is incubated below, and insulating process is second step.The retention time of second step should be more than or equal to 2 hours, with the segregation that guarantees to form in cooling procedure after the first step, can in insulating process, dissolve completely mutually, and pressure should be more than or equal to 90MPa, stops heating and cool to room temperature with the furnace after second step completes.Must there is the reason of second step technique to be, the inner meeting of jacket generating portion liquid phase in first step hot isostatic pressing, in the cooling procedure of these liquid phases after the first step, can form Laves phase (GH4169 and derivative alloy thereof) and γ/γ ' eutectic (nickel base superalloy of γ ' strengthening), Laves phase and γ/γ ' eutectic itself enbrittle, it is potential crackle source in Alloyapplication process, must eliminate.The method of eliminating Laves phase and γ/γ ' eutectic is by alloy insulation for a long time below the fusion temperature of Laves phase or γ/γ ' eutectic.Second step must complete under the condition that has ambient pressure to exist, rather than in pressure less high temperature stove, completes after alloy high temperature insostatic pressing (HIP) completes, and this is because the existence of external pressure can avoid producing in alloy blank thermal induction hole.
Below in conjunction with drawings and Examples, the present invention is described in more detail.
Embodiment 1
The composition of this alloy is in Table 1:
The alloying component of table 1.GH4169G
| Cr | Mo | Al | Ti | Nb | C | B | P | Ni | Fe |
| 19.3 | 2.98 | 0.5 | 1.04 | 4.94 | 0.031 | 0.008 | 0.023 | 53.5 | Surplus |
The present embodiment adopts argon gas atomization to prepare the powder of this alloy, and size is packed in stainless steel jacket at the powder below 105 microns, does high temperature insostatic pressing (HIP) after vacuum degassing.For this alloy, selected following process system (A):
First stage is with stove increasing temperature and pressure, 1245 ℃/150MPa/0.5 hour, cooling with stove after completing;
Second stage insulating process,, is chilled to room temperature with stove by 1110 ℃/150MPa/4 hour.
The hip temperature of this system first stage is higher than Laves phase fusion temperature (1210 ℃) but lower than alloy solidus temperature (1260 ℃)
The microscopic structure of the alloy of preparing by this technique, as shown in Fig. 1 (a) and Fig. 1 (b), can find out, the alloy structure going out of preparing by this technique is evenly tiny, and precipitated phase is evenly distributed, and almost can't see the pattern of starting powder.
The alloy of preparing by this technique is carried out after direct aging is processed testing its room temperature and 650 ℃ of tensile properties and 650 ℃/760MPa enduring quality, the results are shown in Table 2(technique A).As can be seen from the table, the tensile property of Alloy At Room Temperature and 650 ℃ has met the standard of GH4169 alloy, and far above K4169 alloy.Alloy enduring quality is very excellent, particularly surpasses 700 hours the creep rupture life of 650 ℃/690MPa, can match in excellence or beauty with distortion GH4169G alloy phase.
The room temperature of alloy after heat treatment and 650 ℃ of stretching fracture patterns are shown in Fig. 2 (a) and Fig. 2 (b), can find out, fracture mode is the leading fracture of plasticity dimple, and in this explanation hot isostatic pressing, powder has obtained good combination.
Embodiment 2
Difference from Example 1 is, the temperature of the first stage of the present embodiment is more than alloy solidus, in hot isostatic pressing, have more liquid phases and form, thereby the corresponding rising of the temperature of second stage, to guarantee that the Laves of cooling rear formation of first stage is on good terms, fully eliminated.
The present embodiment adopts argon gas atomization to prepare the powder of this alloy, and size is packed in stainless steel jacket at the powder below 105 microns, does high temperature insostatic pressing (HIP) after vacuum degassing.For this alloy, selected following process system (B):
First stage is with stove increasing temperature and pressure, 1265 ℃/150MPa/0.5 hour, cooling with stove after completing;
Second stage insulating process,, is chilled to room temperature with stove by 1140 ℃/150MPa/4 hour.
The hip temperature of this system first stage is higher than Laves phase fusion temperature (1210 ℃) and alloy solidus temperature (1260 ℃).
The microscopic structure of the alloy of preparing by this technique, as shown in Fig. 3 (a) and Fig. 3 (b), can find out, this technique has obtained waiting the microscopic structure of axle completely, and the border carbonization of powder primary granule is separated out and avoided completely mutually.
The alloy of preparing by this technique is carried out after direct aging is processed testing its room temperature and 650 ℃ of tensile properties and 650 ℃/760MPa enduring quality, the results are shown in Table 2(technique B).As can be seen from the table, the tensile property of Alloy At Room Temperature and 650 ℃ has met the standard of GH4169 alloy, and far above K4169 alloy.But due to crystallite dimension than technique A, prepare thick a little, thereby strength level is lower than technique A, alloy enduring quality is also very excellent.
After heat treatment the room temperature of alloy and 650 ℃ of stretching fracture patterns are shown in Fig. 4 (a) and Fig. 4 (b), and the tension failure mode that can find out Alloy At Room Temperature and 650 ℃ is all plasticity dimple fracture completely, and this surface alloy powder has obtained good combination.
The mechanical property of utilizing prepared by the present invention powder metallurgy GH4169G alloy of table 2. after Overheating Treatment
Embodiment result shows, technique of the present invention can avoid the precipitated phases such as carbide to separate out along powder primary granule border, thereby obtain densification and microscopic structure, it is equiax crystal, during stretcher strain with plasticity dimple fracture, the alloy that mechanical property can compare favourably with the wrought alloy performance of same sample ingredient, reduces its manufacturing cost thereby this technique can shorten the manufacturing process of powder metallurgy high-temperature alloy member.Except GH4169G alloy, other ferronickel based high-temperature alloy powder, Ni-base Superalloy Powder are all applicable to using superalloy powder heat and other static pressuring processes of the present invention, to avoid primary granule borderline phase to separate out, reason is that carbon is the intercrystalline strengthening element that all high temperature alloys that is organized as polycrystalline must add.As long as prepare these alloys with powder metallurgical technique, all can there is the problem that the precipitated phases such as carbide are separated out along powder border in them so, and this has report in a large amount of documents.And the temperature of the first step of the present invention is to occur a small amount of liquid phase in powder, occur that liquid phase can make separating out of carbide lose and depend on, under high temperature, alloy also improves greatly to the solvability of carbon, this has also reduced the quantity of possibility carbide precipitate, and alloy partial melting also can make powder lose original pattern simultaneously.And the result of embodiment has also been confirmed these completely.
The low melting point forming when just the nickel base superalloy of γ ' strengthening solidifies is organized as γ/γ ' eutectic, and ferronickel based high-temperature alloy to form low melting point while solidifying be Laves phase mutually.Thereby technique of the present invention can directly apply to the hip moulding of ferronickel based high-temperature alloy powder.And for the nickel base superalloy of γ ' strengthening, only need slightly adjust characteristic temperature, the first step also should be in the temperature that has a small amount of liquid phase to form, and second step should be below the initial melting temperature of γ/γ ' eutectic.
Claims (7)
1. the superalloy powder heat and other static pressuring processes that can avoid the precipitated phases such as carbide to separate out along powder primary granule borderline phase, is characterized in that, concrete technology step is as follows:
(1). with gas atomization or additive method, prepare superalloy powder, powder is sieved to obtain the powder that size is less than or equal to 155 microns, pack the powder sieving out into carbon steel or stainless steel jacket, high-temperature degassing soldering and sealing;
(2). powder jacket prepared by the first step is put into hot isostatic apparatus, with while increasing temperature and pressure or the mode of boosting afterwards of first heating up start high temperature insostatic pressing (HIP) after reaching predetermined condition;
The process conditions of first step high temperature insostatic pressing (HIP) are, the temperature of high temperature insostatic pressing (HIP) is higher than the initial melting temperature of the low melting point phase of alloy powder, lower than above 15 degrees Celsius of the solidus of complete homogenising alloy, pressure is more than or equal to 90MPa, in body of heater, to the rear temperature retention time of temperature, be more than or equal to 20 minutes, be less than or equal to 1 hour;
(3). after the first step completes, stop heating, the initial melting temperature that powder jacket is cooled to the furnace to the low melting point phase of alloy powder is incubated below, and insulating process is second step;
The retention time of second step is more than or equal to 2 hours, with the low melting point that guarantees to form in cooling procedure after the first step, can in insulating process, dissolve completely mutually, and pressure is more than or equal to 90MPa, stops heating and cool to room temperature with the furnace after second step completes.
2. according to the superalloy powder heat and other static pressuring processes of avoiding the precipitated phases such as carbide to separate out along powder primary granule borderline phase claimed in claim 1, it is characterized in that, this technique is applicable to the fixed moulding of high temperature insostatic pressing (HIP) of ferronickel based high-temperature alloy powder or Ni-base Superalloy Powder.
3. according to the superalloy powder heat and other static pressuring processes of avoiding the precipitated phases such as carbide to separate out along powder primary granule borderline phase claimed in claim 1, it is characterized in that, in step (1), by screening, obtain being preferably dimensioned to be and be less than or equal to 105 microns.
4. according to the superalloy powder heat and other static pressuring processes of avoiding the precipitated phases such as carbide to separate out along powder primary granule borderline phase claimed in claim 1, it is characterized in that, in step (1), by screening, obtain size and be preferably and be less than or equal to 55 microns.
5. according to the superalloy powder heat and other static pressuring processes of avoiding the precipitated phases such as carbide to separate out along powder primary granule borderline phase claimed in claim 1, it is characterized in that, for GH4169 and derivative alloy powder thereof, the initial melting temperature of low melting point phase is the Laves phase fusion temperature of GH4169 and derivative alloy thereof; The Ni-base Superalloy Powder of strengthening mutually for other γ ', the initial melting temperature of low melting point phase is γ/γ ' eutectic temperature.
6. according to the superalloy powder heat and other static pressuring processes of avoiding the precipitated phases such as carbide to separate out along powder primary granule borderline phase claimed in claim 1, it is characterized in that, in step (2), the pressure preferable range of high temperature insostatic pressing (HIP) is 120～150MPa.
7. according to the superalloy powder heat and other static pressuring processes of avoiding the precipitated phases such as carbide to separate out along powder primary granule borderline phase claimed in claim 1, it is characterized in that, in step (3), the pressure preferable range of insulating process is 120～150MPa.
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310506601.5A CN103551573B (en) | 2013-10-22 | 2013-10-22 | Previous particle boundary precipitation preventable high-temperature alloy powder hot isostatic pressing process |
| US15/029,900 US20160263655A1 (en) | 2013-10-22 | 2014-06-13 | Hot isostatic pressing process for superalloy powder |
| PCT/CN2014/079806 WO2015058534A1 (en) | 2013-10-22 | 2014-06-13 | Hot isostatic pressing process for high-temperature alloy powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310506601.5A CN103551573B (en) | 2013-10-22 | 2013-10-22 | Previous particle boundary precipitation preventable high-temperature alloy powder hot isostatic pressing process |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103551573A true CN103551573A (en) | 2014-02-05 |
| CN103551573B CN103551573B (en) | 2015-06-17 |
Family
ID=50006021
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201310506601.5A Expired - Fee Related CN103551573B (en) | 2013-10-22 | 2013-10-22 | Previous particle boundary precipitation preventable high-temperature alloy powder hot isostatic pressing process |
Country Status (3)
| Country | Link |
|---|---|
| US (1) | US20160263655A1 (en) |
| CN (1) | CN103551573B (en) |
| WO (1) | WO2015058534A1 (en) |
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105004587A (en) * | 2015-07-09 | 2015-10-28 | 中国航空工业集团公司北京航空材料研究院 | Preparation and test method of nickel-based high temperature alloy powder rapid melting and solidifying sample |
| CN105274373A (en) * | 2014-06-06 | 2016-01-27 | 中国科学院金属研究所 | Powder metallurgy preparation technology of gamma'' phase reinforced high temperature alloy |
| CN105603259A (en) * | 2016-04-11 | 2016-05-25 | 西安欧中材料科技有限公司 | Powder metallurgical method for IN718 alloy |
| WO2016141872A1 (en) * | 2015-03-09 | 2016-09-15 | 中南大学 | Method for removing prior particle boundary and hole defect of powder metallurgy high-temperature alloy |
| CN106378456A (en) * | 2016-11-16 | 2017-02-08 | 中国航空工业集团公司北京航空材料研究院 | Rapid densifying method for powder high-temperature alloy component |
| CN106623941A (en) * | 2016-11-16 | 2017-05-10 | 中国航空工业集团公司北京航空材料研究院 | Staged heating, extruding and form-controlling method of powder superalloy component |
| CN109226767A (en) * | 2018-07-27 | 2019-01-18 | 常州大学 | Prepare the high pressure high temperature synthetic method of second phase particles simulation material in aluminium alloy |
| CN110607464A (en) * | 2019-08-21 | 2019-12-24 | 中国科学院金属研究所 | Ti2Hot isostatic pressing process of AlNb alloy powder |
| CN110643857A (en) * | 2019-09-29 | 2020-01-03 | 西安欧中材料科技有限公司 | Nickel-based alloy powder without original grain boundary and preparation method thereof |
| CN110666175A (en) * | 2019-10-31 | 2020-01-10 | 西安欧中材料科技有限公司 | Hot isostatic pressing forming method of nickel-based high-temperature alloy powder |
| CN114672680A (en) * | 2022-03-07 | 2022-06-28 | 中南大学 | Step-by-step hot isostatic pressing method for additive manufacturing of nickel-based high-temperature alloy |
| CN114855047A (en) * | 2022-04-08 | 2022-08-05 | 大连理工大学 | Laves phase controllable Cr x MoNbWTi refractory high-entropy alloy and preparation method thereof |
| CN115846689A (en) * | 2022-11-15 | 2023-03-28 | 哈尔滨工业大学（威海） | Solution treatment method for melting GH3230 alloy by laser powder bed and GH3230 alloy |
| CN116833409A (en) * | 2021-11-29 | 2023-10-03 | 河冶科技股份有限公司 | Method for preparing precipitation hardening high-speed steel by powder metallurgy process |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106868436B (en) * | 2017-01-18 | 2021-05-14 | 抚顺特殊钢股份有限公司 | Manufacturing method for producing high-temperature alloy GH4169 fine-grained bar through rapid-diameter forging combination |
| GB201707895D0 (en) * | 2017-05-17 | 2017-06-28 | Rolls Royce Plc | Heat treatment method |
| FR3105041B1 (en) * | 2019-12-18 | 2023-04-21 | Commissariat Energie Atomique | Manufacturing process by hot isostatic pressing of a tool part |
| CN111702182A (en) * | 2020-08-05 | 2020-09-25 | 矿冶科技集团有限公司 | Preparation method of low-impurity-content alloy powder for additive manufacturing |
| US11199154B1 (en) | 2020-12-04 | 2021-12-14 | Fca Us Llc | Nested cylinder head |
| CN116460407A (en) * | 2023-04-21 | 2023-07-21 | 西安嘉业航空科技有限公司 | Copper alloy and alloy steel workpiece and hot isostatic pressing diffusion connection method thereof |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61159539A (en) * | 1984-12-29 | 1986-07-19 | Toshiba Corp | Manufacture of shape memory alloy |
| US5034282A (en) * | 1989-03-06 | 1991-07-23 | Boehler Gesellschaft M.B.H. | Process for the powder metallurgical production of working pieces or tools and PM parts |
| US6419770B1 (en) * | 1999-04-01 | 2002-07-16 | Denso Corporation | Cold-warm working and heat treatment method of high carbon-high alloy group steel |
| FR2865671A1 (en) * | 2004-01-30 | 2005-08-05 | Commissariat Energie Atomique | Preparation of multi-element nanopowders, useful for producing refractory, high strength ceramics, involves laser pyrolysis of aerosol containing precursor compounds, hexamethyl disilazane and silane |
| CN102392147A (en) * | 2011-11-16 | 2012-03-28 | 钢铁研究总院 | Preparation method of ultrafine grain nickel base powder high temperature alloy |
| CN102409276A (en) * | 2011-11-16 | 2012-04-11 | 钢铁研究总院 | Method for eliminating original particle boundary in powder metallurgy high-temperature alloy |
| CN102676881A (en) * | 2012-06-12 | 2012-09-19 | 钢铁研究总院 | Nickel-based powder metallurgy high-temperature alloy capable of eliminating previous particle boundary |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62214102A (en) * | 1986-03-14 | 1987-09-19 | Kobe Steel Ltd | Production of structure having corrosion-resistant sintered ni alloy part |
| JPH10152704A (en) * | 1996-11-21 | 1998-06-09 | Daido Steel Co Ltd | Production of high melting point intermetallic compound powder sintered body |
| US20070092394A1 (en) * | 2005-10-26 | 2007-04-26 | General Electric Company | Supersolvus hot isostatic pressing and ring rolling of hollow powder forms |
| CN102251131B (en) * | 2011-06-30 | 2012-11-28 | 北京科技大学 | Method for preparing injection-molding nickel-base ODS (oxide dispersion strengthened) alloy |
| CN102672174A (en) * | 2012-05-15 | 2012-09-19 | 华中科技大学 | Method for manufacturing integral annular case part by using hot isostatic pressing process |
| CN103551273B (en) * | 2013-10-31 | 2016-04-06 | 扬州力士德机械制造有限公司 | A kind of cascade water-spinning spray chamber |
-
2013
- 2013-10-22 CN CN201310506601.5A patent/CN103551573B/en not_active Expired - Fee Related
-
2014
- 2014-06-13 WO PCT/CN2014/079806 patent/WO2015058534A1/en active Application Filing
- 2014-06-13 US US15/029,900 patent/US20160263655A1/en not_active Abandoned
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61159539A (en) * | 1984-12-29 | 1986-07-19 | Toshiba Corp | Manufacture of shape memory alloy |
| US5034282A (en) * | 1989-03-06 | 1991-07-23 | Boehler Gesellschaft M.B.H. | Process for the powder metallurgical production of working pieces or tools and PM parts |
| US6419770B1 (en) * | 1999-04-01 | 2002-07-16 | Denso Corporation | Cold-warm working and heat treatment method of high carbon-high alloy group steel |
| FR2865671A1 (en) * | 2004-01-30 | 2005-08-05 | Commissariat Energie Atomique | Preparation of multi-element nanopowders, useful for producing refractory, high strength ceramics, involves laser pyrolysis of aerosol containing precursor compounds, hexamethyl disilazane and silane |
| CN102392147A (en) * | 2011-11-16 | 2012-03-28 | 钢铁研究总院 | Preparation method of ultrafine grain nickel base powder high temperature alloy |
| CN102409276A (en) * | 2011-11-16 | 2012-04-11 | 钢铁研究总院 | Method for eliminating original particle boundary in powder metallurgy high-temperature alloy |
| CN102676881A (en) * | 2012-06-12 | 2012-09-19 | 钢铁研究总院 | Nickel-based powder metallurgy high-temperature alloy capable of eliminating previous particle boundary |
Cited By (19)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105274373A (en) * | 2014-06-06 | 2016-01-27 | 中国科学院金属研究所 | Powder metallurgy preparation technology of gamma'' phase reinforced high temperature alloy |
| WO2016141872A1 (en) * | 2015-03-09 | 2016-09-15 | 中南大学 | Method for removing prior particle boundary and hole defect of powder metallurgy high-temperature alloy |
| CN106032554A (en) * | 2015-03-09 | 2016-10-19 | 中南大学 | Method for eliminating high temperature alloy primary grain boundaries and hole defects in powder metallurgy |
| CN105004587B (en) * | 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 | A kind of preparation of Ni-base Superalloy Powder rapidly solidification sample and test method |
| CN105004587A (en) * | 2015-07-09 | 2015-10-28 | 中国航空工业集团公司北京航空材料研究院 | Preparation and test method of nickel-based high temperature alloy powder rapid melting and solidifying sample |
| CN105603259A (en) * | 2016-04-11 | 2016-05-25 | 西安欧中材料科技有限公司 | Powder metallurgical method for IN718 alloy |
| CN106623941B (en) * | 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 | A kind of powder metallurgy superalloy element stages heating squeezes control shape method |
| CN106623941A (en) * | 2016-11-16 | 2017-05-10 | 中国航空工业集团公司北京航空材料研究院 | Staged heating, extruding and form-controlling method of powder superalloy component |
| CN106378456A (en) * | 2016-11-16 | 2017-02-08 | 中国航空工业集团公司北京航空材料研究院 | Rapid densifying method for powder high-temperature alloy component |
| CN109226767A (en) * | 2018-07-27 | 2019-01-18 | 常州大学 | Prepare the high pressure high temperature synthetic method of second phase particles simulation material in aluminium alloy |
| CN110607464A (en) * | 2019-08-21 | 2019-12-24 | 中国科学院金属研究所 | Ti2Hot isostatic pressing process of AlNb alloy powder |
| CN110643857A (en) * | 2019-09-29 | 2020-01-03 | 西安欧中材料科技有限公司 | Nickel-based alloy powder without original grain boundary and preparation method thereof |
| CN110666175A (en) * | 2019-10-31 | 2020-01-10 | 西安欧中材料科技有限公司 | Hot isostatic pressing forming method of nickel-based high-temperature alloy powder |
| CN110666175B (en) * | 2019-10-31 | 2022-03-04 | 西安欧中材料科技有限公司 | Hot isostatic pressing forming method of nickel-based high-temperature alloy powder |
| CN116833409A (en) * | 2021-11-29 | 2023-10-03 | 河冶科技股份有限公司 | Method for preparing precipitation hardening high-speed steel by powder metallurgy process |
| CN114672680A (en) * | 2022-03-07 | 2022-06-28 | 中南大学 | Step-by-step hot isostatic pressing method for additive manufacturing of nickel-based high-temperature alloy |
| CN114855047A (en) * | 2022-04-08 | 2022-08-05 | 大连理工大学 | Laves phase controllable Cr x MoNbWTi refractory high-entropy alloy and preparation method thereof |
| CN114855047B (en) * | 2022-04-08 | 2022-11-18 | 大连理工大学 | Controllable Cr of Laves phase x MoNbWTi refractory high-entropy alloy and preparation method thereof |
| CN115846689A (en) * | 2022-11-15 | 2023-03-28 | 哈尔滨工业大学（威海） | Solution treatment method for melting GH3230 alloy by laser powder bed and GH3230 alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| CN103551573B (en) | 2015-06-17 |
| US20160263655A1 (en) | 2016-09-15 |
| WO2015058534A1 (en) | 2015-04-30 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103551573B (en) | Previous particle boundary precipitation preventable high-temperature alloy powder hot isostatic pressing process | |
| CN102121078B (en) | Composite preparation method for fine crystal titanium alloy | |
| CN105385869B (en) | The preparation method of high-niobium TiAl intermetallic compound and TC4 titanium alloy composite components | |
| CN105821359B (en) | A kind of Technology for Heating Processing of high-ductility nickel-base alloy | |
| WO2021031231A1 (en) | Hot isostatic pressing process for ti2alnb alloy powder | |
| CN111151753B (en) | Method for manufacturing shear deformation type phase change crack resistance by laser additive manufacturing | |
| CN112322933B (en) | High-performance near-alpha high-temperature titanium alloy and powder metallurgy preparation method thereof | |
| CN103498065B (en) | A kind of TiAl alloy crystal grain refinement method | |
| CN107190178B (en) | A kind of titanium composite material and preparation method thereof | |
| CN110238401A (en) | A kind of method that powder rolling prepares high-compactness Fine Grain Ti Alloy | |
| CN110343887A (en) | A kind of method that powder extruding prepares high-compactness Fine Grain Ti Alloy | |
| CN107999756A (en) | A kind of method that heat-resisting alloy honeycomb thermal insulation board is prepared based on injection moulding | |
| CN110373561A (en) | A kind of method that power forging prepares high-compactness Fine Grain Ti Alloy | |
| WO2016141872A1 (en) | Method for removing prior particle boundary and hole defect of powder metallurgy high-temperature alloy | |
| CN103160701A (en) | Preparation method for high-temperature-resistant Mo-Si-B alloy | |
| CN105274373A (en) | Powder metallurgy preparation technology of gamma'' phase reinforced high temperature alloy | |
| JP2023520951A (en) | Low stacking fault energy superalloy, structural member and use thereof | |
| CN103469135B (en) | Preparation method of high-niobium TiAl intermetallic compound | |
| CN104342579A (en) | High-strength high-elasticity Cu-Ni-Mn alloy and its preparation method | |
| CN108165780B (en) | Preparation method of Ni-Cr-Al-Fe high-temperature alloy | |
| CN112376003A (en) | Process for improving yield strength of GH141 material | |
| CN110499483A (en) | A kind of high-alloying GH4720Li alloy single-stage homogenizing annealing process | |
| CN104028734B (en) | The method of the low segregation of high niobium containing titanium aluminium alloy and even tissue refinement | |
| CN105983703A (en) | Thermal treatment method for molding automobile turbo by powder injection | |
| CN111001812B (en) | Heat treatment method for additive manufacturing high-temperature alloy working in high-temperature gas environment |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20150617 Termination date: 20151022 |
|
| EXPY | Termination of patent right or utility model |