CN103551573B - 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
- CN103551573B CN103551573B CN201310506601.5A CN201310506601A CN103551573B CN 103551573 B CN103551573 B CN 103551573B CN 201310506601 A CN201310506601 A CN 201310506601A CN 103551573 B CN103551573 B CN 103551573B
- Authority
- CN
- China
- Prior art keywords
- temperature
- powder
- alloy
- equal
- hip
- 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.)
- Expired - Fee Related
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
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 avoiding the precipitated phases such as carbide to separate out along powder primary granule border, be applicable to the powder metallurgy high-temperature alloy component preparing direct hip moulding.
Background technology
High temperature alloy is the material that in aero-engine, consumption is maximum, the mechanical property of high temperature alloy and hold the addition that warm ability greatly depends on intensified element in alloy.Adding intensified element too much can make the macroscopic view of alloy and microsegregation strengthen, and structural homogenity and hot-working character worsen, even can not hot-working.Employing flash set technology prepares the element segregation that alloy powder can suppress the formation in alloy graining process effectively, thus can add more intensified element when not reducing its structural homogenity in high temperature alloy.The high temperature alloy microscopic structure being raw material compaction moulding with the powder of rapid solidification is even, excellent in mechanical performance, extensive application on the hot-end components such as Aero-Space engine turbine disk.But the high temperature alloy prepared with powder metallurgical technique also has the shortcoming of himself, time namely by high temperature insostatic pressing (HIP) consolidated powder, the precipitated phases such as carbide can be separated out along powder surface.The preferentially precipitation of these precipitated phases can make alloy plasticity lower, and simultaneously the granule boundary of powder is also the potential formation of crack of alloy thus affects the reliability of the powder metallurgy superalloy of direct high temperature insostatic pressing (HIP) consolidation.
Separate out with the reliability improving powder metallurgy along powder primary granule border to improve precipitated phase, scientific research personnel both domestic and external has developed a series of method, and this mainly comprises:
1., after Powder hot isostatic pressure consolidation, adopt the techniques such as extruding, cogging forging, isothermal forging powder batch to be carried out to the distortion of aximal deformation value to change the form on powder primary granule border to change the precipitated phase distribution on it;
2. the powder metallurgy blank of high temperature insostatic pressing (HIP) consolidation is carried out long-time high temperature solid solution heat treatment, precipitated phase is partly dissolved;
3. by adding other elements, as: Hf, improves the precipitation mutually on primary granule border.
Certainly, these methods both increase 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 avoiding the precipitated phases such as carbide to separate out along powder primary granule border, directly can obtain the excellent powder metallurgy superalloy blank of structure property by hip moulding.
Technical scheme of the present invention is:
Avoid the superalloy powder heat and other static pressuring processes that the precipitated phases such as carbide are separated out mutually along powder primary granule border, concrete technology step is as follows:
(1). prepare superalloy powder with gas atomization or additive method, powder is carried out sieve to obtain the powder that size is less than or equal to 155 microns, the powder that sieves out is loaded carbon steel or stainless steel jacket, high-temperature degassing soldering and sealing;
(2). the powder jacket first step prepared puts into hot isostatic apparatus, with while increasing temperature and pressure or first the heat up mode of boosting afterwards reach predetermined condition after start high temperature insostatic pressing (HIP);
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 more than the solidus of complete homogenize such alloys 15 degrees Celsius, pressure is more than or equal to 90MPa, be more than or equal to 20 minutes to the rear temperature retention time of temperature in body of heater, be less than or equal to 1 hour;
(3). after the first step completes, stop heating, be incubated below initial melting temperature powder jacket being cooled to the furnace the low melting point phase of alloy powder, insulating process is second step;
The retention time of second step is more than or equal to 2 hours, and can dissolve completely in insulating process mutually with the low melting point formed in cooling procedure after ensureing the first step, pressure is more than or equal to 90MPa, and after second step completes, stopping heating cooling to room temperature with the furnace.
The superalloy powder heat and other static pressuring processes that the precipitated phases such as the described carbide avoided are separated out mutually along powder primary granule border, the high temperature insostatic pressing (HIP) consolidation that this technique is applicable to ferronickel based high-temperature alloy powder or Ni-base Superalloy Powder is shaping.
The superalloy powder heat and other static pressuring processes that the precipitated phases such as the described carbide avoided are separated out mutually along powder primary granule border, in step (1), is less than or equal to 105 microns by sieving to obtain being preferably dimensioned to be.
The superalloy powder heat and other static pressuring processes that the precipitated phases such as the described carbide avoided are separated out mutually along powder primary granule border, 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 mutually along powder primary granule border, 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; For the Ni-base Superalloy Powder that other γ ' strengthen mutually, 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 mutually along powder primary granule border, 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 mutually along powder primary granule border, in step (3), the pressure preferable range of insulating process is 120 ~ 150MPa.
Advantage of the present invention and beneficial effect are:
1, present invention process divides two steps, the hip temperature scope of the first step is: higher than the low melting point phase of alloy powder initial melting temperature and lower than more than the solidus of complete homogenize such alloys 15 degrees Celsius, 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, stopping heating making material cool to below alloy low melting point phase initial melting temperature with the furnace to be incubated, and insulating process is second step.The retention time of second step should be more than or equal to 2 hours, and dissolve completely mutually with the low melting point formed in cooling procedure after ensureing the first step, after second step completes, alloy is cooled to room temperature with stove pressurize.The present invention is used for shaping to the high temperature insostatic pressing (HIP) consolidation of the superalloy powder of rapid solidification, can prepare complex-shaped powder metallurgy superalloy component in conjunction with near-net-shape technology, thus improves the utilization rate of alloy material.
2, the present invention can realize on traditional hot isostatic press, this technique scope of application be ferronickel based high-temperature alloy powder, Ni-base Superalloy Powder high temperature insostatic pressing (HIP) consolidation shaping.
3, the present invention is simple and practical, can shorten the manufacturing process of powder metallurgy superalloy component, thus reduces its manufacturing cost.
Accompanying drawing explanation
The microscopic structure (metallograph) of powder metallurgy GH4169G alloy of Fig. 1 (a)-Fig. 1 (b) for utilizing system A of the present invention and preparing; Wherein, Fig. 1 (a) multiplication factor is × 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 the room temperature of heat treated powder metallurgy GH4169G alloy and 650 DEG C of stretching fractures (stereoscan photograph) for utilizing; Wherein, Fig. 2 (a) is room temperature, and Fig. 2 (b) is 650 DEG C.
The microscopic structure (metallograph) of powder metallurgy GH4169G alloy of Fig. 3 (a)-Fig. 3 (b) for utilizing system B of the present invention and preparing; Wherein, Fig. 3 (a) multiplication factor is × 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 the room temperature of heat treated powder metallurgy GH4169G alloy and 650 DEG C of stretching fractures (stereoscan photograph) for utilizing; Wherein, Fig. 4 (a) is room temperature, and Fig. 4 (b) is 650 DEG C.
Detailed description of the invention
The present invention is the superalloy powder heat and other static pressuring processes that the precipitated phases such as carbide can be avoided to separate out mutually along powder primary granule border, specific as follows:
1. by gas atomization and other party legal system thereof for superalloy powder, obtain size by screening to be less than or equal to 155 microns and (to be preferably less than or equal to 105 microns, be preferably and be less than or equal to 55 microns) powder, powder is loaded low-carbon (LC) steel or stainless steel jacket, soldering and sealing after high-temperature degassing.Fine powder is used to be to reduce ceramic inclusions quantity in powder and reducing the quantity of hollow powder; Use carbon steel or stainless steel jacket to be because in the temperature range that the present invention is used, sheath material for completely solid-state, there is some strength and can not react with powder; High-temperature degassing is the gas in order to remove powder surface absorption to greatest extent, and to reduce the tendency that alloy forms thermal induction hole in follow-up heat treatment process, the temperature range of high-temperature degassing is 180 degrees Celsius to 500 degrees Celsius.
2. the powder jacket first step prepared puts into hot isostatic apparatus, to reach the process conditions of first paragraph with stove increasing temperature and pressure or the mode of boosting again that first heats up and to 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 more than the solidus of complete homogenize such alloys 15 degrees Celsius, 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 thermal creep stress of first paragraph process conditions has two reasons in the temperature range having appropriate liquid phase to be formed, first is that under high temperature, the element such as carbon solubility in alloy substrate raises, carbide etc. are not easily separated out at powder surface mutually, and second is that the partial melting of amount of powder surface location 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 based on following reason: the first, and in the temperature range of the first step of the present invention's selection, 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, be incubated below initial melting temperature powder jacket being chilled to the low melting point phase of alloy powder with stove, insulating process is second step.The retention time of second step should be more than or equal to 2 hours, and can dissolve completely in insulating process mutually with the segregation formed in cooling procedure after ensureing the first step, pressure should be more than or equal to 90MPa, and after second step completes, stopping heating cooling to room temperature with the furnace.The reason of second step technique must be had to be, jacket inside meeting generating portion liquid phase in first step hot isostatic pressing, Laves phase (GH4169 and derivative alloy thereof) and γ/γ ' eutectic (nickel base superalloy of γ ' strengthening) can be formed in the cooling procedure of these liquid phases after the first step, Laves phase and γ/γ ' eutectic itself enbrittle, it is potential crackle source in Alloyapplication process, must eliminate.The method eliminating Laves phase and γ/γ ' eutectic is by the fusion temperature following long-time heat preservation of alloy at Laves phase or γ/γ ' eutectic.Second step must complete having under ambient pressure existent condition, instead of completes in pressure less high temperature stove after alloy high temperature insostatic pressing (HIP) completes, this is because the existence of external pressure can be avoided producing thermal induction hole in alloy blank.
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 the powder of this alloy of argon gas atomization preparation, is loaded in stainless steel jacket by the powder of size below 105 microns, does high temperature insostatic pressing (HIP) after vacuum degassing.Following process system (A) is have selected for this alloy:
First stage, with stove increasing temperature and pressure, 1245 DEG C/150MPa/0.5 hour, cools with stove after completing;
Second stage insulating process, is chilled to room temperature with stove by 1110 DEG C/150MPa/4 hour.
The hip temperature of this system first stage is higher than Laves phase fusion temperature (1210 DEG C) but lower than alloy solidus temperature (1260 DEG C)
The microscopic structure of the alloy prepared by this technique is as shown in Fig. 1 (a) He Fig. 1 (b), can find out, the alloy structure gone out prepared by this technique is evenly tiny, and precipitated phase is evenly distributed, and almost can't see the pattern of starting powder.
Test its room temperature and 650 DEG C of tensile properties and 650 DEG C/760MPa enduring quality after direct aging process is carried out to the alloy prepared by this technique, 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 DEG C has met the standard of GH4169 alloy, and far above K4169 alloy.Alloy enduring quality is very excellent, and particularly the creep rupture life of 650 DEG C/690MPa was more than 700 hours, can match in excellence or beauty with distortion GH4169G alloy phase.
The room temperature of alloy after heat treatment and 650 DEG C of stretching fracture patterns are shown in Fig. 2 (a) and Fig. 2 (b), can find out, fracture mode is the fracture that plasticity dimple is dominated, and this illustrates that in hot isostatic pressing, powder obtains good combination.
Embodiment 2
Difference from Example 1 is, the temperature of the first stage of the present embodiment is more than alloy solidus, have more liquid phases in hot isostatic pressing to be formed, the thus corresponding rising of the temperature of second stage, fully eliminated to ensure that the rear Laves formed of first stage cooling is on good terms.
The present embodiment adopts the powder of this alloy of argon gas atomization preparation, is loaded in stainless steel jacket by the powder of size below 105 microns, does high temperature insostatic pressing (HIP) after vacuum degassing.Following process system (B) is have selected for this alloy:
First stage, with stove increasing temperature and pressure, 1265 DEG C/150MPa/0.5 hour, cools with stove after completing;
Second stage insulating process, is chilled to room temperature with stove by 1140 DEG C/150MPa/4 hour.
The hip temperature of this system first stage is higher than Laves phase fusion temperature (1210 DEG C) and alloy solidus temperature (1260 DEG C).
The microscopic structure of the alloy prepared by this technique, as shown in Fig. 3 (a) He Fig. 3 (b), can be found out, this technique obtains the microscopic structure waiting axle completely, and the border carbonization of powder primary granule is analysed precipitation mutually and avoided completely.
Test its room temperature and 650 DEG C of tensile properties and 650 DEG C/760MPa enduring quality after direct aging process is carried out to the alloy prepared by this technique, 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 DEG C has met the standard of GH4169 alloy, and far above K4169 alloy.But due to crystallite dimension than technique A prepare thick a little, thus strength level is lower than technique A, and alloy enduring quality is also very excellent.
After heat treatment the room temperature of alloy and 650 DEG C of stretching fracture patterns are shown in Fig. 4 (a) and Fig. 4 (b), can find out that the tensile fracture behavior of Alloy At Room Temperature and 650 DEG C is all plasticity dimple fracture completely, this surface alloy powder obtains good combination.
The mechanical property of the powder metallurgy GH4169G alloy that utilize the present invention prepare of table 2. after Overheating Treatment
Embodiment result shows, present invention process can avoid the precipitated phases such as carbide to separate out along powder primary granule border, thus obtain densification and microscopic structure is equiax crystal, with plasticity dimple fracture during stretcher strain, the alloy that mechanical property can compare favourably with the wrought alloy performance of same sample ingredient, this technique can shorten the manufacturing process of powder metallurgy high-temperature alloy component thus reduce its manufacturing cost.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 border to separate out mutually, reason is carbon is the boundary-strengthening element that all high temperature alloys being organized as polycrystalline must add.As long as so 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 boundaries in them, and this has report in a large amount of documents.And the temperature of the first step of the present invention occurs a small amount of liquid phase in powder, occur that liquid phase can make the precipitation of carbide lose and depend on, under high temperature, the solvability of alloy to carbon also improves greatly, this reduces the quantity of possibility carbide precipitate, alloy component fusing simultaneously also can make powder lose original pattern.And the result of embodiment has also confirmed these completely.
The low melting point formed when just the nickel base superalloy of γ ' strengthening solidifies is organized as γ/γ ' eutectic, and when ferronickel based high-temperature alloy solidifies, formation low melting point is Laves phase mutually.Thus, present invention process 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 characteristic temperature slightly be adjusted, the first step also should in the temperature having a small amount of liquid phase to be formed, and second step should below the initial melting temperature of γ/γ ' eutectic.
Claims (7)
1. the superalloy powder heat and other static pressuring processes that primary granule border can be avoided to separate out mutually, is characterized in that, concrete technology step is as follows:
(1). prepare superalloy powder with gas atomization or additive method, powder is carried out sieve to obtain the powder that size is less than or equal to 155 microns, the powder that sieves out is loaded carbon steel or stainless steel jacket, high-temperature degassing soldering and sealing;
(2). powder jacket prepared by step (1) is put into hot isostatic apparatus, with while increasing temperature and pressure or first the heat up mode of boosting afterwards reach predetermined condition after start high temperature insostatic pressing (HIP);
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, than more than the solidus of complete homogenize such alloys 15 degrees Celsius low, pressure is more than or equal to 90 MPa, be more than or equal to 20 minutes to the rear temperature retention time of temperature in body of heater, be less than or equal to 1 hour;
(3). after the first step completes, stop heating, be incubated below initial melting temperature powder jacket being cooled to the furnace the low melting point phase of alloy powder, insulating process is second step;
The temperature retention time of second step is more than or equal to 2 hours, and can melt completely in insulating process mutually with the low melting point formed in cooling procedure after ensureing the first step, pressure is more than or equal to 90 MPa, and after second step completes, stopping heating cooling to room temperature with the furnace.
2. according to the superalloy powder heat and other static pressuring processes avoiding primary granule border to separate out mutually according to claim 1, it is characterized in that, the high temperature insostatic pressing (HIP) consolidation that this technique is applicable to ferronickel based high-temperature alloy powder or Ni-base Superalloy Powder is shaping.
3. according to the superalloy powder heat and other static pressuring processes avoiding primary granule border to separate out mutually according to claim 1, it is characterized in that, in step (1), being less than or equal to 105 microns by sieving to obtain being preferably dimensioned to be.
4. according to the superalloy powder heat and other static pressuring processes avoiding primary granule border to separate out mutually according to claim 1, it is characterized in that, in step (1), obtain size by screening and be preferably and be less than or equal to 55 microns.
5. according to the superalloy powder heat and other static pressuring processes avoiding primary granule border to separate out mutually according to 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; For the Ni-base Superalloy Powder that other γ ' strengthen mutually, 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 avoiding primary granule border to separate out mutually according to claim 1, it is characterized in that, in step (2), the pressure preferable range of high temperature insostatic pressing (HIP) is 120 ~ 150 MPa.
7. according to the superalloy powder heat and other static pressuring processes avoiding primary granule border to separate out mutually according to claim 1, it is characterized in that, in step (3), the pressure preferable range of insulating process is 120 ~ 150 MPa.
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 CN103551573A (en) | 2014-02-05 |
| CN103551573B true 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) |
Families Citing this family (21)
| 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 |
| 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 |
| 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 |
| CN106378456B (en) * | 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 | A kind of method for rapidly densifying for powder metallurgy superalloy component |
| 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 |
| 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 |
| CN110607464B (en) * | 2019-08-21 | 2021-06-29 | 中国科学院金属研究所 | Hot isostatic pressing process of Ti2AlNb 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 |
| 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 |
| 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 |
| 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 |
| CN114672680B (en) * | 2022-03-07 | 2023-04-07 | 中南大学 | Step-by-step hot isostatic pressing method for additive manufacturing of nickel-based high-temperature alloy |
| 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 |
| CN115846689B (en) * | 2022-11-15 | 2023-08-18 | 哈尔滨工业大学（威海） | Solution treatment method for melting GH3230 alloy by laser powder bed and GH3230 alloy |
| 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 |
| CN116809915A (en) * | 2023-07-03 | 2023-09-29 | 中国航发北京航空材料研究院 | Preparation method of uniform standard substance in micro-area of trace element of powder superalloy |
Family Cites Families (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61159539A (en) * | 1984-12-29 | 1986-07-19 | Toshiba Corp | Manufacture of shape memory alloy |
| JPS62214102A (en) * | 1986-03-14 | 1987-09-19 | Kobe Steel Ltd | Production of structure having corrosion-resistant sintered ni alloy part |
| AT392929B (en) * | 1989-03-06 | 1991-07-10 | Boehler Gmbh | METHOD FOR THE POWDER METALLURGICAL PRODUCTION OF WORKPIECES OR TOOLS |
| JPH10152704A (en) * | 1996-11-21 | 1998-06-09 | Daido Steel Co Ltd | Production of high melting point intermetallic compound powder sintered body |
| JP3673136B2 (en) * | 1999-04-01 | 2005-07-20 | 株式会社デンソー | Heat treatment method for cold and warm processed products of high carbon-high alloy steel |
| FR2865671B1 (en) * | 2004-01-30 | 2007-03-16 | Commissariat Energie Atomique | CERAMIC NANOPOUDRE SUITABLE FOR SINTING AND METHOD OF SYNTHESIS |
| 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 |
| CN102392147B (en) * | 2011-11-16 | 2012-11-14 | 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 |
| 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 |
| 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 |
| 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
Also Published As
| Publication number | Publication date |
|---|---|
| WO2015058534A1 (en) | 2015-04-30 |
| US20160263655A1 (en) | 2016-09-15 |
| CN103551573A (en) | 2014-02-05 |
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 | |
| 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 | |
| CN103498065B (en) | A kind of TiAl alloy crystal grain refinement method | |
| US20170216919A1 (en) | Method for removing prior particle boundary and hole defect of powder metallurgy high-temperature alloy | |
| CN107999756A (en) | A kind of method that heat-resisting alloy honeycomb thermal insulation board is prepared based on injection moulding | |
| CN110343887A (en) | A kind of method that powder extruding prepares high-compactness Fine Grain Ti Alloy | |
| CN110373561A (en) | A kind of method that power forging prepares high-compactness Fine Grain Ti Alloy | |
| CN107190178A (en) | A kind of titanium matrix composite and preparation method thereof | |
| CN111151753A (en) | Method for manufacturing shear deformation type phase change crack resistance by laser additive manufacturing | |
| 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 | |
| CN110527796A (en) | A method of passing through Heat Treatment Control high temperature alloy forging grain size | |
| JP2023520951A (en) | Low stacking fault energy superalloy, structural member and use thereof | |
| CN104480347A (en) | TiAl-base alloy and heat treatment technique thereof | |
| CN101988161B (en) | A kind of method when being manufactured on high temperature with the vitallium sintered component of the ductility of raising | |
| CN109957745B (en) | Heat treatment method for optimizing NiTi-Al-based powder alloy precipitated phase | |
| CN103469135B (en) | Preparation method of high-niobium TiAl intermetallic compound | |
| CN104962794A (en) | TiCN/Al2O3 metal ceramic cutter and microwave preparation process thereof | |
| CN104342579A (en) | High-strength high-elasticity Cu-Ni-Mn alloy and its preparation method | |
| CN106475567A (en) | The manufacture method of chrome molybdenum target blankss | |
| CN108165780B (en) | Preparation method of Ni-Cr-Al-Fe high-temperature alloy | |
| CN110499483A (en) | A kind of high-alloying GH4720Li alloy single-stage homogenizing annealing process | |
| CN105957675A (en) | Preparation method of rare-earth permanent magnet material |
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 |