CN108941588A - A kind of preparation method of laser forming Ni-base Superalloy Powder - Google Patents
A kind of preparation method of laser forming Ni-base Superalloy Powder Download PDFInfo
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- CN108941588A CN108941588A CN201810846763.6A CN201810846763A CN108941588A CN 108941588 A CN108941588 A CN 108941588A CN 201810846763 A CN201810846763 A CN 201810846763A CN 108941588 A CN108941588 A CN 108941588A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- 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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/14—Treatment of metallic powder
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y70/00—Materials specially adapted for additive manufacturing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/051—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W
- C22C19/056—Alloys based on nickel or cobalt based on nickel with chromium and Mo or W with the maximum Cr content being at least 10% but less than 20%
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- 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
- B22F2009/088—Fluid nozzles, e.g. angle, distance
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- Powder Metallurgy (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
The invention discloses a kind of preparation methods of laser forming Ni-base Superalloy Powder, belong to high temperature alloy and field of powder metallurgy.The present invention uses vacuum induction melting and argon gas powder by atomization technology, prepares the Ni-base Superalloy Powder of suitable laser forming.Ni-base Superalloy Powder prepared by the present invention, small particle powder yield is high, sphericity is high, oxygen content is low, good fluidity, few without hollow defect, satellite powder, meets laser forming technical requirements.
Description
Technical field
The present invention relates to a kind of preparation methods of laser forming Ni-base Superalloy Powder, belong to high temperature alloy and powder
Field of metallurgy.
Background technique
Nickel base superalloy has excellent high-temperature corrosion resistance, endurance, abrasion resistance properties and high intensity, is widely used in
The fields such as aero-engine turbine disk, rocket engine, aviation aircraft.But nickel base superalloy difficult cutting, forming are certainly
Low by spending, laser forming provides new technological approaches with using problem to solve the forming of nickel base superalloy.Laser forming
It is the important increases material manufacturing technology (additive of one kind that the 1990s, mid-term started to grow up
Manufacturing, AM), including powder bed laser forming technology (precinct laser fusion) and powder laser melting and coating technique.Laser at
Shape can directly obtain the entity component with good metallurgical bonding, consistency close to 100%, be able to achieve material net forming or
Near-net-shape has good applicability for unmanageable material or the component with labyrinth, has a extensive future.So
And the requirement different from conventional powder forming technology to powder, laser forming not only require nothing more than that oxygen content in power is low, sphericity
Height, good fluidity, without hollow defect, and require particle diameter distribution uniform, satellite powder is few and apparent density is high.Wherein, powder bed selects
Powder needed for area's laser forming is usually fine powder of the partial size less than 45 μm, and the mainly partial size that laser cladding forming uses is 45
μm~106 μm of powder.
Currently, superalloy powder preparation method mainly has plasma rotating electrode process (PREP) and gas atomization (AA).
The powder comprehensive quality of PREP method preparation is preferable, based on big diameter powders.The raw material of PREP method are the mothers of complete alloying
Alloy bar material rotation electrode stick obtained after finishing, it is desirable that contain as the master alloy bar uniform ingredients of electrode, impurity
Measure low, equipment requirement complexity high to quality requirements of raw materials.Alloy melt is directly atomized into metal powder by AA method, obtained
Powder size is thinner, and process costs are lower than PREP method.Since demand of the laser forming to powder is big, to powder diameter requirement
The fine powder of height, especially partial size less than 50 μm.For the utilization rate for improving dusty material, laser forming is closed with nickel-base high-temperature at present
Bronze end is mainly prepared using gas atomization.But nickel base high temperature alloy composition is complicated, fusing point is high, the object during aerosolization
Reason, chemical change are extremely complex, the hollow defect of powder easily occur, lead to gas inclusions.Meanwhile powder bed precinct laser shapes institute
Its partial size of the powder of need is usually less than 45 μm, and large specific surface area is very easy to adsorption of oxygen, increases oxygen content, causes to shape sample
Product reduced performance.Currently, powder made from AA method there is also satellite powder and nonmetal inclusion, fine powder (partial size is less than 50 μm)
Recovery rate is lower, is usually no more than 40%, increases the production cost of powder bed precinct laser forming；Needed for laser cladding forming
Partial size is 45 μm~106 μm of powder, often has a more hollow defect, and these defects are during laser forming,
Formation of crack is easily become, the quality and performance of forming sample are reduced.
The present invention provides a kind of preparation methods of laser forming Ni-base Superalloy Powder, have prepared and have met laser
The Ni-base Superalloy Powder that forming technique requires, effectively increases fine powder (partial size is less than 50 μm) recovery rate, solves powder
The problems such as hollow defect in end and satellite powder.
Summary of the invention
The present invention devises a kind of preparation method of laser forming Ni-base Superalloy Powder, the powder oxygen content of preparation
It is low, impurity content is few, sphericity is high, satellite powder is few, and small particle powder yield is high and is evenly distributed, good fluidity, laser at
Shape process powder feeding situation is excellent, and forming property is stablized.
A kind of preparation method of laser forming Ni-base Superalloy Powder of the present invention comprising following step:
Step 1: under vacuum conditions, melting is carried out to the nickel base superalloy raw material of nickel base superalloy or preparation, is taken off
Gas obtains the melt of complete alloying；
Step 2: the melt of complete alloying obtained by step 1 is imported in atomizing furnace, handles, obtains Ni-based through aerosolization
Superalloy powder；Aerosolization processing be metal liquid stream is smashed by the high-pressure atomization medium of annular distance conical nozzle it is thin
Droplet, drop form Ni-base Superalloy Powder through supercooling and solidification in flight course；The annular distance conical nozzle is straight
Diameter is 3.5mm, and the jet velocity of control melt is 3.5~4kg/min when aerosolization is handled, and controls the furnace pressure power in atomizing furnace
0.22~0.23bar, the pressure of the high-pressure atomization medium are 3.5~4.5MPa；
Step 3: Ni-base Superalloy Powder obtained by step 2 is sieved by ultrasonic vibration, 150 mesh mesh screens is crossed and tentatively sieves
Choosing removes >=106 μm of powder, and then, filtering out partial size using 325 mesh mesh screen of ultrasonic vibration screening plant is less than 45 μm, use
In powder bed precinct laser forming Ni-base Superalloy Powder and partial size be 45 μm~106 μm, for laser cladding forming
Ni-base Superalloy Powder.
In certain particular alloy trade mark meltings, need to be added the high-activity components such as Ti and Zr, when melting must be by Ti and Zr
It is placed individually into feeding chamber, Ti and Zr is added by feeding chamber when melt temperature reaches 1570 DEG C.
A kind of preparation method of laser forming Ni-base Superalloy Powder of the present invention, the nickel base superalloy is with quality
Percentages include following components:
Ni:48~52%,
Co:18~22%,
Cr:11~14%,
Mo:3~5%,
W:2~3%,
Al:3~5%,
Ti:3~4%,
Ta:2~3%,
Nb:0.5~1.5%,
Zr:0.05~0.15%,
B:0.03~0.05%,
C:0.03~0.05%.
In step 1, nickel-base high-temperature is closed for a kind of preparation method of laser forming Ni-base Superalloy Powder of the present invention
Gold or the nickel base superalloy raw material prepared are added in smelting furnace, are evacuated to furnace chamber vacuum degree higher than 10-1When MPa, it is filled with lazy
Property gas shield, heats and carries out alloy melting.
A kind of preparation method of laser forming Ni-base Superalloy Powder of the present invention, the temperature of degassing described in step 1
It is 5~10min for 1580~1610 DEG C, time.
A kind of preparation method of laser forming Ni-base Superalloy Powder of the present invention, annular distance tapered injection described in step 2
The number of conical nozzle is 16~22 in mouth.
A kind of preparation method of laser forming Ni-base Superalloy Powder of the present invention, annular distance tapered injection described in step 2
When mouth works, injection gas coning apex angle is 50 ° -65 °.The present invention will be defended by the cooperation of the number of injection gas coning apex angle and nozzle
The generation probability of star powder falls below a very small value (almost can be ignored).
A kind of preparation method of laser forming Ni-base Superalloy Powder of the present invention, high-pressure atomization described in step 2 are situated between
Matter is high-purity argon gas, and the purity of the high-purity argon gas is 99.99wt%, and atomization temperature is liquidus temperature or more 300~400
℃。
The advantages and positive effects of the present invention:
If the nodularization time extends generally, it is considered that atomization temperature is excessively high in gas atomization flouring technology, solidification powder vulnerable to
The influence of many factors and deformation occurs so that atomized powder sphericity reduces, relative to liquid in general flouring technology
The phase line degree of superheat is usually no more than 150 DEG C, and usually tens degree.Meanwhile powder pressure processed is bigger, air-flow is opposite with metal liquid stream
Speed is bigger so that atomization process carry out more abundant, to obtain more thinner powder particles.Aforesaid operations also face
The problem that greatly increases of satellite powder.Present invention firstly provides low melt flow velocity cooperates the high overtemperature of melt, middle ground fog
The technique for changing pressure and annular distance conical nozzle, passes through comprehensively control quality of molten metal flow rate, gas liquid ratio, atomizing medium pressure etc.
Technological parameter, prepared good sphericity, satellite powder it is few (its generate in probability and product there are quantity well below existing
Technology), the powder without hollow defect, fine powder recovery rate is high, and wherein the powder of partial size≤50 μm is higher than 60%, fully meets powder
Bed precinct laser fusion forming technique requirement.
The present invention has successfully been prepared oxygen content and has been lower than by each technique and the synergistic effect of each technological parameter
0.010% Ni-base Superalloy Powder, and it is not necessary that nickel-base alloy bar is pre-machined, process flow is shortened, life is reduced
Cost is produced, the large-scale production of laser forming Co-based alloy powder is conducive to.
Novelty of the invention uses the high overtemperature of melt, medium atomizing pressure, low melt flow velocity and special spray
The annular distance conical nozzle of cone-apex angle of emanating prepares Ni-base Superalloy Powder, while improving gas liquid ratio, reduces the table of metal
Face tension and viscosity.By control atomization temperature be 1620~1720 DEG C, powder air pressure processed is 3.5~4.5MPa, flow stream velocity is
3.5~4kg/min, the powder good sphericity of preparation, oxygen content are lower than 0.010%, and fine powder recovery rate is high, wherein partial size≤50
μm powder be higher than 60%, the fine powder recovery rates of partial size≤45 μm is higher than 58%, fully meet powder bed precinct laser fusion at
Shape technical requirements, and it is not necessary that nickel-base alloy bar is pre-machined, process flow is shortened, production cost is reduced, is conducive to swash
The light forming large-scale production of Co-based alloy powder, greatly improved the production efficiency of powder.
The present invention uses lower flow stream velocity, to improve gas liquid ratio, increases the cooling velocity of molten drop, control system
Powder furnace pressure is 0.22~0.23bar, and powder air pressure processed is 3.5~4MPa, obtains the higher Ni-base Superalloy Powder of sphericity,
The production efficiency of powder greatly improved 60% or more in powder yield of the powder diameter less than 50 μm.Institute of the present invention simultaneously
It obtains in product, the probability that satellite powder generates is also well below the prior art.Powder flowbility prepared by the present invention is good, pine dress
Density is high, and powdering is uniform, fully meets laser sintering (SLS) requirement.
The present invention is by each preparation technology parameter and the synergistic effect of process flow, while improving fine powder recovery rate,
The viscosity and surface tension of molten drop are reduced, so that powder is sufficiently broken and reduces the possibility of package inert gas, is disappeared completely
In addition to the hollow defect of powder, solve the macroscopic cracking as caused by powder quality factor and defect etc. in laser forming process
Problem has prepared the Ni-base Superalloy Powder for meeting laser cladding forming technical requirements.
The present invention eliminates the hollow defect of powder, powder by each preparation technology parameter and the synergistic effect of process flow
Last good sphericity prepares the Co-based alloy powder for meeting laser forming technical requirements, greatly improves the utilization rate of powder.
In short, can efficiently prepare the Ni-base Superalloy Powder for meeting laser forming technical requirements using the present invention.
Detailed description of the invention
Fig. 1 is the grain size distribution of laser forming Ni-base Superalloy Powder particle made from embodiment 1.
Fig. 2 is the pattern of laser forming Ni-base Superalloy Powder particle made from embodiment 1.
Fig. 3 is the sectional view of laser forming Ni-base Superalloy Powder particle made from embodiment 1.
Fig. 4 is the pattern of laser forming Ni-base Superalloy Powder particle made from embodiment 2.
Fig. 5 is the sectional view of laser forming Ni-base Superalloy Powder particle made from embodiment 2.
Fig. 1 shows in embodiment 1 that partial size is that the fine powder recovery rate less than 50 μm is higher than 60% before sieving.
Fig. 2 the result shows that, Ni-base Superalloy Powder made from embodiment 1 have very high sphericity, and satellite powder compared with
It is few.
Fig. 3 the result shows that, in Ni-base Superalloy Powder particle made from embodiment 1, there is not hollow defect.
Fig. 4 the result shows that, Ni-base Superalloy Powder made from embodiment 2 have very high sphericity, and satellite powder compared with
It is few.
Fig. 5 the result shows that, in Ni-base Superalloy Powder particle made from embodiment 2, there is not hollow defect.
Specific embodiment
Present invention will be further explained below with reference to the attached drawings and specific embodiments.
Embodiment 1:
(1) alloy melting: vacuum induction melting furnace is added in the nickel base superalloy raw material of 20kg, Ti and Zr are put on one side
Feeding chamber (Ti:0.82kg, Zr:0.02kg).Hatch door is closed, vacuumizing reduces furnace pressure to 10-1MPa carries out alloy melting, adds
Pass through feeding chamber when heat is to 1570 DEG C and Ti and Zr is added.The nickel base superalloy raw material includes following groups by percentage to the quality
Point: Ni:9.97kg, Co:4.15kg, Cr:2.7kg, Mo:0.765kg, W:0.418kg, Al:0.72kg, Ti:0.82kg, Ta:
0.488kg, Nb:0.182kg, Zr:0.02kg, B:0.06kg, C:0.008kg.
(2) vacuum outgas: after alloy is completely melt, in 1580 DEG C of progress vacuum outgas 10min.
(3) alloy raw material being completely melt powder by atomization: is imported into atomizing furnace by diversion pipe with the flow velocity of 3.5kg/min
In, control atomization temperature is 1650 DEG C, powder furnace pressure processed is 0.22bar, powder air pressure processed is 3.5MPa, is 3.5mm's by diameter
Metal liquid stream is smashed into fine drop by the high pressure, high purity argon gas (purity 99.99wt%) of annular distance conical nozzle, and drop is flying
Through supercooling during row, Ni-base Superalloy Powder quickly is formed after solidification, into cooling 4h in receipts powder tank.(the annular distance
The number of conical nozzle is 16 in conical nozzle.When the annular distance taper nozzle operation, injection gas coning apex angle is 50 °.)
(4) powder sieving: Ni-base Superalloy Powder after cooling is sieved by ultrasonic vibration, passes through 150 mesh mesh screens
Preliminary screening removes >=106 μm of powder.Then, it is filtered out using 325 mesh mesh screen of ultrasonic vibration screening plant required Ni-based
Superalloy powder.
Acquired nickel base superalloy includes following components by percentage to the quality:
Ni: surplus, Co:18.5%, Cr:14%, Mo:4.66%, W:2.17%, Al:3.47%, Ti:3.83%, Ta:
2.29%, Nb:0.89%, Zr:0.12%, B:0.05%, C:0.045%.
The Ni-base Superalloy Powder particle diameter distribution that the present embodiment is prepared is as shown in Figure 1, granule-morphology such as Fig. 2 institute
Show, cross-sectional morphology is as shown in Figure 3.Through detecting, oxygen content in power 0.011%, average grain diameter is 29.23 μm, apparent density
For 4.08g/cm3, tap density 5.20g/cm3。
The application of above-mentioned powder, includes the following steps:
(1) model construction
According to required drip molding feature, threedimensional model is established on computers and saves as the file of STL format, is led
In the construction software for entering powder bed precinct laser fusion former, layered shaping is carried out.
(2) laser forming pre-treatment
It shapes storehouse substrate and uses stainless steel material, carry out sandblasting (SiO2) formation zone is put into after processing, and substrate is leveled,
Then Ni-base Superalloy Powder obtained by step 1 is packed into the powder supply cylinder of powder bed precinct laser fusion former, use scraper
Powder is evenly laid out on forming board, pass hull closure hatch door.
(3) parameter setting and laser forming
In the operating system provisioned in powder bed precinct laser fusion former, adjusting substrate heating temperature is 120 DEG C, is led to
Entering high-purity argon gas (purity 99.99wt%) protection, oxygen content≤0.1% in control chamber, adjusting spot diameter is 80 μm, and
Setting powdering thickness is 30 μm, drip molding filling lasing light input power is 200w, scanning speed 800mm/s, sweep span are
0.08mm and profile lasing light input power be 130w, scanning speed 800, and selects filling+rotation (every layer of rotation clockwise
Turn 67.5 °), workpiece parameter is saved, starts to be sintered.
(4) laser forming post-processes
Drip molding is separated from substrate using wire cutting technology, nickel base superalloy drip molding needed for obtaining.
It is 98.37%, tensile strength 985MPa that nickel base superalloy drip molding consistency, which is made, in the present embodiment, and surrender is strong
Degree is 819MPa, elongation percentage 6.21%.
The product of above-mentioned 3D printing can also carry out subsequent heat treatment.
Embodiment 2:
(1) alloy melting: vacuum induction melting furnace is added in the nickel base superalloy raw material of 20kg, Ti and Zr are put on one side
Feeding chamber (Ti:0.82kg, Zr:0.02kg).Hatch door is closed, vacuumizing reduces furnace pressure to 10-1MPa, heating start to be closed
Ti and Zr is added by feeding chamber when being heated to 1570 DEG C in golden melting.The nickel base superalloy raw material is by percentage to the quality
Including following components: Ni:9.96kg, Co:4.13kg, Cr:2.7kg, Mo:0.758kg, W:0.413kg, Al:0.727kg, Ti:
0.82kg, Ta:0.486kg, Nb:0.182kg, Zr:0.02kg, B:0.06kg, C:0.008kg.
(2) vacuum outgas: after alloy is completely melt, in 1610 DEG C of progress vacuum outgas 5min.
(3) alloy raw material being completely melt powder by atomization: is imported into atomizing furnace by diversion pipe with the flow velocity of 4kg/min
In, control atomization temperature is 1670 DEG C, powder furnace pressure processed is 0.23bar, powder air pressure processed is 4MPa, the ring for being 3.5mm by diameter
Metal liquid stream is smashed into fine drop by the high pressure, high purity argon gas (purity 99.99wt%) of hole conical nozzle, and drop is flying
In the process through supercooling, Ni-base Superalloy Powder quickly is formed after solidification, into cooling 4h in receipts powder tank.(the annular bit
The number of conical nozzle is 20 in shape nozzle.When the annular distance taper nozzle operation, injection gas coning apex angle is 60 °.) (4) powder
End screening: Ni-base Superalloy Powder after cooling is sieved by ultrasonic vibration, removes >=106 μ by 150 mesh preliminary screenings
The powder of m.Then, required Ni-base Superalloy Powder is filtered out using 325 mesh mesh screen of ultrasonic vibration screening plant.
Acquired nickel base superalloy includes following components by percentage to the quality:
Ni: surplus, Co:20%, Cr:12.6%, Mo:3.78%, W:2.14%, Al:3.24%, Ti:3.66%, Ta:
2.05%, Nb:0.82%, Zr:0.057%, B:0.045%, C:0.05%.
The Ni-base Superalloy Powder granule-morphology that the present embodiment is prepared is as shown in figure 4, cross-sectional morphology such as Fig. 5 institute
Show.Through detecting, oxygen content in power 0.009%, average grain diameter is 31.00 μm, apparent density 4.21g/cm3, tap density
For 5.32g/cm3。
The application of above-mentioned powder, includes the following steps:
(1) model construction
According to required drip molding feature, threedimensional model is established on computers and saves as the file of STL format, is led
In the construction software for entering powder bed precinct laser fusion former, layered shaping is carried out.
(2) laser forming pre-treatment
It shapes storehouse substrate and uses stainless steel material, carry out sandblasting (SiO2) formation zone is put into after processing, and substrate is leveled,
Then Ni-base Superalloy Powder obtained by step 1 is packed into the powder supply cylinder of powder bed precinct laser fusion former, use scraper
Powder is evenly laid out on forming board, pass hull closure hatch door.
(3) parameter setting and laser forming
In the operating system provisioned in powder bed precinct laser fusion former, adjusting substrate heating temperature is 110 DEG C, is led to
Entering high-purity argon gas (purity 99.99wt%) protection, oxygen content≤0.1% in control chamber, adjusting spot diameter is 80 μm, and
Setting powdering thickness is 30 μm, drip molding filling lasing light input power is 180w, scanning speed 900mm/s, sweep span are
0.09mm and profile lasing light input power be 120w, scanning speed 900mm/s, and selects filling+rotation (every layer of up time
Needle rotates 67.5 °), workpiece parameter is saved, starts to be sintered.
(4) laser forming post-processes
Drip molding is separated from substrate using wire cutting technology, nickel base superalloy drip molding needed for obtaining.
It is 98.25%, tensile strength 957MPa that nickel base superalloy drip molding consistency, which is made, in the present embodiment, and surrender is strong
Degree is 804MPa, elongation percentage 5.97%.
The product of above-mentioned 3D printing can also carry out subsequent heat treatment.
The injection speed of other schemes, especially injection gas coning the apex angle melt not in 50 ° -65 °, aerosolization processing is attempted
When degree is greater than 4.5kg/min, in gained powder, the quantity of satellite powder be increased significantly.
Claims (8)
1. a kind of preparation method of laser forming Ni-base Superalloy Powder, it is characterised in that include the following steps:
Step 1: under vacuum conditions, carrying out melting, degassing to the nickel base superalloy raw material of nickel base superalloy or preparation,
Obtain the melt of complete alloying；
Step 2: the melt of complete alloying obtained by step 1 is imported in atomizing furnace, is handled through aerosolization, obtains nickel-base high-temperature
Alloy powder；The aerosolization processing is that metal liquid stream is smashed into tiny liquid by the high-pressure atomization medium of annular distance conical nozzle
Drop, drop are cooled down and are solidified in flight course, form powder；The annular distance taper nozzle diameter is 3.5mm, aerosolization is handled
When control melt jet velocity be 3.5~4kg/min, control atomizing furnace in pressure be 0.22~0.23bar, the high pressure
The pressure of atomizing medium is 3.5~4.5MPa；
Step 3: Ni-base Superalloy Powder obtained by step 2 is sieved by ultrasonic vibration, 150 mesh mesh screen preliminary screenings is crossed and goes
Except >=106 μm of powder；Then, partial size is filtered out using 325 mesh mesh screen of ultrasonic vibration screening plant to be 45 μm, select for powder bed
The Ni-base Superalloy Powder and partial size of area's laser forming are 45~106 μm, for the Ni-based height of powder laser cladding forming
Temperature alloy powder.
2. a kind of preparation method of laser forming Ni-base Superalloy Powder according to claim 1, it is characterised in that:
The nickel base superalloy includes following components by percentage to the quality:
Ni:48~52%,
Co:18~22%,
Cr:11~14%,
Mo:3~5%,
W:2~3%,
Al:3~5%,
Ti:3~4%,
Ta:2~3%,
Nb:0.5~1.5%,
Zr:0.05~0.15%,
B:0.03~0.05%,
C:0.03~0.05%.
3. a kind of preparation method of laser forming Ni-base Superalloy Powder according to claim 2, it is characterised in that:
In step 1, nickel base superalloy or the nickel base superalloy raw material of preparation are added in smelting furnace, furnace chamber vacuum is evacuated to
When degree is higher than 10-1MPa, it is filled with inert gas shielding, heats and carries out alloy melting.
4. a kind of preparation method of laser forming Ni-base Superalloy Powder according to claim 1, it is characterised in that:
The temperature of degassing described in step 1 is 1580~1610 DEG C, the time is 5~10min.
5. a kind of preparation method of laser forming Ni-base Superalloy Powder according to claim 1, it is characterised in that:
The number of conical nozzle is 16~22 in annular distance conical nozzle described in step 2.
6. a kind of preparation method of laser forming Ni-base Superalloy Powder according to claim 1, it is characterised in that:
When the nozzle operation of annular distance taper described in step 2, injection gas coning apex angle is 50 °~65 °.
7. a kind of preparation method of laser forming Ni-base Superalloy Powder according to claim 1, it is characterised in that:
High-pressure atomization medium described in step 2 is high-purity argon gas, and the purity of the high-purity argon gas is 99.99wt%.
8. a kind of preparation method of laser forming Ni-base Superalloy Powder according to claim 1, it is characterised in that:
Atomization temperature described in step 2 is 300~400 DEG C of liquidus temperature or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810846763.6A CN108941588B (en) | 2018-07-27 | 2018-07-27 | Preparation method of nickel-based superalloy powder for laser forming |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810846763.6A CN108941588B (en) | 2018-07-27 | 2018-07-27 | Preparation method of nickel-based superalloy powder for laser forming |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN108941588A true CN108941588A (en) | 2018-12-07 |
| CN108941588B CN108941588B (en) | 2020-04-10 |
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| CN110468305A (en) * | 2019-08-26 | 2019-11-19 | 飞而康快速制造科技有限责任公司 | A kind of nickel base superalloy and preparation method thereof |
| CN110643992A (en) * | 2019-10-18 | 2020-01-03 | 山东大学 | Boride reinforced self-lubricating composite coating and preparation method thereof |
| CN110756795A (en) * | 2019-04-16 | 2020-02-07 | 敬业钢铁有限公司 | Nickel-based superalloy powder and preparation method thereof |
| CN111014703A (en) * | 2019-12-26 | 2020-04-17 | 中天上材增材制造有限公司 | Preparation method of nickel-based alloy powder for laser cladding |
| CN111560531A (en) * | 2020-04-15 | 2020-08-21 | 河南中钻新材料有限公司 | Preparation method of low-oxide-inclusion high-performance powder metallurgy nickel-based high-temperature alloy |
| CN111906311A (en) * | 2020-08-30 | 2020-11-10 | 中南大学 | Method for preventing selective laser melting nickel-based high-temperature alloy from cracking |
| CN112775589A (en) * | 2021-01-14 | 2021-05-11 | 有研工程技术研究院有限公司 | Preparation method of high-purity narrow-particle-size nickel-based brazing filler metal alloy powder |
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| CN114592144A (en) * | 2022-03-09 | 2022-06-07 | 上海交通大学 | Nickel-based superalloy powder, nickel-based superalloy workpiece and preparation method |
| JP2022532738A (en) * | 2019-07-05 | 2022-07-19 | ファオデーエム メタルズ インターナショナル ゲゼルシャフト ミット ベシュレンクテル ハフツング | Nickel-based alloy for powder and manufacturing method of powder |
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| CN110756795A (en) * | 2019-04-16 | 2020-02-07 | 敬业钢铁有限公司 | Nickel-based superalloy powder and preparation method thereof |
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| US11767579B2 (en) | 2019-07-05 | 2023-09-26 | Vdm Metals International Gmbh | Nickel based alloy for powder and method for producing a powder |
| CN110468305A (en) * | 2019-08-26 | 2019-11-19 | 飞而康快速制造科技有限责任公司 | A kind of nickel base superalloy and preparation method thereof |
| CN110643992A (en) * | 2019-10-18 | 2020-01-03 | 山东大学 | Boride reinforced self-lubricating composite coating and preparation method thereof |
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| CN111014703A (en) * | 2019-12-26 | 2020-04-17 | 中天上材增材制造有限公司 | Preparation method of nickel-based alloy powder for laser cladding |
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| CN111560531A (en) * | 2020-04-15 | 2020-08-21 | 河南中钻新材料有限公司 | Preparation method of low-oxide-inclusion high-performance powder metallurgy nickel-based high-temperature alloy |
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| CN113186431A (en) * | 2021-05-06 | 2021-07-30 | 哈尔滨工业大学（深圳） | Nickel-based high-temperature alloy powder suitable for powder metallurgy and preparation method thereof |
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| CN115430838A (en) * | 2022-08-26 | 2022-12-06 | 上海材料研究所 | Preparation method of high-tungsten high-boron-content nickel-based alloy powder |
| CN115430838B (en) * | 2022-08-26 | 2023-11-14 | 上海材料研究所有限公司 | Preparation method of nickel-based alloy powder with high tungsten and high boron content |
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