CN110125405A - GH625 alloy property intensifying method - Google Patents
GH625 alloy property intensifying method Download PDFInfo
- Publication number
- CN110125405A CN110125405A CN201910541604.XA CN201910541604A CN110125405A CN 110125405 A CN110125405 A CN 110125405A CN 201910541604 A CN201910541604 A CN 201910541604A CN 110125405 A CN110125405 A CN 110125405A
- Authority
- CN
- China
- Prior art keywords
- powder
- alloy
- mixed material
- mixed
- intensified element
- 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.)
- Pending
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
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
-
- 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
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
-
- 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
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/60—Treatment of workpieces or articles after build-up
- B22F10/64—Treatment of workpieces or articles after build-up by thermal means
-
- 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
-
- 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
- C22C1/05—Mixtures of metal powder with non-metallic powder
-
- 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
-
- 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
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/30—Process control
- B22F10/36—Process control of energy beam parameters
-
- 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
- B22F2003/248—Thermal after-treatment
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
The present invention discloses a kind of GH625 alloy property intensifying method, is related to high temperature alloy preparation technical field.The GH625 alloy property intensifying method the following steps are included: into GH625 alloy powder be added intensified element powder, be mixed to form mixed material；The method for using precinct laser fusion to shape handles the mixed material to form blank；The blank is heat-treated, reinforced alloys are obtained.The treatment temperature that needs reduces the performance of reinforced alloys to avoid high temperature fine grained texture when the present invention is directed to reduce blank heat treatment, and is coexisted by making fine grained texture's structure and hardening constituent, the performance of further reinforced alloys.
Description
Technical field
The present invention relates to high temperature alloy preparation technical field, in particular to a kind of GH625 alloy property intensifying method.
Background technique
Nickel base superalloy has very high fatigue resistance, tensile strength, yield strength, anti-oxidant because of it at high temperature
Property and corrosion resistance, become a kind of critical material indispensable in aero-engine, in fields such as industrial steam turbine, nuclear industry
Also it is widely used.GH 625 has excellent corrosion resistance and inoxidizability, all has good draftability from low temperature to 980 DEG C
Can and anti-fatigue performance, and the stress corrosion under salt spray resistance atmosphere, therefore can be widely used for manufacture aerial motor spare part,
Aerospace structure member and chemical industry equipment.
Blank is made in the method that traditional 625 alloy of GH mostly uses casting or forging, using machining and heat treatment
Parts product is formed, the heterogeneous microstructure of this parts product is common casting or Deformation structure, has certain direction
Property, and 625 alloy of GH will appear certain actual effect hardening phenomenon after 550-700 DEG C of long-time service and cause under alloy plasticity
Therefore drop, needs to find a kind of method that can strengthen GH625 alloy property to limit the service life of parts product.
Summary of the invention
The main object of the present invention is to propose a kind of GH625 alloy property intensifying method, it is intended to solve traditional GH625 and close
The low problem of golden performance.
To achieve the above object, the present invention proposes a kind of GH625 alloy property intensifying method, the GH625 alloy property
Intensifying method the following steps are included:
Intensified element powder is added into GH625 alloy powder, is mixed to form mixed material；
The method for using precinct laser fusion to shape handles the mixed material to form blank；
The blank is heat-treated, reinforced alloys are obtained.
Optionally, described the step of intensified element powder is added into GH625 alloy powder, is mixed to form mixed material
In,
The GH625 alloy powder is spherical morphology；And/or
The partial size of the GH625 alloy powder is 10~80um.
Optionally, described the step of intensified element powder is added into GH625 alloy powder, is mixed to form mixed material
In,
Mass fraction of the intensified element powder in the mixed material is 1~3%；And/or
The partial size of the intensified element powder is 1~10um.
Optionally, described the step of intensified element powder is added into GH625 alloy powder, is mixed to form mixed material
In, the intensified element powder is one or both of Ti powder and Al powder.
Optionally, when the intensified element powder is the mixture of Ti powder and Al powder, in the mixture, Ti powder and Al powder
Mass ratio be (1~3): 1.
Optionally, the step of intensified element powder is added into GH625 alloy powder, is mixed to form mixed material packet
It includes:
Intensified element powder is added into GH625 alloy powder, mix 20 in such a way that three-dimensional motion gravity mixes~
50h is to form mixed material.
Optionally, the step of intensified element powder is added into GH625 alloy powder, is mixed to form mixed material packet
It includes:
Intensified element powder is added into GH625 alloy powder, is sent into ball mill mixing in ball mill and handles 8~20h with shape
Resulting mixture material, wherein ratio of grinding media to material is (5~15): 1, the revolving speed of the ball mill is 400~500r/min.
Optionally, the method for using precinct laser fusion to shape handles the step of mixed material is to form blank
In, the precinct laser fusion shape when technological parameter are as follows: output power be 100~1000W, scanning speed be 300~
6000mm/s, thickness are 0.03~0.1um, and sweep spacing is 0.05~0.4mm.
Optionally, described the step of being heat-treated, obtain reinforced alloys the blank, includes:
Under protection of argon gas, the blank is placed in annealing device, with the heating of 2.2~3.8 DEG C/min rate of heat addition
To 200~800 DEG C, after keeping the temperature 2~25h, 20~30 DEG C is air-cooled to, reinforced alloys are obtained.
In technical solution of the present invention, mixed material is handled by using selective laser melting process, metal powder is allowed to undergo
Instant melting and solidification, institutional framework is more tiny, and the blank of formation has high-compactness, high-performance；Intensified element is added simultaneously
Powder is mixed with GH625 alloy powder, changes the mass ratio of each element in raw material powder, to make it in subsequent heat treatment
Lower treatment temperature is only needed when process, avoids the fine grained texture of high temperature blank and reduces the performance of reinforced alloys,
And the intensified element powder can form precipitation phase with nickel element in heat treatment and be precipitated, and will not both destroy fine grained texture's knot
Structure, and play the role of further reinforced alloys.
Detailed description of the invention
In order to more clearly explain the embodiment of the invention or the technical proposal in the existing technology, to embodiment or will show below
There is attached drawing needed in technical description to be briefly described, it should be apparent that, the accompanying drawings in the following description is only this
Some embodiments of invention for those of ordinary skill in the art without creative efforts, can be with
Other relevant attached drawings are obtained according to these attached drawings.
Fig. 1 is the flow diagram of an embodiment of GH625 alloy property intensifying method proposed by the present invention；
Fig. 2 is the particle shape figure of GH625 alloy powder；
Fig. 3 is the electron-microscope scanning figure of blank.
The embodiments will be further described with reference to the accompanying drawings for the realization, the function and the advantages of the object of the present invention.
Specific embodiment
It in order to make the object, technical scheme and advantages of the embodiment of the invention clearer, below will be in the embodiment of the present invention
Technical solution be clearly and completely described.Obviously, described embodiment is only a part of the embodiments of the present invention,
Instead of all the embodiments.Based on the embodiments of the present invention, those of ordinary skill in the art are not making creative labor
Every other embodiment obtained under the premise of dynamic, shall fall within the protection scope of the present invention.It should be noted that in embodiment not
Actual conditions person is indicated, is carried out according to conventional conditions or manufacturer's recommended conditions.Factory is not specified in agents useful for same or instrument
Shang Zhe is the conventional products that can be obtained by commercially available purchase.In addition, the meaning of the "and/or" occurred in full text, including three
A scheme arranged side by side, by taking " A and/or B " as an example, the scheme including A scheme or B scheme or A and B while satisfaction.
Blank is made in the method that traditional 625 alloy of GH mostly uses casting or forging, using machining and heat treatment
Parts product is formed, the heterogeneous microstructure of this parts product is common casting or Deformation structure, has certain direction
Property, and 625 alloy of GH will appear certain actual effect hardening phenomenon after 550-700 DEG C of long-time service and cause under alloy plasticity
Therefore drop, needs to find a kind of method that can strengthen GH625 alloy property to limit the service life of parts product.
In consideration of it, the present invention proposes GH625 alloy property intensifying method, a kind of high-performance can be prepared using this method
Alloy product.Fig. 1 is the flow diagram for the embodiment that the present invention proposes GH625 alloy property intensifying method, is please referred to
Fig. 1, the preparation method of the GH625 alloy property intensifying method the following steps are included:
Step S10, intensified element powder is added into GH625 alloy powder, is mixed to form mixed material.
In the present embodiment, by adding intensified element powder simply in GH625 alloy powder to further enhance alloy
Intensity and performance.
GH62 alloy is the Ni-based denaturation alloy of solution strengthening that need to strengthen element based on Mo, Nb, is had in 943K or less good
Enduring quality well, fatigue behaviour, anti-oxidant and corrosion resistance have microscopic appearance structure as shown in Figure 2.To improve
The mixed effect of GH625 alloy and intensified element, the difficulty of processing for reducing subsequent handling, in the present embodiment, using GH625 alloy
Powder, and in selection, GH625 alloy powder preferably has the alloy powder of spherical morphology, and partial size is preferably 10~80um,
In this way, GH625 alloy powder can be made to mix well with intensified element powder, to make it in experience precinct laser fusion forming
Being uniformly dispersed when with heat treatment has a uniform reinforced structure with the alloy that ensures to be formed, at the same experience precinct laser fusion at
The tissue formed after shape has lesser fineness.In the specific implementation, GH625 alloy can be placed in in ball mill ball milling into symbol
Close desired metal powder.
In the present embodiment, intensified element powder is one or both of Ti powder and Al powder, for example, it may be single Ti
Powder can be single Al powder, be also possible to the mixture of Ti powder and Al powder.When it is the mixture of Ti powder and Al powder, institute
It states in mixture, the mass ratio of Ti powder and Al powder is (1~3): 1, it can for 1:1,1.2:1,2:1,3:1,2.5:1 etc..This
Strengthening effect when outside, to ensure mixed effect and heat treatment is needed when adding intensified element powder to intensified element powder
The additive amount and partial size at end are controlled, in the present embodiment, quality of the intensified element powder in the mixed material
Score is 1~3%；The partial size of the intensified element powder is 1~10um.
Hardening constituent in known GH625 alloy is mainly γ " (Ni3Nb), this is a kind of with body-centered tetragonal ordered structure
Metastable phase, the coherence of disperse in the base in the form of annular discs is precipitated, but the temperature stability of the phase is not high, in Long-term Aging or length
During phase is applied, it can decline to δ phase transition so as to cause the intensity of alloy.In technical solution of the present invention, strengthened by addition
Element powders are to change the mass ratio of each component of mixed material, to change mixed material experience subsequent step S20, S30
When strengthening mechanism, make γ ' (Ni3(Al, Ti)) become secondary reinforcement phase, which has more stable macroscopic property,
To make reinforced alloys that there is more longlasting reinforcing performance.
In addition, the hybrid mode of GH625 alloy powder and intensified element powder can there are many, for example, mechanical stirring is mixed
Conjunction, ground and mixed, ball milling mixing etc..In one embodiment of inventive energy intensifying method, using the mixing of three-dimensional motion gravity
Mode is mixed, and incorporation time is 20~50h.The mixing staving of three-dimensional motion gravity mixing has multidirectional movement, this
Allow for that the intracorporal material cross-mixing point of bucket is more, and good mixing effect, the uniformity is up to 99.9% or more, and incorporation time is short,
It is high-efficient.In another embodiment of inventive energy intensifying method, mixed by the way of ball mill mixing processing, ball milling is mixed
The material time is 8~20h.Ball mill mixing processing when, using the abrasive body (such as steel ball, cobblestone) of whereabouts percussion and
Abrasive body by crushing material and is mixed with the abrasive action of ball milling inner wall, and material can not only be uniformly mixed rapidly, but also can be into
One step reduces material particular diameter.In the present embodiment, when using ball mill mixing processing, the technological parameter of ball mill be can be set as:
Ratio of grinding media to material is (5~15): 1；The revolving speed of the ball mill is 400~500r/min.
Step S20, the method for using precinct laser fusion to shape handles the mixed material to form blank.
The metal parts of the arbitrarily complicated shape of precinct laser fusion forming technique energy Directly rapid fabrication represents current fast
The latest development direction of fast forming technique.Precinct laser fusion forming technique can reach 2000 ° or more high temperature in moment, make metal
Powder is in instant melting and condensation, so as to form the tiny fine grained texture of institutional framework, so that the blank tool formed
There are high-compactness, high-performance.
When it is implemented, the technological parameter when precinct laser fusion shapes are as follows: output power is 100~1000W, is swept
Retouching speed is 300~6000mm/s, and thickness is 0.03~0.1um, and sweep spacing is 0.05~0.4mm.
When due to precinct laser fusion forming, fusion temperature can reach 2000 ° or more in moment, this allows for fast rapid hardening
Gu after, solidifying phase is in hypersaturated state, similarly, due to adding intensified element powder in the feed, thus it is subsequent at
In shape alloying, the degree of supersaturation of two kinds of elements of this in matrix is increased, so in the follow-up heat treatment process, it is thus only necessary to
Lower initiation temperature can lead to γ ' (Ni3(Al, Ti)) phase Precipitation, so as to avoid high temperature blank
Fine grained texture and the performance for reducing reinforced alloys.
Step S30, the blank is heat-treated, obtains reinforced alloys.
Be heat-treated after forming blank, can further reinforced alloys, promote the performance of alloy.But precinct laser is molten
The advantages of being melted into shape, which is that, quickly forms the high solidifying fine crystal tissue of consistency, so that alloy be made to have high-compactness, Gao Xing
Energy.And high-temperature heat treatment can destroy this fine grained texture's structure, reduce alloy property instead.In technical solution of the present invention, lead to
Crossing addition intensified element powder reduces the initiation temperature of heat treatment, so as to avoid high temperature blank fine grained texture and drop
The performance of low reinforced alloys.
In the specific implementation, step S30 may include: and under protection of argon gas, the blank be placed in annealing device,
200~800 DEG C are warming up to 2.2~3.8 DEG C/min rate of heat addition, after keeping the temperature 2~25h, 20~30 DEG C is air-cooled to, conjunction must be strengthened
Gold.The reinforced alloys have microscopic appearance as shown in Figure 3, from figure 3, it can be seen that the reinforced alloys have fine grained texture.
It is heated up by low temperature procedure, so that γ ' (Ni3(Al, Ti)) phase Precipitation, generate reinforced metal between compound
Phase γ ' (Ni3(Al,Ti)).And since the intensified element powder of addition has minimum partial size, and sufficiently divide in mixed material
It dissipates, this allows for compound phase γ ' (Ni between reinforced metal3(Al, Ti)) it can be evenly dispersed when being precipitated and will not destroy thin
Fine grained texture's structure coexists with hardening constituent in brilliant institutional framework, to play the role of further reinforced alloys.
Technical solution of the present invention is described in further detail below in conjunction with specific embodiments and the drawings, it should be understood that
Following embodiment is only used to explain the present invention, is not intended to limit the present invention.
Embodiment 1
The Al that partial size is 1~10um is added into the GH625 alloy powder (with spherical morphology) that partial size is 15~45um
Powder, and make mass fraction 1.2% of the Al powder in mixed material.Then it is mixed in such a way that three-dimensional motion gravity mixes
25h is to form mixed material.
Mixed material is sent into precinct laser fusion forming machine and forms blank.Wherein, precinct laser fusion forming machine
Technological parameter setting are as follows: output power 180W, scanning speed 1200mm/s, thickness 0.04um, sweep spacing are
0.09mm。
Under protection of argon gas, blank is placed in annealing device, is warming up to 750 DEG C with the 2.2 DEG C/min rate of heat addition, protects
After warm 20h, 20~30 DEG C are air-cooled to, reinforced alloys are obtained.
Embodiment 2
The Ti that partial size is 1~10um is added into the GH625 alloy powder (with spherical morphology) that partial size is 10~38um
Powder, and make mass fraction 1.5% of the Ti powder in mixed material.Then it is mixed in such a way that three-dimensional motion gravity mixes
30h is to form mixed material.
Mixed material is sent into precinct laser fusion forming machine and forms blank.Wherein, precinct laser fusion forming machine
Technological parameter setting are as follows: output power 160W, scanning speed 900mm/s, thickness 0.03um, sweep spacing are
0.06mm。
Under protection of argon gas, blank is placed in annealing device, is warming up to 800 DEG C with the 3.8 DEG C/min rate of heat addition, protects
After warm 16h, 20~30 DEG C are air-cooled to, reinforced alloys are obtained.
Embodiment 3
The Ti that partial size is 1~10um is added into the GH625 alloy powder (with spherical morphology) that partial size is 10~80um
The mixture (mass ratio of Ti powder and Al powder is 2:1) of powder and Al powder, and make the mixture of Ti powder and Al powder in mixed material
Mass fraction be 1%.Then 20h is mixed to form mixed material in such a way that three-dimensional motion gravity mixes.
Mixed material is sent into precinct laser fusion forming machine and forms blank.Wherein, precinct laser fusion forming machine
Technological parameter setting are as follows: output power 100W, scanning speed 6000mm/s, thickness 0.03um, sweep spacing are
0.05mm。
Under protection of argon gas, blank is placed in annealing device, is warming up to 700 DEG C with the 2.5 DEG C/min rate of heat addition, protects
After warm 2h, 20~30 DEG C are air-cooled to, reinforced alloys are obtained.
Embodiment 4
The Ti that partial size is 1~10um is added into the GH625 alloy powder (with spherical morphology) that partial size is 42~70um
The mixture (mass ratio of Ti powder and Al powder is 3:1) of powder and Al powder, and make the mixture of Ti powder and Al powder in mixed material
Mass fraction be 3%.Then 50h is mixed to form mixed material in such a way that three-dimensional motion gravity mixes.
Mixed material is sent into precinct laser fusion forming machine and forms blank.Wherein, precinct laser fusion forming machine
Technological parameter setting are as follows: output power 1000W, scanning speed 300mm/s, thickness 0.1um, sweep spacing 0.4mm.
Under protection of argon gas, blank is placed in annealing device, is warming up to 200 DEG C with the 3 DEG C/min rate of heat addition, heat preservation
After 25h, 20~30 DEG C are air-cooled to, reinforced alloys are obtained.
Embodiment 5
The Al that partial size is 1~10um is added into the GH625 alloy powder (with spherical morphology) that partial size is 10~80um
Powder, and make mass fraction 1% of the Al powder in mixed material.It is then fed into ball mill mixing in ball mill and handles 20h to be formed
Mixed material, wherein ratio of grinding media to material 15:1, the revolving speed of the ball mill are 400r/min.
Mixed material is sent into precinct laser fusion forming machine and forms blank.Wherein, precinct laser fusion forming machine
Technological parameter setting are as follows: output power 100W, scanning speed 300mm/s, thickness 0.1um, sweep spacing 0.4mm.
Under protection of argon gas, blank is placed in annealing device, is warming up to 800 DEG C with the 2.2 DEG C/min rate of heat addition, protects
After warm 2h, 20~30 DEG C are air-cooled to, reinforced alloys are obtained.
Embodiment 6
The Ti that partial size is 1~10um is added into the GH625 alloy powder (with spherical morphology) that partial size is 35~80um
The mixture (mass ratio of Ti powder and Al powder is 2:1) of powder and Al powder, and make the mixture of Ti powder and Al powder in mixed material
Mass fraction be 3%.It is then fed into ball mill mixing in ball mill and handles 8h to form mixed material, wherein ratio of grinding media to material 5:
1, the revolving speed of the ball mill is 500r/min.
Mixed material is sent into precinct laser fusion forming machine and forms blank.Wherein, precinct laser fusion forming machine
Technological parameter setting are as follows: output power 1000W, scanning speed 6000mm/s, thickness 0.03um, sweep spacing are
0.05mm。
Under protection of argon gas, blank is placed in annealing device, is warming up to 500 DEG C with the 2.5 DEG C/min rate of heat addition, protects
After warm 16h, 20~30 DEG C are air-cooled to, reinforced alloys are obtained.
Embodiment 7
The Ti that partial size is 1~10um is added into the GH625 alloy powder (with spherical morphology) that partial size is 29~60um
The mixture (mass ratio of Ti powder and Al powder is 1:1) of powder and Al powder, and make the mixture of Ti powder and Al powder in mixed material
Mass fraction be 1.5%.It is then fed into ball mill ball mill mixing and handles 16h to form mixed material, wherein ratio of grinding media to material is
10:1, the revolving speed of the ball mill are 450r/min.
Mixed material is sent into precinct laser fusion forming machine and forms blank.Wherein, precinct laser fusion forming machine
Technological parameter setting are as follows: output power 800W, scanning speed 800mm/s, thickness 0.05um, sweep spacing 0.3mm.
Under protection of argon gas, blank is placed in annealing device, is warming up to 600 DEG C with the 2.8 DEG C/min rate of heat addition, protects
After warm 21h, 20~30 DEG C are air-cooled to, reinforced alloys are obtained.
Embodiment 8
The Ti that partial size is 1~10um is added into the GH625 alloy powder (with spherical morphology) that partial size is 10~30um
The mixture (mass ratio of Ti powder and Al powder is 3:1) of powder and Al powder, and make the mixture of Ti powder and Al powder in mixed material
Mass fraction be 2.5%.It is then fed into ball mill ball mill mixing and handles 10h to form mixed material, wherein ratio of grinding media to material is
8:1, the revolving speed of the ball mill are 480r/min.
Mixed material is sent into precinct laser fusion forming machine and forms blank.Wherein, precinct laser fusion forming machine
Technological parameter setting are as follows: output power 500W, scanning speed 2000mm/s, thickness 0.08um, sweep spacing are
0.08mm。
Under protection of argon gas, blank is placed in annealing device, is warming up to 700 DEG C with the 3 DEG C/min rate of heat addition, heat preservation
After 25h, 20~30 DEG C are air-cooled to, reinforced alloys are obtained.
Embodiment 9
The Ti that partial size is 1~10um is added into the GH625 alloy powder (with spherical morphology) that partial size is 12~44um
Powder, and make mass fraction 2.2% of the Ti powder in mixed material.It is then fed into ball mill mixing in ball mill and handles 13h with shape
Resulting mixture material, wherein ratio of grinding media to material 12:1, the revolving speed of the ball mill are 480r/min.
Mixed material is sent into precinct laser fusion forming machine and forms blank.Wherein, precinct laser fusion forming machine
Technological parameter setting are as follows: output power 700W, scanning speed 1000mm/s, thickness 0.06um, sweep spacing are
0.1mm。
Under protection of argon gas, blank is placed in annealing device, is warming up to 200 DEG C with the 3.8 DEG C/min rate of heat addition, protects
After warm 20h, 20~30 DEG C are air-cooled to, reinforced alloys are obtained.
The above is only a preferred embodiment of the present invention, is not intended to limit the scope of the invention, for this field
For technical staff, the invention may be variously modified and varied.All within the spirits and principles of the present invention, made any
Modification, equivalent replacement, improvement etc. should all be included within the scope of the present invention.
Claims (9)
1. a kind of GH625 alloy property intensifying method, which comprises the following steps:
Intensified element powder is added into GH625 alloy powder, is mixed to form mixed material；
The method for using precinct laser fusion to shape handles the mixed material to form blank；
The blank is heat-treated, reinforced alloys are obtained.
2. GH625 alloy property intensifying method as described in claim 1, which is characterized in that described into GH625 alloy powder
In the step of intensified element powder is added, is mixed to form mixed material,
The GH625 alloy powder is spherical morphology；And/or
The partial size of the GH625 alloy powder is 10~80um.
3. GH625 alloy property intensifying method as described in claim 1, which is characterized in that described into GH625 alloy powder
In the step of intensified element powder is added, is mixed to form mixed material,
Mass fraction of the intensified element powder in the mixed material is 1~3%；And/or
The partial size of the intensified element powder is 1~10um.
4. GH625 alloy property intensifying method as described in claim 1, which is characterized in that described into GH625 alloy powder
In the step of intensified element powder is added, is mixed to form mixed material, the intensified element powder is one in Ti powder and Al powder
Kind or two kinds.
5. GH625 alloy property intensifying method as claimed in claim 4, which is characterized in that the intensified element powder is Ti
When the mixture of powder and Al powder, in the mixture, the mass ratio of Ti powder and Al powder is (1~3): 1.
6. GH625 alloy property intensifying method as described in claim 1, which is characterized in that described into GH625 alloy powder
Intensified element powder is added, the step of being mixed to form mixed material includes:
Into GH625 alloy powder be added intensified element powder, mixed in such a way that three-dimensional motion gravity mixes 20~50h with
Form mixed material.
7. GH625 alloy property intensifying method as described in claim 1, which is characterized in that described into GH625 alloy powder
Intensified element powder is added, the step of being mixed to form mixed material includes:
Intensified element powder is added into GH625 alloy powder, it is mixed to be formed to be sent into 8~20h of ball mill mixing processing in ball mill
Close material, wherein ratio of grinding media to material is (5~15): 1, the revolving speed of the ball mill is 400~500r/min.
8. GH625 alloy property intensifying method as described in claim 1, which is characterized in that described to use precinct laser fusion
The method of forming was handled in the step of mixed material is to form blank, the technological parameter when precinct laser fusion shapes
Are as follows: output power is 100~1000W, and scanning speed is 300~6000mm/s, and thickness is 0.03~0.1um, and sweep spacing is
0.05~0.4mm.
9. GH625 alloy property intensifying method as described in claim 1, which is characterized in that described that the blank is carried out heat
Processing, the step of obtaining reinforced alloys include:
Under protection of argon gas, the blank is placed in annealing device, is warming up to 200 with 2.2~3.8 DEG C/min rate of heat addition
~800 DEG C, after keeping the temperature 2~25h, 20~30 DEG C is air-cooled to, reinforced alloys are obtained.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910541604.XA CN110125405A (en) | 2019-06-21 | 2019-06-21 | GH625 alloy property intensifying method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910541604.XA CN110125405A (en) | 2019-06-21 | 2019-06-21 | GH625 alloy property intensifying method |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN110125405A true CN110125405A (en) | 2019-08-16 |
Family
ID=67578929
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201910541604.XA Pending CN110125405A (en) | 2019-06-21 | 2019-06-21 | GH625 alloy property intensifying method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN110125405A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114427052A (en) * | 2022-01-26 | 2022-05-03 | 上海大学 | Ni3Al-based alloy and additive manufacturing method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20130228302A1 (en) * | 2011-11-04 | 2013-09-05 | Alstom Technology Ltd | Process for the production of articles made of a gamma-prime precipitation-strengthened nickel-base superalloy by selective laser melting (slm) |
| CN104985182A (en) * | 2015-08-05 | 2015-10-21 | 黑龙江科技大学 | GH4169-alloy laser melting shaping precipitation strengthening method |
| CN105642892A (en) * | 2015-10-14 | 2016-06-08 | 哈尔滨福沃德多维智能装备有限公司 | Forming solution strengthening method for making IN718 alloy through laser additive material |
| CN107186214A (en) * | 2017-04-25 | 2017-09-22 | 江苏大学 | A kind of laser heating power successively interacts the combination unit of increasing material manufacturing |
| CN107803503A (en) * | 2017-12-19 | 2018-03-16 | 湖北理工学院 | A kind of method that complicated high strength alumin ium alloy is prepared using induced with laser electric arc increases material manufacturing technology |
-
2019
- 2019-06-21 CN CN201910541604.XA patent/CN110125405A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20130228302A1 (en) * | 2011-11-04 | 2013-09-05 | Alstom Technology Ltd | Process for the production of articles made of a gamma-prime precipitation-strengthened nickel-base superalloy by selective laser melting (slm) |
| CN104985182A (en) * | 2015-08-05 | 2015-10-21 | 黑龙江科技大学 | GH4169-alloy laser melting shaping precipitation strengthening method |
| CN105642892A (en) * | 2015-10-14 | 2016-06-08 | 哈尔滨福沃德多维智能装备有限公司 | Forming solution strengthening method for making IN718 alloy through laser additive material |
| CN107186214A (en) * | 2017-04-25 | 2017-09-22 | 江苏大学 | A kind of laser heating power successively interacts the combination unit of increasing material manufacturing |
| CN107803503A (en) * | 2017-12-19 | 2018-03-16 | 湖北理工学院 | A kind of method that complicated high strength alumin ium alloy is prepared using induced with laser electric arc increases material manufacturing technology |
Non-Patent Citations (1)
| Title |
|---|
| 中南矿冶学院粉末冶金教研室: "《粉末冶金基础》", 31 December 1974 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114427052A (en) * | 2022-01-26 | 2022-05-03 | 上海大学 | Ni3Al-based alloy and additive manufacturing method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN107747019B (en) | A kind of high entropy high temperature alloy of Ni-Co-Cr-Al-W-Ta-Mo system and preparation method thereof | |
| CN108103346B (en) | Contain micro nano particle aluminium alloy welding wire wire rod and preparation method thereof | |
| RU2703670C9 (en) | Cobalt based alloy additive manufactured article, cobalt based alloy product, and method for manufacturing same | |
| CN109234601A (en) | A kind of solid silk material of high-entropy alloy of electric arc cladding and preparation method thereof | |
| CN108220681B (en) | A kind of β solidification multidirectional canned forging method of TiAl alloy containing Cr and Mo | |
| CN108907212A (en) | A method of Maraging steel is prepared based on injection moulding | |
| US20240123502A1 (en) | Titanium alloy powder for selective laser melting 3d printing, selective laser melted titanium alloy and preparation thereof | |
| CN111378873A (en) | Deformed high-temperature alloy, preparation method thereof, hot-end rotating part of engine and engine | |
| CN112828298B (en) | Preparation method of high-temperature molybdenum alloy spherical powder | |
| TW200812732A (en) | Method for making an electrode for dischage processing of surface and electrode thereof | |
| CN106756372B (en) | A kind of high-performance aluminizing-preparation method of rare earth alloy and its product of preparation | |
| JP3774758B2 (en) | TiB particle reinforced Ti2AlNb intermetallic compound matrix composite and production method thereof | |
| JP7450639B2 (en) | Low stacking fault energy superalloys, structural members and their uses | |
| JPH02255268A (en) | Production of disk made of super heat resisting alloy | |
| CN114606413B (en) | High-temperature alloy for additive manufacturing and application thereof | |
| CN112251646A (en) | Titanium alloy powder of endogenous nano composite ceramic particles and preparation method and application thereof | |
| CN110125405A (en) | GH625 alloy property intensifying method | |
| CN113337786B (en) | Nano zirconium oxide/amorphous alloy composite material and preparation method thereof | |
| CN107234196A (en) | The atomic ratio Ti-Ni alloy large-sized casting ingot forging method such as one kind | |
| JPWO2013099791A1 (en) | Method for producing Mo-Si-B alloy powder, metal material raw material powder and Mo-Si-B alloy powder | |
| CN112247156A (en) | Titanium alloy powder of endogenous nano TiC particles and preparation method and application thereof | |
| CN110468304A (en) | A kind of nickel-base alloy and preparation method thereof | |
| JPS58193335A (en) | Dispersion strengthened type nickel base heat resistant sintered alloy and preparation thereof | |
| KR20160071619A (en) | Method for manufacturing fe-based superalloy | |
| CN113732280A (en) | Graphene reinforced nickel-based high-temperature alloy powder for selective laser melting and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20190816 |
|
| RJ01 | Rejection of invention patent application after publication |