CN104985182B - GH4169-alloy laser melting shaping precipitation strengthening method - Google Patents
GH4169-alloy laser melting shaping precipitation strengthening method Download PDFInfo
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- CN104985182B CN104985182B CN201510474772.3A CN201510474772A CN104985182B CN 104985182 B CN104985182 B CN 104985182B CN 201510474772 A CN201510474772 A CN 201510474772A CN 104985182 B CN104985182 B CN 104985182B
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Abstract
The invention discloses a GH4169-alloy laser melting shaping precipitation strengthening method. The method comprises the following steps: step one, adding pure Ti and/or pure Al nanopowder into commercial GH4169 powder; step two, in order to maintain the sphericity degree of master alloy powder, mixing the added nanopowder with master alloy powder by means of three-dimensional motion gravity mixing; step three, placing the mixed power as a raw material into an SLM shaping machine for shaping; and step four, placing the shaped part blank into a heat treatment furnace to carry out precipitation strengthening processing. According to the invention, the mass percent of a certain element in a powder raw material is adjusted in advance and thus the performance strengthening mechanism, especially precipitation strengthening, of the GH4169 alloy on the SLM shaping condition can be changed; and targeted special heat processing is carried after SLM shaping. Therefore, the beneficial micro fine-grained organization that is generated during the shaping process is maintained and the necessary precipitation strengthening effect is generated.
Description
Technical field
The invention belongs to metal powder laser fusing material increasing field, is related to a kind of GH4169 Alloy by Laser fusing shaping
Precipitation strength method.
Background technology
With constantly bringing forth new ideas and development for science and technology, the market competition is more fierce, and the continuous variation of social need promotees
Shorten the upgrading period of product, and for some in the fields such as Aero-Space, ship and weaponry have property and
Metal parts of labyrinth, such as aero-engine turbine disk etc., the material for generally adopting are difficult-to-machine material.Traditional method
Often the process-cycle is longer to be processed manufacture, and the utilization rate of material is extremely low, particularly with the part with high complexity, very
Manufacture cannot be extremely completed, it is difficult to meet the market demand of society.Metal powder laser fusing increases material manufacturing technology is twentieth century
The class advanced manufacturing technology that end grows up, the technology are superposed to principle to integrate, and are given birth to by the accumulation seam of discrete powder
Long formula forms terminal part.At present, there are two kinds of concrete grammars using above-mentioned technology Prototyping Metal Parts, a kind of method is to be called choosing
Selecting property laser fusion (Selective Laser Melting, SLM) forming technique, another kind of method are called laser-engineered net
Forming technique (Laser Engineering Near-net Shaping, LENS).Two class technologies are made using metal dust
For raw material, it is powder forming of the laser scanning pre-deposition on shaping bed that difference is SLM technologies, and LENS technologies are then
Powder is sent in laser fusion pond by way of nozzle dusts and is formed.It is difficult that two class technologies can shape conventional art
With the labyrinth metallic element that cannot even manufacture.
For the shaping of nickel base superalloy, alloy designations that current two classes technology is still applied using conventional art and
Composition.Wherein, LENS technologies heattransfer effect directionality in the fabrication process are stronger, are generally possible to form columnar structure.And SLM
The characteristics of technology is the fusing and solidification of metal dust experience moment, and the microstructure of resulting inside parts is rapid solidification
Tissue, some alloy systems, this class loading affect larger for the forward direction of performance.But alloy is heavy often through follow-up heat treatment
Reinforcing of forming sediment can break the balance of above-mentioned microstructure, damage the combination property of whole parts, sharp so as to weaken in this regard
The shaping sexual clorminance of light fusing shaping metallic element.
Part hair is formed using casting and the method forged more than traditional handicraft figuration manufacture GH4169 alloy parts
Base, then through machining and heat treatment process.Part formed thereby is not only relatively low in complex degree of structure, and processes
Process cycle is longer, and difficult cutting, stock utilization are low, sometimes stock utilization even up to less than 10%.It is of paramount importance
It is all conventional casting or Deformation structure that any is the heterogeneous microstructure inside part material, with certain directivity.
If with powder as raw material, by SLM process forming parts, the complexity of part forming is not only increased, and
Rapid solidification structure can be internally formed in alloy, organizational structure is more tiny, more superior performance is provided for part material.
As the part or blank after casting and forging is required for carrying out interior microscopic tissue through final heat treatment
Adjustment, the part of current SLM manufactures are also affected by same idea and are carried out necessary heat treatment, cause original SLM shapings
The rapid solidification micro organization that process retains will be destroyed, and may finally be that thicker grain structure is substituted, so as to
Advantages of the SLM in External Shape formation synchronous with interior tissue is weakened to a certain extent.
The content of the invention
It is an object of the invention to provide a kind of GH4169 Alloy by Laser fusing shaping precipitation strength method, by pre-adjusting
The mass percent of certain element in powder stock, changes hydrodynamics mechanism-master of the GH4169 alloys under SLM molding conditions
If precipitation strength, and targetedly special thermal treatment is carried out after SLM shapings, produced in finally both having maintained forming process
Favourable microcosmic fine grained texture, also simultaneously generate necessary precipitation hardening effect.
The purpose of the present invention is achieved through the following technical solutions：
A kind of GH4169 Alloy by Laser fusing shaping precipitation strength method, as shown in figure 4, comprising the steps：
First, pure Ti and/or pure Al nanometer powders are added in commercial GH4169 powder, wherein：Commercial GH4169 powder
Particle size range be 0～60um, for spherical, the ratio of pure Ti and/or the filling of pure Al nanometer powders is controlled whole powder apperance
Between the 1～2% of alloy mass percent, when the mixture that nanometer powder is pure Ti and pure Al, both mass ratioes are 1:1～
2:1。
2nd, to keep the sphericity of master alloy powder, the nanometer powder of addition is by way of three-dimensional motion gravity mixes
Mix with master alloy powder, incorporation time is 20～50 hours.
3rd, mixed powder is put in SLM forming machines as raw material and is shaped, technological parameter is set to laser work(
Rate：130～300W；Scanning speed：400～1500mm/s；Processing thickness：0.03～0.05mm；Sweep spacing 0.03～
0.1mm。
4th, the part blank after shaping is put in heat-treatment furnace carries out precipitation strength process, treatment temperature be 200～
650 DEG C, depending on temperature retention time is mass ratio and reinforcing effect according to addition powder, generally 20～60 hours.
Prior art often selects the alloy powder of GH4169 primitive component ratios in SLM forming processes completely, wherein
Hardening constituent in GH4169 alloys be mainly γ " (Ni3Nb), be body-centered tetragonal ordered structure metastable phase, it is in the form of annular discs
In matrix, disperse coherence is separated out.But this is during Long-term Aging or prolonged application, the trend of oriented δ phase in version is made under intensity
Drop.And the fraction of secondary reinforcement phase γ ' (Ni3 (Al, Ti)) is compared with γ " it is (Ni3Nb) few, but macroscopic property is compared with γ " (Ni3Nb)
It is mutually stable.
Conventional method still carries out heat treatment using traditional heat treatment method, so after SLM shaping GH4169 alloys
In addition to the complexity feature for maintaining SLM formation of parts, there are not more improvement in part performance.
Under general state, in SLM forming processes, powder all exists as fusion temperature is most of through laser rapid solidification
More than 2000 DEG C, in moment process of setting, matrix all in hypersaturated state, therefore, the present invention is main using addition Ti and Al
The method of element, so as in follow-up shaped alloys, increased the degree of supersaturation of this two kinds of elements in matrix, so rear
In continuous heat treatment process, it is thus only necessary to which relatively low initiation temperature can just cause the Precipitation of γ ' (Ni3 (Al, Ti)) phase,
Hardening constituent γ ' (Ni3 (Al, Ti)) is produced, invigoration effect is risen to alloy.
Advantage of this approach is that：
1st, the characteristics of simple addition precipitation-strengthening element powder, ingenious quick high-temp consolidation with laser, combines, and is follow-up
Precipitation heat treatment reinforcement provide more than saturation solid solution structure, so as to meet SLM technologies shaping GH4169 parts complexity and
High intensity advantage；
2nd, the primary and secondary transformation of precipitation phase is completed in the GH4169 alloy parts of SLM shapings, existing side is weakened
The unstable phase transition temperature of γ in method " (Ni3Nb) phases, increased reinforcing effect, and ensure that its persistency；
3rd, after adding precipitation-strengthening element, simplify the Technology for Heating Processing that SLM shapes GH4169 alloys, it is only necessary to which low temperature is analysed
Go out one step of heat treatment and just complete three sections or so long time treatment links of prior art, during section and energy-conservation；
4th, recrystallization temperature of the heat treatment temperature far below GH4169 alloy substrates tissue, thus, it is possible to keep not destroying base
On the premise of body fine grained texture, precipitation phase is separated out, enhancement purpose is reached, so as to maintain SLM shapings to greatest extent
Fine grained texture's feature, reaches fine grained texture and improves the double effectses of part performance with precipitation strength.
Description of the drawings
Fig. 1 is GH4169 alloy powder electronic scanner microscope granule-morphology photo；
Fig. 2 be SLM forming machine schematic diagrams, 1- optical fiber lasers, 2- scanning systems, 3- vacuum systems, 4- protection systems, 5-
Auxiliary powder scraper plate, 6- forming cavities, 7- powder feed systems, 8- computers；
Fig. 3 is the GH4169 alloy material electron scanning microstructure pictures after SLM shapings；
Fig. 4 is operational flowchart.
Specific embodiment
Below in conjunction with the accompanying drawings technical scheme is further described, but is not limited thereto, it is every to this
Inventive technique scheme is modified or equivalent, without deviating from the spirit and scope of technical solution of the present invention, all should cover
In protection scope of the present invention.
Embodiment 1：
1st, according to mass ratio be 1:The 1 pure Ti of ratio and the mixture of pure Al nanometer powders are added into commercial GH4169 powder
In, the particle size range of commercial GH4169 powder is 15～45um, and powder apperance is spherical (powder morphology such as Fig. 1), the ratio of filling
Example control in whole alloy mass than fraction 1.2% between.
2nd, be the sphericity that keeps master alloy powder, the nanometer powder of addition by way of three-dimensional motion gravity mixes with
Master alloy powder mixes, and incorporation time is 30 hours；
3rd, shaping, technique in mixed powder being put into SLM forming machines (forming machine schematic diagram is shown in Fig. 2) as raw material
Parameter is set to laser power：150W；Scanning speed：750mm/s；Processing thickness：0.035mm；Sweep spacing 0.07mm.Shaping
The microstructure of part is as shown in figure 3, the interior microscopic after SLM shaping GH4169 alloys is organized as fine grained texture.
4th, the part blank after shaping is put in heat-treatment furnace carries out precipitation strength process, and treatment temperature is 530 DEG C, is protected
The warm time is 28 hours, and air cooling is to room temperature.
Embodiment 2：
1st, the mixture of pure Ti nanometer powders is added in commercial GH4169 powder, the particle size range of commercial GH4169 powder
For 10～38um, powder apperance is spherical (powder morphology such as Fig. 1), and the ratio control of filling is in whole alloy mass than fraction
0.8%.
2nd, be the sphericity that keeps master alloy powder, the nanometer powder of addition by way of three-dimensional motion gravity mixes with
Master alloy powder mixes, and incorporation time is 25 hours；
3rd, shaping, technique in mixed powder being put into SLM forming machines (forming machine schematic diagram is shown in Fig. 2) as raw material
Parameter is set to laser power：130W；Scanning speed：600mm/s；Processing thickness：0.03mm；Sweep spacing 0.06mm.Shaping
The microstructure of part is as shown in Figure 3.
4th, the part blank after shaping is put in heat-treatment furnace carries out precipitation strength process, and treatment temperature is 600 DEG C, is protected
The warm time is 35 hours, and air cooling is to room temperature.
Embodiment 3：
1st, the mixture of pure Al nanometer powders is added in commercial GH4169 powder, the particle size range of commercial GH4169 powder
For 15～30um, powder apperance is spherical (powder morphology such as Fig. 1), and the ratio control of filling is in whole alloy mass than fraction
1.5%.
2nd, be the sphericity that keeps master alloy powder, the nanometer powder of addition by way of three-dimensional motion gravity mixes with
Master alloy powder mixes, and incorporation time is 40 hours；
3rd, shaping, technique in mixed powder being put into SLM forming machines (forming machine schematic diagram is shown in Fig. 2) as raw material
Parameter is set to laser power：180W；Scanning speed：800mm/s；Processing thickness：0.04mm；Sweep spacing 0.07mm.Shaping
The microstructure of part is as shown in Figure 3.
4th, the part blank after shaping is put in heat-treatment furnace carries out precipitation strength process, and treatment temperature is 630 DEG C, is protected
The warm time is 26 hours, and air cooling is to room temperature.
Claims (3)
1. a kind of GH4169 Alloy by Laser fusing shapes precipitation strength method, it is characterised in that methods described step is as follows：
First, pure Ti and/or pure Al nanometer powders are added in commercial GH4169 powder, wherein：Pure Ti and/or pure Al nano powders
The ratio of end filling is controlled between the 1～2% of whole alloy mass percent；
2nd, to keep the sphericity of master alloy powder, the nanometer powder of addition is by way of three-dimensional motion gravity mixes and female
Alloy powder mixes, and incorporation time is 20～50 hours；
3rd, mixed powder is put in SLM forming machines as raw material and is shaped, technological parameter is set to laser power：130
～300W；Scanning speed：400～1500mm/s；Processing thickness：0.03～0.05mm；0.03～0.1mm of sweep spacing；
4th, the part blank after shaping is put in heat-treatment furnace carries out precipitation strength process, and treatment temperature is 200～650 DEG C,
Temperature retention time is 20～60 hours.
2. GH4169 Alloy by Laser fusing according to claim 1 shapes precipitation strength method, it is characterised in that the step
In rapid one, the particle size range of commercial GH4169 powder is 0～60um, and powder apperance is spherical.
3. GH4169 Alloy by Laser fusing according to claim 1 shapes precipitation strength method, it is characterised in that the step
In rapid one, when the mixture that nanometer powder is pure Ti and pure Al, both mass ratioes are 1:1～2:1.
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| CN106180719B (en) * | 2016-09-27 | 2019-01-18 | 飞而康快速制造科技有限责任公司 | IN718 component, system, heat treatment method and the device of selective laser fusing increasing material manufacturing |
| CN110125405A (en) * | 2019-06-21 | 2019-08-16 | 武汉轻工大学 | GH625 alloy property intensifying method |
| CN114427052B (en) * | 2022-01-26 | 2022-11-29 | 上海大学 | Ni 3 Al-based alloy and additive manufacturing method thereof |
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