CN107876762A - A kind of laser metal 3D printing method for realizing Ni-based function part local solidification tissue customization - Google Patents
A kind of laser metal 3D printing method for realizing Ni-based function part local solidification tissue customization Download PDFInfo
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- CN107876762A CN107876762A CN201711073924.4A CN201711073924A CN107876762A CN 107876762 A CN107876762 A CN 107876762A CN 201711073924 A CN201711073924 A CN 201711073924A CN 107876762 A CN107876762 A CN 107876762A
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- 238000010146 3D printing Methods 0.000 title claims abstract description 48
- 238000000034 method Methods 0.000 title claims abstract description 30
- 239000002184 metal Substances 0.000 title claims abstract description 29
- 229910052751 metal Inorganic materials 0.000 title claims abstract description 29
- 238000007711 solidification Methods 0.000 title claims abstract description 23
- 230000008023 solidification Effects 0.000 title claims abstract description 23
- 230000008859 change Effects 0.000 claims abstract description 19
- 239000010410 layer Substances 0.000 claims abstract description 19
- 239000000956 alloy Substances 0.000 claims abstract description 17
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 16
- 238000012545 processing Methods 0.000 claims abstract description 11
- 230000008520 organization Effects 0.000 claims abstract description 10
- 230000008569 process Effects 0.000 claims abstract description 6
- 239000002356 single layer Substances 0.000 claims abstract description 6
- 238000012546 transfer Methods 0.000 claims abstract description 4
- 210000001787 dendrite Anatomy 0.000 claims description 30
- 230000008014 freezing Effects 0.000 claims description 9
- 238000007710 freezing Methods 0.000 claims description 9
- 239000000843 powder Substances 0.000 claims description 6
- 230000015572 biosynthetic process Effects 0.000 claims description 3
- 238000005755 formation reaction Methods 0.000 claims description 3
- 239000000463 material Substances 0.000 description 26
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 18
- 210000001519 tissue Anatomy 0.000 description 11
- 239000013078 crystal Substances 0.000 description 7
- 210000000988 bone and bone Anatomy 0.000 description 4
- 230000001276 controlling effect Effects 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 230000035882 stress Effects 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 3
- 230000009977 dual effect Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 229910001069 Ti alloy Inorganic materials 0.000 description 2
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 2
- 230000009471 action Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 229910001220 stainless steel Inorganic materials 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 1
- WAIPAZQMEIHHTJ-UHFFFAOYSA-N [Cr].[Co] Chemical compound [Cr].[Co] WAIPAZQMEIHHTJ-UHFFFAOYSA-N 0.000 description 1
- HZEWFHLRYVTOIW-UHFFFAOYSA-N [Ti].[Ni] Chemical compound [Ti].[Ni] HZEWFHLRYVTOIW-UHFFFAOYSA-N 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000010790 dilution Methods 0.000 description 1
- 239000012895 dilution Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000011065 in-situ storage Methods 0.000 description 1
- 229910000816 inconels 718 Inorganic materials 0.000 description 1
- 238000005304 joining Methods 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 238000010310 metallurgical process Methods 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 238000012876 topography Methods 0.000 description 1
- 229910006281 γ-TiAl Inorganic materials 0.000 description 1
Classifications
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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
- 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
- B22F10/30—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
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/30—Process control
- B22F10/36—Process control of energy beam parameters
- B22F10/366—Scanning parameters, e.g. hatch distance or scanning strategy
-
- 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
- B22F10/368—Temperature or temperature gradient, e.g. temperature of the melt pool
-
- 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
- B22F10/80—Data acquisition or data processing
-
- 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
- B33Y10/00—Processes of additive manufacturing
-
- 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
- B33Y50/00—Data acquisition or data processing for additive manufacturing
- B33Y50/02—Data acquisition or data processing for additive manufacturing for controlling or regulating additive manufacturing processes
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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
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/25—Direct deposition of metal particles, e.g. direct metal deposition [DMD] or laser engineered net shaping [LENS]
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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
- 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]
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- 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
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Abstract
The invention discloses a kind of laser metal 3D printing method for realizing Ni-based function part local solidification tissue customization.First draw out the corresponding relation figure of nickel-base alloy solidified structure and Solidification Parameters；Solidification Parameters scope according to corresponding to graph of a relation obtains parts locally destination organization；Temperature field of molten pool is calculated using three-dimensional finite element heat transfer model, reproduces above-mentioned Solidification Parameters scope, and then obtain the technological parameter matched with destination organization；Part all sites solidified structure and processing parameter matching are completed by said process；Monolayer slices processing is carried out to part, obtains technological parameter of the individual layer with change in location, until the section for completing all layers of part is set with technological parameter；Set input 3D printing system to carry out 3D printing the technological parameter of customization, obtain with the Ni-based function part for customizing solidified structure.The present invention is by according to parts locally organizational requirements, using the technological parameter of customization, can effectively realize the customization of parts locally solidified structure.
Description
Technical field
The present invention relates to laser metal material processing field, more particularly to one kind to realize Ni-based function part local solidification group
Knit the laser metal 3D printing method of customization.
Background technology
The generally existing gradient function structure in industrial quarters and nature, its composition are realized with configuration with spatial position change
Its specific function, to adapt to various military services or living environment.At present, gradient function structure mainly has two kinds, i.e., more material gradients
Functional part and homogeneity gradient function part.More material gradient functional parts are to utilize the different material of two kinds of (or a variety of) performances
Material, by continuously changing the Nomenclature Composition and Structure of Complexes of material, makes interface disappear, and then cause the performance of material with the change of locus
And change, such as using Ni-based dual alloy, titanium-based dual alloy and steel-more alloys of titanium-nickel, to realize aircraft engine integral turbine leaf
The high fracture strength of disk core and the high high temperature creep strength of Low Cycle Fatigue Strength and disk edge and blade；Another kind is using of the same race
The performance difference that the different tissues form of material has, by realizing its gradient performance to the space layout of solidified structure, such as exist
Aerospace field, crystal boundary is the source for producing high-temerature creep fracture under hot environment, and solidified structure is regulated to highly oriented post
After shape brilliant (being arranged parallel to principal direction of stress) or even monocrystalline, the high-temperature behavior of turbo blade can be effectively improved and extend its clothes
The life-span is used as a servant, and during room-temperature applications, tissue modulation can be effectively improved to the room temperature strength of material for the equiaxed grain structure of random orientation
And plasticity.
Laser metal 3D printing has the characteristics that thermal source high concentration, the small and heat affected area of dilution are small, and its unique advantage exists
In it with the potentiality for being combined excellent material property with accurate manufacturing process, it is extremely suitable for making space structure and answer
Miscellaneous, structural constituent space layout function part.
At present, domestic and international research institution has carried out extensive laser metal 3D printing to dissimilar metal FGM and ground
Study carefully.Beijing Institute of Aeronautics using Laser Melting Deposition mode manufactured serial titanium alloy high-strength/low strong (TA15/TA2), in strong/high-strength (TC4/
TC11, TA15/TC11), high-strength/high damage tolerance (TC18/TC 21) gradient-structure, and devise serial transition region Novel Titanium
Alloy material.Northwestern Polytechnical University have studied Ti/Rene88DT gradient components.It is double that Beijing non-ferrous metal institute realizes titanium-based
Alloy TC11/ γ-TiAl, TC11/Ti2AlNb, TA15/Ti2AlNb, Ni-based dual alloy GH163/Rene95, stainless steel pairing
Golden SS316L/Stellite31 and more alloy SS316L/ is Ni-based/Ti6Al4V functionally gradient material (FGM)s.Xi'an Communications University have studied
The manufacture of Ti6Al4V/CoCrMo functionally gradient material (FGM)s and Cu/W FGMs.Lancaster University of Britain has manufactured SS316L/
The gradient thin-wall parts of Inconel 718.Lyons, France university realizes Fe/Fe-Al functionally gradient material (FGM).India's science and engineering realizes
Stellite-21/ austenitic stainless steel bi-material layers light wall pipe parts.Polish military technology university realizes Fe-Al/SS316L stainless steels
The preparation of ring.Univ Michigan-Ann Arbor USA realizes the manufacture of Ni/Cr bi-material layers negative temperature coefficient building blocks of functions.However, due to not
Foreign material in proportion undergoes in-situ metallurgical process and alloying action, foreign material gradient function under the high temperature action of molten bath
The laser metal 3D printing of structure still faces problems, as the hot physical difference of foreign material causes laser metal 3D printing zero
Ftractureed inside part caused by complicated thermal stress, dissimilar material joining interface or transition region produce brittle harmful phase, xenogenesis material
Expect collaboration heat treatment optimization of function gradient structure etc..Above-mentioned challenge seriously constrains laser metal 3D printing in more material functions
Application in functionally gradient material (FGM) preparation.
The performance of material depends on the composition and microscopic structure of material.The material that composition is identical, tissue is different has complete
Different performances.By taking Ti60 as an example, equiax crystal is 1.359% in 600 DEG C/160MPa creep compliances, and column crystal is 0.1633%,
Equiax crystal creep rupture life is 48h under 600 DEG C/310MPa situations, and column crystal creep rupture life is 354h.For another example, Ni-based entirety
The core service temperature relative vane of turbine blade is relatively low, by core Organization layout be tiny equiax crystal after can improve fracture strength
And Low Cycle Fatigue Strength, and the tissue modulation of blade is the column crystal parallel to principal direction of stress arrangement even after monocrystalline, can be with
Effectively improve high temperature creep strength.And for example soft inside despite one's hard shell gear, the extremely hard flank of tooth are used to resist face impact stress, compared with
Soft gear core is used for the vibration for alleviating gear.In fact, also generally existing is this real using same material in nature
The structure of existing gradient function.Radial section such as culm in plant mutually realized with fiber reinforcement by spacing gradient base material it is flexible,
Intensity, hardness and stress elimination etc. are according to radial and axial different directionality operations.Such as bone, distribution and the high density of bone surface
Compact bone substance has very strong anti-pressure anti-torsion song, is distributed in the low-density cancellous bone storage marrow of inside.These natural structures are all
It is the product of long-term evolution.
At present, the research about the regulation and control of metal 3D printing solidified structure is relatively fewer.Existing report is mainly by adjusting work
Grain size, pattern and analysis are realized in skill parameter and additional temperature field to change bath temperature gradient, setting rate and cooldown rate
Go out the control of phase；Or by path planning strategy, change grain growth texture, to realize anisotropic properties.Such as
Popovich et al. carries out laser metal 3D printing using with the technological parameter of change in location, by the solidification for obtaining graded
Organize to realize the graded of microhardness and tensile property.The studies above is closed for technique-tissue-performance of metal 3D printing
System etc. provides good opinion and theoretical foundation, also provides good method and thinking for structure property regulation and control.But due to
Physical process during laser metal 3D printing is extremely complex, affecting parameters are numerous, it is desirable to solidified structure and performance completely by
Control, which remains, is greatly challenging.At present, still lack effective method and accuracy controlling or customization are carried out to parts locally solidified structure.
The content of the invention
The purpose of the present invention is to propose to a kind of easy to operate, effective laser metal 3D printing method, this method can be realized
Ni-based function part local solidification tissue customization.The present invention is achieved by the steps of：
Step 1：CET model formations are changed to equiaxed dendrite according to Laser Processing nickel-base alloy column
A, n, N in formula0AndFor nickel-base alloy relevant parameter, 1.25 × 10 are taken respectively6、3.4、2×1015And 0.66%, with
Thermograde G is ordinate, freezing rate R is that abscissa draws out the critical curve that nickel-base alloy CET changes, wherein ordinate
G scope is 103-108K/m, abscissa R scope are 10-4-102G-R two-dimensional coordinate systems are divided into two by m/s, the curve
Region, wherein critical curve upper left side are columnar dendrite region, and critical curve lower right is equiaxed dendrite region；
Step 2：Using cooldown rate G*R as definite value, from G*R=10-1Rise, G*R values often rise two magnitudes, in step 1
A curve is drawn out in the G-R two-dimensional coordinate systems of acquisition, further according to λ1=80* (G*R)-0.33, wherein λ1For an interdendritic
Away from or equiaxed dendrite diameter, unit μm, corresponding λ is marked on curve1Value, and then obtain same in G-R two-dimensional coordinate systems
When include dendrite morphology and the solidified structure of dendrite size information selection figure；
Step 3：Destination organization pattern and size according to needed for parts locally, the solidification group obtained from step 2
Knit and thermograde G and freezing rate R scopes corresponding to destination organization are obtained in selection figure；
Step 4：One group of 3D printing technological parameter is inputted into three-dimensional finite element heat transfer model to count temperature field of molten pool
Calculate, extract laser and open 1 second successor thermograde G on the moving boundary of molten bath in a flash1And freezing rate R1Value, with step
Three G, R scopes obtained are compared, if G1And R1G, R scope are in, obtains corresponding 3D printing technological parameter；If G1And
R1G, R scope are not at, the input of 3D printing technological parameter is adjusted repeatedly, until G1And R1G, R scope are in, acquisition meets bar
The technological parameter of part；
Step 5：Repeat step three and step 4, until completing Ni-based function part all sites solidified structure and technique
The matching of parameter；
Step 6：Monolayer slices processing is carried out to Ni-based function part using Cura Slice Softwares, obtains individual layer with position
The 3D printing technological parameter and scanning pattern of change；
Step 7：Section of the repeat step six until completing Ni-based all layers of function part is set with technological parameter；
Step 8：Set input laser metal 3D printing system to carry out 3D printing the technological parameter of customization, had
There is the Ni-based function part of local customization solidified structure.
It is described that the progress monolayer slices processing of Ni-based functional part is comprised the following steps in step 5：
1) according to the change of solidified structure in individual layer, it is mapped to the change of Solidification Parameters；
2) laser parameter and scanning pattern according to the change adjusting process parameter generation of Solidification Parameters with change in location.
In step 7, the section of described Ni-based all layers of the function part of completion is set with technique to be referred to obtain part
With the laser technical parameterses and scanning pattern of locus graded.
In step 8, described laser metal 3D printing system, including powder feeding formula laser metal 3D printing system and powder
Last bed laser metal 3D printing system；Described technological parameter include laser waveform, spot diameter, peak power, sweep speed,
Powder sending quantity, repetition rate, overlapping rate and dutycycle.Due to by calculating, having obtained dendrite morphology and dendrite size information
Solidified structure selection figure, the present invention, can be effectively real using the technological parameter of customization by according to parts locally organizational requirements
The customization of existing parts locally solidified structure, realizes and carries out accuracy controlling to parts locally solidified structure.
Brief description of the drawings
Fig. 1 is the 3D printing sample solidification group for switching to obtain by successively technological parameter in short transverse with this patent method
Knit figure；
Fig. 2 designs the 3D printing sample solidified structure for becoming technological parameter and being obtained to be directed to same layer with this patent method
Figure.
Embodiment
The present invention will be further described with reference to the accompanying drawings and detailed description.
The present invention specifically includes following steps：
Step 1：CET model formations are changed to equiaxed dendrite according to Laser Processing nickel-base alloy column
A, n, N in formula0AndFor nickel-base alloy relevant parameter, 1.25 × 10 are taken respectively6、3.4、2×1015And 0.66%, with
Thermograde G is ordinate, freezing rate R is that abscissa draws out the critical curve that nickel-base alloy CET changes, wherein ordinate
G scope is 103-108K/m, abscissa R scope are 10-4-102G-R two-dimensional coordinate systems are divided into two by m/s, the curve
Region, wherein critical curve upper left side are columnar dendrite region, and critical curve lower right is equiaxed dendrite region.
Step 2：Using cooldown rate G*R as definite value, from G*R=10-1Rise, G*R values often rise two magnitudes, in step 1
A curve is drawn out in the G-R two-dimensional coordinate systems of acquisition, further according to λ1=80* (G*R)-0.33, wherein λ1For an interdendritic
Away from or equiaxed dendrite diameter, unit μm, corresponding λ is marked on curve1Value, and then obtain same in G-R two-dimensional coordinate systems
When include dendrite morphology and the solidified structure of dendrite size information selection figure.
Step 3：Destination organization pattern and size according to needed for parts locally, the solidification group obtained from step 2
Knit and thermograde G and freezing rate R scopes corresponding to destination organization are obtained in selection figure.
Step 4：One group of 3D printing technological parameter is inputted into three-dimensional finite element heat transfer model to count temperature field of molten pool
Calculate, extract laser and open 1 second successor thermograde G on the moving boundary of molten bath in a flash1And freezing rate R1Value, with step
Three G, R scopes obtained are compared, if G1And R1G, R scope are in, obtains corresponding 3D printing technological parameter；If G1And
R1G, R scope are not at, the input of 3D printing technological parameter is adjusted repeatedly, until G1And R1G, R scope are in, acquisition meets bar
The technological parameter of part；
Step 5：Repeat step three and step 4, until completing Ni-based function part all sites solidified structure and technique
The matching of parameter；
Step 6：Monolayer slices processing is carried out to Ni-based function part using Cura Slice Softwares, obtains individual layer with position
The 3D printing technological parameter and scanning pattern of change；
Step 7：Section of the repeat step six until completing Ni-based all layers of function part is set with technological parameter；
Step 8：Set input laser metal 3D printing system to carry out 3D printing the technological parameter of customization, had
There is the Ni-based function part of local customization solidified structure.
Fig. 1 for using the method that this patent proposes in the case where successively switching process conditions the 3D printing sample solidification group that is obtained
Knit figure.Sample has successively manufacturing feature, and interlamellar spacing is more uniform, and average layer is spaced about 0.6mm (shown in such as Fig. 1 (a)).Explanation
Under the process conditions successively switched, it still is able to control effectively to the floor height of sample.In addition, adjacent layer has different solidifications
Tissue topography, odd-level are made up of columnar dendrite, and even level is mainly made up of equiaxed dendrite/born of the same parents' crystalline substance, illustrate that the technique can
Effectively change Solidification Microstructure Morphology.Fig. 1 (b) and (c) are respectively even level and odd-level typical case's arborescent structure pattern.Fig. 1 (b) is main
To be made up of equiaxed dendrite/born of the same parents' crystalline substance of ordered arrangement, and Fig. 1 (c) is made up of the columnar dendrite of high-sequential.Fig. 1 (c) and (e)
The respectively high power SEM patterns of respective regions, it can be seen that the arborescent structure of sample is highly uniform, an average interdendritic away from
About 4.5 μm, and average equiaxed dendrite diameter is about 3.8 μm.The above results show, can be effectively right using this patent method
Accuracy controlling or customization are carried out along the solidified structure of short transverse.
Fig. 2 is become the 3D printing sample that technological parameter obtained for same layer design for the method that is proposed using this patent and coagulated
Gu organization chart.Fig. 2 (a) is the overall pattern of sample interface.Macroscopically sample left end has typical banded structure, integral color
Relatively deep, tissue is difficult to differentiate, and sample right-hand member color is relatively bright, can distinguish its columnar dendrite form.Fig. 2 (b) and (c) are
The low power of sample left end region and high power metallograph, Fig. 2 (d) are that the SEM of sample schemes.There it can be seen that left end tissue is very
It is fine and closely woven, mainly it is made up of tiny short cylinder or cellular-like dendrite tissue, there is the brilliant string tissue morphology of born of the same parents, its average spacing is about
For 2.9 μm.Fig. 2 (e) and (f) are sample right-hand member low power and high power metallographic structure pattern, and Fig. 2 (g) is SEM patterns.As can be seen that
Sample right-hand member is mainly made up of thick columnar dendrite, and a dendritic arm spacing is 12.8 μm, while also has the secondary of prosperity
Dendrite, Models For Secondary Dendrite Arm are spaced about 4.3 μm.The above results show, using this patent method can effectively to same layer not
Solidified structure with position carries out accuracy controlling or customization.
Claims (4)
- A kind of 1. laser metal 3D printing method for realizing Ni-based function part local solidification tissue customization, it is characterised in that including Following steps：Step 1：CET model formations are changed to equiaxed dendrite according to Laser Processing nickel-base alloy column：A, n, N in formula0AndFor nickel-base alloy relevant parameter, 1.25 × 10 are taken respectively6、3.4、2×1015And 0.66%, with temperature Gradient G is ordinate, freezing rate R is that abscissa draws out the critical curve that nickel-base alloy CET changes, wherein ordinate G's Scope is 103-108K/m, abscissa R scope are 10-4-102G-R two-dimensional coordinate systems are divided into Liang Ge areas by m/s, the curve Domain, wherein critical curve upper left side are columnar dendrite region, and critical curve lower right is equiaxed dendrite region；Step 2：Using cooldown rate G*R as definite value, from G*R=10-1Rise, G*R values often rise two magnitudes, are obtained in step 1 G-R two-dimensional coordinate systems in draw out a curve, further according to λ1=80* (G*R)-0.33, wherein λ1For an interdendritic away from or Equiaxed dendrite diameter, unit μm, corresponding λ is marked on curve1Value, and then obtain and wrapped simultaneously in G-R two-dimensional coordinate systems Containing dendrite morphology and the solidified structure of dendrite size information selection figure；Step 3：Destination organization pattern and size according to needed for parts locally, the solidified structure choosing obtained from step 2 Select and thermograde G and freezing rate R scopes corresponding to destination organization are obtained in figure；Step 4：One group of 3D printing technological parameter is inputted into three-dimensional finite element heat transfer model to calculate temperature field of molten pool, carried Take out laser and open 1 second successor thermograde G on the moving boundary of molten bath in a flash1And freezing rate R1Value, obtained with step 3 G, R scope be compared, if G1And R1G, R scope are in, obtains corresponding 3D printing technological parameter；If G1And R1Do not locate In G, R scope, the input of 3D printing technological parameter is adjusted repeatedly, until G1And R1G, R scope are in, obtains the work for the condition that meets Skill parameter；Step 5：Repeat step three and step 4, join until completing Ni-based function part all sites solidified structure with technique Several matchings；Step 5：Repeat step three and step 4, until completing Ni-based function part all sites solidified structure and technological parameter Matching；Step 6：Monolayer slices processing is carried out to Ni-based function part using Cura Slice Softwares, obtains individual layer with change in location 3D printing technological parameter and scanning pattern；Step 7：Section of the repeat step six until completing Ni-based all layers of function part is set with technological parameter；Step 8：Input laser metal 3D printing system is set to carry out 3D printing the technological parameter of customization, acquisition has office Portion customizes the Ni-based function part of solidified structure.
- A kind of 2. laser metal 3D printing for realizing Ni-based function part local solidification tissue customization according to claim 1 Method, it is characterised in that：It is described that following step is included to the progress monolayer slices processing of Ni-based functional part in step 6 Suddenly：1) according to the change of solidified structure in individual layer, it is mapped to the change of Solidification Parameters；2) laser parameter and scanning pattern according to the change adjusting process parameter generation of Solidification Parameters with change in location.
- A kind of 3. laser metal 3D printing for realizing Ni-based function part local solidification tissue customization according to claim 1 Method, it is characterised in that：In step 7, the section of described Ni-based all layers of the function part of completion is set with technique to be referred to Obtain laser technical parameterses and scanning pattern of the part with locus graded.
- A kind of 4. laser metal 3D printing for realizing Ni-based function part local solidification tissue customization according to claim 1 Method, it is characterised in that：In step 8, described laser metal 3D printing system, including powder feeding formula laser metal 3D printing System and powder bed laser metal 3D printing system；Described technological parameter include laser waveform, spot diameter, peak power, Sweep speed, powder sending quantity, repetition rate, overlapping rate and dutycycle.
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