CN110449578A - A kind of 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance and its application - Google Patents
A kind of 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance and its application Download PDFInfo
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- 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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- 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
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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
- B22F10/30—Process control
- B22F10/34—Process control of powder characteristics, e.g. density, oxidation or flowability
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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
- B22F10/60—Treatment of workpieces or articles after build-up
- B22F10/66—Treatment of workpieces or articles after build-up by mechanical means
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y10/00—Processes of additive manufacturing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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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
- B22F10/30—Process control
- B22F10/36—Process control of energy beam parameters
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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
- B22F12/00—Apparatus or devices specially adapted for additive manufacturing; Auxiliary means for additive manufacturing; Combinations of additive manufacturing apparatus or devices with other processing apparatus or devices
- B22F12/10—Auxiliary heating means
- B22F12/17—Auxiliary heating means to heat the build chamber or platform
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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
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- 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 invention belongs to increasing material manufacturing and powder metallurgical technology, a kind of 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance and its application are disclosed.The drip molding is first to mix Ta powder and 7050 Al alloy powders of sieving；Again using single laser printing, laser power is 450~500W, and preheating temperature is 200~250 DEG C, prints on substrate, obtains 7050 Al-alloy parts containing Ta；Finally 7050 Al-alloy parts containing Ta are cut from substrate using cutting machine obtained.The drip molding can be in the application in powder metallurgy and material increasing field.
Description
Technical field
The invention belongs to increasing material manufacturing and powder metallurgical technologies, close more particularly, to a kind of 7050 aluminium of high-performance
Golden 3D printing precinct laser fusion drip molding and its application.
Background technique
3D printing technique, also referred to as increases material manufacturing technology are known as the core technology of " the third time industrial revolution ".Mainly
Include four kinds of molding modes, selective laser sintering (SLS), electron beam melting (EBM), precinct laser fusion (SLM) and laser
Near-net-shape (LENS), wherein the emphasis studied is precinct laser fusion (SLM).
2011, Erlangen, Germany-Nuremburge Friedrich Alexandria university carried out 7 systems alloy 3D and has beaten
Print SLM single track forming report, it was demonstrated that its feasibility；
Then, Hamburg, Germany polytechnical university Kaufmann N, Imran M, Wischeropp T M etc. joins with regard to SLM technique
Several influences to 7075 aluminium alloy forming qualities expand research, by Optimal Parameters, such as adjust laser power, scanning mode,
Scanning speed, powder thickness etc. are finally obtained consistency up to 99% or more sample[7].However fire check is one still wait solve
Certainly the problem of.Although can be reduced by increasing thickness, improving preheating temperature, laser remolten and increasing the means such as spot diameter
Hot cracking tendency when SLM shapes, can not but eliminate.It is affected by it, stress can be caused to concentrate at fire check in tension test,
Formation of crack is formed, generates brittle fracture, sample is almost without elongation percentage.Simultaneously in the Z-axis direction, by incomplete fusion defective effect, room
A quarter of the warm tensile strength not as good as the direction XOY.
2014, the Kruth team of Belgian Univ Louvain achieved progress on probing into the direction how to reduce crackle.
Although the consistency of final molding part only has 98.9%, the flawless forming of 7xxx series high-strength aluminum alloy is realized.Principle is
Si of the partial size less than 10 μm for adding 4wt%, shapes after mixing with 21 aluminium alloy powder of matrix powder, by refining crystal grain, subtracts
Hot cracking tendency when small 7075 aluminium alloy SLM shapes, to achieve the purpose that eliminate its fire check.
The same year, domestic Central China University of Science and Technology Wuhan photoelectricity National Laboratory have started grinding for 7xxx line aluminium alloy SLM forming
Study carefully, it was found that molten bath mode is formed and distribution ground relationship with fire check.The aluminium alloy of SLM forming can setting according to technological parameter
It sets, such as laser energy size, scanning mode, scanning speed, powder thickness and defocusing amount, that is, laser spot from working substance
The setting of distance adjusts, and the power density of spot center is excessively high at laser crossing point, is easy evaporated metal liquid pore-forming, and leaves sharp
Power density distribution in each plane of optical focus is more uniform.And it can substantially be divided into three kinds according to technological parameter and defocusing amount
Molten bath mode: stable heat transfer, stable deep penetration welding and excessive mode.Under stable heat transfer and excessive mode, hot tearing
Line is parallel with deposition direction respectively, almost vertical-growth and in chaotic shape.These crackles only pass through addition microelement ability
Achieve the purpose that elimination, only adjusting and optimizing technological parameter can not be eliminated.
The second half year in 2017, Martin J H, Yahata the B D, Hundley in California, USA university balabala branch school
J M et al. obtains uniform mixture by electrostatic assembly technology.Nanometer ZrH in powder2Particle is as heterogeneous forming core matter
Point is evenly distributed in 7050 powder surfaces, plays the role of refining crystal grain.And there is directionality originally, it is easy to cause hot tearing
Column crystal be converted into all directions size and differ lesser equiax crystal, enhance heat crack resistance, reduce hot tearing sensibility,
It is achieved to make the SLM of 7050 high strength alumin ium alloy flawlesses shape.The 7 molding major defects of line aluminium alloy 3D printing SLM
Being when forming that hot fire check only relies on optimization print parameters can not eliminate, although and adding the effect after Si by refinement crystal grain
Fire check when aluminium alloy SLM forming is reduced, realizes flawless forming but Si as the impurity element in aluminium alloy, at
The consistency of shape part only has 98.9%, with greatly affected drip molding performance.
Summary of the invention
In order to solve above-mentioned the shortcomings of the prior art and disadvantage, the object of the present invention is to provide a kind of high-performance
7050 aluminium alloy 3D printing precinct laser fusion drip moldings.
Another object of the present invention is the provision of above-mentioned 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance
Application.
The purpose of the present invention is realized by following technical proposals:
A kind of 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance, the drip molding be first by Ta powder and
The 7050 Al alloy powders mixing of sieving；Again using single laser printing, laser power is 450~500W, and preheating temperature is
It 200~250 DEG C, is printed on substrate, obtains 7050 Al-alloy parts containing Ta；Finally 7050 aluminium containing Ta are closed using cutting machine
Golden part cuts obtained from substrate.
Preferably, the aperture of the sieve is 45~90 μm.
Preferably, the mass ratio of the Ta powder and 7050 Al alloy powders is 1:(15~49).
Preferably, the mixed time is 1~2h.
Preferably, the porosity of 7050 Al-alloy parts containing Ta is 5~7%.
The 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance is led in powder metallurgy and increasing material manufacturing
Application in domain.
High strength alumin ium alloy of the present invention is not easy 3D printing forming because its hot tearing sensibility is high, and relative to column crystal, it is tiny
Uniform isometric crystal structure, which can accommodate more strains, prevents hot tearing.In the method for obtaining tiny equiax crystal, most common hand
Section is crystal grain refinement, and introducing alloying element in original alloy system it is made to generate heterogeneous forming core core is a kind of effective crystalline substance
Grain thinning method.The present invention selects Ta element as heterogeneous 7050 aluminium alloy of nucleating agent 3D printing, and passes through optical microscopy, sweeps
The analysis means of testing such as Electronic Speculum, X-ray diffraction, microhardness testers is retouched to study Ta to 7050 aluminum alloy organization of 3D printing and performance
Influence.The result shows that the consistency of alloy can be improved in the introducing of Ta element relative to 7050 aluminium alloy of 3D printing, heat is reduced
Sensibility is split, significantly refinement crystal grain, improves hardness, enhance corrosion resistance.The main reason is that during 3D printing, Ta can be with
Al reaction generates the Al of 300-500nm3Ta refines crystal grain as the heterogeneous forming core core of Al, has 7050-Ta aluminium alloy thin
Small uniform isometric crystal structure, this structure can substantially reduce fire check, and generate refined crystalline strengthening effect.In addition, Dispersed precipitate
Al3Ta can slow down the immersion corrosion rate of alloy.
Compared with prior art, the invention has the following advantages:
1. the present invention, as heterogeneous nucleating agent, is formed by addition alloying element Ta to reduce by 7 series high-strength aluminum alloy SLM
When hot tearing sensibility, eliminate crackle, reduce porosity, improve the performance of drip molding.Ta applies to aluminium alloy as additive
Forming in when, will form hard phase, wrapped up as core by Al, to alloy matrix aluminum rise invigoration effect.
2. the present invention, in forming process, Ta and Al will form Al3Ta.This is a kind of novel high-temperature structural material, In
7050 aluminium alloy SLM can play the role of refining crystal grain and solution strengthening when shaping, to reduce ardent tendency, improve fine and close
Degree reduces porosity, promotes sample performance.
Detailed description of the invention
Fig. 1 is powder morphology and ingredient in embodiment 1: (a, c) Ta powder, (b, d) 7050 Al alloy powder.
Fig. 2 is in comparative example 1 7050 (a) and the metallographic of 7050-Ta (b, c) sample in embodiment 1.
Fig. 3 is that the porosity figure shown after threshold value with gray scale is adjusted in embodiment 1.
Fig. 4 is the X diffracting spectrum of 7050 samples in embodiment 1 in 7050-Ta and comparative example 1.
Fig. 5 be comparative example 1 in 7050 and embodiment 1 in 7050-Ta sample EBSD image and grain size distribution.
Fig. 6 is the microscopic appearance of 3D printing 7050-Ta aluminium alloy in embodiment 1.
Fig. 7 is 7050-Ta microhardness histogram in embodiment 1.
Fig. 8 is 7050-Ta aluminium alloy in metallographic (a, b) after 7050 aluminum alloy specimens corrosion in comparative example 1 and embodiment 1
Metallographic (c, d) after sample corrosion.
Fig. 9 be embodiment 1 in 7050-Ta and comparative example 1 in 7050 samples corrosion after Cross Section Morphology.
Specific embodiment
The contents of the present invention are further illustrated combined with specific embodiments below, but should not be construed as limiting the invention.
Unless otherwise specified, the conventional means that technological means used in embodiment is well known to those skilled in the art.Except non-specifically
Illustrate, reagent that the present invention uses, method and apparatus is the art conventional reagents, method and apparatus.
Embodiment 1
1. sieving powder: using sieving machine (brand and model TURBULAT2F, 220V, 50Hz, 0.18kW) sieving (screen size
90 μm), the case where powder size is not inconsistent appearance can be effectively prevented, and will be partially due to adhesion caused by the reasons such as transport
The powder sieving of reunion falls, and undesirable situation when SLM caused by substantially removing because of factors such as powder sizes shapes occurs
A possibility that.
2. mixed powder: mixed using three-dimensional swing powder mixer according to 2wt%Ta powder and 98wt%7050 Al alloy powder
1-2h is extremely mixed.
3. printing: printing device therefor model (platinum power spy metal additive manufacture machine
S200.Single laser, laser power: 500W；Substrate size: 105mm × 105mm；Preheating temperature: 250 DEG C), print parameters
For laser power 210W, scanning speed 165mm/s, other print parameters are as shown in table table 2, specimen coding (reference numeral 1~6
Example 1~6) as shown in table 3.
4. cutting from substrate after having printed using electro-spark cutting machine, corresponding performance is tested.
Embodiment 2
Different from embodiment 1 is: the mass ratio of the Ta powder and 7050 Al alloy powders is 1:49, and print parameters are
Laser power 310W, scanning speed 165mm/s.
Embodiment 3
Different from embodiment 1 is: the mass ratio of the Ta powder and 7050 Al alloy powders is 1:24, and print parameters are
Laser power 210W, scanning speed 115mm/s.
Embodiment 4
Different from embodiment 1 is: the mass ratio of the Ta powder and 7050 Al alloy powders is 1:24, and print parameters are
Laser power 210W, scanning speed 165mm/s.
Embodiment 5
Different from embodiment 1 is: the mass ratio of the Ta powder and 7050 Al alloy powders is 1:10, and print parameters are
Laser power 260W, scanning speed 115mm/s.
Embodiment 6
Different from embodiment 1 is: the mass ratio of the Ta powder and 7050 Al alloy powders is 3:47, and print parameters are
Laser power 260W, scanning speed 165mm/s.
Comparative example 1
1. sieving powder: using sieving machine (brand and model TURBULAT2F, 220V, 50Hz, 0.18kW) sieving (screen size
90 μm), the case where powder size is not inconsistent appearance can be effectively prevented, and will be partially due to adhesion caused by the reasons such as transport
The powder sieving of reunion falls, and undesirable situation when SLM caused by substantially removing because of factors such as powder sizes shapes occurs
A possibility that.
2. printing: by 7050 Al alloy powders, using three-dimensional swing powder 1-2h to mixing.Print device therefor model
For (platinum power spy metal additive manufacture machine S200.Single laser, laser power: 500W；Base
Board size: 105mm × 105mm；Preheating temperature: 250 DEG C), print parameters be laser power 210W, scanning speed 165mm/s,
His print parameters are as shown in table 2.
3. cutting from substrate after having printed using electro-spark cutting machine, corresponding performance is tested.
Comparative example 2
Different from comparative example 1 is: print parameters are laser power 310W, scanning speed 165mm/s.
Comparative example 3
Different from comparative example 1 is: print parameters are laser power 210W, scanning speed 115mm/s.
Comparative example 4
Different from comparative example 1 is: print parameters are laser power 210W, scanning speed 165mm/s.
Comparative example 5
Different from comparative example 1 is: print parameters are laser power 260W, scanning speed 115mm/s.
Comparative example 6
Different from comparative example 1 is: print parameters are laser power 260W, scanning speed 165mm/s.
7050 Al alloy powder of spherical shape that the elliposoidal Ta powder and granularity that powder used in printing is 45 μm are 90 μm, phase
The powder morphology figure and constituent content answered are as shown in table 1 and Fig. 1:
1 powder body material element of table composition and content
2 print parameters of table
3 embodiment 1-6 sample label of table
The porosity of table 47050-Ta sample
Fig. 2 be comparative example 1 in 7050 (a) and embodiment 1 in 7050-Ta (b, c) sample metallographic.In same printing ginseng
Under several, the consistency for being not added with the 7050 Al alloy powder precinct laser fusion drip moldings of Ta is only 88.6 ± 6%, pore-size
Larger, crack propagation is serious, in Fig. 2 shown in (a).It is easy to cause stress to concentrate in hole and cracks when stress, be made
For formation of crack extension, the mechanical properties such as tensile strength, the elongation percentage of Al-alloy parts are reduced.If as machine components, mechanics
Performance and reliability substantially can not be up to standard.Hole increases the surface area that Al-alloy parts are contacted with the external world, and hole simultaneously
In oxide skin be difficult to remove, the hole of spot corrosion easy to form, and corrosion when as equally distributed particle and sample table
Face formation certain potentials are poor, accelerate the face corrosion of specimen surface, accelerate corrosion rate.Improve workpiece to manufacture, store and make
With the requirement in the process to operating condition and maintenance, increase production and maintenance cost, reduces reliability and service life.From Fig. 2 (b,
C) it is found that the fire check of 7050-Ta sample is less, the hot tearings of 7050 aluminium alloy SLM drip moldings can be reduced and incline by illustrating to add Ta
To raising consistency.
Fig. 3 is that the porosity figure shown after threshold value with gray scale is adjusted in embodiment 1.The printout porosity of addition Ta has
Biggish improvement (table 4).As can be known from Fig. 3,7050-Ta sample mean porosity is minimum to can reach between 5~8%
2.59%.Illustrate that the porosity of 7050 aluminium alloy SLM drip moldings can be reduced by adding Ta.
Fig. 5 be comparative example 1 in 7050 and embodiment 1 in 7050-Ta sample EBSD image and grain size distribution figure.By
(a) is as can be seen that the crystal grain of 7050 aluminium alloy of 3D printing is irregular and coarse, and has columnar crystal structure, fire check edge in Fig. 5
Crystal boundary distribution, average grain size are 74.9 μm.The 3D printing 7050-Ta aluminium alloy of (b) then has fine uniform in Fig. 5
Isometric crystal structure, average grain size are only 4.5 μm, show that the heterogeneous forming core grain refining effect of Ta is significant.
Fig. 4 be comparative example 1 in 7050 and embodiment 1 in 7050-Ta sample X-ray diffractogram, by material carry out X
X ray diffraction, in the diffracting spectrum obtained, the sample of 7050-Ta has had more a peak than 7050 samples, such as the white point institute in Fig. 4
Show, according to the analysis and prediction situation of early period, thus it is speculated that be Al3Ta.Fig. 6 is that the microscopic appearance of 3D printing 7050-Ta aluminium alloy shines
Piece, as seen from the figure, 7050-Ta have fine uniform equiax crystal, and second hand down crystal boundary distribution.Wherein, some having a size of
The particle of 300nm-500nm is present in crystal grain center, by EDX analysis it is found that the Elements Atom percentage of this particle
It is 75.1%Al and 24.9%Ta, therefore, this particle is Al3Ta。
Precinct laser fusion shapes 7050 Al-alloy parts in the case where not adding Ta, average hardness value 76.6~
80HV.And 7050-Ta sample has promotion (Fig. 7) by a small margin under the conditions of 6 kinds of print parameters in average hardness value.This is main
Because Ta element makes the microstructure of 7050 aluminium alloys become the isometric crystal structure of fine uniform, the hot tearing for reducing alloy is quick
Perception reduces the crackle of drip molding, in addition, the Al of the fine uniform of Dispersed precipitate in the base3Ta phase is hard phase, can be strong
Alloy.
During testing hardness, 7050 samples without Ta often will appear the very small situation of hardness number, this be because
For 7050 aluminum alloy specimens, when SLM shapes, consistency is inadequate, and the pressure head of microhardness is small, will appear pole when being pressed onto fault location
Low hardness, it is too low that this also illustrates consistency, and crackle is excessive, and the performance of material is difficult to play completely；In contrast
It is although that, the case where sample of 7050-Ta also occurs hardness decline, in comparison, the number of appearance is seldom, more
Situation is that hardness increases, and reaches 100 or more.It can be analyzed and be obtained by the X ray diffracting spectrum of two kinds of samples, be that Dispersed precipitate is trying
Al in sample3Caused by Ta.When the pressure head of microhardness machine is pressed onto hard phase Al3When Ta, hardness will have on significantly
It rises, simultaneously also by its refined crystalline strengthening and dispersion-strengtherning mechanism, improves the integral hardness of sample.
Fig. 8 is 7050-Ta aluminium alloy in metallographic (a, b) after 7050 aluminum alloy specimens corrosion in comparative example 1 and embodiment 1
Metallographic (c, d) after sample corrosion.As can be seen from Figure 8,7050 specimen surfaces that Ta is not added are corroded completely, and 7050-
Ta specimen surface is more bright, and corrosion focuses primarily upon near hole, is distributed in Pork-pieces spot, is not completely covered entire
Face.It can be seen that the 7050 samples corrosion without Ta is more serious.And the Cross Section Morphology (Fig. 9) after the corrosion of two samples is compared, no
Being difficult to see in 7050 aluminium alloy of 3D printing not only has spot corrosion feature, and there are also the continuous homogeneous corrosion features of bulk, and 7050-Ta is closed
There was only spot corrosion feature in gold, shows that 7050-Ta corrosion resistance is more preferable.Main cause is the Mg and MgZn being dissolved in alloy2The Mg of phase
The increase that hydrogen causes solid solution hydrogen on crystal boundary is easily inhaled, the segregation of hydrogen is formed, the combination of crystal boundary is declined, form corrosion cracking
Source.Al3Ta has very strong corrosion resistance, the tiny Al of Dispersed precipitate3Ta particle can prevent the extension and extension of corrosion cracking.
The above embodiment is a preferred embodiment of the present invention, but embodiments of the present invention are not by above-described embodiment
Limitation, it is other it is any without departing from the spirit and principles of the present invention made by change, modification, substitution, combination and simplify,
It should be equivalent substitute mode, be included within the scope of the present invention.
Claims (6)
1. a kind of 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance, which is characterized in that the drip molding is first
Ta powder and 7050 Al alloy powders of sieving are mixed；Again using single laser printing, laser power is 450~500W, in advance
Hot temperature is 200~250 DEG C, prints on substrate, obtains 7050 Al-alloy parts containing Ta, finally will be containing Ta's using cutting machine
7050 Al-alloy parts cut obtained from substrate.
2. 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance according to claim 1, which is characterized in that
The aperture of the sieve is 45~90 μm.
3. 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance according to claim 1, which is characterized in that
The mass ratio of the Ta powder and 7050 Al alloy powders is 1:(15~49).
4. 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance according to claim 1, which is characterized in that
The mixed time is 1~2h.
5. 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance according to claim 1, which is characterized in that
The porosity of 7050 Al-alloy parts containing Ta is 5~7%.
6. 7050 aluminium alloy 3D printing precinct laser fusion drip molding of high-performance according to claim 1-5 is in powder
Application in last metallurgy and material increasing field.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111097911A (en) * | 2019-12-12 | 2020-05-05 | 南方科技大学 | Ceramic-metal composite foam material and preparation method thereof |
| CN113996807A (en) * | 2021-10-29 | 2022-02-01 | 华中科技大学 | Method for eliminating microcracks in selective laser melting additive manufacturing of 2024 aluminum alloy |
| CN114226736A (en) * | 2021-12-21 | 2022-03-25 | 北京航空航天大学 | Method for inhibiting crack formation and promoting grain refinement of additive manufacturing aluminum alloy |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105154729A (en) * | 2015-09-29 | 2015-12-16 | 济南大学 | Cast aluminum-zinc-magnesium-copper-tantalum alloy and manufacturing method thereof |
| WO2018052515A1 (en) * | 2016-09-19 | 2018-03-22 | Rios, Orlando | Surface-hardened aluminum-race earth alloys and methods of making the same |
| WO2018144323A1 (en) * | 2017-02-01 | 2018-08-09 | Hrl Laboratories, Llc | Aluminum alloys with grain refiners, and methods for making and using the same |
| WO2019055623A1 (en) * | 2017-09-13 | 2019-03-21 | Arconic Inc. | Aluminum alloy products, and methods of making the same |
| CN109904437A (en) * | 2019-02-22 | 2019-06-18 | 上海交通大学 | Increasing material manufacturing aluminium-air cell anode material and preparation method thereof |
-
2019
- 2019-07-02 CN CN201910596778.6A patent/CN110449578A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105154729A (en) * | 2015-09-29 | 2015-12-16 | 济南大学 | Cast aluminum-zinc-magnesium-copper-tantalum alloy and manufacturing method thereof |
| WO2018052515A1 (en) * | 2016-09-19 | 2018-03-22 | Rios, Orlando | Surface-hardened aluminum-race earth alloys and methods of making the same |
| WO2018144323A1 (en) * | 2017-02-01 | 2018-08-09 | Hrl Laboratories, Llc | Aluminum alloys with grain refiners, and methods for making and using the same |
| WO2019055623A1 (en) * | 2017-09-13 | 2019-03-21 | Arconic Inc. | Aluminum alloy products, and methods of making the same |
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