CN108315577A - Laser gain material manufacture 7XXX systems in-situ Al-base composition powder and preparation - Google Patents
Laser gain material manufacture 7XXX systems in-situ Al-base composition powder and preparation Download PDFInfo
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- CN108315577A CN108315577A CN201810107789.9A CN201810107789A CN108315577A CN 108315577 A CN108315577 A CN 108315577A CN 201810107789 A CN201810107789 A CN 201810107789A CN 108315577 A CN108315577 A CN 108315577A
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- 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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y70/00—Materials specially adapted for additive manufacturing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- 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
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0848—Melting process before atomisation
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Abstract
The present invention provides the preparation methods that a kind of laser gain material manufactures 7XXX systems in-situ Al-base composition powder, including commercial-purity aluminium is heated, and heat up melting after being covered with high temperature covering agent；By KBF4、K2TiF6Uniformly mixing is added after drying in melt；After reaction, required intermediate alloy and technical pure Mg and technical pure Zn are sequentially added, refining agent is added in the melt and carries out refinery by de-gassing, then carries out aerosolization；To obtain the final product.This method is prepared for TiB in situ using melt-growth in situ and High Temperature Gas atomization method2Micro-nano granules enhance 7XXX composite materials, by preparing TiB2Particle reinforced aluminium-based composite wood powder, TiB2Particle even dispersion is distributed in aluminum substrate.Aluminum matrix composite powder prepared by this method has good laser absorption rate, is suitable for laser gain material manufacturing technology.
Description
Technical field
The invention belongs to technical field of material, and 7XXX systems aluminum-base composite is manufactured more particularly, to a kind of laser gain material
Material powder and preparation method.
Background technology
With the development of modern science and technology, the requirement in practical application to material property and technology of preparing becomes more severe
It carves.Contour leading-edge field especially is manufactured in aerospace, weapons, structural material is requiring have the same of high-strength high-plasticity
When, should also have high specific stiffness and specific modulus.The high-end equipment field such as large aircraft is to high-performance, high reliability, economy
With the pursuit of environmental protection, cause the demand to large-scale, accurate, the complicated high tough alloy components of integral light more and more urgent.Laser
Increases material manufacturing technology can solve to take into account the technical barrier that complicated shape and high-performance metal component quickly manufacture, and become solution
The certainly effective way of aerospace manufacturing field key technology difficulty.
However commercialized metal powder is mainly pre-alloying powder prepared by atomization or rotary electrode method at present, by
It is formed on the limitation of the key technical index such as laser absorption rate, alloy powder type available at present is limited.Especially in aluminium
Alloy by Laser material increasing field, since aluminium alloy laser absorption rate is relatively low, only the alloy powder of Al-Si systems is relatively suitable at present
It shares and is manufactured in laser gain material, significantly limit the laser gain material manufacturing technology development of alumina-base material.Currently, utilizing such quotient
Industry powder has prepared the parts of higher dimensional precision, and in aerospace, and the fields such as medical treatment obtain some applications.
Such as Boeing companies of the U.S. start LCD large titanium alloy parts being applied to F-18 and F-22 fighter planes since two thousand,
And the United States Patent (USP) in 2015 having applied for airplane parts increasing material manufacturing system.European AirBus companies start since two thousand six
Undercarriage LCD technology is attempted, and is combined topology optimization design with SLM technologies, realizes titanium alloy engine nacelle
The optimization of hinge manufactures.The forefront in SLM technical research and application is then walked by GE companies of the U.S., and SLM technologies is used to manufacture
T25 engine sensor shells have been used for GE90-94B aero-engines, and are answered by the approval aviation of Federal Aviation management board
With.But the part prepared is also easy to produce the defects of crackle and hole of higher residual stress and micron level, and then lead to material
Expect that fatigue strength, plasticity and toughness reduce.Thus part production yield rate is low, reliability is insufficient and cost remains high.Therefore
Traditional business alloy powder cannot fully meet the manufacture of high-performance components.
Invention content
The present invention is limited for above-mentioned material system and Improvement requirement, it is proposed that a kind of laser gain material manufacture 7XXX systems original
Position aluminum matrix composite powder and preparation method, high laser absorption rate can be provided simultaneously with by having prepared, the high aluminium of particle spherical shape rate
Based composites powder, and technological operation is simple and practicable, low-cost high-efficiency, is appropriate for producing in batches.
The purpose of the present invention is what is be achieved through the following technical solutions：
The present invention provides the preparation method that a kind of laser gain material manufactures 7XXX systems in-situ Al-base composition powder, packets
Include following steps：
A1, commercial-purity aluminium is heated, heat up melting after being covered with high temperature covering agent；
A2, by KBF4、K2TiF6Uniformly mixing is added after drying in the melt that step A1 is obtained, and mechanical agitation carries out anti-
It answers；
A3, after step A2 reaction, take out byproduct of reaction, sequentially add required intermediate alloy and technical pure Mg and
Technical pure Zn is added refining agent and carries out refinery by de-gassing in the melt, controlled at 650~800 DEG C of 10~20min of standing, so
Laggard promoting the circulation of qi atomization；7XXX systems in-situ Al-base composition powder is manufactured up to the laser gain material.
Preferably, in step A1, the high temperature covering agent is JZF-03 type high temperature covering agents.
Preferably, described to be warming up to 650~950 DEG C of meltings in step A1.
Preferably, in step A2, the KBF4、K2TiF6Mass ratio be 1:0.5~1:2.
Preferably, in step A2, the reaction time is 5-60min.
Preferably, in step A3, the refining agent is the harmless aluminum refining agent of JZJ types.
Preferably, in step A3, the aerosolization the specific steps are：Solution is warming up to 700~1200 DEG C, uses Ar
And/or be atomized under He gas shields, 0.5~10MPa of atomization air pressure, it is atomized 0.5~5mm of nozzle diameter of use.Using
The aerosolization parameter area can make powder spherical shape rate, the recovery rate highest of acquisition.If in the range, can not cause
Spherical rate, recovery rate decline.
The present invention also provides a kind of laser gain material manufacture prepared according to preceding method is compound with 7XXX systems in-situ Al-base
Material powder, the group of the aluminum matrix composite become Al-Zn (1%~15%)-Mg (1%~8%)-Cu (0.1%~
10%)-Zr (0.05%~3%)-Sc (0%~3%)-Mn (0%~2%)-Ti (0%~1%).
Preferably, the group of the aluminum matrix composite becomes Al-Zn (1%~15%)-Mg (1%~8%)-Cu (0.1%
~10%)-Zr (0.05%~3%)-Sc (0.05%~3%)-Mn (0.05%~2%)-Ti (0.01%~1%).This hair
It is bright while adding tetra- kinds of trace elements of Zr, Sc, Mn, Ti, the mechanical property for the sample that the laser gain material of acquisition subsequently manufactures can be made
Most preferably.
The micro- Mn that the present invention adds is a kind of common to carry high performance alloying element；Present invention addition is micro
Sc, Ti element can significantly crystal grain thinning, and adding micro Zr elements simultaneously can keep except this advantage, improve material
The stability of material in the high temperature environment.In conclusion addition Zr, Sc, Mn, Ti can improve post laser increasing material manufacturing sample
Mechanical property.
Preferably, the median particle diameter of the 7XXX systems in-situ Al-base composition powder is 3~180 μm, and spherical rate is more than
70%；In the 7XXX systems in-situ Al-base composition powder, including the nanoscale TiB that mass fraction is 0.5%~10%2
Grain, the nanoscale TiB2In the distribution of particle even dispersion and aluminum substrate, the TiB2Particle size is 5~2000nm.It is described
TiB2The mass fraction of particle can cause density of material to rise beyond above range, and toughness significantly reduces, or even can not be prepared into
To spherical powder.
Preferably, the grain structure of the 7XXX systems in-situ Al-base composition powder is equiax crystal, and crystallite dimension is
0.1~5 μm.
Compared with the prior art, the substantive distinguishing features and significant progress that the present invention has are：
1) present invention has been effectively combined the advantage that melt-growth in situ prepares micro-nano particle reinforced.
The aluminum matrix composite powder of micro-nano granules enhancing, powder particle median particle diameter are prepared by the method for melt-growth in situ
Controllable, spherical rate ＞ 70%, recovery rate >=60% at 3~180 μm；The micro-nano TiB of in-situ authigenic in dispersion composite material2
Grain, TiB2Particle size distribution is between 5-2000nm, and while greatly improving the strength of materials, the powder that effectively improves swashs
Absorptivity (>30%) the material application range of alumina-base material laser gain material manufacture, is substantially extended.
2) laser gain material manufacture is carried out using the 7XXX composite powders, it is made relative to traditional al-si system powder
Standby strength of materials plasticity is higher, due to nanometer TiB2The humidification of particle and the effect for inhibiting recrystallization growth can be obtained
Uniformly tiny equiax crystal, grain size distribution is in 0.1-5 μm.Due to the micro-nano that even dispersion is distributed in microstructure of composite
Rice TiB2The presence of particle and tiny equiax crystal, laser gain material prepared by the method for the present invention manufacture aluminum matrix composite component energy
There is high intensity and high-ductility simultaneously.
Description of the drawings
Upon reading the detailed description of non-limiting embodiments with reference to the following drawings, other feature of the invention,
Objects and advantages will become more apparent upon：
Fig. 1 aerosolizing device schematic diagrames of the present invention；
Fig. 2 is the SEM photograph of aluminum matrix composite powder prepared by embodiment 1；Wherein, figure (a) is powder entirety photo,
It is single powder section macrograph to scheme (b).
Specific implementation mode
With reference to specific embodiment, the present invention is described in detail.Following embodiment will be helpful to the technology of this field
Personnel further understand the present invention, but the invention is not limited in any way.It should be pointed out that the ordinary skill of this field
For personnel, without departing from the inventive concept of the premise, several changes and improvements can also be made.These belong to the present invention
Protection domain.
Following embodiment provides a kind of preparation side of laser gain material manufacture 7XXX systems in-situ Al-base composition powder
Method includes the following steps：
A1, commercial-purity aluminium is heated, heat up melting after being covered with high temperature covering agent；
A2, by KBF4、K2TiF6Uniformly mixing is added after drying in the melt that step A1 is obtained, and mechanical agitation carries out anti-
It answers；
A3, after step A2 reaction, take out byproduct of reaction, sequentially add required intermediate alloy and technical pure Mg and
Technical pure Zn is added refining agent and carries out refinery by de-gassing in the melt, controlled at 650~800 DEG C of 10~20min of standing, so
Laggard promoting the circulation of qi atomization；7XXX systems in-situ Al-base composition powder is manufactured up to the laser gain material.
In step A1, the high temperature covering agent is JZF-03 type high temperature covering agents.
It is described to be warming up to 650~950 DEG C of meltings in step A1.
In step A2, the KBF4、K2TiF6Mass ratio be 1:0.5~1:2.
In step A2, the reaction time is 5-60min.
In step A3, the refining agent is the harmless aluminum refining agent of JZJ types.
In step A3, the aerosolization the specific steps are：Solution is warming up to 700~1200 DEG C, uses Ar and/or He gas
It is atomized under body protection, 0.5~10MPa of atomization air pressure is atomized 0.5~5mm of nozzle diameter of use.Using the aerosol
Change parameter area, powder spherical shape rate, the recovery rate highest of acquisition can be made.If spherical rate in the range, can not caused, received
Rate declines.
Following embodiment additionally provides a kind of laser gain material manufacture 7XXX systems in-situ Al-base prepared according to preceding method
Composite powder, the group of the aluminum matrix composite become Al-Zn (1%~15%)-Mg (1%~8%)-Cu (0.1%~
10%)-Zr (0.05%~3%)-Sc (0%~3%)-Mn (0%~2%)-Ti (0%~1%).
The micro- Mn that the present invention adds is a kind of common to carry high performance alloying element；Present invention addition is micro
Sc, Ti element can significantly crystal grain thinning, and adding micro Zr elements simultaneously can keep except this advantage, improve material
The stability of material in the high temperature environment.In conclusion addition Zr, Sc, Mn, Ti can improve post laser increasing material manufacturing sample
Mechanical property.And the present invention adds tetra- kinds of trace elements of Zr, Sc, Mn, Ti simultaneously, and the laser gain material of acquisition can be made subsequently to manufacture
The mechanical property of sample is best.
The median particle diameter of the 7XXX systems in-situ Al-base composition powder is 3~180 μm, and spherical rate is more than 70%；Institute
It states in 7XXX systems in-situ Al-base composition powder, including the nanoscale TiB that mass fraction is 0.5%~10%2Particle, it is described
Nanoscale TiB2In the distribution of particle even dispersion and aluminum substrate, the TiB2Particle size is 5~2000nm.The TiB2 particles
Mass fraction density of material can be caused to rise beyond above range, toughness significantly reduces, or even spherical powder can not be prepared
End.
The grain structure of the 7XXX systems in-situ Al-base composition powder is equiax crystal, and crystallite dimension is 0.1~5 μ
m。
Embodiment 1
Experiment is with high-purity Al, technical pure Mg, technical pure Zn, Al-50Cu, Al-12Zr intermediate alloy, KBF4And K2TiF6
In-situ authigenic 5wt.%TiB2 REINFORCED Al -6.7Zn-2.2Mg-2.3Cu-0.1Zr composite materials have been prepared for raw material.It first will be high
Pure Al, which is put into crucible, melts and is warming up to 780 DEG C, is covered with JZF-03 type high temperature covering agents；By KBF4、K2TiF6In mass ratio
1:2 after evenly mixing, is added in melt after drying；Wait for after reaction, take out byproduct of reaction, sequentially add Al-50Cu,
Al-12Zr intermediate alloys and technical pure Mg, technical pure Zn are added the harmless aluminum refining agent of JZJ types and are removed in the melt
Gas refines, and 15min is stood at 750 DEG C, then gas-atomized powder.Its aerosolizing device is as shown in Figure 1, its concrete technology is：
820 DEG C of solution temperature uses He protections and aerosolization, air pressure 2.62MPa, nozzle diameter 2.16mm.The powder of obtained powder
Body structural schematic diagram is as shown in Fig. 2, 34 μm of the average diameter of powder, spherical rate ＞ 90%, recovery rate >=60%, TiB2Particle contains
Measure 5wt.%, 1.8 μm of equiax crystal average grain size in composite powder, laser absorption rate 37%.
Embodiment 2
Experiment is with high-purity Al, technical pure Mg, technical pure Zn, Al-50Cu, Al-12Zr intermediate alloy, KBF4And K2TiF6
In-situ authigenic 5wt.%TiB has been prepared for raw material2REINFORCED Al -6.6Zn-2.2Mg-2.2Cu-0.09Zr composite materials.First will
High-purity Al, which is put into crucible, melts and is warming up to 780 DEG C, is covered with JZF-03 type high temperature covering agents；By KBF4、K2TiF6By quality
Than 1:2 after evenly mixing, is added in melt after drying；Wait for after reaction, take out byproduct of reaction, sequentially add Al-50Cu,
Al-12Zr intermediate alloys and technical pure Mg, technical pure Zn are added the harmless aluminum refining agent of JZJ types and are removed in the melt
Gas refines, and 15min is stood at 750 DEG C, then gas-atomized powder.Its gas atomization is：900 DEG C of solution temperature, uses He
Protect simultaneously aerosolization, air pressure 3.10MPa, nozzle diameter 1.7mm.18 μm of obtained powder average diameter, spherical rate ＞ 90%,
Recovery rate >=60%, TiB2Granule content 5wt.%, 1.1 μm of equiax crystal average grain size in composite powder, laser
Absorptivity 38%.
Embodiment 3
Experiment is with high-purity Al, technical pure Mg, technical pure Zn, Al-50Cu, Al-12Zr intermediate alloy, KBF4And K2TiF6
In-situ authigenic 5wt.%TiB2 REINFORCED Al -6.6Zn-2.2Mg-2.2Cu-0.09Zr composite materials have been prepared for raw material.First will
High-purity Al, which is put into crucible, melts and is warming up to 780 DEG C, is covered with JZF-03 type high temperature covering agents；By KBF4、K2TiF6By quality
Than 1:2 after evenly mixing, is added in melt after drying；Wait for after reaction, take out byproduct of reaction, sequentially add Al-50Cu,
Al-12Zr intermediate alloys and technical pure Mg, technical pure Zn are added the harmless aluminum refining agent of JZJ types and are removed in the melt
Gas refines, and 15min is stood at 750 DEG C, then gas-atomized powder.Its gas atomization is：900 DEG C of solution temperature, uses Ar
Protect simultaneously aerosolization, air pressure 1.20MPa, nozzle diameter 2.16mm.45 μm of obtained powder average diameter, spherical rate ＞
90%, recovery rate >=60%, TiB2Granule content 5wt.%, 2.2 μm of equiax crystal average grain size in composite powder.
Laser absorption rate 38%.
Embodiment 4
Experiment is with high-purity Al, technical pure Mg, technical pure Zn, Al-50Cu, Al-10Mn, Al-12Zr intermediate alloy, KBF4With
And K2TiF6In-situ authigenic 10wt.%TiB has been prepared for raw material2REINFORCED Al -6.6Zn-2.2Mg-2.2Cu-0.7Mn-0.09Zr
Composite material.First high-purity Al is put into crucible and melts and be warming up to 780 DEG C, is covered with JZF-03 type high temperature covering agents；It will
KBF4、K2TiF6In mass ratio 1:2 after evenly mixing, is added in melt after drying；It waits for after reaction, taking out byproduct of reaction,
Al-50Cu, Al-12Zr, Al-10Mn intermediate alloy and technical pure Mg, technical pure Zn are sequentially added, JZJ is added in the melt
The harmless aluminum refining agent of type carries out refinery by de-gassing, 15min is stood at 750 DEG C, then gas-atomized powder.Its gas atomization
For：900 DEG C of solution temperature uses Ar protections and aerosolization, air pressure 5.10MPa, nozzle diameter 2.16mm.Obtained powder is flat
Equal 27 μm of diameter, spherical rate ＞ 90%, recovery rate >=60%, TiB2Granule content 10wt.%, it is isometric in composite powder
1.7 μm of brilliant average grain size, laser absorption rate 56%.
Embodiment 5
Experiment is with high-purity Al, technical pure Mg, technical pure Zn, Al-50Cu, Al-10Mn, Al-12Zr intermediate alloy, KBF4With
And K2TiF6In-situ authigenic 8wt.%TiB has been prepared for raw material2REINFORCED Al -6.6Zn-2.2Mg-2.2Cu-0.7Mn-0.09Zr
Composite material.First high-purity Al is put into crucible and melts and be warming up to 780 DEG C, is covered with JZF-03 type high temperature covering agents；It will
KBF4、K2TiF6In mass ratio 1:2 after evenly mixing, is added in melt after drying；It waits for after reaction, taking out byproduct of reaction,
Al-50Cu, Al-12Zr, Al-10Mn intermediate alloy and technical pure Mg, technical pure Zn are sequentially added, JZJ is added in the melt
The harmless aluminum refining agent of type carries out refinery by de-gassing, 15min is stood at 750 DEG C, then gas-atomized powder.Its gas atomization
For：900 DEG C of solution temperature uses 50%Ar and 50%He mixing gas shielded and aerosolization, air pressure 3.10MPa, nozzle diameter
1.7mm.22 μm of obtained powder average diameter, spherical rate ＞ 90%, recovery rate >=60%, TiB2Granule content 8wt.%,
1.4 μm of equiax crystal average grain size in composite powder, laser absorption rate 49%.
Embodiment 6
Experiment is with high-purity Al, technical pure Mg, technical pure Zn, Al-50Cu, Al-10Mn, Al-12Zr, Al-2Sc, Al-10Ti
Intermediate alloy, KBF4And K2TiF6In-situ authigenic 5wt.%TiB has been prepared for raw material2REINFORCED Al -6.6Zn-2.2Mg-
2.2Cu-0.7Mn-0.1Zr-0.1Sc-0.01Ti composite material.First high-purity Al is put into crucible and melts and be warming up to 780 DEG C,
It is covered with JZF-03 type high temperature covering agents；By KBF4、K2TiF6In mass ratio 1:2 after evenly mixing, is added in melt after drying；
It waits for after reaction, taking out byproduct of reaction, sequentially adding in Al-50Cu, Al-12Zr, Al-2Sc, Al-10Mn, Al-10Ti
Between alloy and technical pure Mg, technical pure Zn, the harmless aluminum refining agent of JZJ types is added in the melt and carries out refinery by de-gassing,
15min is stood at 750 DEG C, then gas-atomized powder.Its gas atomization is：900 DEG C of solution temperature uses Ar protections and aerosol
Change, air pressure 3.07MPa, nozzle diameter 2.16mm.25 μm of obtained powder average diameter, spherical rate ＞ 90%, recovery rate >=
60%, TiB2Granule content 5wt.%, 1.3 μm of composite powder average grain size, laser absorption rate 37%.
Embodiment 7
The present embodiment and the experimental procedure of embodiment 1 are essentially identical, the difference is that only：With high-purity Al, technical pure Mg,
Technical pure Zn, Al-50Cu, Al-12Zr intermediate alloy, KBF4And K2TiF6In-situ authigenic 0.5wt.% has been prepared for raw material
TiB2REINFORCED Al -15Zn-7Mg-10Cu-0.05Zr composite materials.34 μm of obtained powder average diameter, spherical rate ＞
90%, recovery rate >=60%, TiB2Granule content 0.5wt.%, 3.7 μm of composite powder average grain size, laser absorption
Rate 33%.
It is prepared for subsequent sample using laser gain material made from 1-7 of the embodiment of the present invention, obtains extraordinary power
Learn performance.And the mechanical property of the laser gain material of the preparation of embodiment 6 is best.
Specific embodiments of the present invention are described above.It is to be appreciated that the invention is not limited in above-mentioned
Particular implementation, those skilled in the art can make a variety of changes or change within the scope of the claims, this not shadow
Ring the substantive content of the present invention.In the absence of conflict, the feature in embodiments herein and embodiment can arbitrary phase
Mutually combination.
Claims (10)
1. a kind of preparation method of laser gain material manufacture 7XXX systems in-situ Al-base composition powder, which is characterized in that including
Following steps：
A1, commercial-purity aluminium is heated, heat up melting after being covered with high temperature covering agent；
A2, by KBF4、K2TiF6Uniformly mixing is added after drying in the melt that step A1 is obtained, and mechanical agitation is reacted；
A3, after step A2 reaction, take out byproduct of reaction, sequentially add required intermediate alloy and technical pure Mg and industry
Pure Zn, in the melt be added refining agent carry out refinery by de-gassing, controlled at 650~800 DEG C standing 10~20min, then into
Promoting the circulation of qi is atomized；7XXX systems in-situ Al-base composition powder is manufactured up to the laser gain material.
2. the preparation method of laser gain material manufacture 7XXX systems in-situ Al-base composition powder according to claim 1,
It is characterized in that, in step A1, the high temperature covering agent is JZF-03 type high temperature covering agents.
3. the preparation method of laser gain material manufacture 7XXX systems in-situ Al-base composition powder according to claim 1,
It is characterized in that, in step A1, it is described to be warming up to 650~950 DEG C of meltings.
4. the preparation method of laser gain material manufacture 7XXX systems in-situ Al-base composition powder according to claim 1,
It is characterized in that, in step A2, the KBF4、K2TiF6Mass ratio be 1:0.5~1:2.
5. the preparation method of laser gain material manufacture 7XXX systems in-situ Al-base composition powder according to claim 1,
It is characterized in that, in step A2, the reaction time is 5-60min.
6. the preparation method of laser gain material manufacture 7XXX systems in-situ Al-base composition powder according to claim 1,
It is characterized in that, in step A3, the refining agent is the harmless aluminum refining agent of JZJ types.
7. the preparation method of laser gain material manufacture 7XXX systems in-situ Al-base composition powder according to claim 1,
It is characterized in that, in step A3, the aerosolization the specific steps are：Solution is warming up to 700~1200 DEG C, using Ar and/or
It is atomized under He gas shields, 0.5~10MPa of atomization air pressure, is atomized 0.5~5mm of nozzle diameter of use.
8. laser gain material prepared by a kind of method according to claim 1 manufactures 7XXX systems in-situ Al-base composition powder
End, which is characterized in that the group of the aluminum matrix composite becomes Al-Zn (1%~15%)-Mg (1%~8%)-Cu (0.1%
~10%)-Zr (0.05%~3%)-Sc (0%~3%)-Mn (0%~2%)-Ti (0%~1%).
9. the laser gain material that according to claim 8 prepared by method manufactures 7XXX systems in-situ Al-base composition powder,
It is characterized in that, the median particle diameter of the 7XXX systems in-situ Al-base composition powder is 3~180 μm, and spherical rate is more than 70%；Institute
It states in 7XXX systems in-situ Al-base composition powder, including the nanoscale TiB that mass fraction is 0.5%~10%2Particle, it is described
Nanoscale TiB2In the distribution of particle even dispersion and aluminum substrate, the TiB2Particle size is 5~2000nm.
10. the laser gain material that according to claim 9 prepared by method manufactures 7XXX systems in-situ Al-base composition powder,
It is characterized in that, the grain structure of the 7XXX systems in-situ Al-base composition powder is equiax crystal, and crystallite dimension is 0.1~5 μ
m。
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