CN109692964A - A kind of reinforced aluminum matrix composites and preparation method thereof - Google Patents
A kind of reinforced aluminum matrix composites and preparation method thereof Download PDFInfo
- Publication number
- CN109692964A CN109692964A CN201910096909.4A CN201910096909A CN109692964A CN 109692964 A CN109692964 A CN 109692964A CN 201910096909 A CN201910096909 A CN 201910096909A CN 109692964 A CN109692964 A CN 109692964A
- Authority
- CN
- China
- Prior art keywords
- aluminum matrix
- reinforced
- matrix composites
- melt
- reinforced aluminum
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- 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
-
- 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
-
- 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
-
- 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
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
-
- 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
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
- C22C1/1052—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites by mixing and casting metal matrix composites with reaction
-
- 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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
-
- 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
- C22C32/0005—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 at least one oxide and at least one of carbides, nitrides, borides or silicides as the main non-metallic constituents
-
- 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
- C22C32/001—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 only oxides
- C22C32/0015—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 only oxides with only single oxides as main non-metallic constituents
- C22C32/0036—Matrix based on Al, Mg, Be or alloys thereof
-
- 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
-
- 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
- C22C32/0052—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 carbides
-
- 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
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Composite Materials (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Powder Metallurgy (AREA)
Abstract
The present invention provides a kind of reinforced aluminum matrix composites and preparation method thereof, and the preparation method is the following steps are included: S1: reinforced phase reactant being carried out melting together with the raw material of acieral, forms reinforced aluminum matrix composites melt；S2: applying atomizing pressure to reinforced aluminum matrix composites melt makes its aerosolization be cooled into powder.By carrying out to reinforced aluminum matrix composites melt, aerosolization is cooling, and melt forms powder under aerosolization effect；Reinforced phase nano particle also has little time to occur to reunite just to be dispersed and fixed in powder under high cooldown rate; and high cooldown rate can effectively inhibit in process of setting solid/liquid interfaces forward position to the traction of heterogeneous granular (i.e. reinforced phase particle); to promoting the reinforced phase of in-situ authigenic to be uniformly distributed in aluminum matrix composite crystal, reinforced phase particle segregation is overcome well in the crystal boundary the problem of.
Description
Technical field
The present invention relates to aluminum matrix composite fields, more particularly to a kind of reinforced aluminum matrix composites and its preparation side
Method.
Background technique
As energy and environmental problem becomes increasingly conspicuous, the neck such as communications and transportation, aerospace, electronic communication and sports industry
Requirement of the domain to material property is continuously improved, to having both various structures and function in the light high performance metal-based compound material of one
The demand of material is increasing.Ceramic particle reinforced aluminium base composite material has the plasticity of metal and the height of obdurability and reinforcement concurrently
The advantages of intensity, high rigidity, has many advantages, such as that lightweight, specific strength are high, specific modulus is high, designability is strong.But traditional aluminium base is multiple
That there are interfacial wettabilities is poor for condensation material, distribution of particles is uneven, it is at high cost be the problems such as influencing its preparation and promote and apply.
Reinforced aluminum matrix composites are a kind of the new of thermodynamically stable reinforced phase to be mixed in traditional aluminum matrix composite
Profile material.Generally, reinforced aluminum matrix composites are prepared using additional method, that is, after aluminum matrix composite is melted it is straight
It connects and reinforced phase melting together is added.Reinforced phase and aluminum matrix composite knot in reinforced aluminum matrix composites made from this method
Close weaker, stability deficiency.
In contrast, above-mentioned ask can be overcome by in-situ authigenic reinforced aluminum matrix composites being made using the method for in-situ authigenic
Topic.This method is just to joined reinforced phase melting together during preparing aluminum matrix composite using various raw materials, in shape
Reinforced phase is wrapped in inside during at aluminum matrix composite, internal reinforced phase Thermodynamically stable, surface no-pollution,
It is high with aluminum matrix composite bond strength.And the enhancing phase size of in-situ authigenic aluminum matrix composite is tiny, generally less than 2 μm,
Even up to nanoscale；Meanwhile reinforced phase in-situ preparation in the melt, it is good with the compatibility of aluminum matrix composite, it can be to aluminium
Based composites play apparent invigoration effect, so that the performance of aluminum matrix composite be made to further increase.
However, the method for in-situ authigenic is in cooling procedure since reinforced phase particle reaches micro/nano-scale, since its is huge
Surface can will lead to apparent particle agglomeration phenomenon, invigoration effect of the reinforced phase to aluminum matrix composite will be seriously undermined.
Summary of the invention
Based on this, the present invention provides a kind of reinforced aluminum matrix composites and its rapid solidification preparation method, can effectively solve
Certainly in aluminum matrix composite, the reinforced phase of in-situ authigenic is due to size is small, surface can generate greatly agglomeration traits.
The preparation methods of reinforced aluminum matrix composites of the present invention the following steps are included:
S1: reinforced phase reactant is subjected to melting together with the raw material of acieral, it is molten to form reinforced aluminum matrix composites
Body；
S2: applying atomizing pressure to reinforced aluminum matrix composites melt makes its aerosolization be cooled into powder.
Compared with prior art, reinforced phase reactant is carried out melting by the present invention together with the raw material of acieral, molten
Reinforced phase reactant generates reinforced phase in the melt internal in-situ reaction of acieral raw material during refining, the original with acieral
Material forms aluminum matrix composite melt.In the melt of high temperature, reinforced phase has very big mobility and dispersibility, can be to receive
The form of rice grain is dispersed in aluminum matrix composite melt without reuniting.To reinforced aluminum matrix composites melt into
Promoting the circulation of qi atomization cooling, melt form powder under aerosolization effect；Reinforced phase nano particle also has little time under high cooldown rate
Occur to reunite and just be dispersed and fixed in powder, to promote the reinforced phase of in-situ authigenic in aluminum matrix composite crystal
Be uniformly distributed, overcome well in the prior art reinforced phase particle segregation in the crystal boundary the problem of.
Further, the atomizing pressure is 1.0~1.3Mpa.
Further, the reinforced phase is one or both of ceramics, intermetallic compound.
Further, the ceramics include TiB2、ZrB2、TiC、Al2O3In any one or more.
Further, the intermetallic compound includes Al3Ti、Al3Zr、Mg2Any one or more in Si.
Further, smelting temperature described in step S1 is 750~900 DEG C
The present invention also provides a kind of reinforced aluminum matrix composites, including acieral and it is dispersed in inside acieral
Reinforced phase, the particle mean size of the reinforced phase is less than 100nm.
Further, the reinforced phase is one or both of ceramics, intermetallic compound.
Further, the ceramics include TiB2、ZrB2、TiC、Al2O3In any one or more；Change between the metal
Closing object includes Al3Ti、Al3Zr、Mg2Any one or more in Si.
Further, the acieral is 2024 aluminium alloys or alusil alloy.
Detailed description of the invention
Fig. 1 is operational flowchart of the invention；
Fig. 2 and Fig. 3 is the microscopic appearance figure of the reinforced aluminum matrix composites of embodiment 1；
Fig. 4 is the photomacrograph of the reinforced aluminum matrix composites of embodiment 1.
Specific embodiment
The operating process of the preparation method of reinforced aluminum matrix composites of the invention as shown in Figure 1, carry out composite wood first
Expect that ingredient design, preparation raw material are simultaneously dried；Then vacuum melting is carried out, and adds reactant in fusion process and keeps
Stirring；Then powder by gas-atomization and densification are carried out.It is cooling by carrying out aerosolization after melting, in high cooldown rate
The lower agglomeration for effectively inhibiting reinforced phase particle in process of setting, promotes being uniformly distributed for reinforced phase particle.Below by way of tool
Body embodiment carrys out the technical solution that the present invention will be described in detail.
Embodiment 1
The present embodiment 1 is with ceramic TiB2As reinforced phase, reinforced phase reactant selects K2TiF6And KBF4Salt-mixture；Aluminium
Based alloy selects 2024 aluminium alloys, and the raw material of 2024 aluminium alloys includes matrix and complex element, and wherein matrix selects the purity to be
99.95% fine aluminium ingot, complex element select purity for 99.95% copper, manganese, magnesium, chromium and zinc ingot, wherein copper, manganese,
Respectively mass ratio is successively for magnesium, chromium, zinc and fine aluminium ingot are as follows: copper: 3.8~4.9%, manganese: 0.30~1.0%, magnesium: 1.2~1.8%,
Chromium: 0.10%, zinc: 0.25%, surplus is aluminium.The in-situ self-generated TiB in preparing 2024 aluminium alloys2The specific steps of reinforced phase are such as
Under:
S1: carrying out melting for reinforced phase reactant together with the raw material of acieral, keeps reinforced phase reactant multiple in aluminium base
Condensation material internal-response generates reinforced phase, forms reinforced aluminum matrix composites melt.
Specifically, according to the molar ratio of 1:2.2 by K2TiF6And KBF4It is ground into fine powder after mixing, is put into box electricity
It hinders and reserves 2h or more in furnace at 200~300 DEG C as TiB2Reinforced phase reactant.In addition in 200~300 DEG C of box resistance
The fine aluminium ingot that purity is 99.95% is preheated into 2h or more in furnace, then will be melted in the fine aluminium ingot investment vacuum melting furnace after preheating
It is melted into melt.Melt temperature is improved to after 850~900 DEG C, TiB is put into melt2Enhance phase reaction
Object.In the agitating device insertion melt that smelting furnace is covered simultaneously, heat preservation 30min is obtained after stirring 5min with the rate of 300r/min
To in-situ self-generated TiB2Melt.
By in-situ self-generated TiB2Melt standing is cooled to 800 DEG C, then sequentially adds according to the sequence of fusing point from high to low
Copper, manganese, magnesium, chromium and the zinc ingot that purity is 99.95% obtain reinforced aluminum matrix composites melt.
S2: applying atomizing pressure to reinforced aluminum matrix composites melt makes its atomization be cooled into powder.
The substep of reinforced aluminum matrix composites melt made from step S1 is poured into the tundish that temperature is 850 DEG C, then
The atomizing pressure for applying 1.1~1.3MPa to it makes its atomization cooling.It specifically, is during 3.0mm diversion pipe is passed through by a diameter
Between in packet, and atomizing medium nitrogen is made to spray to in-situ authigenic reinforced aluminum matrix composites melt by diversion pipe, makes in-situ authigenic
Reinforced aluminum matrix composites melt is cooled into powder by atomization after the atomizing pressure of 1.1~1.3MPa.After atomization, adopt
It is greater than 74 μm of amount of powder with standard screen removal granularity.
S3: densification is carried out to powder.
Successively powder made from step S2 is carried out at densification by the way of cold moudling, hot pressed sintering and heat treatment
Reason.Specifically, first on 400t hydraulic press, the pressure of 300MPa is applied to above-mentioned powder using punching block and keeps 10s, by it
It is cold-pressed into 50 millimeters of diameter of powder compact.Then powder compact is placed in graphite jig, under protection of argon gas, by powder pressure
Base temperature rises to 500 DEG C.45MPa pressure is applied to powder compact after keeping the temperature 10min, and heat-insulation pressure keeping 60min is allowed to form.At
Cool down after type with furnace, obtains block materials；
Finally above-mentioned bulk material is placed in chamber type electric resistance furnace and keeps the temperature 6h, water quenching after heat preservation at 480 DEG C
But.12 hours are kept the temperature in 185 DEG C later, furnace cooling after heat preservation.
Microscopic appearance characterization is carried out to reinforced aluminum matrix composites obtained above using scanning electron microscope, as a result such as
Shown in Fig. 2 and Fig. 3, wherein light-colored particles indicate the TiB of in-situ authigenic2The particle of reinforced phase.Fig. 2 and Fig. 3 reflection, in this implementation
In the reinforced aluminum matrix composites of example, TiB2Reinforced phase is evenly dispersed in aluminum matrix composite with being in granular form, and TiB2Increase
The particle size of strong phase is uniform, by the way that TiB is calculated2Reinforced phase particle mean size is less than 100nm.Referring to figure 4.,
The figure is the photomacrograph for the reinforced aluminum matrix composites that the present embodiment obtains after densification, utilizes the original position of the present embodiment
Spontaneous reinforced aluminum matrix composites can obtain the flaky material of larger size.
Handled by above-mentioned steps, can in aluminum matrix composite in-situ authigenic reinforced phase, and make reinforced phase with nanometer
The form of particle is dispersed in inside aluminum matrix composite, mainly due to during the preparation process, aluminium, copper, manganese, magnesium, chromium and
The metals such as zinc melt binding at high temperature, gradually forms 2024 alloy melts, K2TiF6And KBF4It is gradually former in the melt of high temperature
Position reaction generates reinforced phase TiB2,TiB2Reinforced aluminum matrix composites melt is mixed to form with 2024 alloy melts.Reinforced phase TiB2
Under the melt of high temperature have very high mobility and dispersibility, can in the form of nano particle it is evenly dispersed in the melt and
Do not reunite.
In reinforced aluminum matrix composites melt process of setting, TiB2The distribution of particle and its process of setting have very high point
System, there are three kinds of basic status for the interaction of particle and freezing interface: (1) particle is solidified interface capture and enters matrix crystalline substance
Intragranular portion；(2) particle is not solidified interface capture, but the insertion matrix mechanical by the inhibition of matrix dendrite
Grain boundary；(3) particle is solidified interface repulsion and segregation at final solidified position.Preparing metal-base composites mistake
Journey, it is desirable to which particle is uniformly distributed in the base, and repulsion mechanism is unfavorable for being uniformly distributed for particle.Therefore, quick solidification is utilized
High cooldown rate obtain homogeneous distribution reinforced phase be the key that prepare high-performance in-situ Al-base nanocomposite.
Based on this, the application carries out aerosolization cooling, melt shape under aerosolization effect to the melt of high temperature at once at this time
At powder；Although melting intracorporal reinforced phase TiB2Particle is in nano-scale range, has great surface energy, but due to gas
Atomization cooling procedure has the cooling rate being exceedingly fast, TiB2Nano particle also has little time to occur to reunite just to be dispersed and fixed on
In powder；And high cooldown rate can effectively inhibit in process of setting solid/liquid interfaces forward position to heterogeneous granular (i.e. reinforced phase
Grain) traction, promote the reinforced phase particle of in-situ authigenic to be uniformly distributed in transgranular, overcome well in the prior art
Reinforced phase particle segregation is in the crystal boundary the problem of, so that reinforced phase nano particle be made to be dispersed in final enhancing aluminum-base composite material
Material is internal, effectively reinforcing aluminum substrate.
Embodiment 2
The present embodiment 2 is with intermetallic compound Mg2Si selects alusil alloy-Al-5Si alloy as aluminium as reinforced phase
Based alloy, the raw material of Al-5Si alloy include matrix and complex element, and it is 99.95% fine aluminium ingot that wherein matrix, which selects purity,
Complex element select silicone content for 30% aluminium silicon intermediate alloy.The synthesized Mg in situ in preparation Al-5Si alloy process2Si increases
Specific step is as follows for strong phase:
S1: carrying out melting for reinforced phase reactant together with the raw material of acieral, keeps reinforced phase reactant multiple in aluminium base
Condensation material internal-response generates reinforced phase, forms reinforced aluminum matrix composites melt.
Fine aluminium, pure magnesium and aluminium silicon intermediate alloy are put into chamber type electric resistance furnace the reservation 2h or more at 200~300 DEG C first
Be fused into the spare fine aluminium ingot investment vacuum melting furnace by after preheating after melt melt temperature is improved to 850~
After 900 DEG C and 5~10min of standing, preheated pure magnesium is put into melt.The agitating device that smelting furnace is covered simultaneously
It is inserted into melt, keeps the temperature 20min after stirring 5min with the rate of 300r/min.
Then it stands addition aluminium silicon intermediate alloy after being cooled to 800 DEG C and obtains reinforced aluminum matrix composites melt.
S2: applying atomizing pressure to reinforced aluminum matrix composites melt makes its atomization be cooled into powder.
The substep of reinforced aluminum matrix composites melt made from step S1 is poured into the tundish that temperature is 850 DEG C, then
The atomizing pressure for applying 1.1~1.3MPa to it makes its atomization cooling.It specifically, is during 2.5mm diversion pipe is passed through by a diameter
Between in packet, and atomizing medium nitrogen is made to spray to in-situ authigenic reinforced aluminum matrix composites melt by diversion pipe, makes in-situ authigenic
Reinforced aluminum matrix composites melt is cooled into powder by atomization after the atomizing pressure of 1.1~1.2MPa.After atomization, adopt
It is greater than 74 μm of amount of powder with standard screen removal granularity.
S3: densification is carried out to powder.
Densification successively is carried out to powder made from step S2 by the way of cold moudling and hot pressed sintering.Specifically
Ground applies the pressure of 300MPa to above-mentioned powder using punching block and keeps 10s, be cold-pressed into first on 400t hydraulic press
The powder compact that 50 millimeters of diameter.Then powder compact is placed in graphite jig, under protection of argon gas, by powder compact temperature
Rise to 500 DEG C.45MPa pressure is applied to powder compact after keeping the temperature 10min, and heat-insulation pressure keeping 60min is allowed to form.
Following variation occurs for each reactant and raw material during the preparation process: magnesium, aluminium and sial intermediate alloy melt at high temperature
Melt is closed, and aluminium and sial intermediate alloy gradually form Al-5Si alloy.Meanwhile the silicon having more in magnesium and sial intermediate alloy is in height
Gradually reaction in-situ generates reinforced phase Mg in the melt of temperature2Si.Reinforced phase Mg2Si has very high flowing under the melt of high temperature
Property and dispersibility, can in the form of nano particle it is evenly dispersed in the melt without reunite.At this time at once to high temperature
Melt carries out aerosolization cooling, and melt forms powder under aerosolization effect；Although melting intracorporal reinforced phase Mg2Si particle is in
In nano-scale range, there is great surface energy, but since aerosolization cooling procedure has the cooling rate being exceedingly fast, Mg2Si
Nano particle also has little time to occur to reunite just to be dispersed and fixed in powder, to make final reinforced aluminum matrix composites
Inside has evenly dispersed reinforced phase nano particle.
Embodiment 3
The present embodiment 3 is with TiB2/Mg2Si is as reinforced phase, TiB2/Mg2The reactant of Si reinforced phase selects K2TiF6With
KBF4Salt-mixture and purity be 99.95% pure magnesium, sial intermediate alloy.Select alusil alloy-Al-7Si alloy as aluminium
Based alloy, the raw material of Al-7Si alloy include matrix and complex element, and it is 99.95% fine aluminium ingot that wherein matrix, which selects purity,
Complex element select silicone content for 30% aluminium silicon intermediate alloy.The in-situ self-generated TiB in preparation Al-7Si alloy process2/
Mg2Specific step is as follows for Si reinforced phase:
S1: carrying out melting for reinforced phase reactant together with the raw material of acieral, keeps reinforced phase reactant multiple in aluminium base
Condensation material internal-response generates reinforced phase, forms reinforced aluminum matrix composites melt.
First, in accordance with the molar ratio of 1:2.2 by K2TiF6And KBF4It is ground into fine powder after mixing, is put into chamber type electric resistance furnace
In at 200~300 DEG C preheat 2h or more it is spare.In addition under the same conditions to fine aluminium ingot, pure magnesium and sial intermediate alloy into
The pre- stand-by heat of row.
Melt will be fused into fine aluminium ingot investment vacuum melting furnace after preheating.By melt temperature improve to
After 850~900 DEG C and 5~10min of standing, preheated pure magnesium and K are put into melt2TiF6With KBF4Mixing
Salt.In the agitating device insertion melt that smelting furnace is covered simultaneously, 30min is kept the temperature after stirring 5min with the rate of 300r/min.
Then it stands addition aluminium silicon intermediate alloy after being cooled to 800 DEG C and obtains reinforced aluminum matrix composites melt.
S2: applying atomizing pressure to in-situ authigenic reinforced aluminum matrix composites melt makes its atomization be cooled into powder.
The substep of reinforced aluminum matrix composites melt made from step S1 is poured into the tundish that temperature is 850 DEG C, then
The atomizing pressure for applying 1.1~1.3MPa to it makes its atomization cooling.It specifically, is during 3.5mm diversion pipe is passed through by a diameter
Between in packet, and atomizing medium nitrogen is made to spray to in-situ authigenic reinforced aluminum matrix composites melt by diversion pipe, makes in-situ authigenic
Reinforced aluminum matrix composites melt is cooled into powder by atomization after the atomizing pressure of 1.1~1.2MPa.After atomization, adopt
It is greater than 74 μm of amount of powder with standard screen removal granularity.
S3: densification is carried out to powder.
Densification is carried out to powder made from step S2 by the way of hot extrusion.Specifically, by load weighted powder
End is fitted into aluminium jacket, in 350 DEG C of vacuum suction 4h.It is heated to 450 DEG C later and keeps the temperature 2h.Finally use 800t extruder pair
Powder applies 400MPa pressure according to 12 extrusion ratio for its extrusion forming.
Following variation occurs for each reactant and raw material during the preparation process: magnesium, aluminium and sial intermediate alloy melt at high temperature
Melt is closed, and aluminium and sial intermediate alloy gradually form Al-7Si alloy.Meanwhile the silicon having more in magnesium and sial intermediate alloy is in height
Gradually reaction in-situ generates reinforced phase Mg in the melt of temperature2Si, K2TiF6And KBF4Gradually reaction in-situ is raw in the melt of high temperature
At reinforced phase TiB2.Reinforced phase TiB2And Mg2Si(TiB2/Mg2Si) there is very high mobility and dispersion under the melt of high temperature
Property, it can be evenly dispersed in the melt without reuniting in the form of nano particle.The melt of high temperature is carried out at once at this time
Aerosolization is cooling, and melt forms powder under aerosolization effect；Although melting intracorporal reinforced phase TiB2/Mg2Si particle is in nanometer
In size range, there is great surface energy, but since aerosolization cooling procedure has the cooling rate being exceedingly fast, TiB2/Mg2Si
Nano particle also has little time to occur to reunite just to be dispersed and fixed in powder, to make final reinforced aluminum matrix composites
Inside has evenly dispersed reinforced phase nano particle.
Compared with the existing technology, the present invention carries out melting in the raw material of acieral together with reinforced phase reactant, enhancing
Phase reaction object mixes inside acieral and in-situ authigenic is at reinforced phase, and evenly dispersed wherein with form of nanoparticles, is formed
Reinforced aluminum matrix composites melts improve the interface bond strength of reinforced phase and aluminum matrix composite and the original position of entirety
The thermal stability of spontaneous reinforced aluminum matrix composites.Aerosolization is carried out to the in-situ authigenic reinforced aluminum matrix composites melt of high temperature
It is cooling, also have little time to occur to reunite under high cooldown rate to be just dispersed and fixed in the powder of aerosolization formation, and
High cooldown rate can effectively inhibit solid/liquid interfaces forward position in process of setting to make the passage of heterogeneous granular (i.e. reinforced phase particle)
With overcoming the prior art well so that the reinforced phase particle of in-situ authigenic be promoted to be uniformly distributed in aluminum matrix composite
Middle reinforced phase particle segregation is in the crystal boundary the problem of.Moreover, preparation method of the invention is by in-situ preparation and quick solidification-powder smelting
Technology for gold combines, and preparation flow has been greatly shortened, and improves the utilization rate and production efficiency of material, is suitble to industry metaplasia
It produces.In addition, the powder that aerosolization is cooled into can continue densification using means such as extruding, forging, 3D printings,
It can be further improved the comprehensive performance of composite material.
The embodiments described above only express several embodiments of the present invention, and the description thereof is more specific and detailed, but simultaneously
It cannot therefore be construed as limiting the scope of the patent.It should be pointed out that coming for those of ordinary skill in the art
It says, without departing from the inventive concept of the premise, various modifications and improvements can be made, these belong to protection of the invention
Range.
Claims (10)
1. a kind of preparation method of reinforced aluminum matrix composites, it is characterised in that the following steps are included:
S1: reinforced phase reactant is subjected to melting together with the raw material of acieral, forms reinforced aluminum matrix composites melt；
S2: applying atomizing pressure to reinforced aluminum matrix composites melt makes its aerosolization be cooled into powder.
2. the preparation method of reinforced aluminum matrix composites according to claim 1, it is characterised in that: the atomizing pressure is
1.0~1.3Mpa.
3. the preparation method of reinforced aluminum matrix composites according to claim 2, it is characterised in that: the reinforced phase is pottery
One or both of porcelain, intermetallic compound.
4. the preparation method of reinforced aluminum matrix composites according to claim 3, it is characterised in that: the ceramics include TiB2、
ZrB2、TiC、Al2O3In any one or more.
5. the preparation method of reinforced aluminum matrix composites according to claim 4, it is characterised in that: the intermetallic compound
Including Al3Ti、Al3Zr、Mg2Any one or more in Si.
6. the preparation method of reinforced aluminum matrix composites according to claim 5, it is characterised in that: melting described in step S1
Temperature is 750~900 DEG C.
7. a kind of reinforced aluminum matrix composites, it is characterised in that: including aluminium acieral and be dispersed in inside acieral
Reinforced phase, the particle mean size of the reinforced phase is less than 100nm.
8. according to claim 7 reinforced aluminum matrix composites, it is characterised in that: the reinforced phase is ceramics, intermetallic compound
One or both of.
9. according to claim 8 reinforced aluminum matrix composites, it is characterised in that: the ceramics include TiB2、ZrB2、TiC、Al2O3
In any one or more；The intermetallic compound includes Al3Ti、Al3Zr、Mg2Any one or more in Si.
10. according to claim 9 reinforced aluminum matrix composites, it is characterised in that: the acieral be 2024 aluminium alloys or
Alusil alloy.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910096909.4A CN109692964A (en) | 2019-01-31 | 2019-01-31 | A kind of reinforced aluminum matrix composites and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910096909.4A CN109692964A (en) | 2019-01-31 | 2019-01-31 | A kind of reinforced aluminum matrix composites and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN109692964A true CN109692964A (en) | 2019-04-30 |
Family
ID=66234667
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201910096909.4A Pending CN109692964A (en) | 2019-01-31 | 2019-01-31 | A kind of reinforced aluminum matrix composites and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109692964A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112453422A (en) * | 2020-10-27 | 2021-03-09 | 中南大学 | Light Al-Si-Mg2Si electronic packaging material and preparation method and application thereof |
| CN112593129A (en) * | 2020-12-11 | 2021-04-02 | 江苏科技大学 | ZrB2Ceramic particle modified Al-Zn-Mg-Cu aluminum alloy welding rod and preparation method thereof |
| CN112725663A (en) * | 2020-12-30 | 2021-04-30 | 江苏智仁景行新材料研究院有限公司 | Ceramic-aluminum composite powder and preparation method thereof |
| CN113770368A (en) * | 2021-09-16 | 2021-12-10 | 浙江吉利控股集团有限公司 | TiC particle reinforced aluminum alloy powder for metal 3D printing and preparation method thereof |
| CN114769604A (en) * | 2022-04-22 | 2022-07-22 | 郑州磨料磨具磨削研究所有限公司 | Method for preparing alloy powder by adding superfine crystal seeds to carry out heterogeneous nucleation |
| CN115383129A (en) * | 2022-08-16 | 2022-11-25 | 燕山大学 | Method for preparing intermetallic compound reinforced aluminum-based gradient composite material by in-situ synthesis and composite material |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20130183189A1 (en) * | 2010-10-04 | 2013-07-18 | Gkn Sinter Metals, Llc | Aluminum powder metal alloying method |
| CN107737941A (en) * | 2017-11-02 | 2018-02-27 | 长沙新材料产业研究院有限公司 | TiB for increasing material manufacturing2Strengthen the preparation method of Al alloy powder |
| CN107760933A (en) * | 2017-09-11 | 2018-03-06 | 南京航空航天大学 | A kind of 3D printing strengthens Al alloy powder and preparation method thereof with in-situ nano complex phase ceramic |
| CN108356259A (en) * | 2018-01-31 | 2018-08-03 | 上海交通大学 | A kind of nanometer of aluminum matrix composite powder and preparation method thereof |
| CN108746625A (en) * | 2018-06-26 | 2018-11-06 | 中南大学 | A kind of preparation method of aluminum-base nano composite material |
-
2019
- 2019-01-31 CN CN201910096909.4A patent/CN109692964A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20130183189A1 (en) * | 2010-10-04 | 2013-07-18 | Gkn Sinter Metals, Llc | Aluminum powder metal alloying method |
| CN107760933A (en) * | 2017-09-11 | 2018-03-06 | 南京航空航天大学 | A kind of 3D printing strengthens Al alloy powder and preparation method thereof with in-situ nano complex phase ceramic |
| CN107737941A (en) * | 2017-11-02 | 2018-02-27 | 长沙新材料产业研究院有限公司 | TiB for increasing material manufacturing2Strengthen the preparation method of Al alloy powder |
| CN108356259A (en) * | 2018-01-31 | 2018-08-03 | 上海交通大学 | A kind of nanometer of aluminum matrix composite powder and preparation method thereof |
| CN108746625A (en) * | 2018-06-26 | 2018-11-06 | 中南大学 | A kind of preparation method of aluminum-base nano composite material |
Non-Patent Citations (1)
| Title |
|---|
| 蔡志勇等: "快速凝固过共晶Al-Si合金的显微组织及其热稳定性", 《中国有色金属学报》 * |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112453422A (en) * | 2020-10-27 | 2021-03-09 | 中南大学 | Light Al-Si-Mg2Si electronic packaging material and preparation method and application thereof |
| CN112453422B (en) * | 2020-10-27 | 2021-07-30 | 中南大学 | Light Al-Si-Mg2Si electronic packaging material and preparation method and application thereof |
| CN112593129A (en) * | 2020-12-11 | 2021-04-02 | 江苏科技大学 | ZrB2Ceramic particle modified Al-Zn-Mg-Cu aluminum alloy welding rod and preparation method thereof |
| CN112725663A (en) * | 2020-12-30 | 2021-04-30 | 江苏智仁景行新材料研究院有限公司 | Ceramic-aluminum composite powder and preparation method thereof |
| CN112725663B (en) * | 2020-12-30 | 2022-07-05 | 江苏智仁景行新材料研究院有限公司 | Ceramic-aluminum composite powder and preparation method thereof |
| CN113770368A (en) * | 2021-09-16 | 2021-12-10 | 浙江吉利控股集团有限公司 | TiC particle reinforced aluminum alloy powder for metal 3D printing and preparation method thereof |
| CN114769604A (en) * | 2022-04-22 | 2022-07-22 | 郑州磨料磨具磨削研究所有限公司 | Method for preparing alloy powder by adding superfine crystal seeds to carry out heterogeneous nucleation |
| CN115383129A (en) * | 2022-08-16 | 2022-11-25 | 燕山大学 | Method for preparing intermetallic compound reinforced aluminum-based gradient composite material by in-situ synthesis and composite material |
| CN115383129B (en) * | 2022-08-16 | 2024-03-19 | 燕山大学 | Preparation method of in-situ synthesized intermetallic compound reinforced aluminum-based gradient composite material and composite material |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109692964A (en) | A kind of reinforced aluminum matrix composites and preparation method thereof | |
| CN108085528B (en) | In-situ generated nano NbB2Method for grain refining and strengthening aluminum alloy | |
| CN106086726B (en) | SiC nanowire reinforced aluminum matrix composites and preparation method thereof | |
| CN107460376B (en) | A kind of hybrid reinforced aluminum-matrix composite material and preparation method thereof | |
| CN107022691B (en) | A method of graphene reinforced aluminum matrix composites are prepared by raw material of multi-layer graphene microplate | |
| CN110016582B (en) | Preparation method of in-situ nanoparticle reinforced aluminum matrix composite | |
| CN108746625A (en) | A kind of preparation method of aluminum-base nano composite material | |
| WO2021035775A1 (en) | Method for preparing aluminum-based composite material | |
| CN101229582A (en) | Semi-solid rheo-extrusion casting technology and equipment of hypereutectic Al-Si alloy casting | |
| CN106399872B (en) | A kind of preparation method of the whisker carbon nanotubes-aluminum composites semi-solid blank of coating alumina | |
| CN110423914B (en) | Preparation method of rare earth magnesium alloy composite material | |
| CN101168810A (en) | High-strength high-modulus aluminum-base composite material and preparation method thereof | |
| CN110438379B (en) | Preparation method of lithium-containing magnesium/aluminum-based composite material | |
| CN106399880A (en) | Preparation method for whisker carbon nanotube-reinforced aluminum matrix composite coated with aluminum oxide | |
| CN101260488A (en) | Silicon nitride ceramic particles enhancement aluminum-base composite material and preparing method thereof | |
| CN106350695A (en) | Preparation method of elemental-copper-coated multiwalled carbon nanotube/aluminum-based composite semisolid-state blank | |
| US20210062315A1 (en) | Preparation method of a lithium-containing magnesium/aluminum matrix composite | |
| CN110205513B (en) | Method for simultaneously improving conductivity and hardness of copper-based composite material | |
| CN111690840A (en) | Amorphous phase silicate particle and SiC particle reinforced aluminum matrix composite material and preparation | |
| CN110117727A (en) | A method of particles reiforced metal-base composition is prepared based on 3D printing technique | |
| CN112176262B (en) | High-volume-fraction multiphase hybrid reinforced magnesium-based composite material and preparation method thereof | |
| CN110229979B (en) | Intragranular grain boundary distribution micro-nano complex phase particle reinforced aluminum matrix composite material and preparation method thereof | |
| WO2021035776A1 (en) | Method for preparing magnesium-based composite material | |
| CN106367696B (en) | A kind of preparation method of whisker CNT/magnesium-base composite material semi-solid state blank of coating alumina | |
| CN114000015B (en) | In-situ multiphase particle coupling reinforced aluminum matrix composite material and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20190430 |
|
| RJ01 | Rejection of invention patent application after publication |