CN109957685A - A kind of high dispersive TiB2/ A356 composite material and preparation method thereof - Google Patents
A kind of high dispersive TiB2/ A356 composite material and preparation method thereof Download PDFInfo
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- CN109957685A CN109957685A CN201910318915.XA CN201910318915A CN109957685A CN 109957685 A CN109957685 A CN 109957685A CN 201910318915 A CN201910318915 A CN 201910318915A CN 109957685 A CN109957685 A CN 109957685A
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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
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
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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
- C22C1/10—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
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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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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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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Abstract
A kind of high dispersive TiB2/ A356 composite material and preparation method thereof, belongs to technical field of material.Enhance granular mass percentage component, TiB2: 3.0-10.0%, matrix alloy mass percent component Si:6.5-7.5%, Mg:0.35-0.45%, surplus Al, it is TiB of the size less than 1 μm that composite material, which enhances particle,2Particle, matrix image composition mainly include α-Al, Mg2Si, eutectic Si.Al-TiB is prepared using melt self- propagating direct synthesis technique2Intermediate alloy, with Al powder, Ti powder, TiO2、H3BO3For raw material, prepares mass fraction and stablize, the lesser TiB of average-size2Particle.The present invention prepares composite material using two-step method, first prepares Al-TiB2Intermediate alloy avoids and directly carries out reaction in-situ in Al-Si-Mg matrix alloy, to cause to be lost to alloying component, and then with Al-TiB2Intermediate alloy is matrix, and aluminium ingot adjusting component is added, prepares composite material.
Description
Technical field
The invention belongs to field of compound material, in particular to a kind of ingredient of composite material designs and prepares method.
Background technique
A356 aluminium alloy is the Al-Si-Mg system cast aluminium alloy gold that the U.S. was developed in 1970.Since its casting character is excellent
Good, good fluidity, the features such as linear shrinkage is small and corrosion resistance is high, are widely used in automobile industry.Si in A356 aluminium alloy
In the presence of the mobility that alloy greatly improved, while also causing the mechanical property of material insufficient.The performance master of A356 alloy
Its as-cast structure is depended on, A356 can further be promoted by the improvement of the eutectic Si to coarse α-Al dendrite and en plaque
Performance.
In-situ endogenic TiB2The addition of particle can be obviously improved the intensity and toughness of aluminium alloy, and TiB2The distribution of particle and
Size has to final material property and its significant impact.At present using A356 alloy as matrix prepare the research of composite material compared with
Few and mostly larger with particle size, particle aggregation is serious, and the SiC of defective tightness is former as enhancing particle in conjunction with basal body interface
The enhancing particle of position preparation is even more to carry out directly in aluminium alloy solution, will certainly be caused centainly to the main component element in alloy
Loss.
Summary of the invention
It is difficult it is an object of the invention to overcome A356 intensity of aluminum alloy to be promoted, TiB is introduced in A356 aluminium alloy2?
Grain prepares composite material using two-step method, adjusts TiB2The mass fraction of particle, it is intended to prepare a kind of particle height and uniformly divide
It dissipates, low-loss, high-intensitive, the advanced composite material (ACM) of high rigidity.
To achieve the above object, the present invention takes following design scheme.
A kind of high dispersive TiB2/ A356 composite material and preparation method thereof, it is characterised in that: using A356 alloy as matrix, quality
Score is 3%-10%, and TiB of the average-size less than 1 μm2To enhance particle, composite material, matrix alloy quality percentage are prepared
Than component Si:6.5-7.5%, Mg:0.35-0.45%, surplus Al.
Using two-step method, i.e., particle will be prepared in situ and separated with matrix alloy founding, prepare composite material, avoid directly
Highly exothermic reaction in-situ scaling loss caused by alloying element is carried out in A356 matrix alloy.Specifically includes the following steps:
(1) with Al powder, Ti powder, TiO2、H3BO3For raw material, wherein Ti/B=1:4, is prepared using melt self- propagating direct synthesis technique
Mass fraction stabilization, average-size are lower than 1 μm of Al-TiB2Intermediate alloy.The main image group of intermediate alloy becomes α-Al, TiB2,
Without TiAl3。TiB2With basal body interface cleaning, combination degree height.
(2) the Al- TiB prepared into step (1)2It is added rafifinal in intermediate alloy, high purity magnesium, among Al-20%Si
Alloy adjusts TiB by control alloying component2The mass fraction of particle is 3%-10%, and conjunction is melting at a temperature of 720-780 DEG C
Gold solution.
(3) classification stirring is carried out to the alloy solution in step (2) and be cast in both fixed molds, whipping temp 700-
900 DEG C, pouring temperature is 720-750 DEG C.T6 heat treatment is carried out to composite material, finally obtains TiB2/ A356 composite material.It is multiple
TiB in condensation material2Particle size is smaller and is evenly distributed, and provides safeguard for the performance of composite material.
The utility model has the advantages that the present invention solves the scaling loss serious problems in endogenetic particle composite material preparation process to element.
And the TiB prepared using high A356 alloy as matrix2In/A356 composite material, TiB2Particle height is evenly distributed, and size is smaller, by force
Degree hardness has apparent raising compared with matrix alloy.
Detailed description of the invention
Fig. 1 is Al-TiB2Intermediate alloy microscopic structure.
Fig. 2 is as cast condition TiB2/ A356 composite material microscopic structure.
Specific embodiment
Embodiment 1
Two-step method prepares TiB2The process of/A356 composite material is as follows:
(1) allocation plan of composite material are as follows: 5%TiB2, 7%Si, 0.4%Mg, surplus Al.Al-TiB2Intermediate alloy is by aluminium
Ingot, aluminium powder, titanium valve, TiO2、H3BO3It is prepared, wherein Ti/B molar ratio 1:4.A356 matrix alloy by fine aluminium ingot, pure magnesium ingot,
It is prepared by Al-20%Si intermediate alloy.
(2) 1kgAl-TiB is prepared2Intermediate alloy weighs TiO as required2、H3BO3, two kinds of powder are uniformly mixed, and
200 DEG C are heated two hours, and H is removed3BO3In moisture.By the TiO after heating2And H3BO3Mixed-powder and the aluminium powder for requiring weighing
It is uniformly mixed with titanium valve, by uniformly mixed powder as in mold, being pressed into 15 × φ 62.5mm3Cylindricality powder agglomates.By mould
Have and one coating of the tools such as slag spoon brushing, prevents Fe magazine element pollution.Intermediate frequency furnace is selected to carry out melting, graphite stirs
Stick is mixed, prevents Si from polluting.Aluminium ingot is heated to 780-800 DEG C using intermediate frequency furnace, is completely melt to aluminium ingot, melt is heated up
To 900-1000 DEG C, graphite bell jar is pressed into the block of step (3), is classified and is stirred using graphite rod, whipping temp 700-900
DEG C, stir 30min；After the reaction was completed, 5 min are stood, skims, aluminum melt is poured into warmed-up 250 DEG C of punching block, are obtained
Al-TiB2Intermediate alloy.
(3) it will be carried out by the matrix alloy composition fine aluminium ingot, pure magnesium ingot, Al-20%Si intermediate alloy of step (1) design
Proportion.
(4) fine aluminium, aluminium are added in order in 780 DEG C of progress refuses to the intermediate alloy of 1 step of example (2) acquisition
Silicon intermediate alloy.After metal and intermediate alloy all dissolve, the dross on solution surface is taken off, solution temperature reaches 715-735 DEG C
When, pure magnesium is added.To keep alloying elements distribution uniform, classification stirring is carried out to solution, is refined later, refined in 710-
10min is stood at 730 DEG C, is skimmed, melt is cast in warmed-up 250 DEG C of punching block, obtains composite material ingot casting.
T6 heat treatment is carried out to the composite material in 1 step of example (4), i.e. at solid solution 535 DEG C/4h+ timeliness, 160 DEG C/5h
Reason.
The TiB obtained by the method2/ A356 composite material have particle height be uniformly distributed, low-loss, high intensity,
The advantages such as high rigidity.Composite material strength improves 25% than matrix alloy, and hardness improves 10% compared with matrix alloy, image composition
Predominantly TiB2Particle, nanoscale Mg2Si phase.
The present invention starts with from microstructure design and control, introduces high-modulus particle TiB2It prepares particle reinforced aluminium-based compound
Material further promotes the strength of materials, hardness, carries out composite material preparation using two-step method, avoids directly in A356 matrix
Highly exothermic reaction in-situ scaling loss caused by alloying element is carried out in alloy, and remains TiB2With the interfacial cleanliness of Al matrix
Degree and interface cohesion degree, after heat treatment, the TiB in composite material2Particle size is smaller and is evenly distributed, and is composite material
Performance provide safeguard.
Embodiment 2:
Difference from Example 1 is, allocation plan are as follows: 3%TiB2Particle 6.5wt.%Si, 0.35wt.%Mg；Block is added
After body, 10min-60min stirring is carried out, preferably mixing time is 30min, and the metal of 250 DEG C of preheating is poured into after isothermal holding
In pattern tool.It can reach preparation effect same as Example 1 with this condition.
Embodiment 3:
Difference from Example 1 is, allocation plan are as follows: 3%TiB2Particle 6.5wt.%Si, 0.35wt.%Mg；To powder agglomates
After the reaction was completed, 3min-20min is stood, preferably time of repose is 5min, and the metal of 250 DEG C of preheating is poured into after isothermal holding
In pattern tool.It can reach preparation effect same as Example 1 with this condition.
Claims (3)
1. a kind of high dispersive TiB2The preparation method of/A356 composite material, it is characterised in that: using A356 alloy as matrix, quality point
Number is 3%-10%, the TiB with average-size less than 1 μm2To enhance particle, composite material, matrix alloy mass percent are prepared
Component Si:6.5-7.5%, Mg:0.35-0.45%, surplus Al.
2. a kind of high dispersive TiB2The preparation method of/A356 composite material, it is characterised in that: composite material is prepared using two-step method,
Specifically includes the following steps:
Step 1: with Al powder, Ti powder, TiO2、H3BO3For raw material, wherein Ti/B=1:4, using melt self- propagating direct synthesis technique
Prepare mass fraction stabilization, Al-TiB of the average-size lower than 1 μm2Intermediate alloy；The main image group of intermediate alloy become α-Al,
TiB2；
Step 2: with fine aluminium, pure magnesium, Al-20%Si intermediate alloy is raw material, the Al-TiB prepared with step 12For matrix, pass through
The above raw material adjusts TiB2The mass fraction of particle is 3%-10%, is melting into alloy solution at a temperature of 720-780 DEG C；
Step 3: classification stirring is carried out to the alloy solution in step 2 and is cast in both fixed molds, whipping temp 700-
900 DEG C, pouring temperature is 720-750 DEG C；
Step 4: step 3 composite board is subjected to T6 heat treatment, finally obtains TiB2/ A356 composite material.
3. a kind of high dispersive TiB according to claim 22The preparation method of/A356 composite material, it is characterised in that: described
Two-step method is that particle will be prepared in situ to separate with matrix alloy founding.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111074116A (en) * | 2020-01-16 | 2020-04-28 | 苏州先准电子科技有限公司 | Electronic packaging high-silicon aluminum-based composite material and preparation method thereof |
| CN111206166A (en) * | 2019-12-10 | 2020-05-29 | 江苏大学 | Preparation method of in-situ ternary nanoparticle reinforced aluminum matrix composite |
| CN114351001A (en) * | 2021-12-17 | 2022-04-15 | 中国船舶重工集团公司第十二研究所 | Preparation method of adjustable TiB2 in-situ reinforced aluminum-based composite material |
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| JPH08109423A (en) * | 1994-10-11 | 1996-04-30 | Furukawa Electric Co Ltd:The | Production of fiber reinforced aluminum composite |
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| CN106367644A (en) * | 2016-09-23 | 2017-02-01 | 北京工业大学 | Super-high strength and high hardness TiB2 particle reinforced Al-Zn-Mg-Cu composite material and preparation method thereof |
| CN106834833A (en) * | 2017-01-12 | 2017-06-13 | 北京工业大学 | The strong TiB of a kind of high-modulus, superelevation2Particle REINFORCED Al Zn Mg Cu composites and preparation method thereof |
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111206166A (en) * | 2019-12-10 | 2020-05-29 | 江苏大学 | Preparation method of in-situ ternary nanoparticle reinforced aluminum matrix composite |
| WO2021114967A1 (en) * | 2019-12-10 | 2021-06-17 | 江苏大学 | Method for preparing aluminum-based composite material reinforced in situ by ternary nanoparticles |
| US11761059B2 (en) | 2019-12-10 | 2023-09-19 | Jiangsu University | Preparation method of in-situ ternary nanoparticle-reinforced aluminum matrix composite |
| CN111074116A (en) * | 2020-01-16 | 2020-04-28 | 苏州先准电子科技有限公司 | Electronic packaging high-silicon aluminum-based composite material and preparation method thereof |
| CN114351001A (en) * | 2021-12-17 | 2022-04-15 | 中国船舶重工集团公司第十二研究所 | Preparation method of adjustable TiB2 in-situ reinforced aluminum-based composite material |
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Application publication date: 20190702 |