CN110576232A - Brazing method for high volume fraction silicon carbide particle reinforced aluminum matrix composite and aluminum-silicon alloy - Google Patents
Brazing method for high volume fraction silicon carbide particle reinforced aluminum matrix composite and aluminum-silicon alloy Download PDFInfo
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- CN110576232A CN110576232A CN201910739111.7A CN201910739111A CN110576232A CN 110576232 A CN110576232 A CN 110576232A CN 201910739111 A CN201910739111 A CN 201910739111A CN 110576232 A CN110576232 A CN 110576232A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K1/00—Soldering, e.g. brazing, or unsoldering
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/0008—Soldering, e.g. brazing, or unsoldering specially adapted for particular articles or work
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K1/00—Soldering, e.g. brazing, or unsoldering
- B23K1/20—Preliminary treatment of work or areas to be soldered, e.g. in respect of a galvanic coating
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Abstract
The invention discloses a brazing method of a high volume fraction silicon carbide particle reinforced aluminum matrix composite and an aluminum-silicon alloy, which comprises the following steps: s1, cleaning the surfaces to be welded of the silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy; s2, presetting ceramic powder on the surfaces to be welded of the aluminum-silicon alloy treated in the step S1; s3, placing brazing filler metal between to-be-welded surfaces of the aluminum-silicon alloy and silicon carbide particle reinforced aluminum matrix composite to form a to-be-welded part; and S4, heating the to-be-welded part under a protective atmosphere, keeping the temperature and pressurizing to 5-20 MPa, continuing keeping the temperature and pressure, and then cooling to room temperature along with the furnace. According to the brazing method, the hard ceramic powder is used for assisting the metal brazing filler metal to break oxide films on the surfaces of the silicon carbide particle reinforced aluminum-based composite material and the aluminum-silicon alloy, the brazing filler metal is fully wetted and spread on the surfaces of the silicon carbide particle reinforced aluminum-based composite material and the aluminum-silicon alloy, and metallurgical bonding of the connecting surfaces of the silicon carbide particle reinforced aluminum-based composite material and the aluminum-silicon alloy is promoted.
Description
Technical Field
The invention relates to the technical field of connection methods of aluminum-based composite materials, in particular to a brazing method of a high-volume-fraction silicon carbide particle reinforced aluminum-based composite material and aluminum-silicon alloy.
Background
With the development of microelectronic devices and semiconductor integrated circuits toward high reliability, high integration, high density and light weight, the number of microelectronic components is increasing, the integration level is increasing, and the heat density is increasing, so that the heat dissipation requirement on the housing of the microelectronic components is becoming stricter. The traditional electronic packaging shell materials such as Kovar, W/Cu and Mo/Cu alloy can not meet the performance requirements due to large specific gravity and low thermal conductivity, and the silicon carbide particle reinforced aluminum matrix composite material with high volume fraction (vol.%) is a newly developed electronic packaging material. It has specific weight 1/3 similar to that of Kovar alloy, expansion coefficient similar to that of ceramic substrate of chip, and heat conductivity 10 times higher than that of Kovar alloy. Therefore, the material is an ideal choice for replacing the traditional electronic packaging material.
the microelectronic assembly has a high requirement on the air tightness of the package shell, and on one hand, the package shell is required to have high compactness, and on the other hand, a welding seam between the package shell and the cover plate is required to have high air tightness. Laser welding has the characteristics of high quality, high precision, low deformation, high efficiency, high speed, low cost and the like, and is one of the main ways for realizing high reliability and air tightness of the packaging shell. But because high volume fraction carborundum granule reinforcing aluminium base composite material encapsulation casing contains a large amount of SiC granule ceramic phase, lead to its laser welding performance relatively poor, can't directly carry out laser seal welding with the apron, need set up the sealing ring in the casing upper end, form gas tightness encapsulation casing through sealing ring and metal cover plate laser welding. The seal ring is generally made of an expansion alloy such as 4J29, 4J33, 4J34, 4J45, and J47, a titanium alloy, and a stainless steel material such as 430 and 410, and has a high density and a low thermal conductivity.
The thermal expansion coefficient of the aluminum-silicon alloy is matched with that of the high volume fraction silicon carbide particle reinforced aluminum matrix composite packaging shell, the thermal conductivity is high, the density is low, the laser welding characteristic is excellent, and the requirements of laser sealing welding of the packaging shell can be well met. Brazing is a common welding method for achieving the connection of aluminum alloys and their composites. The method has the advantages of low connection temperature, simple operation and low cost, but the brazing of the aluminum alloy and the composite material thereof is often restricted by an oxide film on the surface of the aluminum alloy or the aluminum alloy substrate. The oxide film not only hinders the wetting and spreading of the brazing filler metal on the surface of the aluminum alloy, but also seriously hinders the combination of two connecting surfaces, so that the brazing effect cannot be expected. Therefore, how to remove the surface oxide film is the technical key for realizing the brazing connection of the aluminum alloy and the composite material thereof.
Disclosure of Invention
The invention provides a brazing method of a high volume fraction silicon carbide particle reinforced aluminum matrix composite and an aluminum-silicon alloy, and aims to solve the technical problems that brazing of the aluminum-silicon alloy and the high volume fraction silicon carbide particle reinforced aluminum matrix composite is limited by an oxide film on the surface of an aluminum alloy matrix, so that the performance of a welding joint is poor, and the requirement of an electronic packaging shell cannot be met.
according to one aspect of the present invention, there is provided a method of brazing a high volume fraction silicon carbide particle reinforced aluminum matrix composite to an aluminum silicon alloy, comprising the steps of:
S1, cleaning the surfaces to be welded of the high volume fraction silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy;
S2, presetting ceramic powder on the to-be-welded surface of the aluminum-silicon alloy treated in the step S1;
S3, assembling the aluminum-silicon alloy treated in the step S2 and the high volume fraction silicon carbide particle reinforced aluminum matrix composite treated in the step S1, placing brazing filler metal between surfaces to be welded of the aluminum-silicon alloy and the high volume fraction silicon carbide particle reinforced aluminum matrix composite, and clamping to form a piece to be welded;
S4, heating the to-be-welded piece to 390-410 ℃ under a protective atmosphere, preserving heat, pressurizing to 5-20 MPa, continuing preserving heat and maintaining pressure for a period of time, and then cooling to room temperature along with the furnace.
Further, the high volume fraction silicon carbide particle reinforced aluminum matrix composite is 40-80% by volume fraction silicon carbide particle reinforced aluminum matrix composite.
Further, the aluminum-silicon alloy is an aluminum-silicon alloy with 20-50% of silicon particles by mass.
further, in step S2, the preset ceramic powder on the to-be-welded surface of the aluminum-silicon alloy processed in step S1 is prepared by a suspension deposition method, which includes the following steps:
Mixing ceramic powder and absolute ethyl alcohol to obtain a mixed solution of the ceramic powder and the absolute ethyl alcohol, carrying out ultrasonic vibration on the mixed solution to fully disperse the ceramic powder, putting the aluminum-silicon alloy treated in the step S1 into the mixed solution, standing for a period of time until the ceramic powder is deposited on the surface to be welded, removing the absolute ethyl alcohol on the upper layer, taking out the treated aluminum-silicon alloy, and air-drying.
Further, the ceramic powder comprises SiC powder and Al2O3Powder, Si3N4One or more of powder or CBN powder.
further, the grain diameter of the ceramic powder is 1-10 mu m, and the surface density of the ceramic powder is 0.5-20 g/m2。
Further, the ultrasonic vibration frequency is 20-50 kHz, the ultrasonic power is 1000-2000W, the ultrasonic vibration time is 5-20 min, and the standing time is 10-240 min.
Further, in step S3, the brazing filler metal is a rolled zinc-based alloy, and the rolled zinc-based alloy comprises the following components in percentage by mass: al: 2-15%, Cu: 4-4.5% and the balance of Zn.
Further, the melting point of the rolled zinc-based alloy is 380-410 ℃.
Further, in step S4, the heating temperature rise is performed at a temperature rise rate of 5 to 20 ℃/min, the heat preservation time before pressurization is 5 to 20min, and the heat preservation and pressure holding time after pressurization is 10 to 20 min.
The invention has the following beneficial effects:
The invention relates to a brazing method of a high volume fraction silicon carbide particle reinforced aluminum matrix composite and an aluminum-silicon alloy. On one hand, the brazing filler metal is heated and insulated, the structure is changed, the rolled fiber structure is changed into a semi-solid spherical crystal structure, after pressure is applied, spherical crystal grains in the brazing filler metal firstly extrude the surfaces of base metals on two sides, an oxide film on the surfaces of the base metals is broken, secondly, a liquid phase in the brazing filler metal is diffused into the base metals from the broken positions, the base metals are locally dissolved, the combination of the oxide film on the surfaces of the base metals is reduced, then, the spherical crystal grains slide along the surfaces of the base metals, a friction effect is generated, and the broken oxide film is stripped from the surfaces of; on the other hand, the hard structure of the ceramic powder assists the metal brazing filler metal to extrude the surface of the aluminum-silicon alloy base metal under the action of pressure, and the rupture of an oxide film on the surface of the aluminum-silicon alloy base metal is promoted, so that the film removing effect is better. After the oxide film is broken, the brazing filler metal is fully wetted, spread and diffused on the surfaces of the silicon carbide particle reinforced aluminum-based composite material and the aluminum-silicon alloy, so that a brazing joint which meets the expected effect is formed, and the requirements of the microelectronic assembly on the air tightness of the packaging shell and the laser sealing and welding are met.
In the brazing joint obtained by the invention, the transition region of the brazing filler metal and the base metal is made of ceramic powder reinforced metal composite material, so that the difference of the linear expansion coefficients of the brazing filler metal and the base metal is relieved, the residual stress of the joint is reduced, and the joint strength is improved; the maximum shearing strength of the obtained joint can reach 80-90 MPa.
The brazing method of the high-volume-fraction silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy does not need to use brazing flux, the welding process can be carried out in a non-vacuum environment, the defects of corrosion of the brazing flux on joints and the like are avoided, the size of a suitable weldment is wider, equipment is simple, a welding seam is attractive, the forming is good, and the defects of air holes, impurities and the like are avoided; and the welding temperature is 390-410 ℃, so that the defects of coarsening of the structure of the aluminum-silicon alloy, reduction of the service performance and the like in the welding process are avoided.
In addition to the objects, features and advantages described above, other objects, features and advantages of the present invention are also provided. The present invention will be described in further detail below with reference to the drawings.
drawings
The accompanying drawings, which are incorporated in and constitute a part of this application, illustrate embodiments of the invention and, together with the description, serve to explain the invention and not to limit the invention. In the drawings:
FIG. 1 is a schematic flow chart of a method for brazing a high volume fraction SiC particle-reinforced Al matrix composite to an Al-Si alloy according to an embodiment of the present invention;
FIG. 2 is a semi-solid spherulitic structure of the braze filler metal at brazing temperature in example 1 of the present invention;
Fig. 3 is a brazed joint structure obtained by the semi-solid pressure brazing method in example 1 of the present invention.
Detailed Description
The embodiments of the invention will be described in detail below with reference to the accompanying drawings, but the invention can be embodied in many different forms, which are defined and covered by the following description.
As shown in fig. 1, the brazing method of the high volume fraction silicon carbide particle reinforced aluminum matrix composite material and the aluminum-silicon alloy of the embodiment includes the following steps:
s1, cleaning the surfaces to be welded of the high volume fraction silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy;
S2, presetting ceramic powder on the surface to be welded of the aluminum-silicon alloy treated in the step S1;
s3, assembling the aluminum-silicon alloy treated in the step S2 and the silicon carbide particle reinforced aluminum matrix composite treated in the step S1, placing brazing filler metal between the surfaces to be welded of the aluminum-silicon alloy and the silicon carbide particle reinforced aluminum matrix composite, and clamping to form a piece to be welded;
S4, heating the to-be-welded piece to 390-410 ℃ under a protective atmosphere, preserving heat, pressurizing to 5-20 MPa, continuing preserving heat and maintaining pressure for a period of time, and then cooling to room temperature along with the furnace.
the brazing method of the silicon carbide particle reinforced aluminum-based composite material with the high volume fraction and the aluminum-silicon alloy of the embodiment comprises the steps of depositing a layer of ceramic powder on the to-be-welded surface of the aluminum-silicon alloy of one of the to-be-welded parts, then placing brazing filler metal between the to-be-welded surface of the silicon carbide particle reinforced aluminum-based composite material with the high volume fraction and the ceramic powder deposition layer of the aluminum-silicon alloy, and carrying out semi-solid heating and pressurizing brazing, wherein on one hand, according to the principle of deformation mutagenesis activation, the brazing filler metal is heated and insulated to change the structure from a rolled fibrous structure into a semi-solid spherulitic structure (the principle of deformation mutagenesis activation is that on the other hand, after the brazing filler metal is subjected to multi-pass hot rolling, a large amount of distortion energy is generated in the structure, and the brazing filler metal structure is recovered and recrystallized in the heating process under the driving of the distortion energy, the Ostwald mechanism (Ostwald) plays a role, a high-curvature interface of each recrystallized grain is melted and deposited on a low-curvature interface to form a round spherical grain, after pressure is applied, the spherical grain in the brazing filler metal firstly extrudes the surfaces of base metals on two sides to break an oxide film on the surface of the base metals, secondly, a liquid phase in the brazing filler metal is diffused into the base metals from the broken part to locally dissolve the base metals and reduce the combination of the oxide films on the surface of the base metals, and then, the spherical grain slides along the surface of the base metals to generate a friction effect so that the broken oxide film is stripped from the surface of the dissolved base metals; on the other hand, the hard structure of the ceramic powder assists the metal brazing filler metal to extrude the surface of the aluminum-silicon alloy base metal under the action of pressure, and the rupture of an oxide film on the surface of the aluminum-silicon alloy base metal is promoted, so that the film removing effect is better. After the oxide film is broken, the brazing filler metal is fully wetted, spread and diffused on the surfaces of the silicon carbide particle reinforced aluminum-based composite material and the aluminum-silicon alloy, so that a brazing joint which meets the expected effect is formed, and the requirements of the microelectronic assembly on the air tightness of the packaging shell and the laser sealing and welding can be met.
In the brazed joint obtained by the embodiment, the transition region of the brazing filler metal and the base metal is made of the ceramic powder reinforced metal composite material, so that the difference of the linear expansion coefficients of the brazing filler metal and the base metal is relieved, the residual stress of the joint is reduced, and the joint strength is improved. The maximum shearing strength of the obtained joint can reach 80-90 MPa.
The brazing method of the high-volume-fraction silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy does not need brazing flux, the welding process can be carried out in a non-vacuum environment, the defects that the brazing flux corrodes a joint and the like are avoided, the size of a suitable weldment is wider, equipment is simple, a welding line is attractive, forming is good, and the defects of air holes, impurities and the like are avoided; and the welding temperature is 390-410 ℃, so that the defects of coarsening of the structure of the aluminum-silicon alloy, reduction of the service performance and the like in the welding process are avoided.
In the embodiment, the surfaces to be welded of the high-volume-fraction silicon carbide particle reinforced aluminum matrix composite material and the aluminum-silicon alloy of the workpiece to be welded are subjected to surface cleaning, and impurity dust on the surfaces to be welded is removed, so that the influence of the impurity dust on the tissue structure of the welding surface is prevented. The method for cleaning the surface of the workpiece to be welded can adopt a mechanical cleaning method, a chemical cleaning method or a physical cleaning method, such as mechanical polishing, solvent cleaning, ultrasonic cleaning and the like.
in this embodiment, the high volume fraction silicon carbide particle-reinforced aluminum matrix composite is an aluminum matrix composite in which the volume fraction of the silicon carbide particle-reinforced phase is 40% to 80%. The specific gravity of the silicon carbide particle reinforced aluminum matrix composite with high volume fraction (vol.%, 40-80%) is 1/3 of Kovar alloy, the expansion coefficient is close to that of a ceramic substrate of a packaged chip, and the thermal conductivity is 10 times higher than that of the Kovar alloy. The brazing method is suitable for welding the silicon carbide particle reinforced aluminum matrix composite with high volume fraction and the aluminum-silicon alloy, the brazing joint is applied to the electronic packaging shell, the laser welding performance is good, and the air tightness and the heat conductivity are excellent.
In this embodiment, the aluminum-silicon alloy is an aluminum-silicon alloy in which the mass fraction of the silicon particle reinforced phase is 20% to 50%. The aluminum-silicon alloy with the silicon particle reinforced phase mass fraction of 20-50% has high thermal expansion coefficient and thermal conductivity, and meets the performance requirement of the microelectronic assembly on the packaging shell. Meanwhile, the thermal expansion coefficient and the thermal conductivity of the aluminum-silicon alloy are matched with those of the silicon carbide reinforced aluminum-based composite material with high volume fraction, the residual stress of the joint after brazing is small, and the use performance of the joint is high.
With the development of microelectronic devices and semiconductor integrated circuits toward high reliability, high integration, high density and light weight, the number of microelectronic components is increasing, the integration level is increasing, and the heat density is increasing, so that the heat dissipation requirement on the housing of the microelectronic components is becoming stricter. The traditional electronic packaging shell materials such as Kovar, W/Cu and Mo/Cu alloy can not meet the performance requirements due to large specific gravity and low thermal conductivity, and the silicon carbide particle reinforced aluminum matrix composite material with high volume fraction (vol.%) is a newly developed electronic packaging material. It has specific weight 1/3 similar to that of Kovar alloy, expansion coefficient similar to that of ceramic substrate of chip, and heat conductivity 10 times higher than that of Kovar alloy. Therefore, the material is an ideal choice for replacing the traditional electronic packaging material.
in this embodiment, in step S2, the step of placing ceramic powder on the to-be-welded surface of the aluminum-silicon alloy processed in step S1 by a suspension deposition method includes the following steps:
Mixing ceramic powder and absolute ethyl alcohol to obtain a mixed solution of the ceramic powder and the absolute ethyl alcohol, carrying out ultrasonic vibration on the mixed solution to fully disperse the ceramic powder, putting the aluminum-silicon alloy treated in the step S1 into the mixed solution, allowing the aluminum-silicon alloy to stand for a period of time until the ceramic powder is deposited on the surface to be welded, removing the absolute ethyl alcohol on the upper layer, taking out the treated aluminum-silicon alloy, and air-drying.
The suspension deposition method is that a dispersed suspension solution of ceramic powder and absolute ethyl alcohol is obtained firstly, then the ceramic powder is deposited on the surface to be welded of the aluminum-silicon alloy by utilizing the self gravity of the ceramic powder, ultrasonic vibration is beneficial to fully dispersing the ceramic powder, the ceramic powder is prevented from agglomerating, the ceramic powder is uniformly distributed on the surface to be welded of the aluminum-silicon alloy, and the volatility of the absolute ethyl alcohol enables the aluminum-silicon alloy after being treated to be air-dried in a short time. The ceramic powder is a polar surface, and according to the principle of polarity similarity, a polar solvent ethanol is selected as a dispersion medium, so that the ceramic powder is favorably and fully dispersed. And the ethanol solvent has the characteristics of no toxicity, easy volatilization, no residue after pyrolysis, low cost and the like. Therefore, anhydrous ethanol is selected as the dispersion medium for suspension deposition of the ceramic powder. Preferably, the mass volume ratio of the ceramic powder to the absolute ethyl alcohol is 0.1-0.5 mg/ml, and the ceramic powder has a good dispersion effect under the mass volume ratio. In the embodiment, the ceramic powder is preset on the surface of the aluminum-silicon alloy by adopting a suspension deposition method, the process is simple, the operation is flexible, the ceramic powder is uniformly distributed on the to-be-welded surface of the aluminum-silicon alloy, and the deposition amount is accurate and controllable.
In this embodiment, the ceramic powder includes SiC powder and Al powder2O3Powder, Si3N4One or more of powder or CBN powder. The ceramic powder is selected from SiC powder and Al powder2O3powder, Si3N4One or more of the powder or CBN powder, namely the ceramic powder adopts polygonal hard granular ceramic, and the ceramic powder and the metal brazing filler metal extrude and rub the surface of the aluminum-silicon alloy under the action of heating and pressurizing, so that an oxide film is broken, the aluminum-silicon alloy is contacted with the brazing filler metal, and the silicon carbide particle reinforced aluminum-based composite material is promoted to be effectively connected with the aluminum-silicon alloy.
In this embodiment, the ceramic powder has a particle size of 1 to 10 μm and an areal density of 0.5 to 20g/m2。
According to Stokes law:
Wherein V is the settling velocity of the particles, cm/s; d is the particle size of the particles, cm; rhosIs the density of the particles in g/cm3；ρfis the density of the medium, g/cm3(ii) a Eta is the viscosity of the dispersion medium, P; g is gravity acceleration, cm/s2. As can be seen, the particle settling velocity V and the particle diameter D2Proportional, i.e., the larger the particle size, the faster the settling rate. When the grain diameter of the ceramic powder is less than 1 mu m, the precipitation time is too long, and the production efficiency is low; when the grain diameter of the ceramic powder exceeds 10 mu m, the ceramic powder is deposited in the absolute ethyl alcohol solvent too fast, so that the high-silicon aluminum alloy is not put into the mixed liquid, the ceramic powder begins to deposit, and the deposition surface density of the ceramic powder cannot be accurately controlled. The particle size of the ceramic powder is preferably 1-10 mu m, the sedimentation process is easy to control, and the ceramic powder can be ensuredThe powder is uniformly distributed on the aluminum-silicon alloy welding surface, which is beneficial to breaking an oxide film on the surface of the aluminum-silicon alloy. The grain size and the surface density of the ceramic powder have obvious influence on the breaking of an oxide film on the surface of the aluminum-silicon alloy and the mechanical property of a soldered joint. The larger the surface density of the ceramic powder is, the better the oxide film breaking effect is, and the higher the strength of the welded joint is. When a ceramic powder having a small particle diameter is selected, for example, the particle diameter of the ceramic powder is 1 μm, and an appropriate area density (x)1) Is 2.5g/m2～3.5g/m2(ii) a When a ceramic powder having a relatively large particle diameter is selected, for example, the ceramic powder has a particle diameter of 5 μm and a suitable areal density (x)2) Is 2.5g/m2～18g/m2；x2Much larger than x1When the large-particle ceramic powder is aggregated, the porosity among the particles is still high, and the brazing filler metal can be wet-bonded with the base material through the pores among the particles, so that the joint strength is still high at a high surface density. However, when the surface density is too high, the ceramic powders are aggregated to prevent the solder from being wet-bonded to the base material, and the joint strength is reduced accordingly.
in this embodiment, the ultrasonic vibration frequency is 20 to 50kHz, the ultrasonic power is 1000 to 2000W, the ultrasonic vibration time is 5 to 20min, and the standing time is 10 to 240 min. Through ultrasonic treatment, tiny particles suspended in fluid are condensed at nodes under the action of mechanical force, the tiny particles are fully dispersed in absolute ethyl alcohol by utilizing cavitation and acoustic flow effects of ultrasonic waves, proper ultrasonic vibration frequency, ultrasonic power and ultrasonic vibration time are beneficial to uniform dispersion of ceramic powder in the absolute ethyl alcohol, the treatment efficiency is high, after the ultrasonic treatment is finished, an aluminum-silicon alloy is placed in a mixed solution and is kept stand for 10-240 min, the suspended ceramic powder is completely settled on a surface to be welded of the aluminum-silicon alloy, and the optimal standing time can be determined according to the particle size of the ceramic powder, the surface density and the area of the surface to be welded of the aluminum-silicon alloy.
in this embodiment, in step S3, the brazing filler metal is a rolled zinc-based alloy, and the rolled zinc-based alloy includes, by mass: al: 2-15%, Cu: 4-4.5 percent, and the balance of Zn, wherein the melting point of the rolled zinc-based alloy is 380-410 ℃. The brazing filler metal is foil-shaped or sheet-shaped zinc-based alloy brazing filler metal, the melting point is 380-410 ℃, on one hand, the brazing temperature in the step S4 is 390-410 ℃, the brazing temperature is low, the coarsening of the structure of the aluminum-silicon alloy and the reduction of the use performance can be avoided, the brazing filler metal is changed into a semi-solid spherical crystal structure from a rolling state fiber structure at the temperature, the transition region of the brazing filler metal and the base metal is a ceramic powder reinforced zinc-aluminum-based composite material, the difference of linear expansion coefficients of the brazing filler metal and the base metal silicon carbide particle reinforced aluminum-based composite material is relieved, the residual stress of a welding joint is reduced; on the other hand, the spherical grains can generate extrusion and scraping effects on the surfaces of the silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy under the action of pressure, so that the crushing and removal of an oxide film are promoted; the liquid phase can be wetted, spread and diffused on the surfaces to be welded of the aluminum-silicon alloy and the silicon carbide particle reinforced aluminum matrix composite under the action of pressure, so that the metallurgical connection of the silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy is realized.
In this embodiment, in step S4, the heating temperature is increased at a rate of 5-20 ℃/min, the heat-preservation time before pressurization is 10-20 min, and the heat-preservation pressure-maintaining time after pressurization is 10-20 min. Heating and temperature rising are carried out at the temperature rising rate of 5-20 ℃/min, a programmed temperature rising method can be adopted for controlling, so that the temperature rises stably, the defects of air holes, impurities and the like caused by abrupt change of tissue structures of the brazing filler metal and the base metal are prevented, the performance of a welding joint is influenced, the heat preservation before pressurization is used for helping the brazing filler metal to be converted from a rolling fiber tissue into a semi-solid spherulite tissue, the heat preservation time is too short, the change of the tissue of the brazing filler metal is incomplete, the heat preservation time is too long, the tissue is coarsened, and the heat preservation and pressure maintaining after pressurization are used for enabling the surfaces.
Examples
In the following examples, each chemical reagent is commercially available.
Example 1
The brazing method of the high volume fraction silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy of the embodiment comprises the following steps:
s1, preparing an aluminum matrix composite material (63% SiC for short) with silicon carbide particles and 63% of reinforcing phase volume fractionpAl composite materialMaterial) and an aluminum-silicon alloy (CE 11 alloy for short) with the Si particle mass fraction of 50 percent, mechanically polishing the surface to be welded, then ultrasonically cleaning the surface for 10min by using absolute ethyl alcohol, taking out and air-drying the surface for later use.
S2, weighing 0.005g of SiC powder with the particle size of 1 mu m, mixing the SiC powder with 30ml of absolute ethyl alcohol, and putting the mixture into a beaker with the diameter of 50mm to obtain a mixed solution of the SiC powder and the absolute ethyl alcohol; immersing an amplitude transformer of an ultrasonic transducer into a mixed solution of SiC powder and absolute ethyl alcohol, starting ultrasonic vibration, controlling the ultrasonic vibration frequency to be 20kHz, controlling the ultrasonic power to be 1500w, and controlling the ultrasonic time to be 10 min; immediately taking out the beaker after the ultrasonic action is stopped, lightly putting the polished CE11 alloy into the mixed solution, and standing for 120min when the surface is upward; sucking absolute ethyl alcohol on the upper layer of the beaker by a dropper, taking the CE11 alloy at the bottom of the beaker out by a pair of tweezers, and depositing a layer of uniform SiC powder on the to-be-welded surface of the CE11 alloy after air drying, wherein the surface density of the SiC powder is 1.56g/m2。
S3, placing Zn-12.5Al-4.5Cu solder in 63% SiCpand clamping the space between the/Al composite material and the to-be-welded surface of the CE11 alloy deposited with the SiC powder by using a graphite clamp to form a to-be-welded part, and putting the to-be-welded part into a brazing furnace.
And S4, heating the to-be-welded piece to 390 ℃ at the heating rate of 20 ℃/min under the argon atmosphere, and preserving the heat for 15min to convert the brazing filler metal structure into a semi-solid spherical crystal structure. Then applying pressure of 10MPa, keeping the temperature and the pressure for 20min, and then cooling to room temperature along with the furnace to obtain 63% SiCpsemi-solid state pressure brazing of/Al composite and CE11 alloy.
The water-cooled structure of the brazing filler metal at the brazing temperature in this example is shown in FIG. 2. As can be seen from the figure, the brazing filler metal structure is transformed into a semi-solid spherulite structure. The structure of the brazed joint obtained in this example is shown in FIG. 3. As can be seen, SiC at the braze joint interfacepThe oxide films on the Al composite side and the CE11 alloy side completely disappeared, and SiCpthe/Al composite and the CE11 alloy form a strong metallurgical bond. It can also be seen that one side of the CE11 alloy formed a SiC particle-reinforced interface structure. The mechanical properties of the joints were evaluated by the shear results, with a shear strength of 80 MPa. The semi-solid state pressure brazing method can realize high volume divisionNumber SiCpThe effective connection of the/Al composite material and the CE11 alloy and the joint with good bonding performance is obtained.
Example 2
The brazing method of the high volume fraction silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy of the embodiment comprises the following steps:
S1, firstly, the SiC particle reinforced phase volume fraction is 80% of the aluminum matrix composite material (80% SiC for short)pal composite material) and an aluminum-silicon alloy (CE 19 alloy for short) with the Si particle mass fraction of 20 percent, mechanically polishing the surfaces to be welded, then ultrasonically cleaning the surfaces for 10min by using absolute ethyl alcohol, taking out the cleaned surfaces and air-drying the cleaned surfaces for later use.
S2, weighing 0.012g of SiC powder with the particle size of 5 mu m, mixing the SiC powder with 30ml of absolute ethyl alcohol, and putting the mixture into a beaker with the diameter of 50mm to obtain a mixed solution of the SiC powder and the absolute ethyl alcohol; immersing an amplitude transformer of an ultrasonic transducer into a mixed solution of SiC powder and absolute ethyl alcohol, starting ultrasonic vibration, controlling the ultrasonic vibration frequency to be 20kHz, controlling the ultrasonic power to be 2000w, and controlling the ultrasonic time to be 20 min; immediately taking out the beaker after the ultrasonic action is stopped, lightly putting the polished CE19 alloy into the mixed solution, and standing for 30min when the surface is upward; sucking absolute ethyl alcohol on the upper layer of the beaker by a dropper, taking the CE19 alloy at the bottom of the beaker out by a pair of tweezers, and depositing a layer of uniform SiC powder on the to-be-welded surface of the CE19 alloy after air drying, wherein the surface density of the SiC powder is 6g/m2。
S3, placing Zn-12.5Al-4.5Cu solder in 80% SiCpAnd clamping the space between the/Al composite material and the to-be-welded surface of the CE19 alloy deposited with the SiC powder by using a graphite clamp to form a to-be-welded part, and putting the to-be-welded part into a brazing furnace.
And S4, heating the to-be-welded piece to 400 ℃ at the heating rate of 20 ℃/min under the argon atmosphere, and preserving the heat for 10min to convert the brazing filler metal structure into a semi-solid spherical crystal structure. Then applying pressure of 15MPa, keeping the temperature and the pressure for 20min, and then cooling to room temperature along with the furnace to obtain 80% SiCpSemi-solid state pressure brazing of/Al composite and CE19 alloy.
The joint obtained by the implementation method has the shear strength of 72MPa, which shows that the high-silicon aluminum alloy realizes good metallurgical bonding after the oxide film is broken.
Example 3
The brazing method of the high volume fraction silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy of the embodiment comprises the following steps:
S1, firstly, adding 50% SiC to the aluminum matrix composite material with the SiC particle reinforced phase volume fraction of 50% (for short, 50% SiC)pAl composite material) and an aluminum-silicon alloy (CE 17 alloy for short) with the Si particle mass fraction of 27 percent, mechanically polishing the surfaces to be welded, then ultrasonically cleaning the surfaces for 10min by using absolute ethyl alcohol, taking out the cleaned surfaces and air-drying the cleaned surfaces for later use.
S2, weighing Al with the grain diameter of 1 mu m2O30.01g of powder, mixing Al2O3Mixing the powder with 30ml of anhydrous ethanol, and placing into a beaker with a diameter of 50mm to obtain Al2O3A mixed solution of the powder and absolute ethyl alcohol; dipping an amplitude transformer of an ultrasonic transducer into Al2O3Starting ultrasonic vibration in a mixed solution of the powder and absolute ethyl alcohol, controlling the ultrasonic vibration frequency to be 30kHz, controlling the ultrasonic power to be 1000w, and controlling the ultrasonic time to be 5 min; immediately taking out the beaker after the ultrasonic action is stopped, lightly putting the polished CE17 alloy into the mixed solution, and standing for 1h when the surface to be welded faces upwards; sucking absolute ethanol at the upper layer of the beaker by a dropper, taking the CE17 alloy at the bottom of the beaker out by a pair of tweezers, and depositing a layer of uniform Al on the to-be-welded surface of the CE17 alloy after air drying2O3powder of Al2O3the powder had an areal density of 2.3g/m2。
s3, placing Zn-12.5Al-4.5Cu solder in 50% SiCpAnd clamping the space between the/Al composite material and the to-be-welded surface of the CE17 alloy deposited with the SiC powder by using a graphite clamp to form a to-be-welded part, and putting the to-be-welded part into a brazing furnace.
And S4, heating the to-be-welded piece to 396 ℃ at the heating rate of 15 ℃/min under the argon atmosphere, and preserving the heat for 20min to convert the brazing filler metal structure into a semi-solid spherical crystal structure. Then applying pressure of 10MPa, keeping the temperature and the pressure for 20min, and then cooling to room temperature along with the furnace to obtain 50% SiCpsemi-solid state pressure brazing of/Al composite and CE17 alloy. The shear strength of the brazed joint obtained in the embodiment reaches 75 MPa.
Example 4
The brazing method of the high volume fraction silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy of the embodiment comprises the following steps:
S1, firstly, preparing an aluminum matrix composite material (40% SiC for short) with the SiC particle reinforced phase volume fraction of 40%pAl composite material) and an aluminum-silicon alloy (CE 17 alloy for short) with the Si particle mass fraction of 27 percent, mechanically polishing the surfaces to be welded, then ultrasonically cleaning the surfaces for 10min by using absolute ethyl alcohol, taking out the cleaned surfaces and air-drying the cleaned surfaces for later use.
s2, weighing Si with the grain diameter of 1 mu m3N40.01g of powder, mixing Si3N4mixing the powder with 30ml of anhydrous ethanol, and placing into a beaker with a diameter of 50mm to obtain Si3N4A mixed solution of the powder and absolute ethyl alcohol; dipping the horn of an ultrasonic transducer into Si3N4Starting ultrasonic vibration in a mixed solution of the powder and absolute ethyl alcohol, controlling the ultrasonic vibration frequency to be 50kHz, controlling the ultrasonic power to be 1500w, and controlling the ultrasonic time to be 10 min; immediately taking out the beaker after the ultrasonic action is stopped, lightly putting the polished CE17 alloy into the mixed solution, and standing for 1h when the surface to be welded faces upwards; sucking absolute ethanol at the upper layer of the beaker by a dropper, taking the CE17 alloy at the bottom of the beaker out by a pair of tweezers, and depositing a layer of uniform Si on the to-be-welded surface of the CE17 alloy after air drying3N4powder of Si3N4The powder had an areal density of 2.3g/m2。
s3, placing Zn-12.5Al-4.5Cu solder in 40% SiCp/Al composite material and depositing Si3N4And clamping the parts between the to-be-welded surfaces of the powdered CE17 alloy by using a graphite clamp to form a to-be-welded part, and putting the to-be-welded part into a brazing furnace.
and S4, heating the to-be-welded piece to 396 ℃ at the heating rate of 15 ℃/min under the argon atmosphere, and preserving the heat for 15min to convert the brazing filler metal structure into a semi-solid spherical crystal structure. Then applying pressure of 10MPa, keeping the temperature and the pressure for 20min, and then cooling to room temperature along with the furnace to finish 40 percent SiCpSemi-solid state pressure brazing of/Al composite and CE17 alloy. The shear strength of the brazing joint obtained in the embodiment reaches 78 MPa.
The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention, and various modifications and changes may be made by those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (10)
1. A brazing method of a high volume fraction silicon carbide particle reinforced aluminum matrix composite and an aluminum-silicon alloy is characterized by comprising the following steps:
S1, cleaning the surfaces to be welded of the high volume fraction silicon carbide particle reinforced aluminum matrix composite and the aluminum-silicon alloy;
S2, presetting ceramic powder on the surface to be welded of the aluminum-silicon alloy treated in the step S1;
S3, assembling the aluminum-silicon alloy treated in the step S2 and the high volume fraction silicon carbide particle reinforced aluminum matrix composite treated in the step S1, placing brazing filler metal between surfaces to be welded of the aluminum-silicon alloy and the high volume fraction silicon carbide particle reinforced aluminum matrix composite, and clamping to form a piece to be welded;
S4, heating the to-be-welded piece to 390-410 ℃ under a protective atmosphere, preserving heat, pressurizing to 5-20 MPa, continuing preserving heat and maintaining pressure for a period of time, and then cooling to room temperature along with the furnace.
2. The method for brazing high volume fraction SiC particle-reinforced Al matrix composite material to Al-Si alloy as claimed in claim 1,
The high volume fraction silicon carbide particle reinforced aluminum matrix composite is 40-80% of silicon carbide particle reinforced aluminum matrix composite.
3. The method for brazing high volume fraction SiC particle-reinforced Al matrix composite material to Al-Si alloy as claimed in claim 1,
The aluminum-silicon alloy is 20-50% of silicon particles by mass.
4. the method for brazing a high volume fraction SiC particle-reinforced Al-based composite material to an Al-Si alloy according to any one of claims 1 to 3,
In step S2, the preset ceramic powder on the surface to be welded of the aluminum-silicon alloy processed in step S1 is prepared by a suspension deposition method, which includes the following steps:
mixing ceramic powder and absolute ethyl alcohol to obtain a mixed solution of the ceramic powder and the absolute ethyl alcohol, carrying out ultrasonic vibration on the mixed solution to fully disperse the ceramic powder, putting the aluminum-silicon alloy treated in the step S1 into the mixed solution, standing for a period of time until the ceramic powder is deposited on the surface to be welded, removing the absolute ethyl alcohol on the upper layer, taking out the treated aluminum-silicon alloy, and air-drying.
5. the method for brazing high volume fraction SiC particle-reinforced Al matrix composite material to Al-Si alloy as claimed in claim 4,
The ceramic powder comprises SiC powder and Al2O3Powder, Si3N4One or more of powder or CBN powder.
6. The method for brazing high volume fraction SiC particle-reinforced Al matrix composite material to Al-Si alloy as claimed in claim 5,
The grain diameter of the ceramic powder is 1-10 mu m, and the surface density of the ceramic powder is 0.5-20 g/m2。
7. The method for brazing high volume fraction SiC particle-reinforced Al matrix composite material to Al-Si alloy as claimed in claim 4,
The ultrasonic vibration frequency is 20-50 kHz, the ultrasonic power is 1000-2000W, the ultrasonic vibration time is 5-20 min, and the standing time is 10-240 min.
8. The method for brazing a high volume fraction SiC particle-reinforced Al-based composite material to an Al-Si alloy according to any one of claims 1 to 3,
In step S3, the brazing filler metal is a rolled zinc-based alloy, and the rolled zinc-based alloy comprises the following components in percentage by mass: al: 2-15%, Cu: 4-4.5% and the balance of Zn.
9. The method of brazing high volume fraction SiC particle-reinforced Al matrix composite material to Al-Si alloy as claimed in claim 8,
The melting point of the rolled zinc-based alloy is 380-410 ℃.
10. The method for brazing a high volume fraction SiC particle-reinforced Al-based composite material to an Al-Si alloy according to any one of claims 1 to 3,
In step S4, the heating temperature rise is carried out at a temperature rise rate of 5-20 ℃/min, the heat preservation time before pressurization is 5-20 min, and the heat preservation and pressure maintaining time after pressurization is 10-20 min.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111992832A (en) * | 2020-08-27 | 2020-11-27 | 珠海亿特立新材料有限公司 | Preparation method of aluminum silicon carbide water-cooling toothed plate |
| CN113385805A (en) * | 2021-06-15 | 2021-09-14 | 上海交通大学 | Welding method of 65% silicon carbide particle reinforced aluminum matrix composite material with pure Al as intermediate material layer |
| CN113814601A (en) * | 2021-09-24 | 2021-12-21 | 郑州机械研究所有限公司 | Brazing sheet and brazing method |
| CN114478043A (en) * | 2022-01-12 | 2022-05-13 | 中国科学院上海硅酸盐研究所 | Connection method of silicon carbide ceramic based on liquid phase sintering |
| CN115974573A (en) * | 2022-12-15 | 2023-04-18 | 中国科学院上海硅酸盐研究所 | Silicon carbide connecting piece and method for connecting silicon carbide ceramic and composite material thereof by using laser-assisted silicon-aluminum alloy |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101733497A (en) * | 2009-11-30 | 2010-06-16 | 河南理工大学 | Hard soldering method of high volume fraction SiC particle-reinforced Al matrix composite and kovar alloy dissimilar material |
| CN102266994A (en) * | 2011-07-20 | 2011-12-07 | 重庆理工大学 | Heterogeneous semi-solid brazing method for aluminum alloy and magnesium alloy under assistance of external vibration energy |
| CN102658411A (en) * | 2012-05-24 | 2012-09-12 | 哈尔滨工业大学 | Ultrasonic brazing method for high-volume-fraction silicon carbide particle enhanced aluminum-base composite and low-expansion alloy |
| CN102802858A (en) * | 2010-03-18 | 2012-11-28 | 西门子公司 | A method for brazing a surface of a metallic substrate |
| CN105269105A (en) * | 2015-12-03 | 2016-01-27 | 天津理工大学 | High-silicon aluminum alloy welding method for forming particle-reinforced weld joints through thermo-acoustic coupling |
-
2019
- 2019-08-12 CN CN201910739111.7A patent/CN110576232B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101733497A (en) * | 2009-11-30 | 2010-06-16 | 河南理工大学 | Hard soldering method of high volume fraction SiC particle-reinforced Al matrix composite and kovar alloy dissimilar material |
| CN102802858A (en) * | 2010-03-18 | 2012-11-28 | 西门子公司 | A method for brazing a surface of a metallic substrate |
| CN102266994A (en) * | 2011-07-20 | 2011-12-07 | 重庆理工大学 | Heterogeneous semi-solid brazing method for aluminum alloy and magnesium alloy under assistance of external vibration energy |
| CN102658411A (en) * | 2012-05-24 | 2012-09-12 | 哈尔滨工业大学 | Ultrasonic brazing method for high-volume-fraction silicon carbide particle enhanced aluminum-base composite and low-expansion alloy |
| CN105269105A (en) * | 2015-12-03 | 2016-01-27 | 天津理工大学 | High-silicon aluminum alloy welding method for forming particle-reinforced weld joints through thermo-acoustic coupling |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111992832A (en) * | 2020-08-27 | 2020-11-27 | 珠海亿特立新材料有限公司 | Preparation method of aluminum silicon carbide water-cooling toothed plate |
| CN113385805A (en) * | 2021-06-15 | 2021-09-14 | 上海交通大学 | Welding method of 65% silicon carbide particle reinforced aluminum matrix composite material with pure Al as intermediate material layer |
| CN113814601A (en) * | 2021-09-24 | 2021-12-21 | 郑州机械研究所有限公司 | Brazing sheet and brazing method |
| CN114478043A (en) * | 2022-01-12 | 2022-05-13 | 中国科学院上海硅酸盐研究所 | Connection method of silicon carbide ceramic based on liquid phase sintering |
| CN114478043B (en) * | 2022-01-12 | 2023-05-09 | 中国科学院上海硅酸盐研究所 | Connecting method of silicon carbide ceramic based on liquid phase sintering |
| CN115974573A (en) * | 2022-12-15 | 2023-04-18 | 中国科学院上海硅酸盐研究所 | Silicon carbide connecting piece and method for connecting silicon carbide ceramic and composite material thereof by using laser-assisted silicon-aluminum alloy |
| CN115974573B (en) * | 2022-12-15 | 2023-11-10 | 中国科学院上海硅酸盐研究所 | Silicon carbide connecting piece and method for connecting silicon carbide ceramic and composite material thereof by laser-assisted silicon-aluminum alloy |
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