CN114959378B - Aluminum-silicon alloy and preparation method of aluminum-silicon alloy casting - Google Patents
Aluminum-silicon alloy and preparation method of aluminum-silicon alloy casting Download PDFInfo
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Abstract
The invention provides an aluminum-silicon alloy, which comprises the following components: 7.5 to 11.5 weight percent of Si; 4-5 wt% of Cu; ni 2.0-3.5 wt%; 0.4 to 0.8 weight percent of Mg; fe 0.6-1.44 wt%; 0.10 to 0.24 weight percent of Co; v0.3-0.72 wt%; 0.05 to 0.1 weight percent of Hf; y0.05-0.1 wt%; k is 0.005-0.01 wt%; na 0.005-0.010 wt% and the balance of Al. The application also provides a preparation method of the aluminum-silicon alloy casting. According to the method, through selection of the content of various elements in the aluminum-silicon alloy, particularly limitation of the content relation of Fe, V and Co, the obtained aluminum-silicon alloy with short needle-shaped iron phase, excellent high-temperature strength and heat conductivity can be used as a piston material, and the requirements of continuous improvement of the existing and future diesel engine piston technical indexes are met.
Description
Technical Field
The invention relates to the technical field of aluminum alloy, in particular to an aluminum-silicon alloy and a preparation method of a casting of the aluminum-silicon alloy.
Background
In recent years, energy conservation, emission reduction and low-carbon economy are gradually focused and pursued, and the automobile industry as a large oil consumption user is first strived for; and with the aggravation of energy and environmental protection problems and the challenges of electric/hybrid car technology faced by the internal combustion engine industry, the internal combustion engine is promoted to develop towards high power, high rotation speed, high supercharging, low oil consumption and low emission.
In recent years, the technology of the internal combustion engine is rapidly developed, the power rising and the explosion pressure of the engine are continuously improved, and along with the higher and higher work load born by a piston, higher requirements are put on the heat dissipation performance and the heat resistance performance of the piston material, particularly the high-temperature performance, but the tensile strength performance of an aluminum piston in a high-temperature working area is suddenly reduced in contradiction with the high-temperature performance. The capability of the traditional aluminum piston material for bearing high heat load is close to the limit, and the aluminum alloy piston material with high heat resistance and high heat conduction is urgently needed to be developed.
At present, most of domestic and foreign diesel engine pistons adopt eutectic Al-Si alloy, the representative Al-Si alloy piston material is ZL109, meanwhile, in order to further improve the comprehensive performance of the material, the components of the ZL109 material are optimized, the content of strengthening elements such as Cu, ni and the like is improved, and the piston alloy Al-Si-Cu-Mg-Ni material is perfected, and is specifically shown in tables 1 and 2; ZL109 material and Al-Si-Cu-Mg-Ni material are commonly used as piston base materials with the characteristics of small linear expansion coefficient, good wear resistance, good casting performance and the like.
TABLE 1 ZL109 Material composition (wt%)
TABLE 2 Al-Si-Cu-Mg-Ni Material composition (wt%)
Fe is extremely easily excessively dissolved into the aluminum liquid due to various smelting tools and raw materials that come into contact with the aluminum liquid, and is difficult to remove in general casting methods. The Fe element inevitably exists in the existing casting ZL109 material and Al-Si-Cu-Mg-Ni aluminum silicon alloy, exists in the form of a metal compound, forms a hard and brittle thick needle-shaped, skeleton-shaped or sheet-shaped iron-rich phase, severely breaks a matrix to become a stress concentration source, greatly reduces the room temperature mechanical property of the alloy, and in addition, the thick needle-shaped or sheet-shaped iron phase can obstruct the flow of interdendritic liquid in the feeding process, so shrinkage cavities are more easily generated, and a microscopic structure photo of the thick Fe-containing phase of the casting prepared by the conventional method is shown in fig. 6. Therefore, changing the morphology of the iron phase, reducing the harmful effects thereof, even utilizing Fe element and Fe phase, has been a hot spot of people's research
Disclosure of Invention
The invention solves the technical problem of providing an aluminum-silicon alloy with excellent high-temperature strength and heat conductivity.
In view of this, the present application provides an aluminum-silicon alloy comprising:
7.5 to 11.5 weight percent of Si; 4-5 wt% of Cu; ni 2.0-3.5 wt%; 0.4 to 0.8 weight percent of Mg; fe 0.6-1.44 wt%; 0.10 to 0.24 weight percent of Co; v0.3-0.72 wt%; 0.05 to 0.1 weight percent of Hf; y0.05-0.1 wt%; k is 0.005-0.01 wt%; 0.005 to 0.010 weight percent of Na0.005 and the balance of Al; and the mass percentage content of Fe, V, and Co satisfies 6 coowt% = 2Vwt% = 1Fewt%.
Preferably, the content of Fe is 0.75-1.25 wt%, the content of Co is 0.13-0.20 wt%, the content of V is 0.35-0.65 wt%, the content of Hf is 0.06-0.08 wt%, the content of Y is 0.06-0.09 wt%, the content of K is 0.006-0.009 wt%, and the content of Na is 0.006-0.009 wt%.
The application also provides a preparation method of the aluminum-silicon alloy casting, which comprises the following steps:
a) Proportioning high-purity aluminum, silicon nickel raw materials, magnesium raw materials, copper raw materials, iron raw materials, aluminum vanadium intermediate alloy, aluminum cobalt intermediate alloy, aluminum hafnium intermediate alloy and aluminum yttrium intermediate alloy;
b) Melting a silicon-nickel raw material, a high-purity aluminum, a copper raw material, an aluminum-cobalt intermediate alloy and an iron raw material to obtain a pre-alloyed alloy;
c) Adding a potassium/sodium modifier and a magnesium raw material into the pre-alloyed alloy, heating, adding an aluminum-hafnium intermediate alloy and an aluminum-yttrium intermediate alloy, and preserving heat;
d) Sequentially discharging the melt obtained in the step C), rotating for degassing, refining, and pouring after deslagging; simultaneously starting an ultrasonic device when the casting is started, wherein the rapid cooling speed of the casting is more than or equal to 115 ℃/s;
e) Quenching the casting obtained in the step D), and finally sequentially carrying out solution treatment and aging treatment.
Preferably, in the step C), the temperature of the premelted alloy is 750-800 ℃, and the modifier is K and Na composite modifier.
Preferably, in the step C), the temperature of the heat preservation is 820-880 ℃ and the time is more than or equal to 20min.
Preferably, in the step D), the tapping temperature is 830-860 ℃, the temperature of the rotary degassing is 750-770 ℃, the rotor speed of the rotary degassing is 300-400 rpm, the refining time is 10-20 min, and the compressed air flow rate of the refining is 0.5-1.0 m 3 /h。
Preferably, in the step D), the die is preheated before casting, the temperature of the inner die of the die is 310-340 ℃, the temperature of the shaft pin is 250-280 ℃, the temperature of the outer die is 150-180 ℃, and the temperature of the die cover is 100-130 ℃; the mold is filled with water during casting, the water pressure of the filled water is 0.4-1.0 MPa, and the water flow rate is 4.5-10.5L/min.
Preferably, in the step D), the vibration power of the ultrasonic device is 80-90%, the frequency is 10-20 KHz, and the time is 10-20 s.
Preferably, in step E), the quenching is air cooling or water quenching.
Preferably, the temperature of the solution treatment is 400-500 ℃, the time is 5-10 h, the cooling medium is hot water at 60-80 ℃, the aging temperature is 200-300 ℃, the time is 5-6 h, and the cooling medium is air.
The present application provides a silicon-aluminum alloy comprising: 7.5 to 11.5 weight percent of Si; 4-5 wt% of Cu; ni 2.0-3.5 wt%; 0.4 to 0.8 weight percent of Mg; fe 0.6-1.44 wt%; 0.10 to 0.24 weight percent of Co; v0.3-0.72 wt%; 0.05 to 0.1 weight percent of Hf; y0.05-0.1 wt%; k is 0.005-0.01 wt%; 0.005 to 0.010 weight percent of Na0.005 and the balance of Al; and the mass percentage content of Fe, V, and Co satisfies 6 coowt% = 2Vwt% = 1Fewt%. In the present application, fe, co and V, K and Na are all the same body-centered cubic crystal structure (BCC), while the relation of Fe, V and Co content is defined such that Fe, co and V preferentially form fine V (Fe, co) 3 The compound has dispersion and pinning strengthening effects and is effective at the same timeInhibit the formation of coarse AlSiFe and other compounds, and improve the high temperature resistance of the Al-Si alloy at high temperature; k and Na have effective deterioration effect under certain rapid solidification and ultrasonic vibration conditions, and coarse AlSiFe phase compounds are thinned; furthermore, trace elements Hf, Y and the like can be used as heterogeneous nucleation cores for non-uniform nucleation of the matrix melt, so that coarse Fe is effectively prevented 4 Al 13 Coarse, fine matrix structure; the reduction of Si content can improve the plasticity of the aluminum-silicon alloy, reduce the average size of primary crystal silicon by 5% or more, improve the elongation and improve the thermal fatigue resistance; the reduction of the content of Mg element can reduce ablation impurities.
The application also provides a preparation method of the aluminum-silicon alloy casting, and ultrasonic treatment is introduced to crush the iron phase and simultaneously assist in a proper melt rapid cooling control technology, so that ultrasonic crushing is applied to V (Fe, co) 3 、Fe 4 Al 13 Nucleation and growth of iron phases such as AlSiFe compounds, inhibiting growth of iron phases, and strengthening the iron-containing strengthening phase Al 9 FeNi (small amount), fe 2 Al 7.4 Si (small amount) and Fe 2 Al 9 Si 2 The crushing action of the second phases, such as (main) and the like, can be used as alloy phase dispersion strengthening, and is a very important way for improving the alloy performance of the aluminum-silicon alloy casting.
Drawings
FIG. 1 is a macroscopic photograph of an aluminum silicon alloy casting of the present invention incorporating 0.06wt% Hf and 0.07wt% Y;
FIG. 2 shows the addition of 0.005 to 0.001wt% K according to the invention; macroscopic photographs of 0.005-0.001 wt% Na of aluminum-silicon alloy castings;
FIG. 3 is a schematic diagram of the ultrasonic device and piston casting mold used in the casting process of the invention;
FIG. 4 is a graph showing the relationship between the cooling rate and the ultrasonic vibration and the size of the iron phase in example 1 of the present invention;
FIG. 5 is a graph showing the relationship between the cooling rate and the ultrasonic vibration and the size of the iron phase in example 1 of the present invention;
FIG. 6 is a graph showing the relationship between the cooling rate and the ultrasonic vibration and the size of the iron phase in example 3 of the present invention;
FIG. 7 is a photograph of a microstructure of a casting prepared by a conventional method, which contains coarse Fe phases;
FIG. 8 is a photograph of a microstructure of a casting prepared in example 1 of the present invention;
FIG. 9 is a photograph of a microstructure of a casting prepared in example 2 of the present invention;
FIG. 10 is a photograph of a microstructure of a casting prepared in example 3 of the present invention;
FIG. 11 is a macroscopic photograph of the castings prepared according to examples 1 to 3;
FIG. 12 is a photograph showing metallographic structures of castings prepared in examples 1 to 3.
Detailed Description
For a further understanding of the present invention, preferred embodiments of the invention are described below in conjunction with the examples, but it should be understood that these descriptions are merely intended to illustrate further features and advantages of the invention, and are not limiting of the claims of the invention.
Aiming at the problem that Fe element in aluminum-silicon alloy affects high-temperature heat resistance and strength of alloy in the prior art, the application provides a preparation method of aluminum-silicon alloy and aluminum-silicon alloy castings, which is added with Fe, co and V in a certain proportion and limits the proportion relation of the Fe, co and V, and can preferentially form tiny V (Fe, co) 3 A compound; k and Na are added to effectively deteriorate under certain conditions of rapid solidification and ultrasonic vibration, so that the formation of needle-shaped Fe phases is effectively prevented; the trace elements Hf and Y are added to refine the Fe phase and the alloy matrix structure, the rapid solidification is further combined with the adoption of casting, and an ultrasonic vibration mode is combined, so that the aluminum-silicon alloy casting with the short needle-shaped iron phase, excellent high-temperature strength and heat conductivity is obtained, and the requirements of continuous improvement of the existing and future diesel engine piston technical indexes are met. The embodiment of the invention discloses an aluminum-silicon alloy, which comprises the following components:
7.5 to 11.5 weight percent of Si; 4-5 wt% of Cu; ni 2.0-3.5 wt%; 0.4 to 0.8 weight percent of Mg; fe 0.6-1.44 wt%; 0.10 to 0.24 weight percent of Co; v0.3-0.72 wt%; 0.05 to 0.1 weight percent of Hf; y0.05-0.1 wt%; k is 0.005-0.01 wt%; 0.005 to 0.010 weight percent of Na0.005 and the balance of Al; and the mass percentage content of Fe, V and Co satisfies 6co=2v=1fe.
Specifically, the content of Fe is 0.75-1.25 wt%, the content of Co is 0.13-0.20 wt%, the content of V is 0.35-0.65 wt%, the content of Hf is 0.06-0.08 wt%, the content of Y is 0.06-0.09 wt%, the content of K is 0.006-0.009 wt%, and the content of Na is 0.006-0.009 wt%.
More specifically, in the aluminum-silicon alloy provided herein, the content of Si is specifically 7.5 to 11.5wt%, and more specifically, the content of Si is 7.5wt%, 7.8wt%, 8.0wt%, 8.2wt%, 8.4wt%, 8.5wt%, 8.7wt%, 8.9wt%, 9wt%, 9.1wt%, 9.2wt%, 9.3wt%, 9.5wt%, 9.7wt%, 9.8wt%, 9.9wt%, 10wt%, 10.1wt%, 10.3wt%, 10.5wt%, 10.7wt%, 10.8wtt%, 11wt%, 11.2wt%, or 11.5wt%.
The Cu content is specifically 0.41wt%, 0.42wt%, 0.43wt%, 0.44wt%, 0.45wt%, 0.46wt%, 0.47wt%, 0.48wt% or 0.49wt%.
The Mg content is in particular 0.4 wt.%, 0.5 wt.%, 0.6 wt.%, 0.7 wt.% or 0.8 wt.%.
The content of Fe is specifically 0.7wt%, 0.8wt%, 0.9wt%, 1.0wt%, 1.1wt%, 1.2wt%, 1.3wt%, 1.4wt% or 1.42wt%.
The Co content is 0.10wt%, 0.11wt%, 0.12wt%, 0.13wt%, 0.14wt%, 0.15wt%, 0.16wt%, 0.17wt%, 0.18wt%, 0.19wt%, 0.20wt%, 0.21wt%, 0.22wt%, 0.23wt% or 0.24wt%.
The V content is 0.30wt%, 0.32wt%, 0.33wt%, 0.35wt%, 0.38wt%, 0.39wt%, 0.41wt%, 0.43wt%, 0.44wt%, 0.46wt%, 0.52wt%, 0.55wt%, 0.58wt%, 0.62wt%, 0.65wt%, 0.67wt% or 0.70wt%.
The K content is 0.005wt%, 0.006wt%, 0.007wt%, 0.008wt%, 0.009wt% or 0.01wt%.
The Na content was 0.005wt%, 0.006wt%, 0.007wt%, 0.008wt%, 0.009wt% or 0.01wt%.
The content of Hf is 0.05wt%, 0.06wt%, 0.07wt%, 0.08wt%, 0.09wt% or 0.10wt%.
The content of Y is 0.05wt%, 0.06wt%, 0.07wt%, 0.08wt%, 0.09wt% or 0.10wt%.
In the application, the content relation of Fe, V and Co is as follows: when 6Cowt% = 2Vwt% = 1Fewt%, fe, co and V preferentially form fine V (Fe, co) 3 The compound has strengthening effect and can effectively inhibit the formation of coarse AlSiFe and other compounds; trace elements Hf, Y and the like are added to serve as heterogeneous nucleation cores for non-uniform nucleation of the matrix melt, so that coarse Fe is effectively prevented 4 Al 13 Coarse, fine matrix structure, dispersion and pinning strengthening effect, high temperature resistance of Al-Si alloy at high temperature, and specific effect shown in figure 1; k and Na are added to effectively modify the effect under certain conditions of rapid solidification and ultrasonic vibration, and coarse AlSiFe phase compounds are refined, and the specific effect is shown in figure 2; the content of Si element is reduced, the average size of primary crystal silicon is reduced by 5 percent or more, the elongation is improved, and the thermal fatigue resistance is improved; the Mg element is easy to ablate to generate impurities, and compared with the traditional alloy material, the material provided by the invention has the advantages that the content of the Mg element is reduced, and the ablation impurities are reduced.
The application also provides a preparation method of the casting of the aluminum-silicon alloy, which comprises the following steps:
a) Proportioning high-purity aluminum, silicon nickel raw materials, magnesium raw materials, copper raw materials, iron raw materials, aluminum vanadium intermediate alloy, aluminum cobalt intermediate alloy, aluminum hafnium intermediate alloy and aluminum yttrium intermediate alloy;
b) Melting a silicon-nickel raw material, a high-purity aluminum, a copper raw material, an aluminum-cobalt intermediate alloy and an iron raw material to obtain a pre-alloyed alloy;
c) Adding a potassium/sodium modifier and a magnesium raw material into the pre-alloyed alloy, heating, adding an aluminum-vanadium intermediate alloy, an aluminum-hafnium intermediate alloy and an aluminum-yttrium intermediate alloy, and preserving heat;
d) Sequentially discharging the melt obtained in the step C), rotating for degassing, refining, and pouring after deslagging; after the casting is started, simultaneously starting an ultrasonic device, wherein the rapid cooling speed of the casting is more than or equal to 115 ℃/s;
e) Quenching the casting obtained in the step D), and finally sequentially carrying out solution treatment and aging treatment.
In the process of preparing the aluminum-silicon alloy casting, the raw materials are firstly mixed according to the proportion, namely, high-purity aluminum, silicon-nickel raw materials, magnesium raw materials, copper raw materials, iron raw materials, aluminum-vanadium intermediate alloy, aluminum-cobalt intermediate alloy, aluminum-hafnium intermediate alloy and aluminum-yttrium intermediate alloy are mixed; in the present application, the silicon nickel feedstock is specifically selected from crystalline silicon nickel plates, the magnesium feedstock is specifically selected from magnesium blocks, the copper feedstock is specifically selected from cathode copper, and the iron feedstock is specifically selected from industrially pure iron.
After the batching is finished, firstly, melting a silicon-nickel raw material, a high-purity aluminum, a copper raw material, an iron raw material, an aluminum-cobalt intermediate alloy and an aluminum-zirconium intermediate alloy to obtain a pre-alloyed alloy; in the primary melting stage, the temperature should be slowly raised after the melting furnace is stopped for a long time for charging, and the temperature is kept at 500 ℃ for 30-60 minutes and then raised again for melting; for a continuously used melting furnace, firstly cleaning oxidizing slag on the furnace wall, fishing out the furnace bottom slag completely, pouring the slag into a slag leakage barrel, and then starting charging and melting.
After the pre-alloyed alloy is obtained, the temperature is raised to 750-800 ℃, the preheated sample die bottom is used for stripping the oxide film on the surface of the aluminum liquid, the component sample is taken for spectral analysis, a proper amount of potassium/sodium modifier and Mg ingot are added after calculation and weighing, other components can be added with corresponding alloy to adjust if necessary, and then the power of the intermediate frequency furnace is increased to heat. And adding the rest intermediate alloy after the temperature is increased to 800 ℃, in the process, adopting a preheated slag scooping ladle to gently turn the liquid level to ensure that the liquid level has no solid furnace charge, then stirring for 8 times by using a preheated stirring rod, pulling out surface scum, reducing the power of an intermediate frequency furnace, keeping the temperature of the aluminum liquid at 820-880 ℃ for not less than 20 minutes, and timely pouring the aluminum liquid (tapping) in order to reduce the oxidation of the aluminum liquid and the energy consumption.
Sequentially discharging the obtained melt, rotating for degassing, refining and deslagging, and then pouring; in the process, the tapping temperature is 830-860 ℃, the rotary degassing temperature is 750-770 ℃, the rotor speed of the rotary degassing is 300-400 rpm, the refining time is 10-20 min, and the compressed air flow of the refining is 0.5-1.0 m 3 /h; more specificallyIn the process of slag beating, 0.02wt% of slag beating agent can be added on the surface of each furnace aluminum water, slag on the liquid level is turned over by a slag scooping spoon for at least 2 minutes, slag on the aluminum water surface is fished out, and the fished slag is poured into a slag frying platform or a slag frying barrel and is scraped as much as possible.
The application focuses on adjusting the casting process, preheating the die before casting, and specifically comprises the following steps: the temperature of the inner die of the die is 310-340 ℃, the temperature of the shaft pin is 250-280 ℃, the temperature of the outer die is 150-180 ℃, and the temperature of the die cover is 100-130 ℃; and controlling the temperature of the die, so as to control the solidification time of the casting blank. The casting process comprises the following steps: the ladle is used for scooping enough aluminum water required by pouring, and the aluminum water temperature is 750 ℃; after aluminum water is scooped, one face with a nozzle is aligned with a pouring gate to perform pouring according to the principle of firstly, then, slowly and then quickly, and the pouring is continuous and stable; when the aluminum liquid in the casting ladle is poured for the most part and the aluminum liquid in the cavity is covered on the insert ring, the casting mould is slowly put flat (a pedal reset switch or an inductive probe is automatically reset and controlled), and the casting action cannot be stopped until the riser is fully cast; starting the pouring and simultaneously starting an ultrasonic device, and performing ultrasonic vibration power: 80% -90%, frequency 10-20 KHz, ultrasonic time: 10-20 s; meanwhile, the water flowing time and water flowing flow technological parameters of the die are shown in the following table, and the water pressure is 0.4-0.6 MPa. The rapid cooling speed is controlled to be more than or equal to 115 ℃/s when the blank is poured, the ultrasonic action is controlled to be applied to the solidification of the main Fe phase and the strengthening phase, the growth of the iron phase is obviously inhibited, and the casting mechanical property is improved. The ultrasonic device and the piston casting mould adopted by the application are structurally and schematically shown in fig. 3.
Quenching the obtained casting, and finally sequentially carrying out solution treatment and aging treatment; after the casting is solidified, the casting mould is opened, an operator should take down the piston within 30 seconds, then transfer the piston into an air cooling frame or a water through tank within 10 seconds, and then air cooling or water quenching is carried out. The temperature of the solution treatment is 400-500 ℃, the time is 5-10 h, the cooling medium is hot water at 60-80 ℃, the temperature of the aging is 200-300 ℃, the time is 5-6 h, and the cooling medium is air.
In the present application, addition of Fe, co and V preferentially forms fine V (Fe, co) 3 The compound has the functions of dispersion and pinning reinforcement, and simultaneously effectively inhibits the formation of coarse AlSiFe and other compounds, so that the high temperature resistance of the Al-Si alloy at high temperature is improved; the trace elements Hf, Y and the like are added to be used as heterogeneous nucleation cores for non-uniform nucleation of the matrix melt, so that coarse Fe is effectively prevented 4 Al 13 Coarse, and simultaneously, refining the matrix structure; k and Na are added to effectively deteriorate under certain conditions of rapid solidification and ultrasonic vibration, so that coarse AlSiFe phase compounds are refined. Compared with the traditional alloy material, the material reduces the content of Si element. In order to improve the plasticity of the alloy material, the average size of primary silicon is reduced by 5% or more, the elongation is improved, and the thermal fatigue resistance is improved; compared with the traditional alloy material, the material provided by the invention has the advantage that the content of Mg element is reduced. The Mg element generally forms Mg 2 Si has solid solution strengthening effect, the action temperature is below 200 ℃, the heat resistance cannot be improved, and burning impurities can be generated; the ultrasonic treatment of the crushed iron phases is accompanied by a proper melt rapid cooling control technology: the ultrasonic disruption is applied to Fe 4 Al 13 Nucleation of equi-iron phases combined with growth of inhibition phase, strengthening of iron-containing strengthening phase Al 9 FeNi (small amount), fe 2 Al 7.4 Si (small amount), fe 2 Al 9 Si 2 The crushing action of the second phase such as (main) and the like can be used as alloy phase dispersion strengthening, is a very important way for improving the alloy performance of the invention, the second phase forming temperature corresponding to the ultrasonic ending time is critical to the control of the alloy structure morphology, and the closer the ultrasonic ending time is to the solidification end stage, the more remarkable the refining effect on the second phase is; after the ultrasonic wave is applied, a spherical silicon phase and a micron-sized iron phase which are obviously thinned can be formed in a local area; aiming at the characteristics of the ultrasonic vibration and rapid cooling process, the stepped aging process technology is adopted, so that the dimensional stability of a piston product and the hardness of a material are effectively ensured to be within the required range.
The Fe phase is strengthened in different temperature intervals in the alloy of the invention as shown in Table 3;
table 3 utilization of second phase thermal stability and action in Al-Si Multi-element alloys
In order to further understand the present invention, the following examples are provided to illustrate the preparation method of the aluminum-silicon alloy and the casting thereof in detail, and the scope of the present invention is not limited by the following examples.
Example 1
(1) Proportioning materials
Proportioning industrial high-purity aluminum, crystalline silicon nickel plates, magnesium blocks, cathode copper, industrial pure iron, aluminum-vanadium intermediate alloy, aluminum-cobalt intermediate alloy, aluminum-hafnium intermediate alloy, aluminum-yttrium intermediate alloy and the like according to the following proportion;
the chemical components are as follows: 11wt% of Si; cu4wt%; ni 2.5wt%; 0.4wt% of Mg; fe0.6 wt%; 0.10wt% of Co; v0.3 wt%; 0.06wt% of Hf; y0.06 wt%; k0.006wt%; na0.006wt% and the balance of Al.
(2) Melting of charge
Slowly heating up after charging the melting furnace which is stopped for a long time, and heating up to melt after preserving heat for 40 minutes at 500 ℃; for a continuously used melting furnace, firstly cleaning oxidizing slag on the furnace wall, completely removing slag at the furnace bottom, pouring the slag into a slag leakage barrel, and then starting charging and melting;
the charging sequence of the material premelted alloy of the invention is as follows: all crystalline silicon, partial pure aluminum ingot, nickel plate, cathode copper, industrial pure iron and the like, so that the added materials are compacted as much as possible without leaving obvious gaps;
(4) Mg and potassium/sodium modified alloy
The method comprises the steps of (1) removing an oxide film on the surface of an aluminum liquid from the bottom of a preheated sample die in the range of 760 ℃ for pre-alloyed gold, taking a component sample for spectrum analysis, adding a proper amount of potassium/sodium modifier and Mg ingots after calculation and weighing, adding corresponding alloys into other components if necessary for adjustment, and then increasing the power of an intermediate frequency furnace for heating;
(5) Aluminum-hafnium intermediate alloy, aluminum-yttrium intermediate alloy and heat insulation
After the temperature is increased to 800 ℃, adding the intermediate alloy, lightly turning the liquid surface by using a preheated slag scooping ladle to ensure that the liquid surface is free of solid furnace charge, stirring for 8 times by using a preheated stirring rod, pulling out surface scum, regulating the power of an intermediate frequency furnace, keeping the temperature of the aluminum liquid at 850 ℃, keeping the temperature for not less than 20 minutes, and timely pouring the aluminum liquid (discharging) to reduce the oxidation of the aluminum liquid and reduce the energy consumption;
(6) Tapping temperature requirement
The tapping temperature of the molten aluminum is controlled within a certain range, and the temperature of the pre-fusion is Jin Chulu ℃ and 840 ℃;
(7) Rotary degassing
The rotary degassing temperature is 760 ℃, the rotor speed is 400 rpm, the refining time is 12min, and the compressed air flow is 0.6m 3 /h
(8) Slag beating
Adding 0.02wt% of slag-beating agent on the surface of each furnace of molten aluminum, stirring slag on the liquid surface for at least 2 minutes by using a slag-fishing ladle, fishing out slag on the surface of the molten aluminum, pouring the fished slag into a slag-frying platform or a slag-frying barrel, and scraping the slag as much as possible;
(9) Casting process
The preheating temperature of the die before casting is shown in table 4, and the blank solidification time is controlled mainly by controlling the temperature of the die;
table 4 casting mold temperature control
In the pouring process, a ladle is used for ladle-taking enough aluminum water required by pouring, the temperature of the aluminum water is 750 ℃, one face with a nozzle is aligned with a pouring gate for pouring after ladle-taking the aluminum water, and the pouring is continuous and stable according to the principle of firstly, then, slowly and then, quickly; when the aluminum liquid in the casting ladle is poured for the most part and the aluminum liquid in the cavity is covered on the insert ring, the casting mould is slowly put flat (a pedal reset switch or an inductive probe is automatically reset and controlled), and the casting action cannot be stopped until the riser is full, at the moment, an ultrasonic device is started, and ultrasonic vibration power is increased: 80%, frequency 10KHz, ultrasound time: 10s; meanwhile, the water flow time and the water flow process parameters of the die are shown in table 5, and the water pressure is 0.4MPa; the rapid cooling speed is controlled to be more than or equal to 125 ℃/s when the blank is poured, the ultrasonic action is controlled to be applied to the solidification of the main Fe phase and the strengthening phase, the growth of the iron phase is obviously inhibited, and the casting mechanical property is improved.
Table 5 casting mold water control
| Internal mold | Shaft pin | External mold | Mould cover | |
| Lag time of water passage(s) | 0 | 10 | 0 | 20 |
| Water-through time(s) | 60 | 50 | 55 | 35 |
| Water flow (L/min) | 8.5 | 5.5 | 9.0 | 4.5 |
(10) Quenching with residual heat
After the casting is solidified, the casting mould is opened, an operator should take down the piston within 30 seconds, then transfer the piston to an air cooling frame or a water channel within 10 seconds, air cooling or water quenching is carried out according to the requirement,
(11) Heat treatment process
Table 6 heat treatment process
(12) Performance analysis:
1) The cooling rate and the ultrasonic vibration are related to the size of the iron phase, and the result is shown in fig. 4;
2) Tensile strength analysis, as shown in table 7;
table 7 tensile strength comparison
3) Thermal conductivity testing
Taking a sample for thermal expansion coefficient measurement, as shown in table 8;
TABLE 8 measurement of thermal conductivity coefficient (W/(m.K))
Example 2
(1) Proportioning materials
Proportioning industrial high-purity aluminum, crystalline silicon nickel plates, magnesium blocks, cathode copper, industrial pure iron, aluminum-vanadium intermediate alloy, aluminum-cobalt intermediate alloy, aluminum-hafnium intermediate alloy, aluminum-yttrium intermediate alloy and the like according to the following proportion;
the chemical components are as follows: 9wt% of Si; cu4.5wt%; ni 3.0wt%; 0.6wt% of Mg; fe 1.08wt%; co 0.18wt%; v0.54 wt%; 0.07wt% of Hf; y0.08 wt%; k0.008wt%; na0.007wt% and the balance of Al;
(2) Melting of charge
Slowly heating up after charging the melting furnace which is stopped for a long time, and heating up to melt after preserving heat for 40 minutes at 500 ℃; for a continuously used melting furnace, firstly cleaning oxidizing slag on the furnace wall, completely removing slag at the furnace bottom, pouring the slag into a slag leakage barrel, and then starting charging and melting;
the charging sequence of the material premelted alloy of the invention is as follows: all crystalline silicon, partial pure aluminum ingot, nickel plate, cathode copper, industrial pure iron and the like, so that the added materials are compacted as much as possible without leaving obvious gaps;
(4) Mg and potassium/sodium modified alloy
The method comprises the steps of (1) removing an oxide film on the surface of an aluminum liquid from the bottom of a preheated sample die in the range of 760 ℃ for pre-alloyed gold, taking a component sample for spectrum analysis, adding a proper amount of potassium/sodium modifier and Mg ingots after calculation and weighing, adding corresponding alloys into other components if necessary for adjustment, and then increasing the power of an intermediate frequency furnace for heating;
(5) Aluminum-hafnium intermediate alloy, aluminum-yttrium intermediate alloy and heat insulation
After the temperature is increased to 800 ℃, adding the intermediate alloy, lightly turning the liquid surface by using a preheated slag scooping ladle to ensure that the liquid surface is free of solid furnace charge, stirring for 8 times by using a preheated stirring rod, pulling out surface scum, regulating the power of an intermediate frequency furnace, keeping the temperature of the aluminum liquid at 840 ℃ for not less than 20 minutes, and pouring the aluminum liquid in time (discharging) in order to reduce the oxidation of the aluminum liquid and reduce the energy consumption;
(6) Tapping temperature requirement
The tapping temperature of the molten aluminum is controlled within a certain range, and the temperature of the pre-fusion Jin Chulu is 850 ℃;
(7) Rotary degassing
The rotary degassing temperature is 750-770 ℃, the rotor speed is 400 rpm, the refining time is 12min, and the compressed air flow is 0.6m 3 /h；
(8) Slag beating
Adding 0.02wt% of slag-beating agent on the surface of each furnace of molten aluminum, stirring slag on the liquid surface for at least 2 minutes by using a slag-fishing ladle, fishing out slag on the surface of the molten aluminum, pouring the fished slag into a slag-frying platform or a slag-frying barrel, and scraping the slag as much as possible;
(9) Casting process
The preheating temperature of the die before casting is shown in table 9, and the blank solidification time is controlled mainly by controlling the temperature of the die;
TABLE 9 casting mold temperature control
In the pouring process, a ladle is used for ladle-taking enough aluminum water required by pouring, the temperature of the aluminum water is 750 ℃, one face with a nozzle is aligned with a pouring gate for pouring after ladle-taking the aluminum water, and the pouring is continuous and stable according to the principle of firstly, then, slowly and then, quickly; when the aluminum liquid in the casting ladle is poured for the most part and the aluminum liquid in the cavity is covered on the insert ring, the casting mould is slowly put flat (a pedal reset switch or an inductive probe is automatically reset and controlled), and the casting action cannot be stopped until the riser is full, at the moment, an ultrasonic device is started, and ultrasonic vibration power is increased: 85%, frequency 15KHz, ultrasonic time: 15s; meanwhile, the water flow time and the water flow process parameters of the die are shown in table 10, and the water pressure is 0.5MPa; the rapid cooling speed is controlled to be more than or equal to 135 ℃/s when the blank is poured, the ultrasonic action is controlled to be applied to the solidification of the main Fe phase and the strengthening phase, the growth of the iron phase is obviously inhibited, and the casting mechanical property is improved.
Table 10 casting mold water control
| Internal mold | Shaft pin | External mold | Mould cover | |
| Lag time of water passage(s) | 5 | 10 | 0 | 20 |
| Water-through time(s) | 55 | 50 | 55 | 35 |
| Water flow (L/min) | 9 | 6 | 9.5 | 5 |
(10) Quenching with residual heat
After the casting is solidified, the casting mould is opened, an operator should take down the piston within 30 seconds, then transfer the piston to an air cooling frame or a water channel within 10 seconds, air cooling or water quenching is carried out according to the requirement,
(11) Heat treatment process
Table 11 heat treatment process
(12) Performance analysis:
1) The cooling rate and the ultrasonic vibration are related to the size of the iron phase, and the result is shown in fig. 5;
2) Tensile strength analysis, as shown in table 12;
table 12 tensile strength comparison
In the above table, the conventional means that no rapid pit cooling and no ultrasonic vibration are performed, the rapid cooling is performed only, no ultrasonic vibration is performed, and the ultrasonic vibration is performed only, no rapid cooling is performed.
FIG. 7 is a photograph of a microstructure of a casting prepared by a conventional method; FIG. 8 is a photograph of a microstructure of a casting prepared in example 1 of the present invention; FIG. 9 is a photograph of a microstructure of a casting prepared in example 2 of the present invention; FIG. 10 is a photograph of a microstructure of a casting prepared in example 3 of the present invention; FIG. 11 is a macroscopic photograph of the castings prepared according to examples 1 to 3; FIG. 12 is a photograph showing metallographic structures of castings prepared in examples 1 to 3.
3) Thermal conductivity testing
Taking a sample for thermal expansion coefficient measurement, as shown in table 13;
TABLE 13 measurement of thermal conductivity coefficient (W/(m.K))
Example 3
(1) Proportioning materials
Proportioning industrial high-purity aluminum, crystalline silicon nickel plates, magnesium blocks, cathode copper, industrial pure iron, aluminum-vanadium intermediate alloy, aluminum-cobalt intermediate alloy, aluminum-hafnium intermediate alloy, aluminum-yttrium intermediate alloy and the like according to the following proportion;
the chemical components are as follows: 7wt% of Si; cu5wt%; ni 3.5wt%; 0.8wt% of Mg; fe 1.44wt%; co 0.24wt%; v0.72 wt%; 0.1wt% of Hf; y0.09 wt%; k0.01wt%; 0.009wt% of Na0, and the balance of Al;
(2) Melting of charge
Slowly heating up after charging the melting furnace which is stopped for a long time, and heating up to melt after preserving heat for 50 minutes at 500 ℃; for a continuously used melting furnace, firstly cleaning oxidizing slag on the furnace wall, completely removing slag at the furnace bottom, pouring the slag into a slag leakage barrel, and then starting charging and melting;
the charging sequence of the material premelted alloy of the invention is as follows: all crystalline silicon, partial pure aluminum ingot, nickel plate, cathode copper, industrial pure iron and the like, so that the added materials are compacted as much as possible without leaving obvious gaps;
(4) Mg and potassium/sodium modified alloy
The premelted alloy is firstly subjected to aluminum liquid surface oxidation film stripping at the die bottom of a preheated sample in the temperature range of 750-780 ℃, component samples are taken for spectral analysis, a proper amount of potassium/sodium modifier and Mg ingot are added after calculation and weighing, other components can be added with corresponding alloy for adjustment if necessary, and then the power of an intermediate frequency furnace is adjusted to be increased;
(5) Aluminum-hafnium intermediate alloy, aluminum-yttrium intermediate alloy and heat insulation
After the temperature is increased to 800 ℃, adding the intermediate alloy, lightly turning the liquid surface by using a preheated slag scooping ladle to ensure that the liquid surface is free of solid furnace charge, stirring for 8 times by using a preheated stirring rod, pulling out surface scum, regulating the power of an intermediate frequency furnace, keeping the temperature of the aluminum liquid at 860 ℃ for not less than 20 minutes, and timely pouring the aluminum liquid (discharging) to reduce the oxidation of the aluminum liquid;
(6) Tapping temperature requirement
The tapping temperature of the molten aluminum is controlled within a certain range, and the temperature of the pre-fusion Jin Chulu is 850 ℃;
(7) Rotary degassing
The rotary degassing temperature is 760 ℃, the rotor speed is 400 rpm, the refining time is 12min, and the compressed air flow is 0.6m 3 /h；
(8) Slag beating
Adding 0.02wt% of slag-beating agent on the surface of each furnace of molten aluminum, stirring slag on the liquid surface for at least 2 minutes by using a slag-fishing ladle, fishing out slag on the surface of the molten aluminum, pouring the fished slag into a slag-frying platform or a slag-frying barrel, and scraping the slag as much as possible;
(9) Casting process
The preheating temperature of the die before casting is shown in table 14, and the blank solidification time is controlled mainly by controlling the temperature of the die;
table 14 casting mold temperature control
In the pouring process, a ladle is used for ladle-taking enough aluminum water required by pouring, the temperature of the aluminum water is 750 ℃, one face with a nozzle is aligned with a pouring gate for pouring after ladle-taking the aluminum water, and the pouring is continuous and stable according to the principle of firstly, then, slowly and then, quickly; when the aluminum liquid in the casting ladle is poured for the most part and the aluminum liquid in the cavity is covered on the insert ring, the casting mould is slowly put flat (a pedal reset switch or an inductive probe is automatically reset and controlled), and the casting action cannot be stopped until the riser is full, at the moment, an ultrasonic device is started, and ultrasonic vibration power is increased: 90%, frequency 20KHz, ultrasound time: 20s; meanwhile, the water flow time and the water flow process parameters of the die are shown in table 15, and the water pressure is 0.6MPa; the rapid cooling speed is controlled to be more than or equal to 115 ℃/s when the blank is poured, the ultrasonic action is controlled to be applied to the solidification of the main Fe phase and the strengthening phase, the growth of the iron phase is obviously inhibited, and the casting mechanical property is improved.
Table 15 casting mold water control
| Internal mold | Shaft pin | External mold | Mould cover | |
| Lag time of water passage(s) | 10 | 15 | 5 | 25 |
| Water-through time(s) | 50 | 45 | 50 | 30 |
| Water flow (L/min) | 9.5 | 6.5 | 10 | 5.5 |
(10) Quenching with residual heat
After the casting is solidified, the casting mould is opened, an operator should take down the piston within 30 seconds, then transfer the piston to an air cooling frame or a water channel within 10 seconds, air cooling or water quenching is carried out according to the requirement,
(11) Heat treatment process
Table 16 heat treatment process
(12) Performance analysis:
1) The cooling rate and the ultrasonic vibration are related to the size of the iron phase, and the result is shown in fig. 6;
2) Tensile strength analysis, as shown in table 17;
table 17 tensile strength comparison
3) Thermal conductivity testing
Taking a sample for thermal expansion coefficient measurement, as shown in table 18;
TABLE 18 measurement of thermal conductivity coefficient (W/(m.K))
The following examples or prior conventional alloys were prepared in the same manner as in example 1, the specific compositions are shown in Table 19, and the performance data are shown in tables 20 and 21;
table 19 examples and Table of alloy compositions in the prior art (wt%)
| Si | Cu | Ni | Mg | Fe | Co | V | Hf | Y | K | Na | |
| Example 4 | 8 | 4.25 | 3.3 | 0.7 | 1.2 | 0.2 | 0.6 | 0.05 | 0.09 | 0.009 | 0.008 |
| Example 5 | 10 | 4.75 | 2 | 0.5 | 0.78 | 0.13 | 0.39 | 0.08 | 0.07 | 0.007 | 0.01 |
| ZL109 | 12 | 1 | 1.2 | 0.5 | 0.5 | / | / | / | / | / | / |
| Al-Si-Cu-Mg-Ni | 12 | 4 | 2 | 0.8 | 0.5 | / | / | / | / | / | / |
Table 20 comparative data table of tensile Properties (MPa) of alloys of examples and prior art
| Normal temperature | 150℃ | 250℃ | 380℃ | |
| Example 4 | 325 | 276 | 230 | 110 |
| Example 5 | 328 | 276 | 229 | 109 |
| ZL109 | 245 | 188 | 155 | 76 |
| Al-Si-Cu-Mg-Ni | 258 | 193 | 174 | 83 |
Table 21 comparative data table for alloy thermal conductivity coefficient measurement (W/(m.k)) in examples and prior art
| Group of | 20℃ | 350℃ |
| Example 4 | 136 | 143 |
| Example 5 | 128 | 141 |
| ZL109 | 115 | 128 |
The above description of the embodiments is only for aiding in the understanding of the method of the present invention and its core ideas. It should be noted that it will be apparent to those skilled in the art that various modifications and adaptations of the invention can be made without departing from the principles of the invention and these modifications and adaptations are intended to be within the scope of the invention as defined in the following claims.
The previous description of the disclosed embodiments is provided to enable any person skilled in the art to make or use the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.
Claims (10)
1. An aluminum-silicon alloy comprising:
7.5 to 11.5 weight percent of Si; 4-5 wt% of Cu; ni 2.0-3.5 wt%; 0.4 to 0.8 weight percent of Mg; 0.6 to 1.44 weight percent of Fe; 0.10 to 0.24 weight percent of Co; v0.3-0.72 wt%; 0.05 to 0.1 weight percent of Hf; y0.05-0.1 wt%; k is 0.005-0.01 wt%; 0.005 to 0.010 weight percent of Na0.005 and the balance of Al; and the mass percentage content of Fe, V, and Co satisfies 6Cowt% =2vwt% =1fewt%;
the preparation method of the aluminum-silicon alloy casting comprises the following steps:
a) Proportioning high-purity aluminum, silicon nickel raw materials, magnesium raw materials, copper raw materials, iron raw materials, aluminum vanadium intermediate alloy, aluminum cobalt intermediate alloy, aluminum hafnium intermediate alloy and aluminum yttrium intermediate alloy;
b) Melting a silicon-nickel raw material, a high-purity aluminum, a copper raw material, an aluminum-cobalt intermediate alloy and an iron raw material to obtain a pre-alloyed alloy;
c) Adding a potassium/sodium modifier and a magnesium raw material into the pre-alloyed alloy, heating, adding an aluminum-hafnium intermediate alloy and an aluminum-yttrium intermediate alloy, and preserving heat;
d) Sequentially discharging the melt obtained in the step C), rotating for degassing, refining, and pouring after deslagging; simultaneously starting an ultrasonic device when the casting is started, wherein the rapid cooling speed of the casting is more than or equal to 115 ℃/s;
e) Quenching the casting obtained in the step D), and finally sequentially carrying out solution treatment and aging treatment.
2. The aluminum-silicon alloy according to claim 1, wherein the content of Fe is 0.75 to 1.25wt%, the content of Co is 0.13 to 0.20wt%, the content of V is 0.35 to 0.65wt%, the content of Hf is 0.06 to 0.08wt%, the content of Y is 0.06 to 0.09wt%, the content of K is 0.006 to 0.009wt%, and the content of Na is 0.006 to 0.009wt%.
3. A method of making a casting of the aluminum-silicon alloy of claim 1, comprising the steps of:
a) Proportioning high-purity aluminum, silicon nickel raw materials, magnesium raw materials, copper raw materials, iron raw materials, aluminum vanadium intermediate alloy, aluminum cobalt intermediate alloy, aluminum hafnium intermediate alloy and aluminum yttrium intermediate alloy;
b) Melting a silicon-nickel raw material, a high-purity aluminum, a copper raw material, an aluminum-cobalt intermediate alloy and an iron raw material to obtain a pre-alloyed alloy;
c) Adding a potassium/sodium modifier and a magnesium raw material into the pre-alloyed alloy, heating, adding an aluminum-hafnium intermediate alloy and an aluminum-yttrium intermediate alloy, and preserving heat;
d) Sequentially discharging the melt obtained in the step C), rotating for degassing, refining, and pouring after deslagging; simultaneously starting an ultrasonic device when the casting is started, wherein the rapid cooling speed of the casting is more than or equal to 115 ℃/s;
e) Quenching the casting obtained in the step D), and finally sequentially carrying out solution treatment and aging treatment.
4. The method according to claim 3, wherein in the step C), the temperature of the premelted alloy is 750 to 800 ℃, and the modifier is a K and Na composite modifier.
5. The method according to claim 3, wherein in the step C), the temperature of the heat preservation is 820-880 ℃ for not less than 20min.
6. The process according to claim 3, wherein in step D), the tapping temperature is 830 to 860 ℃, the spin degassing temperature is 750 to 770 ℃, the spin degassing rotor speed is 300 to 400 rpm, the refining time is 10 to 20min, and the refining air flow is 0.5 to 1.0m 3 /h。
7. The method according to claim 3, wherein in the step D), the mold is preheated before casting, the temperature of the inner mold of the mold is 310-340 ℃, the temperature of the shaft pin is 250-280 ℃, the temperature of the outer mold is 150-180 ℃, and the temperature of the mold cover is 100-130 ℃; the mold is filled with water during casting, the water pressure of the filled water is 0.4-1.0 MPa, and the water flow rate is 4.5-10.5L/min.
8. The method according to claim 3, wherein in the step D), the vibration power of the ultrasonic device is 80-90%, the frequency is 10-20 KHz, and the time is 10-20 s.
9. A method according to claim 3, wherein in step E), the quenching is air-cooled or water-quenched.
10. The method according to claim 3, wherein the solution treatment is performed at a temperature of 400 to 500 ℃ for 5 to 10 hours, the cooling medium is hot water at 60 to 80 ℃, the aging is performed at a temperature of 200 to 300 ℃ for 5 to 6 hours, and the cooling medium is air.
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