CN111304500B - Cast aluminum alloy for high-power-density piston and preparation method thereof - Google Patents

Cast aluminum alloy for high-power-density piston and preparation method thereof Download PDF

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CN111304500B
CN111304500B CN202010281620.2A CN202010281620A CN111304500B CN 111304500 B CN111304500 B CN 111304500B CN 202010281620 A CN202010281620 A CN 202010281620A CN 111304500 B CN111304500 B CN 111304500B
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aluminum alloy
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cast aluminum
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CN111304500A (en
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汤进军
梁翠
陈大辉
高德
张学昌
王炳涛
张炜
许晨光
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Ningbo Institute of Technology of ZJU
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C22C21/04—Modified aluminium-silicon alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising

Abstract

The invention relates to a cast aluminum alloy for a high-power-density piston and a preparation method thereof, wherein the cast aluminum alloy is characterized in that: the cast aluminum alloy comprises the following components in percentage by mass: 11.0-12.6% of Si, Cu: 3.5-4.5%, Mg: 0.7-1.2%, Ni: 2.2-3.2%, Fe: 0.6-0.8%, Mn: 0.25-0.35%, Sc:0.10 to 0.15%, Zr: 0.13-0.17%, Ti: 0.13-0.17%, V: 0.08 to 0.12 percent, and the balance of Al and inevitable impurities. On the basis of thermodynamic analysis, tissue regulation and experimental test of a material system, the heat-resistant aluminum alloy improves the 350-420 ℃ high-temperature support strengthening phase Al by properly increasing and adjusting the relative addition of elements such as Fe, Ni, Cu and the like9FeNi、Al15Si2(Fe,Mn)3、Al3CuNi、Al7Cu4The Ni content makes the solidification structure present the dispersed net shape, petal shape and diffusion stripe shape distribution, these high temperature strengthening phases can play the role of hindering the grain boundary sliding and dislocation movement in the alloy, and improve the heat resistance, the grain boundary strength and the creep resistance.

Description

Cast aluminum alloy for high-power-density piston and preparation method thereof
Technical Field
The invention belongs to the technical field of cast aluminum alloy, and particularly relates to a cast aluminum alloy for a high-power-density diesel engine piston and a preparation method thereof.
Background
At present, a diesel engine as a current power machine with high thermal efficiency and wide application is irreplaceable in the leading position for a long time.
The high-power density diesel engine piston is used as a high-frequency moving part, the highest temperature of the throat part of the high-power density diesel engine piston reaches 420 ℃, the calibration rotating speed is increased to 4200r/min from 2100r/min, the highest combustion pressure is increased to 22MPa from 14MPa, and the high-temperature mechanical property and the reliability of an alloy material under the working condition environment directly influence the technical index and the service life of the whole engine. Therefore, the development of the heat-resistant cast aluminum alloy which is used at the higher temperature of 350-420 ℃ and the preparation method thereof is a material technical problem which needs to be solved by high-power density diesel engines in China.
For example, the patent application of the invention in China, namely 'a high heat-resistant Al-Cu-Mg-Ag alloy', the patent application number of which is CN200810030979.1 (application publication number is CN 101245430A), discloses a high heat-resistant Al-Cu-Mg-Ag alloy, the quantity of omega phases at high temperature in the alloy is increased by properly increasing the atomic ratio of Ag to Mg, the patent has the advantages of single strengthening means, insufficient high-temperature strengthening effect, unobvious mechanical property advantage of the alloy at room temperature, sharp reduction of the alloy strength after the temperature exceeds 250 ℃, and poor comprehensive mechanical property.
For example, the Chinese patent application "a high-strength heat-resistant cast aluminum alloy material and a preparation process thereof" has a patent application number of CN201810160568.8 (application publication number of CN 108251724A) and discloses a high-strength heat-resistant cast aluminum alloy material, wherein a high Cu/Mg ratio is adopted, and after aging heat treatment, a main strengthening phase in the alloy is theta-Al2Cu phase, alone having a higher strengthening effect than delta-Al3CuNi and T-Al9FeNi phase, and is liable to grow and growCoarsening and being unfavorable to the high-temperature mechanical property of the alloy. As another example, the Chinese patent application "a high Fe content Al-Si-Cu-Mn-Ti heat resistant aluminum alloy" with patent number CN201811512875.4 (application publication number CN 109402473A) discloses that the heat resistance of the alloy is improved by increasing the contents of Fe, Cu and Ti, the copper content of the patent is up to 6.0-8.0% by mass, the composition segregation and heat crack defects are easily generated in the casting process, and the needle Al is caused by too high Ti content3The Ti content is increased, resulting in insufficient high temperature mechanical and fatigue properties of the alloy. The invention patent of China with the publication number of CN 104498785B introduces Er and Zr elements, has low solid solubility of the elements, limited addition amount, limited strengthening effect on the alloy and insufficient comprehensive performance of the alloy.
For example, in the Chinese invention patent of "an Al-Cu-Mg-Fe-Ni series wrought heat-resistant aluminum alloy and a preparation method thereof", the patent application number is cn201611117386.x (the publication number is CN106834837B), the aluminum alloy comprises the following components in percentage by mass: 4.7-5.8% of Cu, 1.5-2.4% of Mg, 1.5-2.0% of Fe, 1.4-1.9% of Ni, 0.04-0.20% of Zr, 0.03-0.10% of Ti, 0.04-0.10% of Sc, 0.08-0.15% of V, 1-3 of Ag 0.3-0.9%, less than or equal to 0.05% of other impurities singly, less than or equal to 0.15% of total amount, and the balance of Al. The intermetallic compound rich in Fe and Ni is uniformly distributed in the alloy in a nanoparticle mode, so that the heat resistance is improved, the alloy has better tensile property and strength at room temperature and higher strength at 200 ℃, but the alloy strength is sharply reduced after the temperature exceeds 250 ℃, and the comprehensive mechanical property is poorer.
Therefore, further improvements to existing aluminum alloys are needed.
Disclosure of Invention
The first technical problem to be solved by the present invention is to provide a cast aluminum alloy for high power density pistons with high strength and high heat resistance in view of the current state of the prior art.
The second technical problem to be solved by the invention is to improve a preparation method of the cast aluminum alloy with high strength and high heat resistance.
The technical scheme adopted by the invention for solving the first technical problem is as follows: a cast aluminum alloy for a piston, characterized by: the aluminum alloy comprises the following components in percentage by mass: 11.0-12.6% of Si, Cu: 3.5-4.5%, Mg: 0.7-1.2%, Ni: 2.2-3.2%, Fe: 0.6-0.8%, Mn: 0.25-0.35%, Sc:0.10 to 0.15%, Zr: 0.13-0.17%, Ti: 0.13-0.17%, V: 0.08 to 0.12 percent, and the balance of Al and inevitable impurities.
The mass ratio of Fe/Mn in the aluminum alloy is 1.71: 1-3.2: 1. thus, the negative factors which may be generated on the alloy performance by the Fe-rich needle phase can be thoroughly eliminated. The Mn element is added mainly for improving Al5FeSi primary iron-rich needle phase, and converting into micron-sized dispersed Al15Si2(Fe,Mn)3(ii) a If the Mn addition is too small (less than 0.25%), it is not enough to convert the iron-rich needle phase; if the Mn addition amount is too large (higher than 0.35), Al15Si2(Fe,Mn)3The grain phase will be inoculated and grown up, which is unfavorable for the high-temperature mechanical property and fatigue property of the alloy.
Preferably, the mass percentage content of the high-temperature support strengthening phase in the aluminum alloy is 6.2-9.6%, the aluminum alloy has a good solidification structure appearance, and the mechanical property and the fatigue property of the alloy in a high-temperature environment can be improved.
Specifically, the precipitated phase in the aluminum alloy is formed by Al5Dispersed Al converted from needle-like primary phase of FeSi15Si2(Fe,Mn)3A high-temperature support strengthening phase in the aluminum alloy is Al9FeNi、Al15Si2(Fe,Mn)3、Al3CuNi and Al7Cu4And (3) Ni. Thus, the support strengthening is carried out at the high temperature of 350-420 ℃, so that the solidification structure is in the dispersed reticular, petal-shaped and diffusion stripe-shaped distribution, and the high-temperature strengthening phases can play a role in hindering the sliding of grain boundaries and the movement of dislocation in the alloy, thereby improving the heat resistance, the grain boundary strength and the creep resistance; precipitation of Al15Si2(Fe,Mn)3The dispersion strengthening phase has better high-temperature performance.
The technical scheme adopted by the invention for solving the second technical problem is as follows: the preparation method of the cast aluminum alloy is characterized by sequentially comprising the following steps of:
s1: preparing ingredients: preparing pure aluminum ingots, pure magnesium ingots, Al-Si intermediate alloys, Al-Cu intermediate alloys, Al-Ni intermediate alloys, Al-Fe intermediate alloys, Al-Mn intermediate alloys and Al-Sc intermediate alloys according to the mass percent of the components of the aluminum alloys, and preheating and insulating the prepared materials;
s2: taking out a certain amount of pure magnesium and Al-Cu intermediate alloy from the mixture, and mixing the rest alloy at T0Smelting, and after the molten materials are completely melted, raising the temperature of the molten materials to T1Preserving heat, and stirring to fully melt the alloy;
s3: cooling the alloy melt to T2Wherein, T0＜T2＜T1Adding a modifier for modification treatment, fully standing after modification, and removing scum on the surface of the melt;
s4: adding the pure magnesium and the Al-Cu intermediate alloy reserved in the step S1 in the step S3, cooling and stirring to ensure that the temperature of the cooled melt is higher than T2And standing;
s5: after the alloy in the step S4 is completely melted, adding an Al-Ti refiner, an Al-Zr refiner and an Al-V refiner into the melt for refining treatment, and simultaneously stirring and standing to remove scum on the surface of the melt;
s6: at a temperature T3Degassing and refining the melt by adopting a rotary blowing mode, wherein T3＞T0Standing and removing scum on the surface of the melt after degassing;
s7: keeping the temperature of the melt, preheating a casting die, and carrying out extrusion casting on the melt to form an aluminum alloy casting blank;
s8: carrying out T6 heat treatment on the aluminum alloy casting blank: and carrying out aging treatment after the solution treatment.
There are many forms of Al-Si master alloy, Al-Cu master alloy, Al-Ni master alloy, Al-Fe master alloy, Al-Mn master alloy and Al-Sc master alloy, but preferably the Al-Si master alloy is AlSi30, the Al-Cu master alloy is AlCu50, the Al-Ni master alloy is AlNi20, the Al-Fe master alloy is aife 20, the Al-Mn master alloy is AlMn10 and the Al-Sc master alloy is AlSc2 master alloy.
There are various forms of the refiner, but preferably, in step S4, the Al — Ti refiner is the master alloy AlTi 10; the Al-Zr refiner is intermediate alloy AlZr 10; the Al-V refiner is master alloy AlV 10.
Preferably, the preheating temperature in the step S1 is 150-170 ℃, and the heat preservation time is 30-60 min; in step S2, the temperature T0At a temperature of 720 ℃ to 740 ℃ and a temperature T1The temperature is 790-810 ℃, and the heat preservation time is 20-30 min; in step S3, T2The temperature is 760-770 ℃, and the standing time is 20-30 min; in step S6, T3750 and 760 ℃, and the standing time is 10-15 min; in step S7, the temperature of the melt is maintained at 750-780 ℃, the mold is preheated to 280-350 ℃, the pressure is 350 tons, and the pressure is maintained for 120 seconds.
Further preferably, the preheating temperature in step S1 is 160 ℃, and in step S2, the temperature T is0At a temperature of 730 ℃ and a temperature T1The temperature was 800 ℃.
Preferably, in step S8, the solid solution temperature of the solid solution treatment is 500 +/-5 ℃, the temperature is kept for 6-8 hours, and the quenching is carried out in hot water at the temperature of 50-70 ℃; the temperature of the aging treatment is 225 +/-10 ℃, the temperature is kept for 8-10 hours, and the air cooling is carried out to the room temperature.
In order to effectively degas and refine the melt, the flow of argon in the rotary blowing is 0.35-0.50m3The speed of the rotor is 150-.
Compared with the prior art, the invention has the advantages that: 1. on the basis of thermodynamic analysis, tissue regulation and experimental test of a material system, the heat-resistant aluminum alloy improves the 350-420 ℃ high-temperature support strengthening phase Al by properly increasing and adjusting the relative addition of elements such as Fe, Ni, Cu and the like9FeNi、Al15Si2(Fe,Mn)3、Al3CuNi、Al7Cu4Ni content in the mixture to make the coagulated tissue show dispersed network, petal-like shape andthe high-temperature strengthening phases can play a role in hindering grain boundary sliding and dislocation movement in the alloy, and improve the heat resistance, the grain boundary strength and the creep resistance; 2. introducing Mn element to make the micro needle-like primary phase Al in the alloy solidification structure5FeSi, which is converted into Al with better high-temperature performance and dispersed and separated out15Si2(Fe,Mn)3Strengthening the phase, and keeping the ratio of Fe to Mn between 1.71:1 and 3.2:1, so that the negative factors possibly generated on the alloy performance by the Fe-rich needle phase can be thoroughly eliminated; 3. al with high micro-calorimetric stability can be formed by adopting a composite micro-alloying means and adding Sc element3(Sc, Zr) and Al3Sc and other strengthening phases can generate precipitation strengthening effect to pin dislocation at high temperature, so that the high temperature resistance of the alloy is further improved; the addition of elements such as Ti, Zr, V and the like can perform composite grain refinement, and improve the stability of structure and performance; 4. the aluminum alloy has good comprehensive mechanical properties, the room-temperature tensile strength is 325-379 MPa, and the elongation is 1.0-1.8%; the tensile strength of the alloy is 92-105 MPa after 30 minutes of heat preservation at 350 ℃, the elongation is 11.5-15.6%, the casting line shrinkage is 1.2-1.6%, and the fatigue strength at 350 ℃ (10℃)7Secondly) reaches 52MPa, the high-temperature use performance of the aluminum alloy is greatly improved, and the application range of the Al-Si-Cu series cast aluminum alloy is expanded; 5. the preparation method of the aluminum alloy has the advantages of simple preparation process, simple added element components, no rare and precious metals, excellent casting performance and reduction of the production cost of the product.
Drawings
FIG. 1 shows Al in the aluminum alloy of example four9SEM image of microstructure appearance of FeNi iron-rich high-temperature strengthening phase;
FIG. 2 shows Al at another position in the aluminum alloy of example four9SEM (same magnification as that of figure 1) of microstructure morphology of the FeNi iron-rich high-temperature strengthening phase;
FIG. 3 shows Al in the aluminum alloy of example four3CuNi and Al7Cu4SEM images of microstructure appearances of Ni-rich high-temperature strengthening phases;
FIG. 4 shows Al at another position in the aluminum alloy of example four3CuNi and Al7Cu4Ni-rich high-temperature strengthening phaseMicrostructure topography SEM images (same magnification as fig. 3).
Detailed Description
The invention is described in further detail below with reference to the accompanying examples.
In the following examples, the cast aluminum alloy for a high power density piston comprises the following components in mass percent: 11.0-12.6% of Si, Cu: 3.5-4.5%, Mg: 0.7-1.2%, Ni: 2.2-3.2%, Fe: 0.6-0.8%, Mn: 0.25-0.35%, Sc:0.10 to 0.15%, Zr: 0.13-0.17%, Ti: 0.13-0.17%, V: 0.08 to 0.12 percent, and the balance of Al and inevitable impurities. Wherein the mass ratio of Fe/Mn in the aluminum alloy is 1.71-3.2, and the mass percentage content of the high-temperature support strengthening phase in the aluminum alloy is 6.2-9.6%; al in aluminium alloy5Conversion of FeSi acicular primary phase into dispersed Al15Si2(Fe,Mn)3Separating out the phases; the high-temperature support strengthening phases in the aluminum alloys in the following examples are all Al9FeNi、Al15Si2(Fe,Mn)3、Al3CuNi and Al7Cu4Ni。
In the following examples, commercially pure aluminum, a commercially pure Mg ingot, an Al-Si master alloy, an Al-Cu master alloy, an Al-Ni master alloy, an Al-Fe master alloy, an Al-Mn master alloy, and an Al-Sc master alloy were used as ingredients of the alloy raw materials, wherein the Al-Si master alloy was AlSi30, the Al-Cu master alloy was AlCu50, the Al-Ni master alloy was AlNi20, the Al-Fe master alloy was AlFe20, the Al-Mn master alloy was AlMn10, and the Al-Sc master alloy was AlSc 2.
The modifier in the following embodiment adopts ZS-ABP10 composite phosphate modifier, and the refiner adopts Al-Ti refiner, Al-Zr refiner and Al-V refiner, specifically, the Al-Ti refiner is intermediate alloy AlTi 10; the Al-Zr refiner is intermediate alloy AlZr 10; the Al-V refiner is master alloy AlV 10.
The first embodiment is as follows:
the aluminum alloy of the present example had a total mass of 50kg, and the cast aluminum alloy for high power density pistons comprised, in mass percent, 11.5% Si, Cu: 3.5%, Mg: 0.9%, Ni: 2.5%, Fe: 0.6%, Mn: 0.25%, Sc: 0.13%, Zr: 0.15%, Ti: 0.15%, V: 0.1%, and the balance of Al and inevitable impurities. The mass ratio of Fe/Mn in the prepared aluminum alloy is 2.4:1, and the mass percentage content of the high-temperature support strengthening phase is 6.2%.
The preparation method of the cast aluminum alloy sequentially comprises the following steps:
s1: preparing ingredients: preparing pure aluminum ingots, pure magnesium ingots, AlSi30, AlCu50, AlNi20, AlFe20, AlMn10 and AlSc2 according to the mass percent of the components of the aluminum alloy, preheating the mixture at 160 ℃, and preserving heat for 30-60 min; calculating the amount of the required raw materials according to the alloy components and the stoichiometric ratio, and controlling the total amount of the prepared alloy melt to be 1/2-2/3 of the capacity of the crucible;
s2: taking out a certain amount of pure magnesium and AlCu50 alloy from the mixture, adding the rest alloy mixture into a crucible of a resistance furnace, and heating for T0Smelting at 730 deg.C, and raising the temperature of the molten material to T1Keeping the temperature at about 800 ℃ for 20-30 min, and stirring for 2-3 times by using a bell jar to fully melt the alloy;
s3: after the alloy melt is melted uniformly, the temperature of the alloy melt is reduced to T2，T2Pressing the ZS-ABP10 composite phosphorus salt modifier into the bottom of the crucible by using a bell jar at 760 ℃, crushing, stirring up and down, modifying and ensuring full modification, standing for 25min after modification is completed, and removing scum on the surface of the melt; the standing time in the step can be within 20-30 min, wherein T is2Can be carried out at 760 ℃ -770 ℃; the addition amount of the modifier is calculated according to 0.008-0.010Kg/KG, namely 0.008-0.010Kg of modifier is added into each kilogram of cast aluminum alloy.
S4: adding pure magnesium and AlCu50 alloy reserved in the step S1 in the step S3, cooling the melt, stirring the melt up and down for 2-3 times, and in the process, adjusting the total amount of the reserved intermediate alloy by controlling to ensure that the temperature of the cooled melt is not lower than 760 ℃, and standing for 20 min; in order to avoid burning and splashing, the Mg ingot is wrapped by aluminum foil and added into the melt, and the standing time in the step can be 15-20 min;
s5: after the alloy in the step S4 is completely melted, adding AlTi10, AlZr10 and AlV10 into the melt for refining treatment, stirring for 2-3 times, standing for 20-30 min, and removing scum on the surface of the melt;
s6: refining: at a temperature T3The melt is degassed and refined by rotary blowing at 750 deg.C, and the flow of argon is 0.35-0.50m3The speed of the rotor is 150-; in this step, at T3Refining at 750-760 deg.C;
s7: keeping the temperature of the melt at 760 ℃, preheating a casting die, keeping the preheating temperature at 300 ℃, performing extrusion casting by using a hydraulic press under the pressure of 350 tons, maintaining the pressure for 120s, and performing extrusion casting on the melt to form an aluminum alloy casting blank, wherein the casting blank is in a round cake shape, and the size of the round cake casting blank is phi 160mmX60 mm; in the step, the temperature of the melt is kept between 750 and 780 ℃, the preheating temperature of the die is kept between 280 and 350 ℃, and the pressure is kept within 120 to 150 seconds during casting;
s8: carrying out T6 heat treatment on the aluminum alloy casting blank: carrying out aging treatment after the solution treatment, wherein the solution temperature of the solution treatment is 500 ℃, keeping the temperature for 6 hours, and quenching in hot water at 60 ℃; the temperature of the aging treatment is 225 ℃, the temperature is kept for 10 hours, and the heat-resistant cast aluminum alloy with high Fe content and high Ni content is obtained after air cooling to the room temperature. In the solid solution treatment, the quenching can be carried out in water at the temperature of 50-70 ℃ as long as the solid solution temperature is 500 +/-5 ℃, the heat preservation time is 6-8 hours; in the aging treatment, the aging temperature is 225 +/-10 ℃, and the heat preservation time can be 8-10 hours.
According to the test of relevant standards such as GB/T228.1-2010 and GB/T228.2-2015, the tensile strength at room temperature of the cast aluminum alloy prepared by the embodiment is 368MPa, and the elongation is 1.6%; the tensile strength is 92MPa, the elongation is 13.6 percent and the linear shrinkage of the aluminum alloy is 1.25 percent when the temperature is kept at 350 ℃ for 30 minutes.
Example two:
the total mass of the aluminum alloy of the present example was 50kg, and the cast aluminum alloy for a high power density piston used in mass percent included the following components, Si: 11.8%, Cu: 3.8%, Mg: 0.9%, Ni: 2.8%, Fe: 0.6%, Mn: 0.28%, Sc: 0.13%, Zr: 0.15%, Ti: 0.15%, V: 0.1%, and the balance of Al and inevitable impurities. The mass ratio of Fe/Mn in the prepared aluminum alloy is 2.14:1, and the mass percentage content of the high-temperature support strengthening phase is 7.2%.
The preparation method of the cast aluminum alloy sequentially comprises the following steps:
s1: preparing ingredients: preparing pure aluminum ingots, pure magnesium ingots, AlSi30, AlCu50, AlNi20, AlFe20, AlMn10 and AlSc2 according to the mass percent of the components of the aluminum alloy, preheating the mixture at 160 ℃, and preserving heat for 30-60 min; calculating the amount of the required raw materials according to the alloy components and the stoichiometric ratio, and controlling the total amount of the prepared alloy melt to be 1/2-2/3 of the capacity of the crucible;
s2: taking out a certain amount of pure magnesium and AlCu50 alloy from the mixture, adding the rest alloy mixture into a crucible of a resistance furnace, and heating for T0Smelting at 730 deg.C, and raising the temperature of the molten material to T1Keeping the temperature at about 800 ℃ for 20-30 min, and stirring for 2-3 times by using a bell jar to fully melt the alloy;
s3: after the alloy melt is melted uniformly, the temperature of the alloy melt is reduced to T2，T2Pressing the ZS-ABP10 composite phosphorus salt modifier into the bottom of the crucible by using a bell jar at 760 ℃, crushing, stirring up and down, modifying and ensuring full modification, standing for 25min after modification is completed, and removing scum on the surface of the melt;
s4: adding the pure magnesium and AlCu50 alloy reserved in the step S1 in the step S3, cooling the melt, stirring the melt up and down for 2-3 times, and controlling the total amount of the reserved intermediate alloy to ensure that the temperature of the cooled melt is controlled at 770 ℃ and standing for 20 min; in order to avoid burning and splashing, Mg ingots are wrapped by aluminum foil and added into the melt;
s5: after the alloy in the step S4 is completely melted, adding AlTi10, AlZr10 and AlV10 into the melt for refining, stirring for 2-3 times, standing for 25min, and removing scum on the surface of the melt;
s6: refining: at a temperature T3Degassing and refining the melt at 750 deg.C by rotary blowing for 10min with argon flow of 0.35-0.50m3The speed of the rotor is 150-;
s7: keeping the temperature of the melt at 760 ℃, preheating a casting die, keeping the preheating temperature at 300 ℃, performing extrusion casting by using a hydraulic press under the pressure of 350 tons, maintaining the pressure for 120s, and performing extrusion casting on the melt to form an aluminum alloy casting blank, wherein the casting blank is in a round cake shape, and the size of the round cake casting blank is phi 160mmX60 mm;
s8: carrying out T6 heat treatment on the aluminum alloy casting blank: carrying out aging treatment after the solution treatment, wherein the solution temperature of the solution treatment is 500 ℃, keeping the temperature for 6 hours, and quenching in hot water at 60 ℃; the temperature of the aging treatment is 225 ℃, the temperature is kept for 10 hours, and the heat-resistant cast aluminum alloy with high Fe content and high Ni content is obtained after air cooling to the room temperature.
According to the test of relevant standards such as GB/T228.1-2010, GB/T228.2-2015, the tensile strength at room temperature of the cast aluminum alloy prepared in the embodiment is 379MPa, and the elongation is 1.5%; the tensile strength is 95MPa, the elongation is 15.6 percent and the linear shrinkage of the aluminum alloy is 1.33 percent when the temperature is kept at 350 ℃ for 30 minutes.
Example three:
the total mass of the aluminum alloy of the embodiment is 50kg, and the cast aluminum alloy for the high power density piston comprises the following components of 12 percent of Si, 12 percent of Cu: 4.0%, Mg: 0.9%, Ni: 3.0%, Fe: 0.6%, Mn: 0.28%, Sc: 0.13%, Zr: 0.15%, Ti: 0.15%, V: 0.1%, and the balance of Al and inevitable impurities. The mass ratio of Fe/Mn in the prepared aluminum alloy is 2.14:1, and the mass percentage content of the high-temperature support strengthening phase is 7.6%.
The preparation method of the cast aluminum alloy sequentially comprises the following steps:
s1: preparing ingredients: preparing pure aluminum ingots, pure magnesium ingots, AlSi30, AlCu50, AlNi20, AlFe20, AlMn10 and AlSc2 according to the mass percent of the components of the aluminum alloy, preheating the mixture at 160 ℃, and preserving heat for 30-60 min; calculating the amount of the required raw materials according to the alloy components and the stoichiometric ratio, and controlling the total amount of the prepared alloy melt to be 1/2-2/3 of the capacity of the crucible;
s2: taking out a certain amount of pure magnesium and AlCu50 alloy from the mixture, adding the rest alloy mixture into a crucible of a resistance furnace, and heating for T0Smelting at 730 deg.C, and raising the temperature of the molten material to T1Keeping the temperature at about 800 ℃ for 20-30 min, and stirring for 2-3 times by using a bell jar to fully melt the alloy;
s3: after the alloy melt is melted uniformly, the temperature of the alloy melt is reduced to T2，T2Pressing the ZS-ABP10 composite phosphorus salt modifier into the bottom of the crucible by using a bell jar at 760 ℃, crushing, stirring up and down, modifying and ensuring full modification, standing for 25min after modification is completed, and removing scum on the surface of the melt;
s4: adding the pure magnesium and AlCu50 alloy reserved in the step S1 in the step S3, cooling the melt, stirring the melt up and down for 2-3 times, and controlling the total amount of the reserved intermediate alloy to ensure that the temperature of the cooled melt is controlled at 770 ℃ and standing for 20 min; in order to avoid burning and splashing, Mg ingots are wrapped by aluminum foil and added into the melt;
s5: after the alloy in the step S4 is completely melted, adding AlTi10, AlZr10 and AlV10 into the melt for refining, stirring for 2-3 times, standing for 25min, and removing scum on the surface of the melt;
s6: refining: at a temperature T3Degassing and refining the melt at 750 deg.C by rotary blowing for 10min with argon flow of 0.35-0.50m3The speed of the rotor is 150-;
s7: keeping the temperature of the melt at 755 ℃, preheating a casting die at 300 ℃, performing extrusion casting by using a hydraulic press under the pressure of 350 tons for 120s, and performing extrusion casting on the melt to form an aluminum alloy casting blank, wherein the size of the round cake casting blank is phi 160mmX60 mm;
s8: carrying out T6 heat treatment on the aluminum alloy casting blank: carrying out aging treatment after the solution treatment, wherein the solution temperature of the solution treatment is 500 ℃, keeping the temperature for 6 hours, and quenching in hot water at 60 ℃; the temperature of the aging treatment is 225 ℃, the temperature is kept for 10 hours, and the heat-resistant cast aluminum alloy with high Fe content and high Ni content is obtained after air cooling to the room temperature. According to the test of relevant standards such as GB/T228.1-2010, GB/T228.2-2015, the tensile strength at room temperature of the cast aluminum alloy prepared in the embodiment is 366MPa, and the elongation is 1.8%; the tensile strength is 98MPa, the elongation is 15.2 percent and the linear shrinkage of the aluminum alloy is 1.26 percent when the temperature is kept at 350 ℃ for 30 minutes.
Example four:
the total mass of the aluminum alloy of the embodiment is 50kg, and the cast aluminum alloy for the high power density piston comprises the following components of 12 percent of Si, 12 percent of Cu: 4.0%, Mg: 0.9%, Ni: 3.1%, Fe: 0.7%, Mn: 0.28%, Sc: 0.13%, Zr: 0.15%, Ti: 0.15%, V: 0.1%, and the balance of Al and inevitable impurities. The mass ratio of Fe/Mn in the prepared aluminum alloy is 2.5:1, and the mass percentage content of the high-temperature support strengthening phase is 9.1%.
The preparation method of the cast aluminum alloy in the fourth embodiment is the same as that in the second embodiment, and the adopted process parameters are also the same, which will not be described in detail in this embodiment.
According to the test of relevant standards such as GB/T228.1-2010 and GB/T228.2-2015, the tensile strength at room temperature of the cast aluminum alloy prepared in the embodiment is 353MPa, and the elongation is 1.4%; the tensile strength is 105MPa and the elongation is 14.3 percent when the temperature is kept for 30 minutes at 350 ℃; fatigue strength at 350 ℃ (10)7Second) was 52MPa, and the linear shrinkage of the aluminum alloy was 1.26%.
Al in cast aluminum alloys9The microstructure morphology of the FeNi iron-rich high-temperature strengthening phase is shown in FIGS. 1 and 2, and it can be seen from FIGS. 1 and 2 that the iron-rich high-temperature strengthening phase is Al9FeNi，Al9The FeNi iron-rich high-temperature strengthening phase is in a net shape or a granular shape, has better tissue morphology, is not easy to cause stress concentration and fatigue failure, increases the Fe content, and increases the heat resistance of the alloy(ii) a Al in cast aluminum alloys3CuNi and Al7Cu4The microstructure morphology of the nickel-rich high-temperature strengthening phase such as Ni is shown in fig. 3 and 4, and as can be seen from fig. 3 and 4, the nickel-rich high-temperature strengthening phase is in a net shape and a petal shape, the microstructure morphology is good, and under a high-temperature use environment, the nickel-rich high-temperature strengthening phase plays roles of hindering grain boundary sliding and dislocation movement and inhibiting crack initiation in the alloy, and is beneficial to improving heat resistance, grain boundary strength and creep resistance.
Example five:
the aluminum alloy of the present example had a total mass of 50kg, and the cast aluminum alloy for high power density pistons comprised, in mass percent, 12.5% Si, Cu: 4.5%, Mg: 0.9%, Ni: 3.5%, Fe: 0.7%, Mn: 0.30%, Sc: 0.13%, Zr: 0.15%, Ti: 0.15%, V: 0.1%, and the balance of Al and inevitable impurities. The mass ratio of Fe/Mn in the prepared aluminum alloy is 2.33:1, and the mass percentage content of the high-temperature support strengthening phase is 9.6%.
The preparation method of the cast aluminum alloy sequentially comprises the following steps:
s1: preparing ingredients: preparing pure aluminum ingots, pure magnesium ingots, AlSi30, AlCu50, AlNi20, AlFe20, AlMn10 and AlSc2 according to the mass percent of the components of the aluminum alloy, preheating the mixture at 160 ℃, and preserving heat for 30-60 min;
s2: taking out a certain amount of pure magnesium and AlCu50 alloy from the mixture, adding the rest alloy mixture into a crucible of a resistance furnace, and heating for T0Smelting at 730 deg.C, and raising the temperature of the molten material to T1Keeping the temperature at about 800 ℃ for 20-30 min, and stirring for 2-3 times by using a bell jar to fully melt the alloy;
s3: after the alloy melt is melted uniformly, the temperature of the alloy melt is reduced to T2，T2Pressing the ZS-ABP10 composite phosphorus salt modifier into the bottom of the crucible by using a bell jar at 760 ℃, crushing, stirring up and down, modifying and ensuring full modification, standing for 25min after modification is completed, and removing scum on the surface of the melt;
s4: adding the pure magnesium and the AlCu50 alloy reserved in the step S1 in the step S3 for cooling, stirring the mixture up and down for 2-3 times, and controlling the total amount of the reserved intermediate alloy to ensure that the temperature of the cooled melt is controlled at 770 ℃ and standing the melt for 20 min; in order to avoid burning and splashing, Mg ingots are wrapped by aluminum foil and added into the melt;
s5: after the alloy in the step S4 is completely melted, adding AlTi10, AlZr10 and AlV10 into the melt for refining, stirring for 2-3 times, standing for 25min, and removing scum on the surface of the melt;
s6: refining: at a temperature T3Degassing and refining the melt at 750 deg.C by rotary blowing for 10min with argon flow of 0.35-0.50m3The speed of the rotor is 150-;
s7: keeping the temperature of the melt at 765 ℃, preheating a casting die at 300 ℃, performing extrusion casting by using a hydraulic press under the pressure of 350 tons for 120s, and performing extrusion casting on the melt to form an aluminum alloy casting blank, wherein the aluminum alloy casting blank is in a round cake shape, and the size of the round cake casting blank is phi 160mmX60 mm;
s8: carrying out T6 heat treatment on the aluminum alloy casting blank: carrying out aging treatment after the solution treatment, wherein the solution temperature of the solution treatment is 500 ℃, keeping the temperature for 6 hours, and quenching in hot water at 60 ℃; the temperature of the aging treatment is 225 ℃, the temperature is kept for 10 hours, and the heat-resistant cast aluminum alloy with high Fe content and high Ni content is obtained after air cooling to the room temperature.
According to the test of relevant standards such as GB/T228.1-2010 and GB/T228.2-2015, the tensile strength at room temperature of the cast aluminum alloy prepared in the embodiment is 359MPa, and the elongation is 1.6%; the tensile strength is 103MPa, the elongation is 13.5 percent and the linear shrinkage of the aluminum alloy is 1.27 percent when the temperature is kept at 350 ℃ for 30 minutes.
Example six:
the aluminum alloy of the present example had a total mass of 50kg, and the cast aluminum alloy for high power density pistons comprised, in mass percent, 12.0% Si, Cu: 4.3%, Mg: 0.9%, Ni: 3.0%, Fe: 0.7%, Mn: 0.32%, Sc: 0.13%, Zr: 0.15%, Ti: 0.15%, V: 0.1%, and the balance of Al and inevitable impurities. The mass ratio of Fe/Mn in the prepared aluminum alloy is 2.19:1, and the mass percentage content of the high-temperature support strengthening phase is 9.3%.
The preparation method of the cast aluminum alloy in this embodiment is the same as that in the fifth embodiment, and the adopted process parameters are also the same, which will not be described in detail in this embodiment.
According to the test of relevant standards such as GB/T228.1-2010, GB/T228.2-2015, the tensile strength at room temperature of the cast aluminum alloy prepared in the embodiment is 346MPa, and the elongation is 1.5%; the tensile strength is 103MPa, the elongation is 13.2 percent and the linear shrinkage of the aluminum alloy is 1.46 percent when the temperature is kept at 350 ℃ for 30 minutes.
Example seven:
the aluminum alloy of the present example had a total mass of 50kg, and the cast aluminum alloy for high power density pistons comprised, in mass percent, 12.0% Si, Cu: 4.0%, Mg: 0.9%, Ni: 2.8%, Fe: 0.8%, Mn: 0.35%, Sc: 0.13%, Zr: 0.15%, Ti: 0.15%, V: 0.1%, and the balance of Al and inevitable impurities. The mass ratio of Fe/Mn in the prepared aluminum alloy is 2.29:1, and the mass percentage content of the high-temperature support strengthening phase is 8.6%.
The preparation method of the cast aluminum alloy in this embodiment is the same as that in the fifth embodiment, and the adopted process parameters are also the same, which will not be described in detail in this embodiment.
According to the test of relevant standards such as GB/T228.1-2010 and GB/T228.2-2015, the tensile strength at room temperature of the cast aluminum alloy prepared in the embodiment is 325MPa, and the elongation is 1.4%; the tensile strength is 101MPa, the elongation is 11.5 percent and the linear shrinkage of the aluminum alloy is 1.33 percent when the temperature is kept at 350 ℃ for 30 minutes.
Example eight:
the total mass of the aluminum alloy of the embodiment is 50kg, and the aluminum alloy for the high power density piston comprises the following components of 11.0 percent of Si, and Cu: 4.5%, Mg: 0.7%, Ni: 3.2%, Fe: 0.7%, Mn: 0.25%, Sc: 0.10%, Zr: 0.13%, Ti: 0.13%, V: 0.12%, and the balance of Al and inevitable impurities. The mass ratio of Fe/Mn in the prepared aluminum alloy is 2.8:1, and the mass percentage content of the high-temperature support strengthening phase is 8.7%.
The cast aluminum alloy of this example was produced in the same manner as in example V except that the preheating temperature in step S1 was 150 ℃ and the temperature T in step S2 was set to0At a temperature of 720 ℃ and a temperature T1The temperature is 790 ℃, and other process parameters are the same, which will not be described in detail in this embodiment.
According to the test of relevant standards such as GB/T228.1-2010 and GB/T228.2-2015, the tensile strength at room temperature of the cast aluminum alloy prepared in the embodiment is 356MPa, and the elongation is 1.1%; the tensile strength is 103MPa, the elongation is 12.7 percent and the linear shrinkage of the aluminum alloy is 1.29 percent when the temperature is kept at 350 ℃ for 30 minutes.
Example nine:
the total mass of the aluminum alloy of the embodiment is 50kg, and the aluminum alloy for the high power density piston comprises the following components of 12.6 percent of Si and Cu: 3.5%, Mg: 1.2%, Ni: 2.2%, Fe: 0.8%, Mn: 0.25%, Sc: 0.15%, Zr: 0.17%, Ti: 0.17%, V: 0.08%, and the balance of Al and inevitable impurities. The mass ratio of Fe/Mn in the prepared aluminum alloy is 3.2:1, and the mass percentage content of the high-temperature support strengthening phase is 6.9%.
The cast aluminum alloy of this example was produced in the same manner as in example five except that the preheating temperature in step S1 was 170 ℃ and the temperature T in step S20At a temperature of 740 ℃ and a temperature T1For 810 ℃, other process parameters are the same, and will not be described in detail in this embodiment. According to the test of relevant standards such as GB/T228.1-2010 and GB/T228.2-2015, the tensile strength at room temperature of the cast aluminum alloy prepared in the embodiment is 362MPa, and the elongation is 1.2%; the tensile strength is 98MPa, the elongation is 13.1 percent and the linear shrinkage of the aluminum alloy is 1.26 percent when the temperature is kept at 350 ℃ for 30 minutes.
The properties of the prior art piston cast aluminum alloy are shown in Table 1 below.
TABLE 1
Figure BDA0002446783070000111
As can be seen from the comparison of the above table 1, the tensile strength and elongation at room temperature of each example of the invention are obviously superior to the performance of the existing piston casting aluminum alloy at room temperature; the tensile strength and the elongation at 350 ℃ of each embodiment of the invention are both clearly superior to the performance of each existing piston casting aluminum alloy at 350 ℃, the casting aluminum alloy of the embodiment of the invention only gives the performance at 350 ℃ of high temperature, and the embodiment of the invention has better tensile strength and elongation at 350-420 ℃.
The above description is only an embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art can easily conceive of changes or substitutions within the technical scope of the present invention, and therefore, the scope of the present invention should be determined by the scope of the claims.

Claims (9)

1. A cast aluminum alloy for a high power density piston, comprising: the aluminum alloy comprises the following components in percentage by mass: 11.0-12.6% of Si, Cu: 3.8-4.5%, Mg: 0.7-1.2%, Ni: 2.2-3.2%, Fe: 0.6-0.8%, Mn: 0.25-0.35%, Sc:0.10 to 0.15%, Zr: 0.13-0.17%, Ti: 0.13-0.17%, V: 0.08-0.12 percent of Al and inevitable impurities as the balance, wherein the mass ratio of Fe to Mn in the aluminum alloy is 1.71-3.2, the mass percentage content of the high-temperature support strengthening phase in the aluminum alloy is 6.2-9.6 percent, the room-temperature tensile strength is 325-379 MPa, the elongation is 1.0-1.8 percent, and the high-temperature support strengthening phase in the aluminum alloy is Al9FeNi、Al15Si2(Fe,Mn)3、Al3CuNi and Al7Cu4Ni。
2. The cast aluminum alloy of claim 1, wherein: the precipitated phase in the aluminum alloy is Al5Dispersed Al converted from needle-like primary phase of FeSi15Si2(Fe,Mn)3And (4) phase(s).
3. A method of producing the cast aluminum alloy of claim 1 or 2, comprising the steps of, in order:
s1: preparing ingredients: preparing pure aluminum ingots, pure magnesium ingots, Al-Si intermediate alloys, Al-Cu intermediate alloys, Al-Ni intermediate alloys, Al-Fe intermediate alloys, Al-Mn intermediate alloys and Al-Sc intermediate alloys according to the mass percent of the components of the aluminum alloys, and preheating and insulating the prepared materials;
s2: taking out a certain amount of pure magnesium and Al-Cu intermediate alloy from the mixture, and mixing the rest alloy at T0Smelting, and after the molten materials are completely melted, raising the temperature of the molten materials to T1Preserving heat, and stirring to fully melt the alloy;
s3: cooling the alloy melt to T2Wherein, T0＜T2＜T1Adding a modifier for modification treatment, fully standing after modification, and removing scum on the surface of the melt;
s4: adding the pure magnesium and the Al-Cu intermediate alloy reserved in the step S1 in the step S3, cooling and stirring to ensure that the temperature of the cooled melt is higher than T2And standing;
s5: after the alloy in the step S4 is completely melted, adding an Al-Ti refiner, an Al-Zr refiner and an Al-V refiner into the melt for refining treatment, and simultaneously stirring and standing to remove scum on the surface of the melt;
s6: at a temperature T3Degassing and refining the melt by adopting a rotary blowing mode, wherein T3＞T0Standing and removing scum on the surface of the melt after degassing;
s7: keeping the temperature of the melt, preheating a casting die, and carrying out extrusion casting on the melt to form an aluminum alloy casting blank;
s8: carrying out T6 heat treatment on the aluminum alloy casting blank: and carrying out aging treatment after the solution treatment.
4. The production method according to claim 3, characterized in that: the Al-Si intermediate alloy is AlSi30, the Al-Cu intermediate alloy is AlCu50, the Al-Ni intermediate alloy is AlNi20, the Al-Fe intermediate alloy is AlFe20, the Al-Mn intermediate alloy is AlMn10, and the Al-Sc intermediate alloy is AlSc 2.
5. The production method according to claim 3, characterized in that: in step S5, the Al-Ti refiner is an intermediate alloy AlTi 10; the Al-Zr refiner is intermediate alloy AlZr 10; the Al-V refiner is master alloy AlV 10.
6. The production method according to claim 3, characterized in that: the preheating temperature in the step S1 is 150-170 ℃, and the heat preservation time is 30-60 min; in step S2, the temperature T0At a temperature of 720 ℃ to 740 ℃ and a temperature T1The temperature is 790-810 ℃, and the heat preservation time is 20-30 min; in step S3, T2The temperature is 760-770 ℃, and the standing time is 20-30 min; in step S6, T3750 and 760 ℃, and the standing time is 10-15 min; in step S7, the temperature of the melt is maintained at 750-780 ℃, the mold is preheated to 280-350 ℃, the pressure is 350 tons, and the pressure is maintained for 120 seconds.
7. The method of claim 6, wherein: the preheating temperature in step S1 is 160 ℃, and in step S2, the temperature T0At a temperature of 730 ℃ and a temperature T1The temperature was 800 ℃.
8. The production method according to claim 3, characterized in that: in step S8, the solid solution temperature of the solid solution treatment is 500 plus or minus 5 ℃, the temperature is kept for 6 to 8 hours, and the quenching is carried out in hot water with the temperature of 50 to 70 ℃; the temperature of the aging treatment is 225 +/-10 ℃, the temperature is kept for 8-10 hours, and the air cooling is carried out to the room temperature.
9. The production method according to claim 3, characterized in that: the flow of argon in the rotary blowing is 0.35-0.50m3The speed of the rotor is 150-.
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