CN117821812A - High-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy and preparation method thereof - Google Patents
High-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy and preparation method thereof Download PDFInfo
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 48
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 title claims abstract description 27
- 238000002360 preparation method Methods 0.000 title abstract description 10
- 238000005266 casting Methods 0.000 claims abstract description 27
- 230000032683 aging Effects 0.000 claims abstract description 19
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 11
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 9
- 238000010791 quenching Methods 0.000 claims abstract description 7
- 230000000171 quenching effect Effects 0.000 claims abstract description 7
- 239000006104 solid solution Substances 0.000 claims abstract description 7
- 229910052796 boron Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 238000004519 manufacturing process Methods 0.000 claims abstract 8
- 229910045601 alloy Inorganic materials 0.000 claims description 115
- 239000000956 alloy Substances 0.000 claims description 115
- 239000011777 magnesium Substances 0.000 claims description 39
- 239000010949 copper Substances 0.000 claims description 32
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 26
- 229910052709 silver Inorganic materials 0.000 claims description 20
- 229910052749 magnesium Inorganic materials 0.000 claims description 19
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 16
- 239000000155 melt Substances 0.000 claims description 16
- 239000004332 silver Substances 0.000 claims description 16
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 claims description 13
- 238000003756 stirring Methods 0.000 claims description 12
- 229910052802 copper Inorganic materials 0.000 claims description 11
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 10
- 238000000034 method Methods 0.000 claims description 9
- 238000007670 refining Methods 0.000 claims description 7
- 229910052751 metal Inorganic materials 0.000 claims description 6
- 239000002184 metal Substances 0.000 claims description 6
- 229910052791 calcium Inorganic materials 0.000 claims description 5
- 238000007872 degassing Methods 0.000 claims description 4
- 229910052712 strontium Inorganic materials 0.000 claims description 4
- 238000005303 weighing Methods 0.000 claims description 4
- 229910017143 AlSr Inorganic materials 0.000 claims description 3
- 229910052790 beryllium Inorganic materials 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 239000004576 sand Substances 0.000 claims description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 230000005484 gravity Effects 0.000 claims description 2
- 239000000243 solution Substances 0.000 claims description 2
- 238000010438 heat treatment Methods 0.000 description 11
- 230000000694 effects Effects 0.000 description 10
- 238000005728 strengthening Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 6
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 5
- 230000005496 eutectics Effects 0.000 description 5
- 239000010703 silicon Substances 0.000 description 5
- 230000006866 deterioration Effects 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 229910017818 Cu—Mg Inorganic materials 0.000 description 3
- 238000001816 cooling Methods 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
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- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 229910010038 TiAl Inorganic materials 0.000 description 2
- 238000005054 agglomeration Methods 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 238000001938 differential scanning calorimetry curve Methods 0.000 description 2
- 230000009977 dual effect Effects 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 230000002045 lasting effect Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 241001424392 Lucia limbaria Species 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 229910019015 Mg-Ag Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- -1 aluminum-titanium-boron Chemical compound 0.000 description 1
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Abstract
The invention relates to a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy and a preparation method thereof, and aims to solve the problems that the hypoeutectic aluminum-silicon cast aluminum alloy has lower room temperature mechanical property and insufficient heat intensity when the service temperature exceeds 200 ℃, and the high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy consists of Si, cu, mg, ag, mn, ti, V, be, ca, sr, B and Al according to mass fraction. The high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy is obtained through smelting, pouring, three-stage solid solution treatment, quenching, pre-ageing treatment and ageing treatment, has high tensile strength and yield strength, and can work for a long time in an environment of 220 ℃ without failure. The invention is applied to the manufacturing field of casting aluminum alloy.
Description
Technical Field
The invention relates to the technical field of alloy preparation, in particular to a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy and a preparation method thereof.
Background
The existing common hypoeutectic aluminum-silicon cast aluminum alloy such as ZL101A, ZL A and other alloys has the advantages of good fluidity, narrow solid-liquid temperature range, low loosening tendency, easy feeding and good repair welding manufacturability, and is ideal cast aluminum alloy. The method is suitable for various casting methods, can be used for producing products with complex structures, thin walls, corrosion resistance and high air tightness, and is mainly used for structural members bearing medium loads and shell members with complex shapes. But the room temperature mechanical property of the material is general (the tensile strength of a single casting sample is generally lower than 350 MPa). In addition, when the service temperature exceeds 200 ℃, the strengthening phase is easy to coarsen, so that the material is softened and fails, and the material cannot bear critical components. In addition, the specific strength is lower than that of the common ZM6 magnesium alloy, and the requirement of light weight design is difficult to meet.
Disclosure of Invention
The invention aims to solve the problems of low room-temperature mechanical property and insufficient heat intensity of materials when the service temperature exceeds 200 ℃ of hypoeutectic aluminum-silicon cast aluminum alloy, and provides a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy and a preparation method thereof.
The invention relates to a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy which comprises, by mass, 6.5-7.5% of Si, 1-1.3% of Cu, 0.70-0.80% of Mg, 0.50-0.90% of Ag, 0.10-0.25% of Mn, 0.08-0.12% of Ti, 0.04-0.10% of V, 0.0015-0.0030% of Be, 0.0030% of Ca, 0.0070-0.030% of Sr, 0.015% of B and the balance of Al.
The invention relates to a preparation method of a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy, which comprises the following steps:
1. weighing refined aluminum ingot, alSi30 intermediate alloy, alMn20 intermediate alloy, alTi10 intermediate alloy, alBe5 intermediate alloy, alV4 intermediate alloy, pure magnesium, pure silver, cathode copper, alB3 intermediate alloy, alSr5 intermediate alloy and AlCa10 intermediate alloy according to the mass fraction of 6.5-7.5% Si, 1-1.3% Cu, 0.70-0.80% Mg, 0.50-0.90% Ag, 0.10-0.25% Mn, 0.08-0.12% Ti, 0.04-0.10% V, 0.0015-0.0030% Be, 0.0030% Ca, 0.0070-0.030% Sr, 0.015% B and the balance Al;
2. placing the refined aluminum ingot, the AlSi30 intermediate alloy, the AlMn20 intermediate alloy, the AlTi10 intermediate alloy, the AlBe5 intermediate alloy and the AlV4 intermediate alloy into a crucible for smelting, and stirring the melt and deslagging when the temperature of the melt reaches 755-765 ℃;
3. immersing pure magnesium, pure silver and cathode copper into a melt, stirring uniformly after all the pure magnesium, the pure silver and the cathode copper are melted, adding AlB3 intermediate alloy to refine grains, stirring uniformly after the pure magnesium, the pure silver and the cathode copper are melted completely, and standing for 5-10 min;
4. adding AlSr5 intermediate alloy and AlCa10 intermediate alloy when the temperature of the melt is 740-750 ℃, standing for 5min after the intermediate alloy and the AlSr 10 intermediate alloy are completely melted, degassing and refining, and pouring to obtain an aluminum alloy casting;
5. and carrying out three-stage solid solution treatment, quenching, pre-aging treatment and aging treatment on the aluminum alloy casting to obtain the aluminum alloy casting.
In Al-Si-Cu-Mg alloy, the sequence of precipitated phases is greatly affected by the mass ratio of Cu/Mg, and when the mass ratio of Cu/Mg in the alloy components is lower than 2.1, the structure of the alloy is composed of alpha-Al, eutectic silicon and beta phase (Mg 2 Si), Q phase (Al 5 Cu 2 Mg 8 Si 6 ) Quaternary phase composition. When the Cu/Mg mass ratio in the alloy composition is 2.1, the beta phase (Mg 2 Si) is completely disappeared, and the structure is composed of alpha-Al, eutectic silicon and Q phase (Al 5 Cu 2 Mg 8 Si 6 ) Ternary phase composition. When the Cu/Mg mass ratio in the alloy composition is more than 2.1, the alloy structure is not formed of alpha-Al, eutectic silicon, Q phase (Al 5 Cu 2 Mg 8 Si 6 ) In addition, theta phase (Al 2 Cu). At room temperature, beta phase (Mg 2 Si) has a strengthening effect greater than that of the theta phase (Al 2 Cu)。
Thus, the Cu/Mg mass ratio is controlled to be 1.6-1.7, and a beta phase (Mg 2 Si), Q phase (Al 5 Cu 2 Mg 8 Si 6 ) The dual strengthening phase has excellent tensile property at room temperature, the Q phase has excellent thermal stability, and the strengthening effect is not attenuated at 200 ℃.
Further, ag is usually alloyed with Al-Mg-Si and Al-Cu-Mg alloys to improve the performance. The invention adds a proper amount of Ag atoms to Al-Si-Cu-Mg alloy to replace part of Mg atoms as strengthening phase in the aging treatment process to obtain nucleation points to form Si-Mg-Ag vacancy clusters, which results in the increase of the quantity of nucleation points in the alloy and finally promotes the precipitation of beta'. In addition, ag element is enriched on the surface of beta', so that the growth of the Ag element is inhibited, and the strength can be improved.
The addition of 0.0030% Ca element can make coarse Mg 2 The Si phase is transformed into fine particles, thereby improving the solid solution degree of the beta phase in the solid solution process, and is transformed into beta' phase in the aging process, thereby improving the alloy strength.
Adding proper amount of Mn elementIntermetallic compounds formed with Cu element are distributed in the grain boundary to prevent grain boundary sliding, so that the heat resistance of the aluminum alloy can be improved. Adding Ti, V and B elements for alpha-Al grain refinement, wherein if the content of Ti is too high, si can be biased to play a role in TiAl for aluminum alloy with Si content of more than 5 percent 3 The reaction is performed and the grain refining effect of Ti element is further improved, so that the content of Ti element is controlled to be 0.08-0.12%. The Sr has the effects of converting coarse lath-shaped eutectic silicon into fine fibers, reducing the cracking effect of the eutectic silicon on a matrix and improving the elongation of the alloy. The trace Be element can reduce the oxidation burning loss of Mg element, promote the precipitation of beta 'phase during the aging treatment of the alloy, and increase the quantity of the reinforced phase beta', thereby improving the mechanical property of the alloy.
In the preparation process, refined aluminum ingots, alSi30 intermediate alloy, alMn20 intermediate alloy, alTi10 intermediate alloy and AlBe5 intermediate alloy which are not easy to oxidize are firstly placed into a melting furnace, wherein Be is configured according to 0.0015-0.0030% of the total weight of the total furnace burden, and pure magnesium is firstly placed after the AlBe5 intermediate alloy is melted, so that the oxidation burning loss of Mg element can Be timely and effectively avoided.
The Cu element of the cast aluminum alloy is generally added in the form of an AlCu50 master alloy, and is mainly because the AlCu50 master alloy dissolves faster than pure copper. However, the Cu element belongs to inverse segregation element in the aluminum alloy, the copper content of the AlCu50 intermediate alloy can only be controlled between 48% and 52%, so that the copper content in the cast aluminum alloy is difficult to accurately control.
The heating temperature in the second step is 760 ℃, and the dissolution of silver particles and small copper sheets can be accelerated at the heating temperature; and thirdly, heating to 745 ℃, refining and removing hydrogen at the temperature, wherein the temperature is close to the casting temperature, the time from deterioration to casting is shortened, and the hydrogen absorption of the melt is controlled.
The general aluminum alloy adopts an aluminum-titanium-boron intermediate alloy (containing TiAl) 3 And TiB 2 Grain as crystal nucleus), but the refining effect is far less than that of Al-B intermediate alloy for Al-Si cast aluminum alloy, and Sr element is easy to be compared with TiB 2 Agglomeration and precipitation occur, and the effects of deterioration and grain refinement are affected. The invention adopts the filiform AlB3 intermediate alloy, can be quickly dissolved into an aluminum alloy melt, and can form a large amount of tiny dispersed AlB in the aluminum melt by controlling the alloy B element to be 0.015 percent 2 As crystal nucleus, crystal grains are refined, and agglomeration with Sr does not occur to influence the deterioration effect.
The AlSr5 intermediate alloy is added to be quickly dissolved into an aluminum alloy melt, and the Sr element is controlled to be 0.0075 percent for the casting method with higher cooling speed of a metal mold and the like to obtain the best modification effect; for casting methods in which cooling is slow, such as sand mold, the Sr element is controlled to 0.025% to obtain the best deterioration effect.
The invention has the beneficial effects that:
after the alloy casting metal type single casting sample is subjected to heat treatment, the room temperature tensile strength is 380-410 MPa, the yield strength is 325-360 MPa, and the elongation is 4-6%.
The tensile strength is between 290 and 320MPa, the yield strength is between 275 and 290MPa, and the elongation is between 5 and 7 percent at 220 ℃.
The lasting strength can reach 180MPa after 150 hours at 220 ℃.
The alloy provides a cast aluminum alloy with high specific strength for the lightweight structural design of components in the fields of aerospace, automobiles and the like.
Drawings
FIG. 1 is a DSC curve of an alloy prepared in example one;
fig. 2 shows the morphology of the HRTEM observation strengthening phase.
Detailed Description
The first embodiment is as follows: the high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy of the present embodiment comprises, by mass, 6.5 to 7.5% of Si, 1 to 1.3% of Cu, 0.70 to 0.80% of Mg, 0.50 to 0.90% of Ag, 0.10 to 0.25% of Mn, 0.08 to 0.12% of Ti, 0.04 to 0.10% of V, 0.0015 to 0.0030% of Be, 0.0030% of Ca, 0.0070 to 0.030% of Sr, 0.015% of B, and the balance of Al.
The second embodiment is as follows: the present embodiment differs from the specific embodiment in that: the hypoeutectic aluminum-silicon cast aluminum alloy comprises, by mass, 7.3% of Si, 1.3% of Cu, 0.75% of Mg, 0.8% of Ag, 0.2% of Mn, 0.1% of Ti, 0.07% of V, 0.0025% of Be, 0.0030% of Ca, 0.0075-0.025% of Sr, 0.015% of B and the balance of Al. The other steps are the same as in the first embodiment.
And a third specific embodiment: the preparation method of the high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy comprises the following steps:
1. weighing refined aluminum ingot, alSi30 intermediate alloy, alMn20 intermediate alloy, alTi10 intermediate alloy, alBe5 intermediate alloy, alV4 intermediate alloy, pure magnesium, pure silver, cathode copper, alB3 intermediate alloy, alSr5 intermediate alloy and AlCa10 intermediate alloy according to the mass fraction of 6.5-7.5% Si, 1-1.3% Cu, 0.70-0.80% Mg, 0.50-0.90% Ag, 0.10-0.25% Mn, 0.08-0.12% Ti, 0.04-0.10% V, 0.0015-0.0030% Be, 0.0030% Ca, 0.0070-0.030% Sr, 0.015% B and the balance Al;
2. placing the refined aluminum ingot, the AlSi30 intermediate alloy, the AlMn20 intermediate alloy, the AlTi10 intermediate alloy, the AlBe5 intermediate alloy and the AlV4 intermediate alloy into a crucible for smelting, and stirring the melt and deslagging when the temperature of the melt reaches 755-765 ℃;
3. immersing pure magnesium, pure silver and cathode copper into a melt, stirring uniformly after all the pure magnesium, the pure silver and the cathode copper are melted, adding AlB3 intermediate alloy to refine grains, stirring uniformly after the pure magnesium, the pure silver and the cathode copper are melted completely, and standing for 5-10 min;
4. adding AlSr5 intermediate alloy and AlCa10 intermediate alloy when the temperature of the melt is 740-750 ℃, standing for 5min after the intermediate alloy and the AlSr 10 intermediate alloy are completely melted, degassing and refining, and pouring to obtain an aluminum alloy casting;
5. and carrying out three-stage solid solution treatment, quenching, pre-aging treatment and aging treatment on the aluminum alloy casting to obtain the aluminum alloy casting.
The specific embodiment IV is as follows: the third difference between this embodiment and the specific embodiment is that: the cathode copper is a copper sheet cut from a cathode copper plate with the thickness of 1cm. The other steps are the same as in the third embodiment.
Fifth embodiment: the difference between this embodiment and the third or fourth embodiment is that: the dimensions of the copper sheet were 5cm by 1cm. The other steps are the same as those of the third or fourth embodiment.
Specific embodiment six: the present embodiment differs from the third to fifth embodiments in that: and (3) pouring by adopting a gravity or countergravity casting method, wherein if the metal mold casting is poured, the mass fraction of Sr in the alloy is 0.0075%, and if the sand mold casting is poured, the mass fraction of Sr in the alloy is 0.025%. The other steps are the same as those of the third to fifth embodiments.
Seventh embodiment: the present embodiment differs from the third to sixth embodiments in that: the three-stage solid solution treatment is to heat at 503 ℃ for 5 hours, heat to 525 ℃ for 5 hours, and heat to 530 ℃ for 15 hours. The other steps are the same as those of the third to sixth embodiments.
Eighth embodiment: the present embodiment differs from the third to seventh embodiments in that: the quenching water temperature is 20-40 ℃. The other steps are the same as those of the third to seventh embodiments.
Detailed description nine: the present embodiment differs from the third to eighth embodiments in that: the pre-ageing treatment is carried out for 8 to 10 hours at room temperature. The other steps are the same as those of the third to eighth embodiments.
Detailed description ten: the present embodiment differs from one of the third to ninth embodiments in that: the aging temperature of aging treatment is 170-180 ℃, and the temperature is kept for 8-15 h. The other steps are the same as those of the third to ninth embodiments.
The following examples are used to verify the benefits of the present invention:
embodiment one: the preparation method of the high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy comprises the following steps of:
1. weighing refined aluminum ingot, alSi30 master alloy, alMn20 master alloy, alTi10 master alloy, alBe5 master alloy, alV4 master alloy, pure magnesium, pure silver, cathode copper, alB3 master alloy, alSr5 master alloy and Alca10 master alloy according to the mass fraction of 7.3% of Si, 1.3% of Cu, 0.75% of Mg, 0.8% of Ag, 0.2% of Mn, 0.1% of Ti, 0.07% of V, 0.0025% of Be, 0.0030% of Ca, 0.0075% of Sr, 0.015% of B and the balance of Al;
2. firstly, placing a refined aluminum ingot, an AlSi30 intermediate alloy, an AlMn20 intermediate alloy, an AlTi10 intermediate alloy, an AlBe5 intermediate alloy and an AlV4 intermediate alloy into a crucible, and stirring and deslagging when the temperature of the melt reaches 760 ℃; pure magnesium blocks, pure silver particles and cathode copper sheets are added by a strainer, and the pure magnesium blocks, the pure silver particles and the cathode copper sheets are submerged below the liquid level of the melt, so that oxidation of Cu, mg and Ag elements is avoided. Stirring uniformly after the mixture is completely dissolved, adding AlB3 intermediate alloy to refine grains, stirring uniformly after the mixture is completely dissolved, and standing for 5min. When the temperature is regulated to 745 ℃, adding a wire-shaped AlSr5 intermediate alloy and an AlCa10 intermediate alloy to respectively enable the Sr and Ca content to reach 0.0075 percent and 0.0030 percent, standing for 5min after the wire-shaped AlSr5 intermediate alloy and the AlCa10 intermediate alloy are completely melted, and then carrying out degassing refining by a refiner to pour the metal mold casting.
FIG. 1 is a DSC curve of the alloy in the heating stage of this example, wherein the endothermic peak (No. 2) is 507.9 ℃, and the low melting point phase melts at this temperature, and in order to avoid over-firing, it is necessary to keep the temperature for a period of time before this temperature so that the melting point phase is completely dissolved and diffused into the matrix, and then the heating can be continued.
Therefore, the heat treatment process of this embodiment is as follows:
solution treatment: the temperature is kept at 503 ℃ for 5 hours. Heating to 525 ℃ and preserving heat for 5h, heating to 530 ℃ and preserving heat for 15h, quenching with water at room temperature, and transferring time is not more than 10s.
Placing for 10 hours at room temperature, carrying out pre-ageing treatment, then placing into an ageing furnace at 180 ℃ for heat preservation for 9 hours, and discharging and air-cooling.
The strengthening phase after heat treatment of the alloy of this example is beta' (Mg 2 Si) andq' phase (Al) 5 Cu 2 Mg 8 Si 6 ) The dual reinforcement phase is shown in fig. 2.
After the alloy casting metal type single casting sample is subjected to heat treatment, the room temperature tensile strength is 380-410 MPa, the yield strength is 325-360 MPa, and the elongation is 4-6%. The tensile strength is between 290 and 320MPa, the yield strength is between 275 and 290MPa, and the elongation is between 5 and 7 percent at 220 ℃. The lasting strength can reach 180MPa after 150 hours at 220 ℃.
The alloy of the embodiment has good fluidity, the solid-liquid temperature is 549-613 ℃, the temperature difference is 64 ℃, the loosening tendency is slightly lower than that of ZL114A alloy, and the fluidity is close to that of the alloy. The tensile strength and the yield strength are both higher than those of ZL114A by more than 70MPa, the ZL114A alloy is used in an environment below 150 ℃, and the alloy can work for a long time in an environment of 220 ℃ without failure.
Claims (10)
1. The high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy is characterized by comprising, by mass, 6.5-7.5% of Si, 1-1.3% of Cu, 0.70-0.80% of Mg, 0.50-0.90% of Ag, 0.10-0.25% of Mn, 0.08-0.12% of Ti, 0.04-0.10% of V, 0.0015-0.0030% of Be, 0.0030% of Ca, 0.0070-0.030% of Sr, 0.015% of B and the balance of Al.
2. The high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy according to claim 1, wherein the hypoeutectic aluminum-silicon cast aluminum alloy comprises, by mass, 7.3% of Si, 1.3% of Cu, 0.75% of Mg, 0.8% of Ag, 0.2% of Mn, 0.1% of Ti, 0.07% of V, 0.0025% of Be, 0.0030% of Ca, 0.0075-0.025% of Sr, 0.015% of B and the balance of Al.
3. The method for preparing the high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy as claimed in claim 1, which is characterized by comprising the following steps:
1. weighing refined aluminum ingot, alSi30 intermediate alloy, alMn20 intermediate alloy, alTi10 intermediate alloy, alBe5 intermediate alloy, alV4 intermediate alloy, pure magnesium, pure silver, cathode copper, alB3 intermediate alloy, alSr5 intermediate alloy and AlCa10 intermediate alloy according to the mass fraction of 6.5-7.5% Si, 1-1.3% Cu, 0.70-0.80% Mg, 0.50-0.90% Ag, 0.10-0.25% Mn, 0.08-0.12% Ti, 0.04-0.10% V, 0.0015-0.0030% Be, 0.0030% Ca, 0.0070-0.030% Sr, 0.015% B and the balance Al;
2. placing the refined aluminum ingot, the AlSi30 intermediate alloy, the AlMn20 intermediate alloy, the AlTi10 intermediate alloy, the AlBe5 intermediate alloy and the AlV4 intermediate alloy into a crucible for smelting, and stirring the melt and deslagging when the temperature of the melt reaches 755-765 ℃;
3. immersing pure magnesium, pure silver and cathode copper into a melt, stirring uniformly after all the pure magnesium, the pure silver and the cathode copper are melted, adding AlB3 intermediate alloy to refine grains, stirring uniformly after the pure magnesium, the pure silver and the cathode copper are melted completely, and standing for 5-10 min;
4. adding AlSr5 intermediate alloy and AlCa10 intermediate alloy when the temperature of the melt is 740-750 ℃, standing for 5min after the intermediate alloy and the AlSr 10 intermediate alloy are completely melted, degassing and refining, and pouring to obtain an aluminum alloy casting;
5. and carrying out three-stage solid solution treatment, quenching, pre-aging treatment and aging treatment on the aluminum alloy casting to obtain the aluminum alloy casting.
4. The method for producing a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy according to claim 3, wherein the cathode copper is a copper sheet cut from a cathode copper plate having a thickness of 1cm.
5. The method for producing a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy according to claim 4, wherein the copper sheet has dimensions of 5 cm. Times.5 cm. Times.1 cm.
6. The method for producing a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy according to claim 3, wherein the casting is performed by gravity or countergravity, the mass fraction of Sr in the alloy is 0.0075% if a metal mold casting is cast, and the mass fraction of Sr in the alloy is 0.025% if a sand mold casting is cast.
7. The method for producing a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy according to claim 3, wherein the three-stage solution treatment is performed at 503 ℃ for 5 hours, heated to 525 ℃ for 5 hours, and heated to 530 ℃ for 15 hours.
8. The method for producing a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy according to claim 3, wherein the quenching water temperature is 20 to 40 ℃.
9. The method for producing a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy according to claim 3, wherein the pre-aging treatment is carried out at room temperature for 8 to 10 hours.
10. The method for producing a high-strength heat-resistant hypoeutectic aluminum-silicon cast aluminum alloy according to claim 3, wherein the aging temperature of the aging treatment is 170-180 ℃ and the temperature is kept for 8-15 hours.
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