CN112442612B - Method for improving fluidity of cast aluminum-copper alloy - Google Patents
Method for improving fluidity of cast aluminum-copper alloy Download PDFInfo
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Abstract
The invention relates to a method for improving the flow property of cast aluminum-copper alloy, which comprises 50wt% of Al powder, 40-45 wt% of Ti powder, 3-8 wt% of graphite powder and La powder2O30.5-1% of powder, Y2O3Mixing and pressing 0.5-1% of powder for forming, performing self-propagating combustion by high-energy laser to obtain a self-propagating product, adding the self-propagating product into molten aluminum, diluting to 5-5.3 wt% of Ti element, pouring to obtain an intermediate alloy, adding an Al-Ti-C-La-Y intermediate alloy ingot with the mass of 0.3-1.5 wt% of aluminum-copper alloy into the uniformly-smelted aluminum-copper alloy, and uniformly smelting to obtain an aluminum-copper alloy solution with improved flow property. According to the invention, Al-Ti-C-La-Y intermediate alloy is introduced into the smelted cast aluminum-copper alloy to refine grains, fuse dendritic crystals and shorten the crystallization interval of the cast aluminum-copper alloy, so that the flowing property and the casting property of the cast aluminum-copper alloy are improved, and technical support is provided for producing complex thin-wall aluminum-copper alloy castings.
Description
Technical Field
The invention belongs to the technical field of aluminum-copper alloy casting, and relates to a method capable of improving the flowability of cast aluminum-copper alloy.
Background
The cast aluminum-copper alloy is used as a high-strength aluminum alloy, and is widely applied to the fields of aerospace, automobiles, ships, military industry and the like by virtue of good room temperature performance and high temperature performance.
The cast aluminum-copper alloy has high strength, high modulus and high corrosion resistance, simultaneously has excellent obdurability through heat treatment, can show excellent comprehensive mechanical property, is light in weight, and is an ideal material for realizing the future replacement of forging by casting and steel by aluminum.
However, the following problems are mainly present in the current cast aluminum-copper alloys compared to other series cast aluminum alloys: 1) the solidification mode of casting the aluminum-copper alloy belongs to pasty solidification, because the crystallization temperature range of the alloy is wider, the temperature distribution of a casting is relatively flat, and in the wider solidification range, a solidification area with liquid and solid simultaneously penetrates through the whole section, so that the viscosity of alloy liquid is higher, and the fluidity is poorer. 2) In the solidification process of the aluminum-copper alloy, dendritic crystals continuously grow along a solid-liquid interface, and the growth of secondary dendritic crystal arms hinders the flowing and feeding capacity of aluminum liquid, so that a dendritic crystal structure with larger grain size is generated.
Due to the above factors, the flowability of the cast aluminum-copper alloy is poor, and the defects of cold shut, insufficient casting and the like are easily generated in the casting process, so that the mold filling performance of the aluminum-copper alloy is directly influenced. Especially for complex thin-wall components which are precisely cast, the thin wall part cannot be formed frequently. The above problems seriously hinder the further development of aluminum bronze alloys in the casting field.
The traditional improvement method is to improve the flow property of the aluminum-copper alloy liquid by increasing the pouring temperature. However, high temperature casting often results in coarse structure grains of the casting and reduced casting properties.
In another improvement mode, rare earth elements such as Ce, Nd, Er and the like are singly added to modify the aluminum-copper alloy, and the composition supercooling is generated at the front edge of a solid-liquid interface to refine aluminum-copper alloy grains, so that the fluidity of the aluminum-copper alloy liquid is improved. However, when rare earth is added, the smelting time needs to be prolonged to fully dissolve the rare earth elements, which causes the burning loss of other elements to be increased and also reduces the performance of castings.
The key to the improvement of the fluidity of the cast aluminum-copper alloy is to solve and improve the two problems of the cast aluminum-copper alloy.
Disclosure of Invention
The invention aims to provide a method for improving the fluidity of a cast aluminum-copper alloy, so as to improve the fluidity of the cast aluminum-copper alloy, further improve the casting performance of the cast aluminum-copper alloy and provide technical support for producing a complex thin-wall aluminum-copper alloy casting.
The method for improving the fluidity of the cast aluminum-copper alloy is characterized by adding Al-Ti-C-La-Y intermediate alloy cast ingots with the mass of 0.3-1.5 wt% of the aluminum-copper alloy into the uniformly smelted aluminum-copper alloy, and uniformly smelting to obtain the aluminum-copper alloy melt with improved fluidity.
Wherein the Al-Ti-C-La-Y intermediate alloy comprises 50wt% of Al powder, 40-45 wt% of Ti powder, 3-8 wt% of graphite powder and La2O30.5-1% of powder, Y2O3Mixing and pressing 0.5-1% of powder for forming, performing self-propagating combustion by high-energy laser to obtain a self-propagating product, adding the self-propagating product into molten aluminum, diluting until the content of Ti element is 5-5.3 wt%, and pouring to obtain the intermediate alloy.
The cast aluminum-copper alloy of the present invention may include, but is not limited to, various cast aluminum-copper alloys such as ZL201A, ZL202, ZL203, ZL205A, ZL207, and the like.
The invention uses Al powder, Ti powder, graphite powder and La powder2O3Powder and Y2O3The powder is taken as a raw material, high-energy laser self-propagating high-temperature synthesis is carried out, and pure aluminum dilution is carried out to obtain the high-energy laser self-propagating high-temperature synthesis aluminum-based composite material containing a large amount of Al3Ti, TiC and a small amount of Al3The Al-Ti-C-La-Y intermediate alloy of (La, Y) particles is introduced into the smelted cast aluminum-copper alloy, so that crystal grains can be refined, dendrites can be fused, the crystallization interval of the cast aluminum-copper alloy can be shortened, and the flowing property of the cast aluminum-copper alloy can be improved.
And pouring the uniformly smelted aluminum-copper alloy melt into a concentric triple-spiral fluidity sand mold for fluidity test, and comparing the lengths of the spiral lines to prove that the fluidity of the cast aluminum-copper alloy prepared by the method is improved by more than 30% compared with that of the cast aluminum-copper alloy.
Further, the invention provides a method for more specifically improving the flow property of the cast aluminum-copper alloy.
1) 50wt% of Al powder, 40-45 wt% of Ti powder, 3-8 wt% of graphite powder and La2O30.5-1% of powder, Y2O3And mixing the raw materials in a proportion of 0.5-1%, and performing ball milling and mixing in a vacuum ball milling tank to obtain alloy powder.
2) And carrying out cold press molding on the alloy powder, and carrying out high-energy laser self-propagating reaction in an inert atmosphere at 945-955 ℃ to obtain a self-propagating product.
3) And adding the self-propagating product into molten aluminum until the content of Ti element in the molten aluminum is 5-5.3 wt%, uniformly smelting, cooling to 700-710 ℃, and pouring to prepare an Al-Ti-C-La-Y intermediate alloy ingot.
4) After the aluminum-copper alloy is refined and melted, adding an Al-Ti-C-La-Y intermediate alloy ingot with the mass of 0.3-1.5 wt% of the aluminum-copper alloy under the protection of inert gas, smelting uniformly, and standing to obtain the aluminum-copper alloy melt with improved fluidity.
In the above method of the present invention, it is preferable to use powder raw materials having a particle size of not more than 200 μm for the various raw materials for preparing the Al-Ti-C-La-Y master alloy.
In the method, the ball milling and mixing of the raw materials are specifically (2.0-3.0) x 10-3Pa under vacuum.
More specifically, under the vacuum condition, the raw materials are ball-milled and mixed for 5-6 h at the rotating speed of 230-250 rpm according to the ball-material ratio of 8: 1.
And after the ball milling and mixing are finished, restoring the vacuum ball milling tank to normal pressure, standing for 1-2 h, and then taking out the alloy powder uniformly mixed in the vacuum ball milling tank.
Further, the uniformly mixed alloy powder is subjected to cold press molding by a load of 15-30 kN.
Specifically, the molten aluminum is obtained by completely melting a pure aluminum ingot at 940-960 ℃.
More specifically, in the process of adding the self-propagating product into molten aluminum for smelting, stirring for 1-2 min every 10-15 min until the self-propagating product particles in the aluminum liquid are completely molten, then standing and cooling to 700-710 ℃ of the aluminum liquid, and ensuring that the standing time is not less than 10 min.
Further, the aluminum liquid after standing and cooling is poured into an ingot casting mold preheated to 230-250 ℃ to prepare an Al-Ti-C-La-Y intermediate alloy ingot.
In the method, the refining and melting of the aluminum-copper alloy are carried out at 730-780 ℃, and the refining comprises C2Cl6Degassing and slagging-off treatment, and the temperature of the molten aluminum-copper alloy during degassingThe temperature should not be lower than 730 ℃.
The invention uses Al powder, Ti powder, graphite powder and La powder2O3Powder and Y2O3The powder is used as a raw material, and high-energy laser self-propagating high-temperature synthesis is carried out to obtain the high-performance Al-containing material3Ti, TiC and a small amount of Al3The Al-Ti-C-La-Y intermediate alloy of (La, Y) particles has fast reaction process and high product purity.
In the invention, Al-Ti-C-La-Y intermediate alloy is directly added into aluminum-copper alloy for smelting in inert atmosphere, and the Al contained in the intermediate alloy3The Ti and TiC particles can improve the nucleation rate of the aluminum-copper alloy, crush dendritic crystals, refine grains and form grains with the shape of equiaxed crystals, the refining effect on the aluminum-copper alloy grains is obvious, and the performance of the aluminum-copper alloy is indirectly improved. Furthermore, by adding the rare earth La and the rare earth Y in a compounding way, the super-cooling of the front component of the solid-liquid interface is enhanced, the dendritic crystal is fused, the crystallization interval of the aluminum-copper alloy is shortened, and the pasty solidification interval of the aluminum-copper alloy is reduced, so that the crystallization temperature of the aluminum-copper alloy is increased, and the feeding capacity and the fluidity of the aluminum-copper alloy melt are enhanced.
Drawings
Fig. 1 is a schematic structural view of a concentric triple helix flow sand mold.
FIG. 2 is a scanning electron micrograph of the self-propagating product 50Al-42Ti-7C-0.5La-0.5Y prepared in example 1.
FIG. 3 is a scanning electron micrograph of the Al-5Ti-0.8C-La-Y master alloy prepared in example 1.
FIG. 4 is a drawing of a concentric triple helix casting of aluminum bronze alloy ZL201A and modified aluminum bronze alloy ZL 201A.
FIG. 5 is a scanning electron micrograph of as-cast grains of the aluminum bronze alloy ZL201A and the modified aluminum bronze alloy ZL 201A.
Fig. 6 is a crystallization plot of the aluminum bronze alloy ZL201A and the modified aluminum bronze alloy ZL 201A.
FIG. 7 is a scanning electron micrograph of the self-propagating product 50Al-40Ti-8C-La-Y prepared in example 2.
FIG. 8 is a scanning electron micrograph of the Al-5Ti-C-La-Y master alloy prepared in example 2.
Figure 9 is a drawing of a concentric triple helix casting of aluminum bronze alloy ZL205A and modified aluminum bronze alloy ZL 205A.
FIG. 10 is a scanning electron micrograph of as-cast grains of the aluminum bronze alloy ZL205A and the modified aluminum bronze alloy ZL 205A.
FIG. 11 is a graph of the crystallization curves of the aluminum bronze alloy ZL205A and the modified aluminum bronze alloy ZL 205A.
Detailed Description
The following examples further describe embodiments of the present invention. The following examples are only for more clearly illustrating the technical solutions of the present invention so as to enable those skilled in the art to better understand and utilize the present invention, and do not limit the scope of the present invention. The following examples of the present invention are not intended to be exhaustive or to limit the invention to the precise forms disclosed. Various changes, modifications, substitutions and alterations to these embodiments will be apparent to those skilled in the art without departing from the principles and spirit of this invention.
In the present invention, the terms such as "upper", "lower", "left", "right" and "middle" are used for clarity of description only, and are not used to limit the scope of the present invention, and the relative relationship changes or adjustments may be made without substantial technical changes and modifications.
In the following examples of the present invention, the fluidity of an aluminum-copper alloy melt was measured using a concentric triple helix fluidity sand mold as shown in FIG. 1.
The concentric three-helix fluid sand mold is designed by referring to Zhao Jun et al (Zhao Jun, Chen Guang, Liu Xue Lin. development and application of concentric three-helix alloy fluidity tester [ J ]. proceedings of the institute of Engineers, 1987(03): 51-58.).
The casting sand adopted by the flowing sand mold is resin sand with the granularity not more than 500 mu m, the resin sand, the adhesive, the curing agent and the catalyst are mixed according to the proportion of 100: 1 and then molded, and after the mold is turned over and taken out, the sand mold is dried in the air for 1 day. And (3) uniformly coating the sand mold cavity with a casting alcohol-based coating before pouring, wherein the coating thickness is 0.3-0.5 mm.
The sand mould is provided with distance measuring points, and the distance between the distance measuring points is 50 mm.
Example 1.
Weighing 50g of Al powder, 42g of Ti powder, 7g of graphite powder and La2O3Powder 0.5g and Y2O3And (3) putting 0.5g of powder into a vacuum ball milling tank, putting grinding balls into the vacuum ball milling tank according to the ball-material ratio of 8: 1, setting the rotating speed to be 230rpm, and carrying out ball milling for 5 hours in a vacuum state.
And opening the air valve after the ball milling is finished, standing for 2h, taking out alloy powder, putting the alloy powder into a cold pressing die, and setting the load to be 20kN for cold pressing and molding. Then, in an inert atmosphere, high-energy laser self-propagating combustion is carried out by using laser with the power of 4kW, and 95g of self-propagating product 50Al-42Ti-7C-0.5La-0.5Y is obtained by high-temperature synthesis.
FIG. 2 is an SEM image of a self-propagating product 50Al-42Ti-7C-0.5 La-0.5Y. As can be seen from FIG. 2, there is a dense distribution of Al in the self-propagating product3Ti、Al3(La, Y) and TiC particles.
Crushing the obtained self-propagating product 50Al-42Ti-7C-0.5La-0.5Y by a hydraulic press at the pressure of 1 t.
Weighing 222g of pure aluminum according to the mass ratio of the Ti element in the intermediate alloy being 5%, adding the pure aluminum into a resistance furnace, smelting at 950 ℃, adding 30g of crushed self-propagating product into molten aluminum, stirring for 1min at intervals of 15min until the pure aluminum is completely molten, standing for 15min until the temperature of the aluminum liquid is 710 ℃.
And pouring the molten aluminum into a metal type ingot casting mold preheated to 230 ℃, and cooling to obtain an Al-5Ti-0.8C-La-Y intermediate alloy ingot.
As can be seen more clearly from the SEM image of FIG. 3, the intermediate alloy obtained after dilution of the self-propagating product contains Al uniformly distributed3Ti、Al3(La, Y) and TiC particles.
The aluminum-copper alloy ZL201A is prepared according to the following components and percentage content thereof.
2.4kg of aluminum-copper alloy ZL201A is added into a smelting furnace and heated to 750 ℃ for smelting.
Standing for 10min after the aluminum-copper alloy is completely melted, stirring with a graphite rod, cooling to 730 ℃, and adding 14.4g C2Cl6And refining, degassing and slagging off to obtain refined aluminum-copper alloy melt.
The aluminum-copper alloy melt is heated to 750 ℃ again, 7.2g (0.3wt%) of Al-5Ti-0.8C-La-Y intermediate alloy ingot is added, and argon is introduced at the speed of 1.0L/min for atmosphere protection. Stopping introducing argon after the intermediate alloy is completely melted, standing the aluminum liquid, naturally cooling to 710 ℃, and pouring into the prepared concentric triple-spiral flowing sand mold.
And opening the box after the casting is cooled, taking the length of the three spiral lines, taking the average length of the three spiral lines as the actual flowing length, and repeating the test for three times to ensure the stability of data.
Meanwhile, the fluidity test was performed on the aluminum-copper alloy ZL201A without adding the master alloy.
Fig. 4 shows the concentric triple helix casting of the aluminum bronze alloy ZL201A (a) without addition of master alloy and the modified aluminum bronze alloy ZL201A (b) with addition of master alloy. The test result shows that the flow length of the cast casting of the common aluminum-copper alloy ZL201A at 710 ℃ is only 482mm, while the flow length of the cast casting of the modified aluminum-copper alloy ZL201A added with the intermediate alloy is increased to 652mm, which is increased by 35.2% compared with the flow length without the intermediate alloy, and the flow performance is obviously improved.
FIG. 5 is a graph comparing the grain sizes of the aluminum bronze alloy ZL201A before and after modification. As is apparent from the figure, the ZL201A with the addition of Al-5Ti-0.8C-La-Y master alloy (b) has a significantly finer grain size compared to that before modification (a). The fine crystal grains can improve the fluidity of the melt, so the fluidity of the aluminum-copper alloy ZL201A can be improved by adding 0.3wt% of Al-5Ti-0.8C-La-Y intermediate alloy.
Furthermore, as can be seen from the comparison of the DSC crystallization curves of the aluminum-copper alloy ZL201A and the modified aluminum-copper alloy ZL201A in fig. 6, the crystallization interval of the aluminum-copper alloy ZL201A with the intermediate alloy is shortened by 4 ℃, which is beneficial to melt flow, thereby improving the fluidity of the aluminum-copper alloy ZL 201A.
Example 2.
Weighing 50g of Al powder, 40g of Ti powder, 8g of graphite powder and La2O3Powder 1g and Y2O31g of powder is put into a vacuum ball milling tank, grinding balls are put into the vacuum ball milling tank according to the ball-material ratio of 8: 1, the rotating speed is set to be 250rpm, and the ball milling is carried out for 5 hours in a vacuum state.
And opening the air valve after the ball milling is finished, standing for 2h, taking out alloy powder, putting the alloy powder into a cold pressing die, and setting the load to be 20kN for cold pressing and molding. Then, in an inert atmosphere, high-energy laser self-propagating combustion is carried out by using laser with the power of 4kW, and 97g of self-propagating product 50Al-40Ti-8C-La-Y is obtained through high-temperature synthesis.
FIG. 7 is an SEM image of a self-propagating product 50Al-40 Ti-8C-La-Y. As can be seen from FIG. 7, there is a dense distribution of Al in the self-propagating product3Ti、Al3(La, Y) and TiC particles.
The obtained self-propagating product 50Al-40Ti-8C-La-Y is crushed by a hydraulic press at the pressure of 2 t.
Weighing 350g of pure aluminum according to the mass ratio of Ti element in the intermediate alloy being 5%, adding the pure aluminum into a resistance furnace, smelting at 950 ℃, adding 50g of crushed self-propagating product into molten aluminum, stirring for 1min at intervals of 15min until the pure aluminum is completely molten, standing for 15min until the temperature of the aluminum liquid is 710 ℃.
And pouring the molten aluminum into a metal type ingot casting mold preheated to 230 ℃, and cooling to obtain an Al-5Ti-C-La-Y intermediate alloy ingot.
As can be seen more clearly from the SEM image of FIG. 8, the master alloy obtained after dilution of the self-propagating product contains Al uniformly distributed3Ti、Al3(La, Y) and TiC particles.
The aluminum-copper alloy ZL205A is prepared according to the following components and percentage content thereof.
2.4kg of aluminum-copper alloy ZL205A is added into a smelting furnace and heated to 780 ℃ for smelting.
Standing for 10min after the aluminum-copper alloy is completely melted, stirring with a graphite rod, cooling to 730 ℃, and adding 14.4g C2Cl6And refining, degassing and slagging off to obtain refined aluminum-copper alloy melt.
The furnace temperature of the aluminum-copper alloy melt is increased to 780 ℃ again, 16.8g (0.7wt%) of Al-5Ti-C-La-Y intermediate alloy ingot is added, and argon is introduced at the speed of 1.0L/min for atmosphere protection. Stopping introducing argon after the intermediate alloy is completely melted, standing the aluminum liquid, naturally cooling to 710 ℃, and pouring into the prepared concentric triple-spiral flowing sand mold.
And opening the box after the casting is cooled, taking the length of the three spiral lines, taking the average length of the three spiral lines as the actual flowing length, and repeating the test for three times to ensure the stability of data.
The fluidity test was also performed on the aluminum bronze alloy ZL205A without the addition of the master alloy.
Figure 9 shows a diagram of concentric triple helix castings of the aluminium bronze alloy ZL205A (a) without addition of master alloy and the modified aluminium bronze alloy ZL205A (b) with addition of master alloy. The test result shows that the flow length of a cast part of a common aluminum-copper alloy ZL205A at 710 ℃ is only 596mm, while the flow length of a cast part of a modified aluminum-copper alloy ZL205A added with a master alloy is improved to 915mm, compared with the flow length of the cast part of the modified aluminum-copper alloy ZL205A not added, the flow length is improved by 53.5%, and the flow performance is obviously improved.
FIG. 10 is a graph comparing the grain sizes of the aluminum bronze alloy ZL205A before and after modification. As is evident from the figure, the ZL205A with the addition of Al-5Ti-C-La-Y master alloy (b) is significantly refined compared to the Al-5Ti-C-La-Y master alloy (a) before modification. The fine grains can improve the fluidity of the melt, so the fluidity of the aluminum-copper alloy ZL205A can be improved by adding 0.7wt% of Al-5Ti-C-La-Y intermediate alloy.
Furthermore, as can be seen from the comparison of the DSC crystallization curves of the aluminum-copper alloy ZL205A and the modified aluminum-copper alloy ZL205A in fig. 11, the crystallization interval of the aluminum-copper alloy ZL205A with the intermediate alloy is shortened by 8 ℃, which is favorable for melt flow, thereby improving the fluidity of the aluminum-copper alloy ZL 205A.
Claims (10)
1. An improvementThe method for casting the fluidity of the aluminum-copper alloy comprises the steps of adding Al-Ti-C-La-Y intermediate alloy cast ingots with the mass of 0.3-1.5 wt% of the aluminum-copper alloy into the uniformly smelted aluminum-copper alloy, and uniformly smelting to obtain aluminum-copper alloy melt with improved fluidity; wherein the Al-Ti-C-La-Y intermediate alloy comprises 50wt% of Al powder, 40-45 wt% of Ti powder, 3-8 wt% of graphite powder and La2O30.5 to 1 wt% of powder, Y2O3Mixing and pressing 0.5-1 wt% of powder, performing self-propagating combustion by high-energy laser to obtain a self-propagating product, adding the self-propagating product into molten aluminum, diluting until the content of Ti element is 5-5.3 wt%, and pouring to obtain the intermediate alloy.
2. The method as set forth in claim 1, wherein the aluminum-copper alloy is any one of ZL201A, ZL202, ZL203, ZL205A, and ZL 207.
3. The method of claim 1, comprising:
1) 50wt% of Al powder, 40-45 wt% of Ti powder, 3-8 wt% of graphite powder and La2O30.5 to 1 wt% of powder, Y2O3Mixing the raw materials in a proportion of 0.5-1 wt%, and performing ball milling and mixing in a vacuum ball milling tank to obtain alloy powder;
2) cold-pressing and molding the alloy powder, and performing high-energy laser self-propagating reaction in an inert atmosphere at 945-955 ℃ to obtain a self-propagating product;
3) adding the self-propagating product into molten aluminum until the content of Ti element in the molten aluminum is 5-5.3 wt%, uniformly smelting, cooling to 700-710 ℃, and pouring to prepare an Al-Ti-C-La-Y intermediate alloy ingot;
4) after the aluminum-copper alloy is refined and melted, adding an Al-Ti-C-La-Y intermediate alloy ingot with the mass of 0.3-1.5 wt% of the aluminum-copper alloy under the protection of inert gas, smelting uniformly, and standing to obtain the aluminum-copper alloy melt with improved fluidity.
4. The method as set forth in claim 3, characterized in that said starting material has a particle size of not more than 200 μm.
5. The method of claim 3, wherein the ball milling mixing is at (2.0-3.0) x 10-3And under the vacuum condition of Pa, ball-milling and mixing the raw materials for 5-6 h at the rotating speed of 230-250 rpm according to the ball-material ratio of 8: 1.
6. The method as set forth in claim 3, wherein the alloy powder is cold-pressed under a load of 15 to 30 kN.
7. The method as claimed in claim 3, wherein the molten aluminum is a melt obtained by completely melting a pure aluminum ingot at 940-960 ℃.
8. The method as claimed in claim 3, wherein the self-propagating product is added into the molten aluminum, stirred for 1-2 min every 10-15 min until the self-propagating product particles are completely melted, and then kept standing and cooled to 700-710 ℃ of the aluminum liquid, and the standing time is not less than 10 min.
9. The method as claimed in claim 3, wherein the aluminum liquid after standing and cooling is poured into an ingot casting mold preheated to 230-250 ℃ to prepare an Al-Ti-C-La-Y intermediate alloy ingot.
10. The method as set forth in claim 3, wherein the aluminum bronze alloy is refined and melted at 730 to 780 ℃, and the refining includes C2Cl6Degassing and slagging-off treatment, wherein the temperature of the aluminum-copper alloy melt is not lower than 730 ℃ during degassing.
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| UA96812C2 (en) * | 2010-01-21 | 2011-12-12 | Юлий Викторович Мильман | Aluminium cast alloy containing magnesium and silicon |
| CN101935772B (en) * | 2010-09-26 | 2012-05-30 | 郑州大学 | Method for preparing aluminum titanium carbon rare earth refiner |
| CN110835697B (en) * | 2019-11-29 | 2023-08-01 | 中北大学 | Method for directly preparing aluminum alloy refiner by recycling waste aluminum |
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