CN115233046A - Al-Si-Mg-Fe aluminum alloy with high iron content based on non-heat treatment of secondary aluminum and preparation method thereof - Google Patents
Al-Si-Mg-Fe aluminum alloy with high iron content based on non-heat treatment of secondary aluminum and preparation method thereof Download PDFInfo
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- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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Abstract
The invention provides a non-heat-treatment high-iron-content Al-Si-Mg-Fe aluminum alloy based on secondary aluminum and a preparation method thereof, wherein the aluminum alloy consists of the following components in percentage by mass: fe:0.2-0.8%, si:7.0-10.0%, mg:0.15-0.45%, mn:0.2% -0.8%, cr:0.1-0.3%, cu:0.15-0.7%, zr:0.1-0.3%, la:0.05-0.12%, ce:0.06-0.12%, ti:0.08-0.2%, sr:0.008-0.02% and the balance of aluminum; the method comprises the following steps: pretreating the regenerated aluminum material, and heating and melting to obtain regenerated aluminum liquid; adding preheated raw materials of other elements into the regenerated aluminum liquid according to the raw material proportion, heating and melting, electromagnetically stirring to obtain alloy liquid, keeping the temperature of 740-750 ℃, standing, then cooling, and casting and molding under high pressure to obtain the Al-Si-Mg-Fe aluminum alloy. The Al-Si-Mg-Fe aluminum alloy provided by the invention takes the regenerated aluminum material as the melt, so that the application field of the regenerated aluminum material is expanded, the upper limit of the content of the Fe element in the high-toughness aluminum alloy material is improved, and the strength and the toughness of the product are obviously improved.
Description
Technical Field
The invention relates to the field of preparation of alloy materials, in particular to a preparation method of Al-Si-Mg-Fe aluminum alloy with non-heat treatment and high iron content based on regenerated aluminum (the raw material accounts for 30-80%) and Al-Si-Mg- (0.2% -0.8%) Fe aluminum alloy.
Background
Around the implementation of the targets of carbon peak reaching and carbon neutralization, the recycling of aluminum for steel and casting for forging and the recycling of secondary aluminum resources become the first-choice technology and process approach for realizing the lightweight of new energy automobiles. At present, the existing commercial die-casting aluminum-silicon alloy has the defects of low strength or toughness and the like, and meanwhile, the strength or toughness needs to be improved through T6 heat treatment (solution treatment and aging treatment), which easily causes deformation and surface bubbles of automobile thin-walled parts and increases energy consumption. In order to realize the high strength and toughness of the newly developed high strength and toughness die-casting aluminum-silicon alloy, the content of iron (Fe) needs to be controlled below 0.15%, which limits the application of the regenerated aluminum material in the fields of automobiles and the like. The main reason is that the Fe phase in the existing die-casting aluminum alloy is needle-shaped or blocky, and the elongation of the product is reduced. As is known, high-Fe aluminum alloy is mainly used for high-pressure castings, and the elongation of low-pressure castings and the like is obviously deteriorated (for example, the national standard requirement of Fe content in A356 is controlled within 0.2%), so that the safety requirement of products cannot be met. Therefore, there is a need to develop a non-heat treated self-strengthening high-iron (0.2% or more) aluminum-silicon alloy based on secondary aluminum and having excellent castability and mechanical properties.
Disclosure of Invention
The invention aims to provide a preparation method of Al-Si-Mg- (0.2% -0.8%) Fe aluminum alloy with high strength, toughness and high iron content based on non-heat treatment of regenerated aluminum.
The invention also aims to provide the Al-Si-Mg- (0.2-0.8%) Fe aluminum alloy with high strength, toughness and high iron content, which is prepared by the preparation method.
In order to achieve the purpose, the invention adopts the technical scheme that:
a non-heat treated high iron content Al-Si-Mg-Fe aluminum alloy based on secondary aluminum, the Al-Si-Mg-Fe aluminum alloy consisting of, in mass percent: fe:0.2-0.8%, si:7.0-10.0%, mg:0.15-0.45%, mn:0.2% -0.8%, cr:0.1-0.3%, cu:0.15-0.7%, zr:0.1-0.3%, la:0.05-0.12%, ce:0.06-0.12%, ti:0.08-0.2%, sr:0.008-0.02% and the balance of aluminum; the Al-Si-Mg-Fe aluminum alloy is prepared by the following method: pretreating the regenerated aluminum material, and heating and melting to obtain regenerated aluminum liquid; adding preheated raw materials of other elements into the regenerated aluminum liquid according to the raw material proportion, heating and melting, electromagnetically stirring to obtain alloy liquid, keeping the temperature of 740-750 ℃, standing, cooling, and high-pressure casting and molding to obtain the Al-Si-Mg-Fe aluminum alloy based on the non-heat treatment high-iron content of the regenerated aluminum.
The mass of the regenerated aluminum liquid is 30-80% of the total mass of the final alloy liquid, and preferably 50-80%.
The recycled aluminum material comprises pop cans, sectional materials, aluminum wires, automobile scrap aluminum materials and the like. The mass content of Fe in the regenerated aluminum material is 0.2-1%.
The pretreatment of the regenerated aluminum material comprises sorting, crushing, iron removal, paint removal and the like. As is well known to those skilled in the art.
The regenerated aluminum material is generally heated to 730-740 ℃ for melting, and the regenerated aluminum liquid is obtained after purification treatment and standing.
In the method, the input raw materials are generally preheated to 170-200 ℃.
In the method, after all the input raw materials are melted, scum on the surface is removed, and then electromagnetic stirring is carried out.
The frequency of the electromagnetic stirring is 20Hz-40Hz, and the time of the electromagnetic stirring is generally 5-10 minutes
The die casting temperature of the high-pressure casting is generally 680-710 ℃.
The high-pressure casting process method comprises the following steps: and cooling the alloy liquid after purification treatment to 680-710 ℃ for die-casting molding. The high-pressure casting is vacuum die casting, and the vacuum pressure in the cavity is less than 100mbr so as to reduce the influence of air holes in the casting on the performance of the casting.
The Al-Si-Mg-Fe aluminum alloy preferably comprises the following components in percentage by mass: fe:0.25-0.8%, si:8.0-9.0%, mg:0.3-0.4%, mn:0.6% -0.8%, cr:0.2-0.3%, cu:0.5-0.7%, zr:0.1-0.2%, la:0.05-0.1%, ce:0.08-0.12%, ti:0.1-0.2%, sr:0.01-0.02% and the balance of aluminum.
When the casting product requires to be subjected to related heat treatment to improve the elongation or strength, the die-casting product obtained by high-pressure casting can be subjected to annealing treatment and post-aging treatment to improve the elongation of the die-casting product; or the die-casting product is subjected to simple aging treatment, so that the strength of the die-casting product is improved.
The annealing treatment is carried out by keeping the temperature at 300-350 ℃ for 120-180 minutes.
The post-aging treatment is to preserve heat for 120 to 240 minutes at 160 to 180 ℃.
The simple aging treatment is to keep the temperature at 160-180 ℃ for 60-180 minutes.
When the iron content of the Al-Si-Mg-Fe aluminum alloy is more than or equal to 0.2% and less than 0.3%, the yield strength of the Al-Si-Mg-Fe aluminum alloy at room temperature is more than or equal to 180MPa, the tensile strength is more than or equal to 290MPa, the elongation is more than or equal to 10%, the yield strength at 200 ℃ is more than or equal to 160MPa, the tensile strength is more than or equal to 270MPa, and the elongation is more than or equal to 10%; the yield strength of the die-casting product cast under high pressure is more than or equal to 175MPa at room temperature, the tensile strength is more than or equal to 280MPa, and the elongation is more than or equal to 9 percent;
when Fe is more than or equal to 0.2% and less than or equal to 0.8%, the yield strength of the Al-Si-Mg-Fe aluminum alloy at room temperature is more than or equal to 170MPa, the tensile strength is more than or equal to 280MPa, the elongation is more than or equal to 8%, the yield strength at 200 ℃ is more than or equal to 150MPa, the tensile strength is more than or equal to 240MPa, and the elongation is more than or equal to 9%; the die-casting product cast under high pressure has yield strength not less than 170MPa, tensile strength not less than 270MPa and elongation not less than 7.5% at room temperature.
The invention also provides a preparation method of the Al-Si-Mg-Fe aluminum alloy with high iron content based on the non-heat treatment of the secondary aluminum, which comprises the following steps:
(1) Pretreating the regenerated aluminum material, and heating to 730-740 ℃ for melting to obtain regenerated aluminum liquid;
(2) Adding pure aluminum ingots, pure magnesium ingots, al-Si, al-Mn, al-Cr and Al-Cu intermediate alloys preheated to 170-200 ℃ into the 730-740 ℃ regenerated aluminum liquid according to the raw material ratio, after all the materials are melted, electromagnetically stirring the materials, keeping the temperature of the materials at 740-750 ℃ for 15-20 minutes, and then heating the materials to 750-760 ℃;
(3) According to the raw material ratio, preheated Al-La, al-Ce, al-Zr and Al-Ti intermediate alloy are put into the molten aluminum, and after all the intermediate alloy is melted, the intermediate alloy is electromagnetically stirred and then is kept at the temperature of 750-760 ℃ for 15-20 minutes;
(4) And (3) cooling the alloy liquid in the step (3) to 740-750 ℃, refining for 12-15 minutes, adding preheated Al-Sr intermediate alloy according to the raw material proportion, electromagnetically stirring, removing floating slag, standing for 20-25 minutes, cooling the alloy liquid to 680-710 ℃, and carrying out high-pressure casting molding to obtain a non-heat-treated high-iron-content Al-Si-Mg-Fe aluminum alloy die-cast product based on the regenerated aluminum.
In the method, the mass of the regenerated aluminum liquid is 30-80% of the total mass of the final alloy liquid, and preferably 50-80%.
And during feeding, calculating the feeding weight of the pure aluminum ingot, the pure magnesium ingot and the intermediate alloy according to the estimated total mass of the alloy, the set content ratio of each element in the Al-Si-Mg-Fe aluminum alloy and the percentage content of each element in the intermediate alloy. This is a method well known to those skilled in the art.
Further, in the step (1), the recycled aluminum material comprises pop cans, profiles, aluminum wires, automobile scrap aluminum materials and the like. The mass content of Fe in the regenerated aluminum material is 0.2-1%.
The pretreatment of the regenerated aluminum material comprises sorting, crushing, iron removal, paint removal and the like.
In the step (1), the regenerated aluminum material is generally heated to 730-740 ℃ for melting, and the regenerated aluminum liquid is obtained after purification treatment and standing.
In the step (2), the charged raw materials are generally preheated to 170-200 ℃.
In the step (2), after all the charged raw materials are melted, scum on the surface is removed, and then electromagnetic stirring is carried out.
In the step (3), the charged raw materials are generally preheated to 170-200 ℃.
In the step (3), after all the charged raw materials are melted, scum on the surface is removed, and then electromagnetic stirring is carried out.
In the step (4), the added Al-Sr intermediate alloy is generally preheated to 170-200 ℃.
In the step (4), the casting molding process is high-pressure casting, and the die-casting temperature is 680-710 ℃.
The high-pressure casting process method comprises the following steps: and cooling the alloy liquid after purification treatment to 680-710 ℃ for die-casting molding. The high-pressure casting is vacuum die casting, and the vacuum pressure in the cavity is less than 100mbr so as to reduce the influence of air holes in the casting on the performance of the casting.
In the invention, the frequency of electromagnetic stirring is 20Hz-40Hz. In the step (2), the step (3) and the step (4), the electromagnetic stirring time is generally 5 to 10 minutes.
When the casting product requires related heat treatment to improve the elongation or strength, the method can further comprise the step (5), the prepared die-casting product is subjected to annealing treatment and post-aging treatment, or the die-casting product is subjected to simple aging treatment;
the annealing treatment is carried out by keeping the temperature at 300-350 ℃ for 120-180 minutes.
The post-aging treatment is to preserve heat for 120 to 240 minutes at 160 to 180 ℃.
The simple aging treatment is to keep the temperature at 160-180 ℃ for 60-180 minutes.
The annealing treatment and the post-aging treatment can improve the elongation of the die cast product.
The strength of the die-casting product can be improved by simple aging treatment.
The invention takes the secondary aluminum, the primary aluminum or the mixture of the secondary aluminum and the primary aluminum as the melt, not only can refine alpha-Al and Mg by strictly controlling the molar ratio of alloy elements and combining the strong shearing action (electromagnetic stirring is 20Hz-40 Hz) of an energy field 2 Si particles, al 2 Cu is equal, so that the Cu is dispersed and distributed, the shape of the Fe phase can be changed (long needle-shaped or blocky Al (FeMnCr) Si is changed into dispersed and distributed Al (MnFeCr) Cu nano-scale spherical particles), the strength and the elongation of the aluminum-silicon alloy (especially the high-Fe aluminum-silicon alloy taking the secondary aluminum as the raw material) are obviously improved, and the aluminum-silicon alloy is more suitable for the field of aviation or automobile manufacturing.
The invention also provides the Al-Si-Mg- (0.2-0.8%) Fe aluminum alloy prepared by the preparation process, which not only has high strength and high toughness at room temperature and high temperature, but also can adopt a regenerated aluminum material with higher Fe content as a main body and can realize high dispersion strengthening effect without heat treatment (such as T6 treatment, solid solution treatment and aging treatment), thereby reducing the adverse effect of acicular or blocky Fe on the elongation of the alloy, avoiding the problems of deformation of a thin-wall casting and bubbles on the surface of the casting in the high-temperature solid solution treatment process, saving carbon emission and production cost, and having extremely high market application value.
In one embodiment of the invention, the yield strength of the prepared Al-Si-Mg- (0.2% -0.3%) Fe aluminum alloy at room temperature is more than or equal to 180MPa, the tensile strength is more than or equal to 310MPa, and the elongation is more than or equal to 10%; the yield strength at 200 ℃ is more than or equal to 170MPa, the tensile strength is more than or equal to 280MPa, and the elongation is more than or equal to 10%. In another embodiment of the invention, the yield strength of the prepared Al-Si-Mg- (0.3% -0.8%) Fe aluminum alloy at room temperature is more than or equal to 175MPa, the tensile strength is more than or equal to 295MPa, and the elongation is more than or equal to 9%; the yield strength at 200 ℃ is more than or equal to 160MPa, the tensile strength is more than or equal to 260MPa, and the elongation is more than or equal to 9%. The comprehensive performance of the non-heat-treated aluminum-silicon alloy prepared by the invention is higher than that of the die-casting aluminum alloy materials (such as ADC12 and AlSi9Cu 3) commercially available in the market at present, and is close to that of the current non-heat-treated low-Fe (0.15%) die-casting aluminum alloy materials (such as JDA1 of Shanghai university of transportation, but the elongation rate is obviously reduced when the Fe content in the materials exceeds 0.15). The tensile strength of the material after heat treatment is improved, but the elongation is reduced.
In one embodiment of the invention, when Fe is less than 0.3%, the yield strength of the product cast under high pressure (namely vacuum die-casting) at room temperature is more than or equal to 175MPa, the tensile strength is more than or equal to 290MPa, and the elongation is more than or equal to 9%; when Fe is more than or equal to 0.3 percent, the yield strength of the high-pressure cast product at room temperature is more than or equal to 170MPa, the tensile strength is more than or equal to 275MPa, and the elongation is more than or equal to 8 percent.
In one embodiment of the invention, when the casting product requires the related heat treatment to improve the elongation or strength, in order to prevent the casting deformation and surface bubbles during the high-temperature solid solution (not less than 450 ℃) treatment, the high-pressure casting product can adopt the annealing treatment (namely, the heat preservation is carried out for 120 to 180 minutes at 300 to 350 ℃) followed by the aging treatment (namely, the heat preservation is carried out for 120 to 240 minutes at 160 to 180 ℃) and the simple aging treatment (namely, the heat preservation is carried out for 60 to 180 minutes at 160 to 180 ℃). After the prepared Al-Si-Mg- (0.2% -0.3%) Fe aluminum alloy is subjected to annealing treatment and aging treatment, the yield strength at room temperature is more than or equal to 140MPa, the tensile strength is more than or equal to 230MPa, and the elongation is more than or equal to 15-18%; the yield strength of the prepared Al-Si-Mg- (0.2-0.3%) Fe aluminum alloy at room temperature after pure aging treatment is not less than 195MPa, the tensile strength is not less than 330MPa, and the elongation is not less than 9%.
In one embodiment of the invention, after the prepared Al-Si-Mg- (0.3% -0.8%) Fe aluminum alloy is subjected to annealing treatment and aging treatment, the yield strength at room temperature is more than or equal to 130MPa, the tensile strength is more than or equal to 215MPa, and the elongation is more than or equal to 14-16%; the yield strength of the prepared Al-Si-Mg- (0.3% -0.8%) Fe aluminum alloy at room temperature after pure aging treatment is more than or equal to 185MPa, the tensile strength is more than or equal to 305MPa, and the elongation is more than or equal to 8%.
The invention takes the secondary aluminum as raw material (0.2-0.8 percent of Fe, the secondary material accounts for 30-80 percent of the alloy liquid), and can lead the aluminum-silicon alloy to realize stronger dispersion strengthening effect without heat treatment by reasonably adjusting the molar fraction ratio of elements and combining the shearing action of an energy field, and can directly obtain high-Fe precision castings with excellent comprehensive mechanical property by a high-pressure casting mode.
On the premise of ensuring the casting performance of the aluminum-silicon alloy, the invention takes a regenerated aluminum material as a main body, and can not only refine the structure, but also promote the Fe-rich phase to be converted from a long needle-shaped or block-shaped phase Al (MnFeCr) Si (see figure 9, the diameter is about 2 mu m-10 mu m, the molar ratio of the elements Mn: fe: cr: si is (14-23): 3-4): 0.3-1): 17-21) into spheroidized nano-particle phase Al (MnFeCr) Cu (see figure 6, the diameter is about 0.5 mu m-2 mu m, and the molar ratio of the elements Mn: fe: cr: cu in the particle phase is (11-13): 7-9): 5-7): 0.4-1.2) by adjusting the molar fraction ratio of alloy elements and combining the shearing action of an energy field. The nano-particle Fe phase can reduce the adverse effect of needle-shaped or block-shaped Fe on the plasticity of the Al-Si-Mg alloy with high iron content, and can play a better role in dispersion strengthening and improve the strength of the Al-Si-Mg alloy with high iron content, thereby expanding the application of the secondary aluminum in high-strength and high-toughness die-casting aluminum alloy.
The invention has the following beneficial effects:
(1) The regenerated aluminum material is used as a melt, so that the carbon emission and the production cost of the aluminum-silicon alloy material are reduced, and the application of the regenerated aluminum material in the fields of high-strength and high-toughness aluminum alloy materials, automobiles and aerospace is expanded;
(2) The molar fraction ratio of La, ce, ti and Zr elements to Fe, cr and Mn elements is optimized, and the ratio mode can obviously improve the ratio of Fe-rich phase and Mg 2 Si phase, al 2 The refining effects of the Cu phase and the alpha-Al phase particularly promote the acicular or blocky Fe phase (see figures 8 and 9) influencing the elongation of the aluminum alloy material to be changed into dispersed and distributed fine spherical particles (see figures 5, 6 and 7), and a large amount of new Al (MnFeCr) Cu nano-scale particle strengthening phase and a small amount of blocky Al (TiZr) FeCu phase (the molar ratio of elements Ti: zr: cu: fe in the blocky phase is (8-12): (7-9): (5-7): (0.4-1.2)) are formed, so that the strength and the toughness of the aluminum-silicon alloy are obviously improved, the elongation is greatly improved compared with the prior art, and the influence of a heat treatment link on energy consumption, deformation of a thin-wall part and surface quality (reduction of foaming on the surface of a casting) is reduced.
(3) The upper limit of the content of the Fe element in the high-toughness aluminum alloy material is improved (from less than 0.15% to 0.2% -0.8%), the production cost and the process control cost are reduced, and the continuous large-scale production can be realized, and the high-toughness aluminum alloy material is applied to the fields of automobiles, aerospace and the like in a large scale.
Drawings
Fig. 1 is a process flow diagram of a preparation method of example 1 of the present invention.
Fig. 2 is a process flow diagram of a preparation method of example 2 of the present invention.
Fig. 3 is a process flow diagram of a preparation method of comparative example 1 of the present invention.
Fig. 4 is a process flow diagram of a preparation method of comparative example 2 of the present invention.
FIG. 5 is a 1000X SEM photograph of the Al-Si-Mg- (0.3% -0.8%) Fe aluminum alloy of example 2 of the present invention.
FIG. 6 is a 5000X SEM photograph of the Al-Si-Mg- (0.3% -0.8%) Fe aluminum alloy of example 2 of the present invention.
FIG. 7 is a TEM photograph of Al-Si-Mg- (0.3% -0.8%) Fe aluminum alloy nano-scale Fe phase particles of example 2 of the present invention.
FIG. 8 is an SEM photograph of 1000X of the Al-Si-Mg- (0.3% to 0.8%) Fe aluminum alloy of comparative example 2.
FIG. 9 is a SEM photograph of 5000X of the Al-Si-Mg- (0.3% to 0.8%) Fe aluminum alloy of comparative example 2.
Detailed Description
In order that the above objects, features and advantages of the present invention can be more clearly understood, a more particular description of the invention will be rendered by reference to the appended drawings. It should be noted that the embodiments and features of the embodiments of the present application may be combined with each other without conflict.
In the following description, numerous specific details are set forth in order to provide a thorough understanding of the present invention, however, the present invention may be practiced in other ways than those specifically described herein, and thus the scope of the present invention is not limited by the specific embodiments disclosed below.
Example 1
As shown in FIG. 1, the preparation method of the non-heat-treated Al-Si-Mg- (0.2-0.3) Fe aluminum alloy based on the regenerated aluminum (50%) and the original aluminum (50%) specifically comprises the following steps: preparing target components of the alloy according to mass percentage, namely: 8% Si,0.4% Mg,0.25% Fe,0.8% Mn,0.25% Cr,0.15% Ti,0.15% Zr,0.05% La,0.1% Ce,0.01% Sr and 0.5% Cu, the balance Al and unavoidable impurity elements.
(1) Putting the sorted pop can (with Fe content of about 0.4-0.45% after magnetic separation) and 600kg of the preheated pop can (with burning loss considered and yield of about 82%) into a resistance furnace, heating to 730-740 ℃, stirring and sampling from a position 20cm below the liquid level of the melt by using a spoon after complete melting, and testing alloy components by mass percent: 0.42% Fe, 0.63% Si, 0.13% Cu,0.72% Mn,0.73% Mg,0.02% Cr and 0.02% Ti, the balance being Al and unavoidable impurity elements, to obtain 500kg of regenerated aluminum liquid;
(2) According to the requirements of the current alloy components, adding pure aluminum ingots (157 kg, containing 0.08 percent of Fe) preheated to 160-170 ℃, pure magnesium ingots (0.5 kg), al-30Si (256 kg), al-10Mn (44 kg), al-30Cr (8 kg) and Al-30Cu (14.5 kg) intermediate alloys into the aluminum liquid at the temperature of 730-740 ℃, electromagnetically stirring (30 Hz) for 8 minutes, then preserving the heat at the temperature of 740-750 ℃ for 20 minutes and raising the temperature to 760 ℃;
(3) Adding preheated Al-30La (1.7 kg), al-30Ce (3.3 kg), al-30Zr (5 kg) and Al-15Ti (9.3 kg) intermediate alloy into the molten aluminum, after all the intermediate alloy is melted, electromagnetically stirring (30 Hz) for 8 minutes, and then preserving heat at 760 ℃ for 20 minutes;
(4) Cooling the alloy liquid to 740-750 ℃, refining for 12 minutes, adding preheated Al-10Sr (1 kg) intermediate alloy, electromagnetically stirring (30 Hz) for 8 minutes, removing floating slag, standing for 20 minutes, cooling the alloy liquid to 680-710 ℃, and performing die-casting molding.
The Al-Si-Mg-0.25% Fe aluminum alloy prepared in this example was tested according to ASTM B557-06 to prepare a die-cast test round bar (diameter 6.4mm, gauge length 64 mm), yield strength at room temperature of 180MPa or more, tensile strength of 310MPa or more, and elongation of 10% or more; the yield strength at 200 ℃ is more than or equal to 170MPa, the tensile strength is more than or equal to 280MPa, and the elongation is more than or equal to 10 percent; the die-casting product is directly subjected to body sampling test, the yield strength at room temperature is more than or equal to 175MPa, the tensile strength is more than or equal to 280MPa, and the elongation is more than or equal to 9%.
After the Al-Si-Mg-0.25% Fe aluminum alloy die-casting test round bar prepared in the embodiment is subjected to annealing treatment (namely, heat preservation at 330 ℃ for 120 minutes) and aging treatment (namely, heat preservation at 180 ℃ for 120 minutes), the yield strength at room temperature is more than or equal to 140MPa, the tensile strength is more than or equal to 230MPa, and the elongation is more than or equal to 15-18%; 0.25 percent of the prepared Al-Si-Mg-Fe aluminum alloy die-casting test round bar has the yield strength of more than or equal to 195MPa, the tensile strength of more than or equal to 330MPa and the elongation of more than or equal to 9 percent after the aging treatment (namely, the heat preservation is carried out for 120 minutes at 180 ℃).
Example 2
As shown in FIG. 2, the preparation method of the non-heat-treated Al-Si-Mg- (0.3-0.8) Fe aluminum alloy based on the secondary aluminum (55%) and the primary aluminum (45%) specifically comprises the following steps: preparing target components of the alloy according to mass percentage, namely: 8% Si,0.4% Mg,0.5% Fe,0.8% Mn,0.25% Cr,0.15% Ti,0.15% Zr,0.05% La,0.1% Ce,0.01% Sr and 0.5% Cu, the balance Al and unavoidable impurity elements.
(1) Placing unsorted (Fe content in the pop can is about 0.79-0.84% after magnetic separation) and 670kg of pop can after preheating treatment (considering burning loss and yield is about 82%) into a resistance furnace, heating to 730-740 ℃, stirring and sampling from a position 20cm below the liquid level of the melt by using a spoon after complete melting, and testing alloy components by mass percent: 0.82% Fe, 0.71% Si, 0.15% Cu,0.74% Mn,0.63% Mg,0.023% Cr and 0.018% Ti, the balance being Al and unavoidable impurity elements, to prepare 550kg of regenerated aluminum liquid;
(2) According to the requirements of the current alloy components, adding pure aluminum ingots (136 kg, containing 0.11 percent of Fe) preheated to 160-170 ℃, pure magnesium ingots (0.15 kg), al-30Si (253 kg), al-10Mn (39.3 kg), al-30Cr (7.9 kg) and Al-30Cu (13.9 kg) intermediate alloys into the aluminum liquid at the temperature of 730-740 ℃, after all the pure aluminum ingots are melted, electromagnetically stirring (30 Hz) for 8 minutes, keeping the temperature at the temperature of 740-750 ℃ for 20 minutes and raising the temperature to 760 ℃;
(3) Adding preheated Al-30La (1.7 kg), al-30Ce (3.3 kg), al-30Zr (5 kg) and Al-15Ti (9.3 kg) intermediate alloy into the molten aluminum, after all the intermediate alloy is melted, electromagnetically stirring (30 Hz) for 8 minutes, and then preserving heat at 760 ℃ for 20 minutes;
(4) Cooling the alloy liquid to 740-750 ℃, refining for 12 minutes, adding preheated Al-10Sr (1 kg) intermediate alloy, electromagnetically stirring (30 Hz) for 8 minutes, removing floating slag, standing for 20 minutes, cooling the alloy liquid to 680-710 ℃, and performing die-casting molding.
The Al-Si-Mg-0.5% Fe aluminum alloy die-casting test round bar prepared by the embodiment has the yield strength of more than or equal to 175MPa, the tensile strength of more than or equal to 295MPa and the elongation of more than or equal to 9% at room temperature; the yield strength at 200 ℃ is more than or equal to 160MPa, the tensile strength is more than or equal to 260MPa, and the elongation is more than or equal to 9 percent; the yield strength of the die-casting product at room temperature is more than or equal to 170MPa, the tensile strength is more than or equal to 275MPa, and the elongation is more than or equal to 8 percent.
After the Al-Si-Mg-0.5% Fe aluminum alloy die-casting test round bar prepared in the embodiment is subjected to annealing treatment (namely, heat preservation at 330 ℃ for 120 minutes) and aging treatment (namely, heat preservation at 180 ℃ for 120 minutes), the yield strength at room temperature is more than or equal to 130MPa, the tensile strength is more than or equal to 215MPa, and the elongation is more than or equal to 14-16%; the prepared Al-Si-Mg-0.5 percent Fe aluminum alloy die-casting test round bar has the yield strength of more than or equal to 185MPa, the tensile strength of more than or equal to 305MPa and the elongation of more than or equal to 8 percent after the aging treatment (namely, the heat preservation is carried out for 120 minutes at 180 ℃).
Taking example 2 as an example, FIGS. 5 to 7 are photographs of the microstructure of Al-Si-Mg- (0.3% -0.8%) Fe aluminum alloy prepared by the present invention. Obviously, the aluminum-silicon alloy prepared by the invention has obviously refined structure, fe phase and Mg 2 Si phase, al 2 The Cu phase and α -Al phases are equally finer and more dispersed, while some spheroidized nanoscale Al (MnFeCr) Cu phase particles appear in the structure (see white particles in fig. 6 and 7). The dispersed phase particles can not only improve the strength of the aluminum-silicon alloy, but also obviously improve the elongation of the high-Fe aluminum-silicon alloy.
Comparative example 1
As shown in FIG. 3, the preparation method of the non-heat-treated Al-Si-Mg- (0.2-0.3) Fe aluminum alloy based on the recycled aluminum (50%) and the virgin aluminum (50%) provided by the invention specifically comprises the following steps: preparing target components of the alloy according to mass percentage, namely: 8% Si,0.4% Mg,0.25% Fe,0.5% Mn,0.25% Cr,0.15% Ti,0.01% Sr and 0.5% Cu, the balance being Al and unavoidable impurity elements.
(1) Putting 600kg of sorted pop cans (considering burning loss and yield of about 82%) and preheated pop cans (the Fe content in the pop cans is about 0.4-0.45% after magnetic separation) into a resistance furnace, heating to 730-740 ℃, stirring and sampling from a position 20cm below the liquid level of a melt by using a spoon after complete melting, and testing alloy components to prepare 500kg of regenerated aluminum liquid;
(2) According to the requirements of the current alloy components, adding pure aluminum ingots, pure magnesium ingots, al-30Si, al-10Mn, al-30Cr and Al-30Cu intermediate alloys preheated to 160-170 ℃ into aluminum liquid at 730-740 ℃, after all the intermediate alloys are melted, manually stirring for 8 minutes, keeping the temperature at 740-750 ℃ for 20 minutes, and heating to 750-760 ℃;
(3) Adding preheated Al-15Ti intermediate alloy into the molten aluminum, after the intermediate alloy is completely melted, manually stirring the intermediate alloy for 8 minutes, and then preserving the heat of the intermediate alloy for 20 minutes at the temperature of between 750 and 760 ℃;
(4) Cooling the alloy liquid to 740-750 ℃, refining for 12 minutes, adding preheated Al-10Sr (1 kg) intermediate alloy, manually stirring for 8 minutes, removing floating slag, standing for 20 minutes, cooling the alloy liquid to 680-710 ℃, and performing die-casting molding.
Compared with the example 1, the content of Mn element is reduced without adding Zr, la and Ce elements, and the yield strength of the prepared Al-Si-Mg-0.25% Fe aluminum alloy die-casting test round bar at room temperature is not less than 165MPa, the tensile strength is not less than 275MPa, and the elongation is not less than 7.5% by adopting manual stirring; the yield strength at 200 ℃ is more than or equal to 150MPa, the tensile strength is more than or equal to 240MPa, and the elongation is more than or equal to 9 percent; the yield strength of the die-casting product at room temperature is more than or equal to 160MPa, the tensile strength is more than or equal to 265MPa, and the elongation is more than or equal to 7 percent.
Comparative example 2
As shown in FIG. 4, the method for preparing non-heat-treated Al-Si-Mg- (0.3-0.8) Fe aluminum alloy based on recycled aluminum (55%) and virgin aluminum (45%) provided by the invention specifically comprises the following steps: preparing target components of the alloy according to mass percentage, namely: 8% Si,0.4% Mg,0.5% Fe,0.5% Mn,0.25% Cr,0.15% Ti,0.01% Sr and 0.5% Cu, the balance being Al and unavoidable impurity elements.
(1) Placing unsorted (the Fe content in the pop can which is not subjected to magnetic separation is about 0.79-0.84%) and 670kg of pop can which is subjected to preheating treatment (the yield is about 82% in consideration of burning loss) into a resistance furnace, heating to 730-740 ℃, stirring and sampling from a position 20cm below the liquid level of the melt by using a spoon after complete melting, and testing alloy components to prepare 550kg of regenerated aluminum liquid;
(2) According to the requirements of the current alloy components, adding pure aluminum ingots, pure magnesium ingots, al-30Si, al-10Mn, al-30Cr and Al-30Cu intermediate alloys preheated to 160-170 ℃ into aluminum liquid at 730-740 ℃, after all the intermediate alloys are melted, manually stirring for 8 minutes, keeping the temperature at 740-750 ℃ for 20 minutes, and heating to 750-760 ℃;
(3) Adding preheated Al-15Ti intermediate alloy into the molten aluminum, after the intermediate alloy is completely melted, manually stirring the intermediate alloy for 8 minutes, and then preserving the heat of the intermediate alloy for 20 minutes at the temperature of between 750 and 760 ℃;
(4) Cooling the alloy liquid to 740-750 ℃, refining for 12 minutes, adding preheated Al-10Sr (1 kg) intermediate alloy, manually stirring for 8 minutes, removing floating slag, standing for 20 minutes, cooling the alloy liquid to 680-710 ℃, and performing die-casting molding.
Compared with the example 2, the content of Mn element is reduced without adding Zr, la and Ce elements, and the prepared Al-Si-Mg-0.5% Fe aluminum alloy die-casting test round bar has the yield strength of more than or equal to 160MPa, the tensile strength of more than or equal to 260MPa and the elongation of more than or equal to 6 percent by adopting manual stirring; the yield strength at 200 ℃ is more than or equal to 150MPa, the tensile strength is more than or equal to 245MPa, and the elongation is more than or equal to 7.5%; the yield strength of the die-casting product at room temperature is more than or equal to 155MPa, the tensile strength is more than or equal to 255MPa, and the elongation is more than or equal to 5.5%. In contrast to the results of example 2, the strength and toughness were significantly reduced.
FIGS. 8 to 9 are photographs of the microstructure of Al-Si-Mg-0.5% Fe aluminum alloy prepared in comparative example 2. It is apparent that when the composition of elements and the manufacturing process are changed, for example, the Zr, la and Ce elements are not added, the content of Mn is changed, and the electromagnetic stirring is not used, the Fe-rich phase in the aluminum-silicon alloy prepared in comparative example 2 is a bulk Al (MnFeCr) Si phase (see fig. 9, diameter about 2 μm to 10 μm), and the nano-sized Al (MnFeCr) Cu phase particles are not formed in the structure. The block-shaped Fe phase particles can not play a good dispersion strengthening effect, but easily deteriorate the elongation of the high-Fe aluminum-silicon alloy, and limit the application of the high-Fe aluminum-silicon alloy in automobiles and aerospace.
In the description herein, the terms "one embodiment," "some embodiments," and the like, describe or imply that a particular feature, structure, material, or characteristic described in connection with the embodiment or example is included in at least one embodiment or example of the invention. In this specification, the schematic representations of the terms used above do not necessarily refer to the same embodiment or example. Furthermore, the particular features, structures, materials, or characteristics described may be combined in any suitable manner in any one or more embodiments or examples.
The above description is only an embodiment of the present invention, and not intended to limit the scope of the present invention, and all modifications of equivalent structures and equivalent processes performed by the present invention or directly or indirectly applied to other related technical fields are included in the scope of the present invention.
Claims (10)
1. A non-heat treated high iron content Al-Si-Mg-Fe aluminum alloy based on secondary aluminum, characterized in that the Al-Si-Mg-Fe aluminum alloy consists of the following components in mass percent: fe:0.2-0.8%, si:7.0-10.0%, mg:0.15-0.45%, mn:0.2% -0.8%, cr:0.1-0.3%, cu:0.15-0.7%, zr:0.1-0.3%, la:0.05-0.12%, ce:0.06-0.12%, ti:0.08-0.2%, sr:0.008-0.02% and the balance of aluminum; the Al-Si-Mg-Fe aluminum alloy is prepared by the following method: pretreating the regenerated aluminum material, and heating and melting to obtain regenerated aluminum liquid; adding preheated raw materials of other elements into the regenerated aluminum liquid according to the raw material proportion, heating and melting, electromagnetically stirring to obtain alloy liquid, keeping the temperature of 740-750 ℃, standing, cooling, and high-pressure casting and molding to obtain the Al-Si-Mg-Fe aluminum alloy based on the non-heat treatment high-iron content of the regenerated aluminum.
2. The Al-Si-Mg-Fe aluminum alloy with non-heat treated high iron content based on secondary aluminum as claimed in claim 1, wherein the mass of the secondary aluminum liquid is 30-80% of the total mass of the final alloy liquid.
3. The Al-Si-Mg-Fe aluminum alloy with non-heat treatment and high iron content based on recycled aluminum as claimed in claim 1, wherein the recycled aluminum material comprises pop cans, section bars, aluminum wires or automobile scrap aluminum materials, and the mass content of Fe in the recycled aluminum material is 0.2-1%.
4. The secondary aluminum-based, non-heat treated, high iron content Al-Si-Mg-Fe aluminum alloy of claim 1, wherein said Al-Si-Mg-Fe aluminum alloy is comprised of, in mass percent: fe:0.25-0.8%, si:8.0-9.0%, mg:0.3-0.4%, mn:0.6% -0.8%, cr:0.2-0.3%, cu:0.5-0.7%, zr:0.1-0.2%, la:0.05-0.1%, ce:0.08-0.12%, ti:0.1-0.2%, sr:0.01-0.02% and the balance of aluminum.
5. Method for the preparation of a non-heat treated high iron content Al-Si-Mg-Fe aluminium alloy based on secondary aluminium according to any one of claims 1 to 4, characterised in that it comprises the following steps:
(1) Pretreating the regenerated aluminum material, and heating to 730-740 ℃ for melting to obtain regenerated aluminum liquid;
(2) Adding preheated pure aluminum ingot, pure magnesium ingot, al-Si, al-Mn, al-Cr and Al-Cu intermediate alloy into the regenerated aluminum liquid at the temperature of 730-740 ℃ according to the raw material ratio, after all the pure aluminum ingot, the pure magnesium ingot, the Al-Si, the Al-Mn, the Al-Cr and the Al-Cu intermediate alloy are melted, after electromagnetic stirring, keeping the temperature at the temperature of 740-750 ℃ for 15-20 minutes, and then heating to the temperature of 750-760 ℃;
(3) According to the raw material ratio, preheated Al-La, al-Ce, al-Zr and Al-Ti intermediate alloy are put into the molten aluminum, and after all the intermediate alloy is melted, the intermediate alloy is electromagnetically stirred and then is kept at the temperature of 750-760 ℃ for 15-20 minutes;
(4) And (3) cooling the alloy liquid in the step (3) to 740-750 ℃, refining for 12-15 minutes, adding preheated Al-Sr intermediate alloy according to the raw material proportion, electromagnetically stirring, removing floating slag, standing for 20-25 minutes, cooling the alloy liquid to 680-710 ℃, and carrying out high-pressure casting molding to obtain a non-heat-treated high-iron-content Al-Si-Mg-Fe aluminum alloy die-cast product based on the regenerated aluminum.
6. The method according to claim 4, wherein in the step (2), the step (3) and the step (4), the frequency of the electromagnetic stirring is 20Hz-40Hz; the electromagnetic stirring time is 5-10 minutes.
7. The method according to claim 4, wherein in the step (4), the casting and forming process is high-pressure casting, the casting temperature is 680-710 ℃, the high-pressure casting is vacuum casting, and the vacuum pressure in the cavity is less than 100mbr.
8. The method according to claim 4, characterized in that the method comprises the steps of (5) annealing and post-aging the obtained die cast product to increase the elongation of the die cast product; or the die-casting product is subjected to simple aging treatment, so that the strength of the die-casting product is improved.
9. The method of claim 8, wherein the annealing is performed at 300 ℃ to 350 ℃ for 120 to 180 minutes;
the post-aging treatment is to preserve heat for 120 to 240 minutes at 160 to 180 ℃;
the simple aging treatment is to keep the temperature at 160-180 ℃ for 60-180 minutes.
10. The Al-Si-Mg-Fe aluminum alloy with high non-heat-treated iron content based on secondary aluminum as claimed in any one of claims 1 to 4, wherein when the Al-Si-Mg-Fe aluminum alloy contains 0.2% to Fe < 0.3%, the Al-Si-Mg-Fe aluminum alloy has a yield strength of 180MPa or more, a tensile strength of 290MPa or more, an elongation of 10% or more, a yield strength of 160MPa or more, a tensile strength of 270MPa or more and an elongation of 10% or more at 200 ℃; the yield strength of the die-casting product cast under high pressure is more than or equal to 175MPa at room temperature, the tensile strength is more than or equal to 280MPa, and the elongation is more than or equal to 9 percent;
when Fe is more than or equal to 0.2% and less than or equal to 0.8%, the yield strength of the Al-Si-Mg-Fe aluminum alloy at room temperature is more than or equal to 170MPa, the tensile strength is more than or equal to 280MPa, the elongation is more than or equal to 8%, the yield strength at 200 ℃ is more than or equal to 150MPa, the tensile strength is more than or equal to 240MPa, and the elongation is more than or equal to 9%; the yield strength of the die-casting product cast at high pressure is more than or equal to 170MPa at room temperature, the tensile strength is more than or equal to 270MPa, and the elongation is more than or equal to 7.5%.
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Inventor after: Ge Bingzao Inventor after: Li Zhenming Inventor after: Liu Baoliang Inventor after: Ge Qianyun Inventor before: Ge Bingzao Inventor before: Li Zhenming Inventor before: Liu Baoliang Inventor before: Ge Qianyun |
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