CN112159917A - Large-size high-purity homogeneous fine-grain aluminum alloy ingot and casting method - Google Patents
Large-size high-purity homogeneous fine-grain aluminum alloy ingot and casting method Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/002—Castings of light metals
- B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
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- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D7/00—Casting ingots, e.g. from ferrous metals
- B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
Abstract
The invention relates to the technical field of large-size aluminum alloy homogeneous fine grain casting, in particular to a large-size high-purity homogeneous fine grain aluminum alloy ingot and a casting method. The composition comprises the following components in percentage by weight: 0.55 to 0.85 percent of Si, less than or equal to 0.25 percent of Fe, less than or equal to 0.20 percent of Cu, less than or equal to 0.50 percent of Mn, 0.45 to 0.7 percent of Mg0.45, less than or equal to 0.30 percent of Cr, less than or equal to 0.10 percent of Zn, less than or equal to 0.10 percent of Ti, less than or equal to 0.05 percent of Na, less than or equal to 0.05 percent of Ca, less than or equal to 0.05 percent of K, less than or equal to 0. The optimal homogenization process is determined and the ingot casting performance is improved by optimizing components and a smelting casting process and researching the influence of factors such as heating temperature, heat preservation time, cooling rate and the like on the structural performance of the large-size cast rod.
Description
Technical Field
The invention relates to the technical field of large-size aluminum alloy homogeneous fine grain casting, in particular to a large-size high-purity homogeneous fine grain aluminum alloy ingot and a casting method.
Background
The preparation of large-size fine-grain and homogeneous aluminum alloy cast ingots is a precondition for preparing high-end large-size high-performance aluminum alloy sections. However, as the size of the ingot increases, several control difficulties arise: due to the difference between the cooling speed and the diffusion speed of alloy elements, the uniformity of chemical components of each part of the cast ingot is reduced. Due to the large diameter of the ingot and the limitation of the cooling speed, under the condition of a certain addition amount of the grain refiner, uniform and fine grain structure is difficult to realize. The grain size distribution of the crystal grains is characterized in that fine crystal grains are easily realized at the periphery of the cast ingot, and coarse crystal grains are easily generated near the center of the cast ingot. In addition, by combining the solidification characteristics of the aluminum alloy, a part of gas is likely to not escape in time during the solidification process of the cast ingot with the super-large diameter, so that gas looseness is easily formed.
The 6005A aluminum alloy is a medium-strength wrought aluminum alloy developed on the basis of the 6005 alloy, has good extrusion performance, and can realize on-line quenching on an extruder. The 6005A alloy is mainly used as a thin-wall, hollow large-scale aluminum alloy wallboard profile required by transportation vehicles and other industrial structural profiles abroad.
The alloy 6005A contains, as alloying elements, mainly Si, Mg, Mn, Cr and a small amount of Fe as impurities, as typical Al-Mg-Si alloys.
Disclosure of Invention
Aiming at a series of defects of uneven grain structure and the like in the casting process of the large-size aluminum alloy cast ingot in the prior art, the invention provides the large-size high-purity homogeneous fine-grain aluminum alloy cast ingot and the casting method thereof, so as to solve the technical problems.
The technical scheme of the invention is as follows:
a large-size high-purity homogeneous fine-grain aluminum alloy cast ingot comprises the following components in percentage by weight: 0.55 to 0.85 percent of Si, less than or equal to 0.25 percent of Fe, less than or equal to 0.20 percent of Cu, less than or equal to 0.50 percent of Mn, 0.45 to 0.7 percent of Mg0.45, less than or equal to 0.30 percent of Cr, less than or equal to 0.10 percent of Zn, less than or equal to 0.10 percent of Ti, less than or equal to 0.05 percent of Na, less than or equal to 0.05 percent of Ca, less than or equal to 0.05 percent of K, less than or equal to 0.
Designing main alloying elements Si and Mg: si 0.55-0.85%, Mg0.45-0.70%, excess Si 0.2-0.4%, Mg2The Si content is controlled to be 0.7-1.0%. When the content of Mg in the alloy ingot is excessive within the 6005A composition range, the Mg content is reduced2The solubility of Si in solid solution weakens the aging strengthening effect of the alloy and seriously influences the forming performance of the alloy; on the other hand, excess Si increases the strength and increases the plasticity to improve the castability and weldability, but the decrease in corrosion resistance may cause intergranular corrosion. Mg (magnesium)2When the content of Si and excessive Si (less than or equal to 0.5 percent) is more, the tensile property of the alloy cast ingot is better, which indicates that Mg2The Si and the excessive Si have certain strengthening effect on the alloy cast ingot. When the excess Si exceeds 0.5%, the yield strength, tensile strength, and elongation of the alloy ingot are significantly reduced, indicating that the excess Si seriously impairs the strength and plasticity of the alloy ingot. Finally, the internal control is determined to be Si0.55-0.85%, Mg0.45-0.70%, the excess Si is controlled to be 0.2-0.4%, and Mg2The Si content is controlled to be 0.7-1.0%.
Mg and Si are main alloy elements in Al-Mg-Si series alloy, and form strengthening phase Mg in the alloy2Si plays a main strengthening role for the alloy. The ratio of Mg to Si is 1.73, and if the ratio is not in conformity, Si or Mg is excessive. Mg in alloy ingot structure2Si, in different forms, has a great influence on the extrudability of the ingot. When Mg2When the Si phase is present as a coarse precipitate in the alloy ingot, the alloy contains only a very small amount of Mg2Si solid solution, so that the deformation resistance is reduced during extrusion and the extrusion speed is increased. But because of insufficient Mg produced during extrusion2The mechanical properties of the Si remelted and extruded product are reduced and the surface quality is deteriorated after artificial aging due to the existence of coarse precipitates in a die to cause micro-tearing; when Mg2When the Si phase is sufficiently dissolved in the matrix α (a1), the alloy strength increases, but the deformation resistance increases, and the extrusion rate decreases. When Mg2When the Si phase is distributed in the matrix Al as fine dispersed particles, the fine particles are easily dissolved by high heat generated during the extrusion process. Therefore, the initial deformation resistance of the structure is low, the higher extrusion speed can be adopted, the surface quality can be improved, and the aging strengthening effect is not influenced.
Design of grain refining elements Mn, Cr and Ti: when 0.15% or less of Mn and 0.08% or less of Cr are added to the alloy, the amount of particles precipitated in the homogenized structure of the alloy is small, and the β - α conversion of the impurity phase AlFeSi is incomplete. The alloy structure after hot extrusion is a partially recrystallized deformed structure; when 0.15-0.50% Mn and 0.08-0.30% Cr are added, dispersed fine particles containing Mn and Cr are precipitated from the homogenized structure, and the needle-like or flake-like beta AlFeSi is substantially converted into a coarse granular phase alpha AlFeSi. The alloy structure after hot extrusion is a fibrous unrecrystallized structure. The formed fibrous structure can greatly improve the strength of the alloy due to the structure strengthening (extrusion effect), reduce the sensitivity to stress corrosion cracking and improve the toughness of the alloy. Meanwhile, the beta-alpha conversion of the AlFeSi phase can reduce brittle failure effect, improve the extrusion performance of the alloy and improve the surface quality. Therefore, finally, after 0.15-0.50% of Mn and 0.08-0.30% of Cr are added, the 6005A alloy shows higher strength, can also obtain higher plasticity and toughness and better surface quality, and the Ti content is controlled to be 0.03-0.10% to avoid TiB2 aggregation when the Ti content meets 0.1% and can achieve the effect of refining grains.
The addition amount of Mn and Cr in the alloy should not be too large or too small, and too small the addition amount does not inhibit recrystallization, promote AlFeSi phase transformation and uniformityExcessive deformation will form coarse compound with other elements and impurity elements to reduce alloy performance greatly or become reinforcing phase Mg during extrusion on-line quenching2The core of Si precipitation improves the quenching sensitivity of the alloy, and less than 0.1 percent of Ti is added while Cr is added, so that the columnar crystal structure of the cast ingot can be reduced, the forging performance of the alloy is improved, and the crystal grains of the product are refined.
The invention also aims to provide a casting method of a large-size high-purity homogeneous fine-grain aluminum alloy cast ingot, which comprises the following melt purification process steps:
(a) feeding structure: adopting a self-feeding solid material mode to feed materials, and charging the materials in sequence: 99.85-99.9% of high-purity aluminum ingot → primary waste, and before feeding, confirming that furnace burden is clean and dry without mixing materials, and weighing; when charging, the temperature of the hearth is at 600-; and charging the primary waste, the high-purity aluminum ingot and 90% of the intermediate alloy in sequence, and adding the AlTi alloy and the Mg before sampling and stirring in a smelting furnace.
(b) The Na content is effectively controlled to be less than 15ppm and the fusion casting time is controlled to be as follows: except that Na-free flux is used, high-temperature smelting at the temperature of below 700-; after the furnace burden is completely melted, the process time of adjusting components, refining, slagging off and adjusting the temperature of the converter is controlled within 3-4 h. Because the melting temperature is high, particularly in a liquid state, the retention time of the melt is too long, so that the air suction quantity of the melt is increased, the oxidation burning loss is increased, the non-spontaneous crystal nuclei are reduced, and the tendency of forming cracks, coarse crystals and feather-like crystals in the ingot is increased.
(c) Improving the purity of the melt: on the premise of completely cleaning the furnace, before charging and guiding the furnace, scattering a refining agent into the furnace, wherein the dosage of the refining agent is 1.5-2 kg/tAl; 10-15kg of Na-free covering agent is scattered into the mixture after refining to completely cover the mixture; smelting for 4-6h, and standing for 1-1.5h after refining and slagging-off till casting; degassing in a holding furnace, replacing nitrogen with high-purity argon, and blowing air for 30-35min from bottom to top through a furnace bottom air brick; the free hydrogen will diffuse into the bubbles of the inert gas and bring out the aluminum liquid along with the rising of the bubbles of the inert gas, thus achieving the purpose of degassing; in addition, in the process of rising of the high-purity inert gas, the aluminum liquid can be taken out of the fine impurities adsorbed on the surface, the purpose of deslagging is achieved, only very fine particles can be adsorbed and removed, and the impurities of larger particles still need to be removed in a filtering mode.
In the subsequent on-line treatment process, degassing is carried out again through a degassing box, and the content of hydrogen detected on line is less than 0.15ml/100 gAl; to reduce the tendency to loosen.
The last on-line treatment process is to filter and purify the melt by using a 40-80ppi high-quality foamed ceramic filter plate through an on-line filter box.
Further, the sodium-free covering agent of the melt purification process step is imported pyrotek sodium-free C2.
Further, the large-size high-purity homogeneous fine-grain aluminum alloy ingot casting method further comprises the fine-grain casting process optimization step, and the method specifically comprises the following steps: according to the characteristics of the alloy, the secondary cooling in the casting process is increased, and a grain refiner is selected for refining grains, wherein the casting speed is as follows: 23mm/min-30mm/min, cooling water flow: 65-88m3The cooling water temperature is 20-30 ℃, and the speed of feeding the grain refiner wire rod is controlled at 35-45 cm/min.
Further, the grain refiner is an imported AMG5Ti1B grain refiner.
Further, the method for casting the large-size high-purity homogeneous fine-grained aluminum alloy ingot further comprises the step of optimizing an ingot homogenization system, and specifically comprises the following steps: a three-level homogenization system is adopted: 560 +/-5 ℃ multiplied by 260min +540 +/-5 ℃ multiplied by 210min +575 +/-5 ℃ multiplied by 420 min; through increasing one-level high temperature 560 ℃ homogenization stage, the homogenization temperature is promoted more quickly, three-level high temperature homogenization is optimized, and after 575 ℃ multiplied by 420min high-temperature homogenization treatment, the dendritic crystal structure can be completely disappeared, coarse precipitates in the crystal are basically redissolved, the size and the number of the eutectic phase of the crystal boundary are greatly reduced, and the beta phase is basically eliminated. The whole dendritic crystal network becomes thin and discontinuous, which shows that solute atoms in the ingot are fully diffused, and the alloy components are more uniform.
The cooling process is fine-tuned, and the cooling strength is increased. The segregation of grain boundary on the product is greatly reduced, the compound on the grain boundary is partially dissolved, and except some intermetallic compound particles containing Mn and Cr are precipitated, Mg is not basically contained2And (4) precipitation of an Si phase. Such a structure not only reduces the extrusion resistance and increases the extrusion speed, but also promotes the uniformity of deformation, suppresses recrystallization, and improves the final properties of the alloy.
The alloy of the invention is mainly AlFeSi phase. For 6005A alloy for extruding large-sized thin-wall section bars, a better homogenization treatment process can eliminate the non-uniformity of Mg and Si concentration distribution and Mg in ingot2The segregation of Si phase promotes the beta-alpha conversion of insoluble phase AlFeSi compound, so that the microstructure of the ingot does not contain much Mg2Si is precipitated, and fine particles of an intermetallic compound containing Mn and Cr which play a role of suppressing recrystallization during extrusion exist. The cast ingot structure can reduce the extrusion resistance, improve the extrusion speed and improve the mechanical property of a semi-finished product.
The beneficial effect of the invention is that,
in the feeding structure in the casting method, 90% of intermediate alloy is added, the intermediate alloy is pre-estimated to be 90%, and the phenomenon that elements exceed standards and are diluted is avoided, so that the production efficiency and the proportion of other elements are greatly influenced.
According to the invention, the large-size high-purity homogeneous fine-grain aluminum alloy is optimized through composition optimization and smelting and casting processes, and the optimal homogenization process is determined and the ingot casting performance is improved by researching the influence of factors such as heating temperature, heat preservation time and cooling rate on the structure performance of a large-size cast rod.
The invention researches the key scientific problem of grain refinement and macro segregation inhibition of the large-size aluminum alloy ingot, and provides scientific basis for the preparation of large-size fine-grain and homogeneous aluminum alloy ingots. The casting method is particularly suitable for the 6005A aluminum alloy.
Drawings
In order to more clearly illustrate the embodiments or technical solutions in the prior art of the present invention, the drawings used in the description of the embodiments or prior art will be briefly described below, and it is obvious for those skilled in the art that other drawings can be obtained based on these drawings without creative efforts.
FIG. 1 is a graph of the microstructure analysis, a being example 1, b being example 2, and c being example 3.
FIG. 2 is a graph of the microscopic structure analysis, wherein a is example 1, b is example 2, and c is example 3.
FIG. 3 is a scanning electron micrograph, wherein a is example 1, b is example 2, and c is example 3.
Detailed Description
In order to make those skilled in the art better understand the technical solution of the present invention, the technical solution in the embodiment of the present invention will be clearly and completely described below with reference to the drawings in the embodiment of the present invention, and it is obvious that the described embodiment is only a part of the embodiment of the present invention, and not all embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1: 2030206 smelting 6005A alloy 660 specification cast rod production, which comprises the following components by weight percent: 0.63-0.70% of Si, less than or equal to 0.15% of Fe, less than or equal to 0.05% of Cu, 0.21-0.26% of Mn, 0.52-0.60% of Mg0.11-0.16% of Cr0.11, less than or equal to 0.04% of Zn, less than or equal to 0.03-0.05% of Ti, Mn + Cr: 0.3 to 0.45 percent of Na, less than or equal to 0.001 percent of Ca, less than or equal to 0.04 percent of K, less than or equal to 0.01 percent of Pb, less than or equal to 0.15 percent of impurity and the balance of Al.
The composition design is shown in table 1.
Table 1 composition design table
(a) Feeding structure: adopting a self-feeding solid material mode to feed materials, and charging the materials in sequence: 99.9 percent of high-purity aluminum ingot → primary waste, and confirming that the furnace burden is clean and dry without mixing materials before feeding, and weighing; when charging, the temperature of the hearth is at 600-; and charging the first-grade waste, the high-purity aluminum ingot and 90% of intermediate alloy (the estimated amount of the intermediate alloy is 90%, the element exceeding standard is prevented from being diluted, the production efficiency is greatly influenced and the proportion of other elements) in sequence, and adding the AlTi alloy and the Mg before sampling and stirring in a smelting furnace. In the embodiment, 99.9 percent of high-purity aluminum ingots are adopted, and the impurity content and the alkali metal content are controlled, so that the proportion of waste materials is strictly controlled to be less than or equal to 30 percent. The feed design is shown in table 2.
TABLE 2 feeding structure design table
(b) The Na content is effectively controlled to be less than 10ppm and the fusion casting time is controlled to be as follows: except that Na-free flux is used, high-temperature smelting is adopted at the temperature of 700-760 ℃; the smelting time is 4.5h, the furnace burden is collapsed, the sodium-free C2 covering agent is uniformly scattered into the furnace burden after the furnace burden is collapsed, the furnace burden is completely melted, the temperature of the melt is measured once every 1 hour, the temperature of the melt is ensured to be within the required range of 720-760 ℃, and the overtemperature is strictly forbidden. After the furnace burden is completely melted, the process time of adjusting components, refining, slagging off, adjusting the temperature of a converter and the like is controlled to be 3.6h, the high melting temperature is avoided, particularly under the liquid state condition, the retention time of the melt is too long, the non-spontaneous crystal nucleus is reduced, and the tendency of generating cracks, coarse crystals and feather-like crystals of the cast ingot is increased.
(c) Improving the purity of the melt: on the premise of completely cleaning the furnace, a refining agent is scattered into the furnace before charging and guiding the furnace, and the dosage of the refining agent is 1.5-2 kg/tAl; 10-15kg of imported pyrotek sodium-free C2 covering agent is scattered into the mixture after refining to completely cover the mixture; the standing time from the completion of slag skimming to the time before casting after refining is 1.2 h; degassing in a holding furnace, replacing nitrogen with high-purity argon, blowing the furnace bottom air brick for 35min from bottom to top, diffusing free hydrogen into bubbles of inert gas, and taking out aluminum liquid along with the rising of the bubbles of the inert gas to achieve the purpose of degassing; in the process of rising the high-purity inert gas, the fine impurities adsorbed on the surface can be taken out of the aluminum liquid, so that the aim of removing slag is fulfilled, only very fine particles can be adsorbed and removed, and the impurities of larger particles still need to be removed in a filtering manner; in the subsequent on-line treatment process, degassing is carried out again through a degassing box, and the content of hydrogen detected on line is ensured to be less than 0.15ml/100gAl so as to reduce the loosening tendency; the last on-line treatment procedure is to use a 50 plus 80ppi high-quality foamed ceramic filter plate to carry out double-stage filtration through an on-line filter box to carry out melt filtration and purification.
Further, in this example, according to the characteristics of the alloy, the secondary cooling during the casting process is increased, and a high-quality grain refiner (imported AMG company 5Ti1B) is selected to refine grains, wherein the casting speed is as follows: 23mm/min-30mm/min, cooling water flow: 65-88m3The cooling water temperature is 20-30 ℃, and the speed of feeding the grain refiner wire rod is controlled at 35-45 cm/min. The melt casting process configuration is shown in table 3.
TABLE 3 fusion casting process configuration table
(d) Further, the method for casting the large-size high-purity homogeneous fine-grained aluminum alloy ingot further comprises the step of optimizing an ingot homogenization system, and specifically comprises the following steps: a three-level homogenization system is adopted: 560. + -. 5 ℃ X260 min + 540. + -. 5 ℃ X210 min + 575. + -. 5 ℃ X420 min. Through increasing one-level high temperature 560 ℃ homogenization stage, the homogenization temperature is promoted more quickly, three-level high temperature homogenization is optimized, and after 575 ℃ multiplied by 420min high-temperature homogenization treatment, the dendritic crystal structure can be completely disappeared, coarse precipitates in the crystal are basically redissolved, the size and the number of the eutectic phase of the crystal boundary are greatly reduced, and the beta phase is basically eliminated. The whole dendritic crystal network becomes thin and discontinuous, which shows that solute atoms in the ingot are fully diffused, and the alloy components are more uniform. The cooling process is fine-tuned, and the cooling strength is increased. The segregation of grain boundary on the product is greatly reduced, and the compound on the grain boundary is partially dissolved, except that some Mn-containing compounds are precipitatedAnd substantially no Mg except the intermetallic compound particles of Cr2And (4) precipitation of an Si phase. Such a structure not only reduces the extrusion resistance and increases the extrusion speed, but also promotes the uniformity of deformation, suppresses recrystallization, and improves the final properties of the alloy. The homogenization process configuration is shown in table 4.
TABLE 4 homogeneous Process configuration is shown in the Table
Example 2: production of 2030207 fusion 6005A alloy 660 specification cast rod
Example 3: production of 2030208 fusion 6005A alloy 660 specification cast rod
The steps are the same as example 1, and the specific parameters are as follows:
(a) the composition is designed as follows in table 5.
TABLE 5 ingredient design Table
(b) The feed structure design is as follows in table 6:
table 6 feeding structure design table
(C) The melting process is shown in table 7 below:
TABLE 7 fusion casting Process configuration
(d) The homogenization process is shown in table 8 below:
TABLE 8 homogeneous technological process table
The test, detection and verification results of the products obtained in the above examples 1 to 3 are shown in fig. 1 to 3, and it can be seen from fig. 1 that the cast ingot is homogeneous and not corroded, wherein the product obtained in example 1 has the least unmelted phase and impurity phase and the least grains, and meets the requirements of high purity and fine grains of large-size cast ingot tissues; FIG. 2 shows the ingot in a homogeneous state, with the smallest grains in FIG. 1, and the grains analyzed for corrosion; the ingot is shown in a homogeneous state in the electron micrograph of FIG. 3.
Claims (8)
1. A large-size high-purity homogeneous fine-grain aluminum alloy ingot is characterized by comprising the following components in percentage by weight: 0.55 to 0.85 percent of Si, less than or equal to 0.25 percent of Fe, less than or equal to 0.20 percent of Cu, less than or equal to 0.50 percent of Mn, 0.45 to 0.7 percent of Mg0.45, less than or equal to 0.30 percent of Cr, less than or equal to 0.10 percent of Zn, less than or equal to 0.10 percent of Ti, less than or equal to 0.05 percent of Na, less than or equal to 0.05 percent of Ca, less than or equal to 0.05 percent of K, less than or equal to 0.
2. The large-size high-purity homogeneous fine-grained aluminum alloy ingot according to claim 1, wherein the Si is 0.55-0.85%, the Mg0.45-0.70%, the excess Si is controlled to be 0.2-0.4%, and the Mg is added2The Si content is controlled to be 0.7-1.0%.
3. The large-size, high-purity, homogeneous, fine-grained aluminum alloy ingot of claim 1 or 2, wherein 0.15 to 0.50% Mn and 0.08 to 0.30% Cr, and the Ti content is controlled to 0.03 to 0.10%.
4. A method of casting a large-size high-purity homogeneous fine-grained aluminum alloy ingot according to any one of claims 1 to 3, comprising the melt purification process steps, in particular as follows:
(a) feeding structure: adopting a self-feeding solid material mode to feed materials, and charging the materials in sequence: 99.85-99.9% of high-purity aluminum ingot → primary waste, and before feeding, confirming that furnace burden is clean and dry without mixing materials, and weighing; when charging, the temperature of the hearth is at 600-; sequentially charging the primary waste, the high-purity aluminum ingot and 90% of the intermediate alloy, and adding the AlTi alloy and the Mg before sampling and stirring in a smelting furnace;
(b) the Na content is effectively controlled to be less than 15ppm and the fusion casting time is controlled to be as follows: except that Na-free flux is used, high-temperature smelting at the temperature of below 700-; after the furnace burden is completely melted, the process time of adjusting components, refining, slagging off and adjusting the temperature of the converter is controlled to be 3-4 h;
(c) improving the purity of the melt: on the premise of completely cleaning the furnace, before charging and guiding the furnace, scattering a refining agent into the furnace, wherein the dosage of the refining agent is 1.5-2 kg/tAl; 10-15kg of Na-free covering agent is scattered into the mixture after refining to completely cover the mixture; smelting for 4-6h, and standing for 1-1.5h after refining and slagging-off till casting; degassing in a holding furnace, using high-purity argon gas, and blowing air for 30-35min from bottom to top through a furnace bottom air brick;
in the subsequent on-line treatment process, degassing is carried out again through a degassing box;
the last on-line treatment process is to filter and purify the melt by using a 40-80ppi high-quality foamed ceramic filter plate through an on-line filter box.
5. The method of casting a large-size, high-purity, homogeneous, fine-grained aluminum alloy ingot as claimed in claim 4 wherein the sodium-free covering agent of the melt purification process step is imported pyrotek sodium-free C2.
6. A casting method according to claim 4 or 5, further comprising a fine grain casting process optimization step, as follows: increasing secondary cooling in the casting process, and refining grains by using a grain refiner, wherein the casting speed is as follows: 23mm/min-30mm/min, cooling water flowQuantity: 65-88m3The cooling water temperature is 20-30 ℃, and the speed of feeding the grain refiner wire rod is controlled at 35-45 cm/min.
7. The casting method as recited in claim 6, wherein said grain refiner is an inlet AMG5Ti1B grain refiner.
8. The casting method according to claim 4, 5 or 7, further comprising an ingot homogenization regime optimization step, specifically as follows: a three-level homogenization system is adopted: 560. + -. 5 ℃ X260 min + 540. + -. 5 ℃ X210 min + 575. + -. 5 ℃ X420 min.
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