CN111411247B - Composite treatment method for regenerated wrought aluminum alloy melt - Google Patents
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Abstract
The invention discloses a composite treatment method of a regenerated wrought aluminum alloy melt, which is mainly characterized in that a 6xxx series regenerated aluminum alloy melt is subjected to composite treatment through Mg, Sr and a C-containing refiner, the shape and distribution of a second phase of an alloy are changed, needle-shaped impurity phases are changed into Chinese characters, eutectic structures are uniformly distributed, crystal grains are refined, and the solidification mode of the alloy is changed. After the composite treatment of the invention, the ingot casting hot cracking sensitivity of the regenerated wrought aluminum alloy is obviously reduced, the reduction rate is up to 32 percent, the comprehensive mechanical property is also obviously improved, the tensile strength is improved by 35 percent to the maximum, and the hardness is improved by 45 percent to the maximum.
Description
Technical Field
The invention relates to the technical field of composite treatment of regenerated wrought aluminum alloy melts, in particular to a composite treatment method capable of reducing the heat cracking sensitivity of a 6xxx series regenerated wrought aluminum alloy cast ingot and improving the comprehensive mechanical property of the cast ingot.
Background
Aluminum and aluminum alloy have the characteristics of small specific gravity, good conductivity, good heat dissipation performance, high specific strength, easiness in processing and the like, are increasingly applied to the fields of automobiles, traffic, aviation and the like, and become indispensable basic raw materials of national economy. On one hand, the demand of the high-speed development of national economy on aluminum products is continuously increased, and on the other hand, the large-batch aluminum products reach the service life each year, so that a large amount of waste aluminum resources are enriched, and the rapid development of the secondary aluminum industry is promoted. In addition, the regenerated metal has the characteristic of energy conservation, and the unit energy consumption of the production of the regenerated aluminum is not more than 5 percent of that of the production of electrolytic aluminum. The development of the secondary aluminum industry has important significance for realizing the strategy of green economy and sustainable development.
The secondary aluminum is aluminum alloy or aluminum metal obtained by remelting and refining various recovered waste aluminum serving as raw materials, and is an important source for obtaining metal aluminum. The waste aluminum has various types and different components, so that the components of the regenerated aluminum are very complex, main impurities comprise Zn, Fe, Cu, Mn and the like, and the existence of the impurity elements reduces the performance of the regenerated aluminum alloy, so that the degraded use of the aluminum alloy is caused. Particularly, in the casting and forming process of the regenerated aluminum alloy, the existence of the impurity elements obviously increases the heat crack sensitivity of the aluminum alloy cast ingot, reduces the yield and causes the waste of resources.
Heat cracking is a common casting defect and is a major factor that restricts casting production and the diversified application of alloys. From the property of the alloy, the composition, the grain size and the morphology of the alloy greatly influence the hot cracking sensitivity of the alloy. The patent (CN102127665B) adopts the compound microalloying treatment of higher Zn and Mg contents and Sc and Zr to realize the purposes of increasing the proportion of eutectic phase, inhibiting the growth of dendrite and changing the solidification mode of the alloy, thereby reducing the hot cracking sensitivity of the alloy and improving the casting performance of the alloy. However, this patent would increase the content of alloying elements significantly, and does not deal with the complicated melt processing of alloys with large amounts of impurity elements. From the perspective of alloy melt processing, the purification, modification and refinement techniques of aluminum alloy melt are particularly critical. In the patent (CN109439975A), Mn, Al-B and Al-Sr intermediate alloys are used for the composite modification of the regenerated cast aluminum alloy, so that the purpose of synchronously refining three phases of an iron-rich phase, a primary alpha-Al phase and eutectic silicon in the alloy is achieved, and the elongation of the alloy can be improved. However, the patent is the same as a large amount of research on the structural change and the performance of the alloy, and does not relate to the influence of the alloy on the hot cracking defect of the aluminum alloy casting.
Currently, research on the hot cracking tendency of aluminum alloys is mainly focused on mature commercial alloys, and relatively few hot cracking tendency of scrap-based secondary aluminum alloys is focused. The 6xxx series wrought aluminum alloy represented by 6061 is one of the aluminum alloys with the largest market share at present, is mainly applied to the civil field, and has large recovery amount which exceeds 300 million tons per year. After remelting and recycling, the components are complex, so that the casting production process has a great hot cracking tendency, the process yield is reduced, and the performance is obviously reduced. Therefore, for regenerated 6xxx series wrought aluminum alloy with complex components, how to utilize a melt composite treatment method reduces the heat cracking sensitivity of the alloy in the casting process, and simultaneously gives consideration to excellent comprehensive performance, thereby having important significance for practical application of the regenerated aluminum.
Disclosure of Invention
In order to solve the defects and shortcomings in the prior art, the invention aims to provide a composite treatment method for a regenerated wrought aluminum alloy melt. The regenerated wrought aluminum alloy treated by the method has small hot cracking sensitivity in the casting process, high casting blank yield, excellent comprehensive mechanical property and wide application range.
In order to achieve the purpose, the technical scheme adopted by the invention comprises the following aspects:
a composite treatment method for a regenerated wrought aluminum alloy melt comprises the following steps:
(1) melting 6xxx series waste aluminum, and obtaining a regenerated wrought aluminum alloy melt after slagging-off;
(2) adding a metal Mg, an Al-Ti series refiner and an Al-10Sr alterant into the melt obtained in the step (1) for composite treatment, uniformly stirring after melting, and standing at a constant temperature;
(3) refining and deslagging the melt obtained in the step (2), and preserving heat and standing after deslagging;
(4) casting and molding the melt obtained in the step (3) to obtain a regenerated wrought aluminum alloy ingot;
(5) carrying out homogenization heat treatment on the aluminum alloy ingot obtained in the step (4) to obtain a cast plate;
(6) and (5) rolling the cast plate obtained in the step (5) for multiple times to obtain the regenerated wrought aluminum alloy.
Preferably, in the step (1), the melting temperature of the 6xxx series aluminum scrap is 750 ℃.
Preferably, in the step (2), the addition amount of the Al-Ti series refiner accounts for 0.3-0.7% of the mass of the melt, and the addition amount of the Al-10Sr alterant accounts for 0.2-0.6% of the mass of the melt.
Preferably, the Al-Ti series refiner includes at least one of a C-containing refiner and an Al-5Ti-B refiner. More preferably, the Al-Ti series refiner is a C-containing refiner. The C-containing refiner comprises the following components in percentage by mass: 4.5 to 5.5 percent of Ti, 0.25 to 0.35 percent of B and 0.15 to 0.25 percent of C.
Preferably, after the metal Mg is added, the mass percentage of Mg in the melt is 0.8-1.4%.
Preferably, in the step (2), the temperature of the composite treatment is 720-750 ℃, and the time of heat preservation and standing is 10-20 min.
Preferably, in the step (3), the refining and deslagging treatment is to add a refining agent and a deslagging agent into the melt, the treatment temperature is controlled to be 720-750 ℃, and the treatment time is 10-20 min.
Preferably, the total adding amount of the refining agent and the slag removing agent is 1% of the mass of the melt, and the mass ratio of the refining agent to the slag removing agent is 1: 4.
preferably, the refining agent and the slag former are uniformly mixed and then added into the melt by a blowing method.
Preferably, the commercial brands of the refining agent and the slagging agent are the refining agent YT-J-1 and the slagging agent YT-D-4 respectively.
Preferably, in the step (3), the heat preservation and standing time is 30 min.
Preferably, in the step (4), the casting and forming manner is gravity casting and forming.
Preferably, in the step (5), the homogenizing heat treatment process comprises: the temperature is 480-500 ℃, and the heat preservation time is 8-12 h.
Preferably, in step (6), the rolling process is as follows: the maximum deformation of each pass is 10 percent, and the total deformation is 50 percent.
The invention also provides a 6xxx series regenerative wrought aluminum alloy prepared by the composite treatment method of the regenerative wrought aluminum alloy melt.
Because the raw material source of the 6xxx series regenerated wrought aluminum alloy is complex, the 6xxx series regenerated wrought aluminum alloy contains a plurality of impurity elements such as Fe, Cu, Mn, Zn and the like, and the content is high, such as Fe: 0.95%, Cu: 0.45 percent. The impurity elements are easy to form coarse and brittle iron-copper-rich impurity phases and other low-melting-point phases in the alloy, so that the continuity of a matrix is damaged, the solidification interval of the alloy is increased, the hot cracking sensitivity of the alloy is increased, the mechanical property is reduced, and the alloy can only be degraded for use. In the treatment method, the purification treatment of the regenerated wrought aluminum alloy melt can effectively reduce air holes and oxide slag inclusion and reduce crack sources. Meanwhile, under the action of Sr alterant and C-containing refiner, the broken long-needle-shaped iron-rich phase in the alloy is converted into Chinese character shape and is combined with the matrix more tightly, the crystal grains are further refined, and the thermal stress resistance is enhanced. Mg is an important alloy element in 6xxx series aluminum alloy, Mg is added for component regulation and control, and Mg is generated at the final stage of alloy solidification2Si eutectic phase can be well fed, the generation of hot cracks is prevented, and Mg2Si is a main hard strengthening phase of the 6xxx series aluminum alloy, and can improve the hardness and the mechanical property. Therefore, compared with single modification treatment, the composite treatment of the invention on the melt can effectively reduce the hot cracking sensitivity of the alloy, and simultaneously improve the mechanical property of the alloy, so that the obtained regenerated aluminum alloy can meet the requirements of household and light industrial manufacturing molds, and the like, thereby not only realizing the grade-keeping utilization of the regenerated and deformed aluminum alloy, but also expanding the application range and field of the regenerated and deformed aluminum alloy.
Compared with the prior art, the invention has the beneficial effects that: according to the invention, the composite treatment of Mg, Sr alterant and C-containing refiner is carried out on the 6xxx series regenerative wrought aluminum alloy melt, so that the multielement composite effect is fully exerted, the form and distribution of the second phase in the regenerative wrought aluminum alloy are improved, the iron-rich impurity phase is changed into a Chinese character shape from a needle shape, the eutectic phase is uniformly distributed, the grain structure is refined, and the alloy solidification mode is changed; the invention also purifies the melt, further reduces crack sources in the alloy, finally performs homogenization and rolling deformation control, finally obtains the 6xxx series regenerated wrought aluminum alloy with small casting hot cracking sensitivity, excellent comprehensive mechanical property and high casting yield, and widens the industrial application of the 6xxx series regenerated wrought aluminum alloy.
Drawings
FIG. 1 is an as-cast optical microstructure of a virgin wrought aluminum alloy prepared in comparative example 1;
FIG. 2 is an as-cast optical microstructure of a wrought aluminum alloy prepared in comparative example 2;
FIG. 3 is an as-cast optical microstructure of a wrought aluminum alloy prepared in comparative example 3;
FIG. 4 is an as-cast optical microstructure of a wrought aluminum alloy prepared in comparative example 4;
FIG. 5 is an as-cast optical microstructure of a wrought aluminum alloy prepared in example 1;
FIG. 6 is a CRC restraint bar hot crack test sample of a virgin wrought aluminum alloy prepared in comparative example 1;
FIG. 7 is a CRC restraint bar hot crack test sample of the wrought aluminum alloy prepared in example 1.
FIG. 8 is a comparison of the hot crack sensitivity of the regenerated wrought aluminum alloy ingots made in the examples and comparative examples.
Detailed Description
To better illustrate the objects, aspects and advantages of the present invention, the present invention is further illustrated by the following examples. It is apparent that the following examples are only a part of the embodiments of the present invention, and not all of them. It should be understood that the embodiments of the present invention are only for illustrating the technical effects of the present invention, and are not intended to limit the scope of the present invention.
Comparative example 1
Preparation of original 6xxx series regenerated wrought aluminum alloy: melting the primarily screened 6xxx series recycled aluminum scrap, including 6061, 6063, 6151, 6201 and the like, wherein the melting temperature is 750 ℃, fully melting and stirring until the melt components are uniform, removing dross on the surface of the melt, and keeping the temperature and standing for 20 min. Uniformly mixing a refining agent YT-J-1 and a slag striking agent YT-D-4 according to the mass ratio of 1:4, adding the mixture into a melt by using a nitrogen blowing method, carrying out refining and slag striking treatment on the melt, controlling the treatment temperature to be 720 ℃, treating for 20min, taking the total addition amount of the refining agent and the slag striking agent as 1% of the mass of the melt, removing floating slag on the surface of the melt, and standing for 30min under heat preservation to obtain a regenerated wrought aluminum alloy melt, wherein the regenerated wrought aluminum alloy melt comprises the following components in percentage by mass: si: 0.63%, Fe: 0.95%, Mg: 0.72%, Cu: 0.45%, Mn: 0.12%, Zn: 0.15%, the total amount of other impurities is not more than 0.30%, and the balance is Al. And (3) casting and molding the regenerated wrought aluminum alloy melt by using a gravity casting method to obtain a regenerated wrought aluminum alloy ingot, wherein the preheating temperature of the metal mold is 200 ℃. And placing the cast ingot in a resistance furnace for homogenization heat treatment, wherein the homogenization temperature is 480 ℃, and the heat preservation time is 8 hours. And (3) rolling the ingot subjected to the homogenization heat treatment for multiple times, wherein the deformation amount of each time is 5 percent, and the total deformation amount is 50 percent, so as to obtain the original regeneration deformation aluminum alloy.
In order to compare the structure and performance characteristics of the alloy, the thermal cracking sensitivity of the regenerated aluminum alloy is evaluated by a CRC (constrained RodCast) constraint rod thermal cracking evaluation method; meanwhile, preparing a metallographic specimen for tissue observation; testing the hardness value of the alloy by using a HB3000 Brinell hardness tester; and tensile tests are carried out by using an AG-X100KN universal testing machine to obtain mechanical property parameters.
FIG. 1 is an optical microstructure of the wrought aluminum alloy prepared in comparative example 1, in which it can be seen that the wrought aluminum alloy without the compound treatment has coarse dendrites, eutectic structure phase and impurity phase, and is concentrated and distributed at grain boundaries. As-cast properties were measured, the tensile strength of the alloy was 178.9MPa, the elongation 9.4%, and the hardness 48 HB. FIG. 6 is a thermal cracking test sample of the CRC restraining rod of the alloy, wherein the long arm and the second long arm are completely cracked, the second short arm is partially cracked, and according to the evaluation mode of CRC, the thermal cracking sensitivity coefficient HTS of the alloy is calculated to be 178, and the casting thermal cracking sensitivity is high. The rolling state performance is measured, the tensile strength of the alloy is only 202.2MPa, the elongation is 6.2%, the hardness is 63.9HB, and the comprehensive performance is poor.
Comparative example 2
Preparation of a Mg-treated-alone 6 xxx-series wrought aluminum alloy: the 6xxx series recycled aluminum scrap after primary screening is melted according to the method of the comparative example 1, the initial basic components are the same as the comparative example 1, the scum is removed, and the aluminum scrap is kept warm and kept stand for 20 min. Adding Mg ingots into the melt, keeping the temperature of the melt at 720 ℃, uniformly stirring after melting, and keeping the temperature and standing for 20 min; wherein the addition amount of Mg is 0.55 percent of the mass of the melt, the burning loss rate is 10 percent, and the Mg content mass fraction of the added alloy is 1.2 percent. And casting the melt into an ingot by the method of the comparative example 1, and then placing the ingot in a resistance furnace for homogenization heat treatment, wherein the homogenization temperature is 490 ℃, and the heat preservation time is 10 hours. And (4) carrying out multi-pass rolling after homogenization, wherein the deformation amount of each pass is 5%, and the total deformation amount is 50%, so as to obtain the regenerated wrought aluminum alloy.
FIG. 2 is an as-cast optical microstructure of a wrought aluminum alloy prepared in comparative example 2 and subjected to melt processing with Mg alone, and it can be seen that bulk interconnected eutectic structures appear in the alloy and that eutectic structures and impurity phases are increased at grain boundaries. The hot cracking sensitivity coefficient HTS of the alloy in an as-cast state is 154, the tensile strength of the alloy in the as-cast state is 185.2MPa, the elongation is 9.1 percent, and the hardness is 54.4 HB. In the rolled state, the tensile strength of the alloy was 212.5MPa, the elongation was 7.2%, and the hardness was 75.4 HB.
Comparative example 3
Preparation of Sr-treated 6 xxx-series wrought aluminium alloys: the 6xxx series recycled aluminum scrap after primary screening is melted according to the method of the comparative example 1, the initial basic components are the same as the comparative example 1, the scum is removed, and the aluminum scrap is kept warm and kept stand for 20 min. Adding Al-10Sr alterant into the melt, keeping the melt temperature at 720 ℃, uniformly stirring after melting, and standing for 20min with heat preservation; wherein the addition amount of the Al-10Sr alterant is 0.5 percent of the mass of the melt. And casting the melt into an ingot by the method of the comparative example 1, and then placing the ingot in a resistance furnace for homogenization heat treatment, wherein the homogenization temperature is 480 ℃ and the heat preservation time is 8 hours. And (4) carrying out multi-pass rolling after homogenization, wherein the deformation amount of each pass is 5%, and the total deformation amount is 50%, so as to obtain the regenerated wrought aluminum alloy.
FIG. 3 is an as-cast optical microstructure of the wrought aluminum alloy prepared in comparative example 3 after being subjected to melt treatment with Mg alone, which is similar to the as-cast optical microstructure of the wrought aluminum alloy prepared in comparative example 2 after being subjected to melt treatment with Mg alone, and it can be seen from FIG. 3 that bulk eutectic structures and impurity phases in the alloy disappear and are uniformly distributed around grains. The hot cracking sensitivity coefficient HTS of the alloy in an as-cast state is 164, the tensile strength is 190.2MPa, the elongation is 10.2 percent, and the hardness is 53.7 HB. The tensile strength of the alloy in the rolled state is 217.5MPa, the elongation is 6.9 percent, and the hardness is 68.5 HB.
Comparative example 4
Preparation of a 6xxx series wrought aluminum alloy compositely treated with Sr/Al-5 Ti-B: the 6xxx series recycled aluminum scrap after primary screening is melted according to the method of the comparative example 1, the initial basic components are the same as the comparative example 1, the scum is removed, and the aluminum scrap is kept warm and kept stand for 20 min. Adding an Al-10Sr alterant and an Al-5Ti-B refiner into the melt, keeping the temperature of the melt at 720 ℃, uniformly stirring after melting, and standing for 20min with heat preservation; wherein the addition amount of the Al-10Sr alterant and the Al-5Ti-B refiner is 0.5 percent of the mass of the melt. And casting the melt into an ingot by the method of the comparative example 1, and then placing the ingot in a resistance furnace for homogenization heat treatment, wherein the homogenization temperature is 480 ℃ and the heat preservation time is 8 hours. And (4) carrying out multi-pass rolling after homogenization, wherein the deformation amount of each pass is 5%, and the total deformation amount is 50%, so as to obtain the regenerated wrought aluminum alloy.
FIG. 4 shows the as-cast optical microstructure of the wrought aluminum alloy prepared in comparative example 4, in which the morphology of the wrought aluminum alloy phase prepared in comparative example 4 by Sr/Al-5Ti-B complex treatment is changed, the dendritic structure is broken, the needle-like phase is transformed into Chinese character-like, and other impurity phases are transformed into ellipsoid-like phases distributed in the interior of the grains or in the grain boundary. The hot cracking sensitivity coefficient HTS of the alloy in an as-cast state is 160, the tensile strength is 200.2MPa, the elongation is 10.8 percent, and the hardness is 53.3 HB. The tensile strength of the alloy in the rolled state was 229.4MPa, the elongation was 7.5%, and the hardness was 69.6 HB.
Example 1
Preparation of Mg/Sr/C-containing refiner composite treated 6xxx series wrought aluminium alloys: the 6xxx series recycled aluminum scrap after primary screening is melted according to the method of the comparative example 1, the initial basic components are the same as the comparative example 1, the scum is removed, and the aluminum scrap is kept warm and kept stand for 20 min. Adding Mg ingot, Al-10Sr alterant and Al-5Ti-0.3B-0.2C refiner into the melt, keeping the temperature of the melt at 720 ℃, uniformly stirring after melting, and standing for 20min under heat preservation; wherein the addition amount of the Al-10Sr alterant is 0.6 percent of the mass of the melt, the addition amount of the Al-5Ti-0.3B-0.2C refiner is 0.7 percent of the mass of the melt, and the mass percentage content of Mg in the melt is adjusted to 1.2 percent after the Mg ingot is added. And refining and deslagging the melt according to the method of the comparative example 1, and casting the melt after refining and deslagging into a cast ingot. And then placing the cast ingot in a resistance furnace for homogenization heat treatment, wherein the homogenization temperature is 500 ℃, and the heat preservation time is 10 hours. And (4) carrying out multi-pass rolling after homogenization, wherein the deformation amount of each pass is 5%, and the total deformation amount is 50%, so as to obtain the regenerated wrought aluminum alloy.
FIG. 5 is the optical microstructure of the Mg/Sr/C refiner melt compounded wrought aluminum alloy of example 1, in which the rich iron phase structure is cross-linked and has good connection with the matrix, the needle phase is greatly reduced, and other impurity phases are ellipsoidal and uniformly distributed in the grain boundary and crystal. FIG. 7 is a thermal cracking test sample of CRC restraining bar for the wrought aluminum alloy of this example, where it can be seen that only the long and the second long arms cracked but not completely cracked, and the alloy was calculated to have a minimum thermal cracking susceptibility HTS of 122, which is 32% lower than that of the original wrought aluminum alloy of comparative example 1. Compared with the original regenerated wrought aluminum alloy of comparative example 1, the mechanical property of the alloy of the embodiment is remarkably improved, and the tensile strength and the hardness in the as-cast state are respectively improved by 25% and 21%. Under the condition of rolling state, the tensile strength of the alloy of the embodiment is 268.2MPa, the elongation is 8.3 percent, and the hardness is 93.8HB, so that compared with the original regenerated wrought aluminum alloy of the comparative example 1, the tensile strength and the hardness of the alloy of the embodiment under the rolling state are respectively improved by 33 percent and 47 percent. Therefore, the Mg/Sr/C-containing refiner composite treatment method for the 6xxx series regenerative wrought aluminum alloy melt can obviously reduce the hot cracking sensitivity of the alloy, improve the yield of castings and simultaneously improve the comprehensive mechanical property of the alloy.
Example 2
Preparation of Mg/Sr/C-containing refiner composite treated 6xxx series wrought aluminium alloys: the manufacturing method of this example 2 is similar to that of example 1 except that Mg ingot, Al-10Sr alterant and Al-5Ti-0.3B-0.2C refiner are added in different amounts. In example 2, the amount of Al-10Sr modifier added was 0.6% of the mass of the melt, the amount of Al-5Ti-0.3B-0.2C refiner added was 0.3% of the mass of the melt, and the mass percentage of Mg in the melt was adjusted to 1.0% after the addition of Mg ingot.
The optical microstructure of the wrought aluminum alloy of this example is similar to the microstructure of the wrought aluminum alloy of example 1, but the eutectic structure of this example is reduced and the acicular dendrites are broken. The alloy of this example has a hot crack susceptibility HTS of 130, a tensile strength of 207.3MPa, an elongation of 9.7% and an as-cast hardness of 54.5HB as cast. The alloy of this example, when rolled, had a tensile strength of 254.8MPa, an elongation of 7.9%, and a hardness of 84.1 HB. Compared with the original regenerated wrought aluminum alloy of comparative example 1, the hot cracking sensitivity coefficient of the alloy of the embodiment is reduced by 27%, and the rolling tensile strength and hardness are respectively improved by 26% and 32%. Namely, the embodiment realizes the comprehensive improvement of the heat cracking resistance and the mechanical property of the regenerated aluminum alloy at low cost (low-content additive composite treatment).
Example 3
Preparation of Mg/Sr/C-containing refiner composite treated 6xxx series wrought aluminium alloys: the manufacturing method of this example 3 is similar to that of example 1 except that Mg ingot, Al-10Sr alterant and Al-5Ti-0.3B-0.2C refiner are added in different amounts. In example 3, the amount of Al-10Sr modifier added was 0.2% of the mass of the melt, the amount of Al-5Ti-0.3B-0.2C refiner added was 0.5% of the mass of the melt, and the mass percentage of Mg in the melt was adjusted to 1.2% after the addition of Mg ingot.
The optical microstructure of the wrought aluminum alloy prepared in this example is similar to that of the wrought aluminum alloy prepared in example 1, and the grains are refined and the eutectic structure is distributed around the grain boundaries in a dotted or blocky manner. The alloy of this example has a hot crack susceptibility HTS of 126, a tensile strength of 218.9MPa, an elongation of 10.4% and an as-cast hardness of 57.6HB in the as-cast condition. The alloy of this example has a tensile strength of 257.1MPa, an elongation of 7.2% and a hardness of 89.4HB when rolled. Compared with the original regenerated wrought aluminum alloy of the comparative example 1, the hot cracking sensitivity coefficient of the alloy of the embodiment is reduced by 29%, and the as-cast tensile strength and the hardness are respectively improved by 22% and 20%; the tensile strength and the hardness in a rolling state are respectively improved by 27 percent and 40 percent.
Example 4
Preparation of Mg/Sr/C-containing refiner composite treated 6xxx series wrought aluminium alloys: the manufacturing method of this example 4 is similar to that of example 1 except that Mg ingot, Al-10Sr alterant and Al-5Ti-0.3B-0.2C refiner are added in different amounts. In example 4, the amount of Al-10Sr modifier added was 0.2% of the mass of the melt, the amount of Al-5Ti-0.3B-0.2C refiner added was 0.3% of the mass of the melt, and the mass percentage of Mg in the melt was adjusted to 1.0% after the addition of Mg ingot.
The optical microstructure of the wrought aluminum alloy of this example is similar to that of the wrought aluminum alloy of example 1, but the acicular phase of this example is increased. The alloy of the embodiment has a hot cracking sensitivity coefficient HTS of 134, a tensile strength of 208.4MPa and an elongation of 10.6 percent in an as-cast state; the as-cast hardness was 53.7 HB. The alloy of this example has a tensile strength of 260.5MPa, an elongation of 7.6% and a hardness of 87.5HB when rolled. Compared with the original regenerated wrought aluminum alloy of the comparative example 1, the hot cracking sensitivity coefficient of the alloy of the embodiment is reduced by 25%, and the as-cast tensile strength and the hardness are respectively improved by 17% and 12%; the tensile strength and the hardness in a rolling state are respectively improved by 29 percent and 37 percent.
Example 5
Preparation of Mg/Sr/C-containing refiner composite treated 6xxx series wrought aluminium alloys: the manufacturing method of this example 5 is similar to that of example 1 except that Mg ingot, Al-10Sr alterant and Al-5Ti-0.3B-0.2C refiner are added in different amounts. In example 5, the amount of Al-10Sr modifier added was 0.4% of the mass of the melt, the amount of Al-5Ti-0.3B-0.2C refiner added was 0.5% of the mass of the melt, and the mass percentage of Mg in the melt was adjusted to 1.4% after the addition of Mg ingot.
The optical microstructure of the wrought aluminum alloy of this example was similar to that of the wrought aluminum alloy of example 1, but the eutectic structure of this example was increased, and a portion of the bulk eutectic structure appeared to be concentrated around the grain boundaries. The alloy of this example has a hot crack susceptibility HTS of 128, a tensile strength of 218.2MPa, an elongation of 9.9% and an as-cast hardness of 61HB in the as-cast state. The alloy of this example has a tensile strength of 265MPa, an elongation of 7.3% and a hardness of 92.4HB when rolled. Compared with the original regenerated wrought aluminum alloy of the comparative example 1, the hot cracking sensitivity coefficient of the alloy of the embodiment is reduced by 28%, and the as-cast tensile strength and the hardness are respectively improved by 22% and 27%; the tensile strength and the hardness in a rolling state are respectively improved by 31 percent and 45 percent.
For better comparison of the effects of the examples, FIG. 8 shows the results of summarizing the coefficients of thermal cracking tendency of the ingots of wrought aluminum alloys produced in the comparative examples and examples. As can be seen from FIG. 8, the coefficient of thermal cracking tendency of the comparative example alloy decreased by 7% to 13%, while that of the example alloy decreased by 20% to 32%. The result shows that the casting process stability of the regenerated wrought aluminum alloy is further improved after the melt composite treatment of the invention.
Tables 1 and 2 show the results of summarizing the mechanical properties of the wrought aluminum alloys produced in the comparative examples and examples, respectively.
TABLE 1
TABLE 2
As can be seen from Table 1, the cast tensile strength of the comparative alloy is improved by 5-10%, and the cast tensile strength of the comparative alloy is improved by 15-25% in the examples; the hardness of the alloy in the comparative example is improved by 7-15%, the hardness of the alloy in the embodiment is improved by 25-30%, and the improvement effect of the embodiment is obvious. The 6xxx series alloy belongs to wrought aluminum alloy, rolling deformation treatment is needed in the processing process, and the mechanical properties of the alloy after rolling are summarized in table 2. As can be seen from Table 2, the rolling tensile strength of the comparative example alloy is improved by 5-10%, and the rolling tensile strength of the example alloy is improved by 25-35%; the hardness of the alloy of the comparative example is improved by 5-20 percent, and the hardness of the alloy of the embodiment is improved by 30-45 percent. The result shows that the mechanical property of the regenerated wrought aluminum alloy is obviously improved after the melt composite treatment of the invention.
Finally, it should be noted that the above embodiments are only used for illustrating the technical solutions of the present invention and not for limiting the protection scope of the present invention, and although the present invention is described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that modifications or equivalent substitutions can be made on the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention.
Claims (8)
1. The composite treatment method of the regenerated wrought aluminum alloy melt is characterized by comprising the following steps of:
(1) melting 6xxx series waste aluminum, and obtaining a regenerated wrought aluminum alloy melt after slagging-off;
(2) adding a metal Mg, an Al-Ti series refiner and an Al-10Sr alterant into the melt obtained in the step (1) for composite treatment, uniformly stirring after melting, and standing at a constant temperature;
(3) refining and deslagging the melt obtained in the step (2), and preserving heat and standing after deslagging;
(4) casting and molding the melt obtained in the step (3) to obtain a regenerated wrought aluminum alloy ingot;
(5) carrying out homogenization heat treatment on the aluminum alloy ingot obtained in the step (4) to obtain a cast plate;
(6) performing multi-pass rolling on the cast plate obtained in the step (5) to obtain a regenerated wrought aluminum alloy;
the adding amount of the Al-Ti series refiner accounts for 0.3-0.7% of the mass of the melt, the adding amount of the Al-10Sr alterant accounts for 0.2-0.6% of the mass of the melt, and the mass percentage content of Mg in the melt after the metal Mg is added is 0.8-1.4%; the Al-Ti series refiner is a C-containing refiner; the temperature of the composite treatment is 720-750 ℃, and the time of heat preservation and standing is 10-20 min.
2. The method for compositely treating a wrought aluminum alloy melt according to claim 1, wherein the C-containing refiner comprises the following components in mass fraction: 4.5 to 5.5 percent of Ti, 0.25 to 0.35 percent of B and 0.15 to 0.25 percent of C.
3. The composite treatment method of the renewable wrought aluminum alloy melt as claimed in claim 1, wherein in the step (3), the refining deslagging treatment is to add a refining agent and a deslagging agent into the melt, the treatment temperature is controlled to be 720-750 ℃, and the treatment time is 10-20 min.
4. The method of compositely treating a wrought aluminum alloy melt according to claim 3, wherein the refining agent and the slag-forming agent are added by blowing.
5. The composite treatment method of the wrought aluminum alloy melt as claimed in claim 3, wherein in the step (3), the total addition amount of the refining agent and the slag striking agent is 1% of the melt mass, and the mass ratio of the refining agent to the slag striking agent is 1: 4.
6. the composite treatment method of the wrought aluminum alloy melt of claim 1, wherein in step (5), the homogenizing heat treatment process comprises: the temperature is 480-500 ℃, and the heat preservation time is 8-12 h.
7. The method for producing a wrought aluminum alloy according to claim 1, wherein in step (6), the rolling process comprises: the maximum deformation of each pass is 10 percent, and the total deformation is 50 percent.
8. A6 xxx series wrought aluminum alloy produced by a composite treatment method of the wrought aluminum alloy melt of any of claims 1-7.
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| CN112662922A (en) * | 2020-12-11 | 2021-04-16 | 清远市正通金属制品有限公司 | Regenerated deformation aluminum alloy melt |
| CN113151717A (en) * | 2021-03-24 | 2021-07-23 | 辽宁忠旺集团有限公司 | 6063 aluminum alloy casting and production process thereof |
| CN114323848B (en) * | 2021-12-22 | 2023-01-17 | 河北新立中有色金属集团有限公司 | Preparation method of casting aluminum alloy 360Z.3 as-cast spectrum single-point standard sample |
| CN115058618A (en) * | 2022-06-29 | 2022-09-16 | 铜山县丰华工贸有限公司 | Slag remover for aluminum alloy smelting |
| CN115216662A (en) * | 2022-08-18 | 2022-10-21 | 山东南山铝业股份有限公司 | Production method of circulation-guaranteed 8-series unscrewing cover material |
| CN115896514B (en) * | 2022-12-14 | 2023-05-23 | 中信戴卡股份有限公司 | Preparation method of aluminum alloy casting |
| CN115976352A (en) * | 2023-02-14 | 2023-04-18 | 湖南中创空天新材料股份有限公司 | Method for preparing wrought aluminum alloy by utilizing recycled aluminum |
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