CN111945040B - Al-Si-Cu-Mg-Zr aluminum alloy and short-process heat treatment process thereof - Google Patents
Al-Si-Cu-Mg-Zr aluminum alloy and short-process heat treatment process thereof Download PDFInfo
- Publication number
- CN111945040B CN111945040B CN202010855258.5A CN202010855258A CN111945040B CN 111945040 B CN111945040 B CN 111945040B CN 202010855258 A CN202010855258 A CN 202010855258A CN 111945040 B CN111945040 B CN 111945040B
- Authority
- CN
- China
- Prior art keywords
- alloy
- temperature
- furnace
- intermediate alloy
- aluminum
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Classifications
-
- 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
-
- C—CHEMISTRY; METALLURGY
- 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
- C22C1/026—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- 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
-
- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- 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
- C22F1/043—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 with silicon as the next major constituent
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
The invention discloses an Al-Si-Cu-Mg-Zr aluminum alloy and a short-process heat treatment process thereof, wherein the Al-Si-Cu-Mg-Zr aluminum alloy comprises the following elements in percentage by mass: si: 6.80-7.00%, Cu: 0.65-0.75%, Mg: 0.33 to 0.35%, Zr: 0.12-0.18%, Ti: 0.12-0.16%, Sr: 0.012-0.014%, except the above indicated element components, the total content of other metal and non-metal impurity elements is not more than 0.3%, and the balance is Al. The aluminum alloy is subjected to solution treatment at the charging temperature, so that the mechanical property of the alloy can be improved, the heat treatment time can be shortened, and the alloy can be used for manufacturing an auxiliary frame of an automobile chassis, so that the self weight of the automobile is greatly reduced.
Description
Technical Field
The invention belongs to the technical field of metal materials and preparation, and particularly relates to an Al-Si-Cu-Mg-Zr aluminum alloy and a short-flow heat treatment process thereof.
Background
In recent years, high-strength and light-weight aluminum alloys have become important research objects in the industrial field, particularly in the automobile industry. The hypoeutectic Al-Si alloy is the most common cast aluminum alloy, and has good fluidity and good casting performance due to high Si content. However, the conventional Al — Si alloy cannot be heat-treated for strengthening, which limits further improvement in mechanical properties thereof.
Usually, a trace amount of Mg element is added to achieve the purpose of heat treatment strengthening. Secondly, because of the high content of Si, acicular eutectic silicon can be produced in the casting process, the mechanical property of the alloy is seriously influenced, and Mg can be separated out from Mg and Si in the heat treatment process2The Si strengthening phase is a hard and brittle strengthening phase, can improve the strength of the alloy in a limited way, but seriously damages the ductility and toughness of the alloy, and needs to add alloy elements capable of achieving grain refinement and prepare a proper heat treatment process to improve the comprehensive mechanical property of the alloy; finally, the alloy is heated with the furnace at normal temperature or charged into the furnace for heat treatment at normal temperature, and the aluminum alloy usually contains multiple alloy elements and different compoundsThe solid solubility of the gold element in the aluminum alloy is greatly different along with the temperature change, the overall temperature of the sample rises slowly along with the temperature rise of the furnace, so that the solid solution efficiency is low, the heat preservation time needs to be prolonged to achieve the homogenization of the solid solution of the alloy element, the phenomenon is more obvious particularly for a large sample or a sample with high content of the alloy element, and the heat preservation time needs to be longer to achieve the complete sufficiency and uniformity of the solid solution of the alloy element; if the heat treatment process of the warm charging furnace is adopted, longer holding time is needed in the solid solution process to achieve dissolution and homogenization of alloy elements, and the formation of some strengthening phases is not facilitated.
Disclosure of Invention
In order to avoid the defects of the alloy components and the solid solution process, the invention provides a novel Al-Si-Cu-Mg-Zr aluminum alloy added with trace Cu and Zr elements and a short-flow heat treatment process thereof on the basis of the traditional Al-Si alloy containing Mg, Ti and other elements.
The Al-Si-Cu-Mg-Zr aluminum alloy comprises the following elements in percentage by mass:
si: 6.80-7.00%, Cu: 0.65-0.75%, Mg: 0.33 to 0.35%, Zr: 0.12-0.18%, Ti: 0.12-0.16%, Sr: 0.012-0.014%, except the above indicated element components, the total content of other metal and non-metal impurity elements is not more than 0.3%, and the balance is Al.
The invention discloses a short-flow heat treatment process of an Al-Si-Cu-Mg-Zr aluminum alloy, which sequentially comprises the following steps of material preparation, blanking, smelting, casting molding and the like:
step 1: preparation of alloy ingot
1a, preparing materials: weighing Al-Si intermediate alloy, Al-Mg intermediate alloy, Al-Cu intermediate alloy, Al-Sr intermediate alloy, Al-Zr intermediate alloy, Al-Ti intermediate alloy and industrial pure aluminum with the purity of 99.9% according to the proportion, and finishing the batching;
1b, preparing a coating according to the mixture ratio of sodium silicate nonahydrate (5%) + zinc oxide (15%) + water (the balance), uniformly coating the coating on a graphite clay crucible, a smelting tool and a mould, and preheating at 320 ℃;
1c, melting: firstly, adding Al-Si intermediate alloy into the bottom of a crucible preheated to 320 ℃ along with a furnace, then adding industrial pure aluminum, then heating to 720 ℃ along with the furnace, standing and preserving heat for 60-70 min; then adding Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Zr intermediate alloy, Al-Ti intermediate alloy and Al-Sr intermediate alloy into the molten alloy in sequence, standing and preserving heat for 10min after the alloys are completely molten;
1d, refining: rapidly removing dross on the surface layer of the alloy melt by using a skimming ladle, and adding C after skimming2Cl6(accounting for 1 percent of the total mass) refining and degassing, standing and preserving heat for 15min, and removing slag;
1e, pouring: keeping the temperature of the alloy melt for 10min after deslagging, and pouring the alloy melt into a metal mold preheated at 280 ℃ to obtain an alloy ingot;
step 2: solution treatment
And (2) putting the alloy ingot obtained in the step (1) into a furnace at the furnace temperature of 350-370 ℃, heating the alloy ingot to 535 ℃ along with the furnace, performing solid solution treatment, keeping the temperature for 120min, and then quenching the alloy ingot in warm water at the temperature of 60-80 ℃ for 15s, wherein the quenching treatment time is less than 10 s.
And step 3: aging treatment
And (3) aging the sample subjected to the solution treatment in the step (2) at 170 ℃ for 180 min.
The design basis of the method is as follows:
the conventional cast aluminum alloy is usually strengthened by adding trace alloying elements and controlling the heat treatment process. For adding alloy elements, Cu is used as a strong aging strengthening element, when the adding amount is small, a good strengthening effect can be achieved, the strength and hardness of the alloy are obviously improved, but the plasticity of the alloy is slightly reduced, Zr is a common grain refining element in the aluminum alloy, when the adding amount is small, the plasticity of the alloy can be improved while the strengthening of the alloy is improved, the adding amount is generally 0.1-0.2%, and if the adding amount is too large, the poisoning effect of Zr can be generated. On the other hand, if the amount of Cu element added is 0.8% or more, the strength of the alloy is significantly improved, but the plasticity of the alloy is extremely poor, and the alloy cannot be used normally, but if the amount of Cu element added is 0.Less than 6%, Al is hardly formed due to its high solid solubility in aluminum2In the Cu strengthening phase, the addition of Cu only produces solid solution strengthening, and the effect of strengthening the second phase cannot be achieved, so that the strengthening effect of the Cu element is seriously reduced. Therefore, the composite addition of 0.65-0.75% of Cu and 0.12% -0.18-Zr can make the alloy have Al with the volume fraction of 4:1 after heat treatment2Cu、Al3Zr strengthening phase, and Al2Cu、Al3The sizes of Zr particles are respectively 600nm and 200nm, Al2Al having Cu particle size ratio obtained by adding only Cu element2Smaller Cu particles (800-1000 nm), indicating Al3Zr particle pair Al2The Cu particles have a certain thinning effect, and on the one hand, Al2Cu can obviously improve the strength of the alloy, and on the other hand, Al3Zr can be used as a second phase nucleation point to play a role in refining grains, improve the plasticity of the alloy and improve the comprehensive performance of the alloy.
The Cu element has great solid solubility in the aluminum alloy, the solid solubility is extremely sensitive to the change of temperature, and the limit solid solubility can reach 0.5% at 350 ℃; at the temperature, the solid solubility of the Zr element is extremely low and can be ignored. Therefore, in the case of an aluminum alloy in which Cu and Zr are compositely added, the charging temperature during solution treatment greatly affects the effect of solution treatment (particularly solution treatment of large-sized industrial parts). The solution treatment temperature of the aluminum alloy is high, generally about 540 ℃, and if the temperature is raised along with a furnace, the heating time of several hours is needed. In the process of temperature rise along with the furnace, the overall temperature of the sample rises slowly, the heat treatment time is long, and the efficiency is low. If the sample is charged at the furnace temperature of 350-370 ℃, the temperature difference between the surface temperature of the sample and the furnace temperature is above 300 ℃, and the furnace temperature is continuously increased, the surface temperature of the sample quickly reaches above 350 ℃, the Cu element on the surface layer of the sample is dissolved into the aluminum matrix of the surface layer, and then the Cu element is gradually dissolved into the matrix from the surface layer to the core of the sample. At this time, because the ultimate solid solubility of Zr element at this temperature is very small, Zr element can not be dissolved into the matrix, and trace Zr element can only be slowly dissolved in the subsequent slow temperature riseSolid-soluted into the matrix. The Cu element can be basically dissolved in the matrix in the early-stage heating process, so that the heat preservation time of the subsequent solution treatment can be shortened. Because the time required for reaching the solid solution heat preservation temperature is much shorter than the time required for temperature rise along with the furnace from room temperature, and the scheme of short-time heat preservation is adopted during heat preservation, although Cu is dissolved into the matrix and is uniformly distributed, Zr is less dissolved into the matrix, and Al is mainly used3Zr is dispersed in the matrix, so that the performance of the alloy is improved; if the mode of entering the furnace at a warm state is adopted, the longer heat preservation time is needed for the dissolution and homogenization of the Cu element, and the more Zr is dissolved, which is not beneficial to the formation of the structure.
Compared with the prior art, the invention has the beneficial effects that:
1. the Al-Si-Cu-Mg-Zr aluminum alloy added with alloy elements such as Cu, Zr and the like is provided, wherein the content of Cu is 0.65-0.75%, the content of Zr is 0.12-0.18%, the poor alloy plasticity or the poisoning effect caused by the excessively high addition of Cu and Zr elements is avoided, and the second phase strengthening effect of Cu is not weakened caused by the low content of Cu. Cu and Zr are added compositely, and Al is precipitated after heat treatment2Cu、Al3Strengthening phase of Zr or the like, on the one hand, Al2Cu can obviously improve the strength of the alloy, and on the other hand, Al3Zr can be used as a second phase nucleation point to play a role in refining grains and improve the comprehensive performance of the alloy.
2. The alloy is charged into a furnace at the charging temperature of 350-370 ℃ for solution treatment, the Cu element can be basically dissolved into a matrix in the early-stage heating process, the subsequent solution treatment heat preservation time can be reduced, and the heat preservation time is shorter, so that although Cu is dissolved into the matrix and is uniformly distributed, Zr is less dissolved into the matrix, and Al is mainly used3Zr is dispersed in the matrix, thereby improving the performance of the alloy. The tensile strength of the alloy after the conventional heat treatment is 280MPa, and the elongation is 7%, while the tensile strength of the alloy can reach 305MPa at most under the heat treatment process, and the alloy keeps the elongation of 8.5% and has excellent comprehensive mechanical properties.
3. According to the short-flow heat treatment process of the aluminum alloy, different alloy elements are subjected to solid solution treatment at the charging temperature of 350-370 ℃, so that the different alloy elements are subjected to solid solution step by step into a matrix, complete solid solution is finally achieved, the heat preservation time of the solid solution treatment is shortened, the comprehensive performance of the alloy is ensured, and the effect of saving energy is achieved at the same time. Generally, the heat preservation time of the solution treatment along with the temperature rise of the furnace is more than 180min to achieve the purpose that the alloy elements are uniformly dissolved in the matrix, but the solution treatment process of the invention can achieve homogenization only by preserving the heat for 120min, and can shorten the solution time by more than 60 min.
Detailed Description
The Al-Si-Cu-Mg-Zr aluminum alloy in the embodiment comprises the following elements in percentage by mass:
si: 6.80-7.00%, Cu: 0.65-0.75%, Mg: 0.33 to 0.35%, Zr: 0.12-0.18%, Ti: 0.12-0.16%, Sr: 0.012-0.014%, except the above indicated element components, the total content of other metal and non-metal impurity elements is not more than 0.3%, and the balance is Al.
The elemental composition of the aluminum alloys in each example is shown in Table 1 below:
TABLE 1 alloy compositions and Heat treatment Processes for examples
Example 1:
this example prepares alloy specimens as follows:
1. preparation of alloy ingot
(1) And (3) ingredient calculation: weighing industrial pure aluminum, Al-Si intermediate alloy, Al-Mg intermediate alloy, Al-Cu intermediate alloy, Al-Ti intermediate alloy and Al-Zr intermediate alloy according to the mass percent of 91.98 percent of Al, 6.8 percent of Si, 0.65 percent of Cu, 0.33 percent of Mg, 0.12 percent of Zr, 0.12 percent of Ti and 0.012 percent of Sr to finish batching;
(2) preparing a coating according to the mixture ratio of sodium silicate nonahydrate (5%), zinc oxide (15%) and water (the balance), uniformly coating the coating on a graphite clay crucible, a smelting tool and a mould, and preheating at 320 ℃;
(3) melting: firstly, adding Al-Si intermediate alloy into the bottom of a crucible preheated with a furnace at 320 ℃, then adding industrial pure aluminum, then heating with the furnace to 720 ℃, standing and preserving heat for 20-30min after the alloy is completely melted; and then sequentially adding Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Zr intermediate alloy, Al-Ti intermediate alloy and Al-Sr intermediate alloy into the molten alloy, standing and keeping the temperature for 10min after the alloys are completely molten.
(4) Refining: rapidly removing dross on the surface layer of the melt by using a skimming ladle, and adding C after skimming2Cl6Refining and degassing (accounting for 1 percent of the total mass), standing and preserving heat for 20min, and removing slag;
(5) pouring: keeping the temperature of the molten aluminum for 10min after deslagging, and pouring the molten aluminum into a metal mold preheated at 280 ℃ to obtain an ingot;
2. and (2) heating the as-cast alloy obtained in the step (1) to 535 ℃ at the furnace temperature of 350 ℃ for solution treatment, keeping the temperature for 120min, and then quenching in warm water at 60-80 ℃ for 15s, wherein the quenching time is less than 10 s.
3. And (3) aging the sample subjected to the solution treatment in the step (2) at 170 ℃ for 180 min.
Example 2:
the preparation process of this example is as shown in example 1, except that alloy components and heat treatment process are shown in table 1, and alloy samples are obtained.
Example 3:
the preparation process of this example is as shown in example 1, except that alloy components and heat treatment process are shown in table 1, and alloy samples are obtained.
Example 4:
the preparation process of this example is as shown in example 1, except that alloy components and heat treatment process are shown in table 1, and alloy samples are obtained.
Example 5:
the preparation process of this example is as shown in example 1, except that alloy components and heat treatment process are shown in table 1, and alloy samples are obtained.
In example 1, the mass percentage of Si was 6.80%, which can ensure that the Si content was relatively highThe fluidity and the casting performance of the alloy are better; 0.33% Mg can form Mg with Si2The strengthening phases such as Si and the like ensure that the alloy has certain strength, and meanwhile, the addition of 0.65 percent of Cu can form a large amount of Al after solid solution aging2The Cu strengthening phase, 0.12% Ti and 0.12% Zr may form Al3Ti、Al3Zr and Al3The strengthening phases (Ti, Zr) and the like play roles in refining crystal grains and improving the structure, and ensure that the alloy has higher strength and certain ductility and toughness. In addition, the temperature of the cast alloy sample is increased to 535 ℃ at 350 ℃ for solution treatment for 120min, Cu element is firstly dissolved into the matrix from outside to inside along with the increase of the temperature of the sample, then the temperature of the sample is continuously increased, and Zr element is gradually dissolved into the matrix, so that the Cu alloy element and the Zr alloy element are sequentially dissolved into the matrix, and the subsequent heat preservation time can be shortened. Performing a tensile test on the alloy sample subjected to heat treatment on a CMT-5105 electronic universal tester, wherein the tensile rate is 2mm/min, the test result is the average value of three independent measurements, and the mechanical property index of the obtained sample is as follows: the tensile strength was 292MPa, and the elongation was 8.1%.
In example 2, the content of Si was 6.8%, and the castability thereof could be secured. Compared with the embodiment 1, the contents of Cu and Zr are both improved, and the contents of Cu and Zr are improved, so that the alloy can form more strengthening phases, and the mechanical property of the alloy is further improved; and the alloy sample is charged in a furnace at the furnace temperature of 360 ℃ for heat treatment, Cu and Zr elements are sequentially dissolved in the matrix in a solid mode, and then the strengthening effect of the alloy elements can be improved after aging treatment at 170 ℃ for 180 min. The mechanical property indexes of the obtained sample after heat treatment are as follows: the tensile strength was 296MPa, and the elongation was 8.2%.
In example 3, the content of Si is still 7.00%, compared with example 1, the content of Cu is increased by 15.4%, the content of Zr is increased by 25%, and the increase of the content of Cu and Zr is more beneficial to the alloy to generate more Al after heat treatment3Zr and other strengthening phases. The alloy casting after smelting and casting is charged in a furnace at the furnace temperature of 370 ℃ for solution treatment, and at the moment, the temperature difference between the surface of the sample and the furnace temperature can enable the Cu element on the surface of the sample to start solution treatment firstlyThe Cu element on the surface can start to be homogenized while the Cu element is dissolved in the solution, and the Cu element is almost completely dissolved during the solution heat preservation time, only trace Zr element and other alloy elements are dissolved in the solution, so that the heat preservation time of the solution is effectively reduced. After the alloy sample is subjected to artificial aging treatment, the time-effect precipitated phase dispersity of the alloy sample is obviously improved, the age hardening effect is improved, and the alloy is ensured to have better strength and elongation. The tensile strength of the alloy sample after heat treatment is 305MPa, the elongation is 8.5%, compared with the previous two groups of examples, the comprehensive performance of the alloy can be improved by adding 0.18% of Zr element, and the heat treatment time can be shortened by matching with the proper charging temperature, so that the purpose of saving energy is achieved.
In example 4, the contents of the various alloying elements were the same as those in example 2, but the charging temperature was 360 ℃ and the same as that in example 1, and the alloy had good castability in terms of alloy composition, and the alloy was charged into the furnace at a furnace temperature of 360 ℃ and then heated to 535 ℃ with the furnace for solution treatment, and after the heat treatment, the alloy was able to precipitate a large amount of Al2Cu、Al3Strengthening phases such as Zr, etc., and further improves the performance of the alloy. The tensile strength of the alloy sample after heat treatment is 298MPa, and the elongation is 8.2%.
In example 5, the alloy composition was kept the same as in example 3, and the charging temperature of the alloy was kept the same as in example 1, and the alloy was charged at 350 ℃ and heated to 535 ℃ with the furnace to perform solution treatment. The alloy is subjected to 535 ℃ solution treatment for 120min, and then is artificially aged for 180min at 170 ℃, the tensile strength is 300MPa, the elongation is 8.3%, and compared with the examples, the aluminum alloy provided by the invention is charged at the charging temperature of the invention for heat treatment, the mechanical property is stable, and the comprehensive mechanical property is high.
Claims (3)
1. An Al-Si-Cu-Mg-Zr aluminum alloy is characterized by comprising the following elements in percentage by mass:
si: 6.80-7.00%, Cu: 0.65-0.75%, Mg: 0.33 to 0.35%, Zr: 0.12-0.18%, Ti: 0.12-0.16%, Sr: 0.012-0.014%, except the above indicated element components, the total content of other metal and non-metal impurity elements is not more than 0.3%, and the balance is Al;
the Al-Si-Cu-Mg-Zr aluminum alloy is prepared by a method comprising the following steps:
step 1: preparation of alloy ingot
1a, preparing materials: weighing Al-Si intermediate alloy, Al-Mg intermediate alloy, Al-Cu intermediate alloy, Al-Sr intermediate alloy, Al-Zr intermediate alloy, Al-Ti intermediate alloy and industrial pure aluminum with the purity of 99.9% according to the proportion, and finishing the batching;
1b, uniformly coating the coating on a graphite clay crucible, a smelting tool and a mould, and preheating at 320 ℃;
1c, melting: firstly, adding Al-Si intermediate alloy into the bottom of a crucible preheated to 320 ℃ along with a furnace, then adding industrial pure aluminum, then heating to 720 ℃ along with the furnace, standing and preserving heat for 60-70 min; then adding Al-Cu intermediate alloy, Al-Mg intermediate alloy, Al-Zr intermediate alloy, Al-Ti intermediate alloy and Al-Sr intermediate alloy into the molten alloy in sequence, standing and preserving heat for 10min after the alloys are completely molten;
1d, refining: rapidly removing dross on the surface layer of the alloy melt by using a skimming ladle, and adding C after skimming2Cl6Refining, degassing, standing, keeping the temperature for 15min, and removing residues;
1e, pouring: keeping the temperature of the alloy melt for 10min after deslagging, and pouring the alloy melt into a metal mold preheated at 280 ℃ to obtain an alloy ingot;
step 2: solution treatment
Putting the alloy ingot obtained in the step 1 into a furnace at the furnace temperature of 350-370 ℃, heating the alloy ingot to 535 ℃ along with the furnace for solution treatment, keeping the temperature for 120min, and then quenching the alloy ingot in warm water at the temperature of 60-80 ℃ for 15s, wherein the quenching treatment time is less than 10 s;
and step 3: aging treatment
And (3) carrying out aging treatment on the sample subjected to the solution treatment in the step (2).
2. The Al-Si-Cu-Mg-Zr aluminum alloy according to claim 1, characterized in that:
in the step 1b, the coating is formed by compounding sodium silicate nonahydrate, zinc oxide and water.
3. The Al-Si-Cu-Mg-Zr aluminum alloy according to claim 1, characterized in that:
and in the step 3, the temperature of the aging treatment is 170 ℃, the time is 180min, and the steel is discharged from the furnace and cooled in air.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010855258.5A CN111945040B (en) | 2020-08-24 | 2020-08-24 | Al-Si-Cu-Mg-Zr aluminum alloy and short-process heat treatment process thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010855258.5A CN111945040B (en) | 2020-08-24 | 2020-08-24 | Al-Si-Cu-Mg-Zr aluminum alloy and short-process heat treatment process thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111945040A CN111945040A (en) | 2020-11-17 |
| CN111945040B true CN111945040B (en) | 2021-12-10 |
Family
ID=73359208
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010855258.5A Active CN111945040B (en) | 2020-08-24 | 2020-08-24 | Al-Si-Cu-Mg-Zr aluminum alloy and short-process heat treatment process thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111945040B (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112941377B (en) * | 2021-01-28 | 2022-09-30 | 北京工业大学 | Er-containing cast heat-resistant Al-Si-Cu-Mg alloy |
| CN113667865B (en) * | 2021-08-30 | 2022-08-30 | 合肥工业大学 | Preparation process of hypoeutectic Al-Si-Mg-Ge casting alloy |
| CN114250388B (en) * | 2021-12-29 | 2022-08-02 | 北京理工大学 | High-strength cast aluminum-silicon alloy part with complex shape for automobile and preparation method thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101338395A (en) * | 2007-07-06 | 2009-01-07 | 日产自动车株式会社 | Casting aluminum alloy and internal combustion engine cylinder head |
| CN104073699A (en) * | 2014-06-25 | 2014-10-01 | 衢州职业技术学院 | Al-Si-Cu-Mg cast aluminum alloy and preparation method thereof |
| KR20150127887A (en) * | 2014-05-07 | 2015-11-18 | 한국기계연구원 | Aluminum alloy with excellent castability and mechanical property and method of manufacturing thereof |
| CN106048330A (en) * | 2010-06-16 | 2016-10-26 | 诺尔斯海德公司 | Castable heat resistant aluminium alloy |
| CN108251715A (en) * | 2018-02-08 | 2018-07-06 | 山东弗泽瑞金属科技有限公司 | Suitable for the aluminum alloy materials of vacuum low speed pressure casting method |
| CN108588513A (en) * | 2018-08-10 | 2018-09-28 | 合肥工业大学 | A kind of modified A356 aluminium alloys and its multiple ageing hot processing method |
-
2020
- 2020-08-24 CN CN202010855258.5A patent/CN111945040B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101338395A (en) * | 2007-07-06 | 2009-01-07 | 日产自动车株式会社 | Casting aluminum alloy and internal combustion engine cylinder head |
| CN106048330A (en) * | 2010-06-16 | 2016-10-26 | 诺尔斯海德公司 | Castable heat resistant aluminium alloy |
| KR20150127887A (en) * | 2014-05-07 | 2015-11-18 | 한국기계연구원 | Aluminum alloy with excellent castability and mechanical property and method of manufacturing thereof |
| CN104073699A (en) * | 2014-06-25 | 2014-10-01 | 衢州职业技术学院 | Al-Si-Cu-Mg cast aluminum alloy and preparation method thereof |
| CN108251715A (en) * | 2018-02-08 | 2018-07-06 | 山东弗泽瑞金属科技有限公司 | Suitable for the aluminum alloy materials of vacuum low speed pressure casting method |
| CN108588513A (en) * | 2018-08-10 | 2018-09-28 | 合肥工业大学 | A kind of modified A356 aluminium alloys and its multiple ageing hot processing method |
Also Published As
| Publication number | Publication date |
|---|---|
| CN111945040A (en) | 2020-11-17 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN111945040B (en) | Al-Si-Cu-Mg-Zr aluminum alloy and short-process heat treatment process thereof | |
| CN112143945B (en) | High-strength and high-toughness cast aluminum-silicon alloy containing multiple composite rare earth elements and preparation method thereof | |
| CN108396204B (en) | Hypoeutectic aluminum-silicon alloy casting and process method for improving performance thereof | |
| CN109778027B (en) | Preparation method of high-strength A356 alloy | |
| CN111155000A (en) | Rapid heat treatment strengthening high-strength and high-toughness aluminum alloy material for die-casting thin-walled piece and preparation method and application thereof | |
| CN112662921B (en) | High-strength and high-toughness die-casting aluminum-silicon alloy and preparation method thereof | |
| WO2024021367A1 (en) | Cast al-si alloy and preparation method thereof | |
| CN111519071A (en) | Novel high-strength and high-toughness die-casting aluminum alloy with remarkable ultrashort aging characteristic and preparation method thereof | |
| CN112680615B (en) | Preparation method, heat treatment method and die-casting method of high-strength and high-toughness die-casting aluminum alloy material | |
| CN111763856B (en) | Hypoeutectic Al-Si-Mg-Ti-Sn casting alloy and preparation method thereof | |
| CN111690844B (en) | Eutectic Al-Fe-Mn-Si-Mg die casting alloy and preparation method and application thereof | |
| CN115418537B (en) | Heat treatment-free die-casting aluminum alloy and preparation method and application thereof | |
| CN108441659B (en) | Smelting process of high-strength high-toughness die-casting A356 aluminum alloy | |
| CN115044810A (en) | Aluminum alloy, preparation method thereof and automobile material | |
| CN114214534A (en) | Modified aluminum alloy and preparation method thereof | |
| CN114293044B (en) | High-plasticity composite modified aluminum alloy part and preparation method thereof | |
| CN117026023A (en) | Heat-treatment-free high-strength high-toughness die-casting aluminum alloy and preparation method thereof | |
| CN112626362B (en) | Preparation method of Al-Mg series cast heat-resistant aluminum alloy | |
| CN113667864A (en) | Preparation process of Al-Si-Mg-B-Mn casting alloy with excellent fluidity | |
| CN109182804A (en) | A kind of high intensity aluminum bronze line aluminium alloy preparation method | |
| CN112522557A (en) | High-strength and high-toughness die-casting aluminum alloy material | |
| WO2018099272A1 (en) | Semisolid die-casting aluminum alloy and method for preparing semisolid die-casting aluminum alloy castings | |
| CN108866460B (en) | Aging process of Al-Si-Mg-Zr-Ti-Sc alloy | |
| CN110408821B (en) | Al-Si-Zn-Mg-Ti alloy and manufacturing method thereof | |
| CN113046606B (en) | Aluminum alloy, preparation method thereof and aluminum alloy structural part |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |