CN113061787A - High-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti series casting alloy and preparation method thereof - Google Patents
High-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti series casting alloy and preparation method thereof Download PDFInfo
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Abstract
The invention belongs to the technical field of nonferrous metals, and relates to a high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti series casting alloy which comprises the following components in percentage by mass: 7.0-8.5% of Si, 0.5-1.0% of Cu, 0.35-0.5% of Mg, 0.1-0.3% of Cr, 0.1-0.2% of Mn, 0.1-0.15% of Ti, 0.015-0.025% of Sr, less than or equal to 0.15% of the total amount of other impurities and the balance of Al. The invention also discloses a manufacturing method of the alloy, which is characterized in that a water-cooling copper mold is adopted for casting, the type and content of alloy elements and a heat treatment process are regulated, the Cu element is added to enable the alloy to generate second-phase reinforcement, the Ti element refines crystal grains, the Mn element and the Cr element improve the appearance of an iron-rich phase, the mechanical property of the alloy is greatly improved, the tensile strength is 330-355 MPa, the yield strength is 210-275 MPa, and the elongation after fracture is 7-13%. The manufacturing process disclosed by the invention is simple and feasible, the raw materials are easy to obtain, the production cost is low, the mechanical property of the alloy can be improved by regulating and controlling the element content and the heat treatment process, and the method has a very large application prospect in the automobile hub manufacturing industry.
Description
Technical Field
The invention belongs to the technical field of nonferrous metals, relates to an aluminum alloy, and particularly relates to a high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti series casting alloy and a preparation method thereof.
Background
With the increasing requirements on energy conservation and emission reduction of automobiles and the development of new energy automobiles, the requirement on light weight of the automobiles is more urgent, and higher requirements are also provided. The lightweight automobile can reduce the production cost, reduce the running resistance and oil consumption, save energy and protect the environment, and is a common target of automobile design and production personnel.
The wheel is of a great importance for the automobile, and is an important part for transmitting power during the running process of the automobile. The reduction of the weight of the wheel can be started from the material and the design, and one way is to optimize the structural design of the wheel. Under the condition that the material and the specification (the size and the width of an outer circle) of the wheel are fixed, the weight of the wheel is reduced, and only the thickness of a wheel rim and the size of a wheel spoke can be reduced. The wheel is one of important parts for bearing the weight of the automobile and is one of key parts for ensuring the driving stability and safety of the automobile, and when the sizes of the rim and the spoke are too small, the strength and toughness required by the wheel cannot be met, so that safety accidents are easily caused. Therefore, the development of a hub with more excellent mechanical properties is urgently needed.
The A356.2(ZL101) aluminum alloy is a heat-treatable reinforced cast aluminum alloy, has high specific strength, good casting performance, excellent corrosion resistance and heat treatment performance, is widely used for manufacturing automobile wheels, and the manufactured wheel hub has the characteristics of light weight, attractive appearance, corrosion resistance, long service life and the like, but has lower mechanical property, and the tensile strength in the T6 state is only 270MPa, so that the application of the alloy is greatly limited. Alloying, refining modification treatment and heat treatment are the main methods for greatly improving the mechanical property and ensuring the economical efficiency on the basis of keeping the original excellent characteristics of A356.2.
CN110592438A discloses a formula and a preparation method of a high-performance A356 aluminum alloy, wherein Ti and Sr elements are added into the alloy in a reasonable proportioning mode, and Fe, Ca, Zn, Mn, Ni, P and Cu elements are controlled on a reasonable low content level, so that the obtained as-cast alloy has uniform structure, tensile strength of 220MPa, yield strength of 198MPa and elongation of 8.1, and the strength and toughness are improved, and the demand of market development can be well met. However, the mechanical property of the alloy is improved to a small extent and is to be further improved.
CN110184503A discloses a refiner for refining aluminum alloy grains by using aluminum yttrium as a refiner, so as to obtain an aluminum alloy with more excellent mechanical properties to meet the requirements of the fields of wheels and the like, wherein the aluminum alloy refiner comprises 8098% of aluminum (Al) and 220% of yttrium (Y) by atomic percentage, so that the tensile strength of the alloy is 314.2MPa, the yield strength is 243.8MPa, the elongation is 8.9%, and the mechanical properties are greatly improved. However, yttrium belongs to rare earth elements, has high cost and is not suitable for industrial large-scale production.
The CN110952048A patent discloses a heat treatment method suitable for a356.2 alloy low-pressure cast hub, which comprises the following steps: homogenizing the low-pressure cast hub at the temperature of 440-. The heat treatment method improves the comprehensive mechanical property of the low-pressure cast hub, and has the tensile strength of 272MPa, the yield strength of 213MPa and the elongation after fracture of 9 percent. But modification treatment is not carried out at the early stage of the alloy, and the mechanical property has a space for further improvement.
Therefore, in view of the production cost and mechanical property of the alloy, the development of a high-strength, high-toughness and low-cost alloy is needed to meet the requirement of the aluminum alloy wheel hub for the automobile.
Disclosure of Invention
Aiming at the defects of insufficient mechanical properties and higher cost of the existing aluminum alloy, the invention aims to provide a high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti alloy for solving the problem of light weight of an automobile hub.
A high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti series casting alloy comprises the following components in percentage by mass: 7.0-8.5% of Si, 0.5-1.0% of Cu, 0.35-0.5% of Mg, 0.1-0.3% of Cr, 0.1-0.2% of Mn, 0.1-0.15% of Ti, 0.015-0.025% of Sr, less than or equal to 0.15% of the total amount of other impurities and the balance of Al.
In the preferred embodiment of the invention, the alloy comprises the following components in percentage by mass: 7.4% of Si, 0.6% of Cu, 0.45% of Mg, 0.2% of Cr, 0.15% of Mn, 0.1% of Ti, 0.02% of Sr and the balance of Al.
According to the high-strength and high-toughness cast aluminum alloy disclosed by the invention, a casting is subjected to tensile sample according to the national standard GB/T228.1-2010, the tensile strength is 330-355 MPa, the yield strength is 210-275 MPa, and the elongation after fracture is 7-13%.
Another object of the present invention is to disclose a method for preparing the above Al-Si-Cu-Mg-Cr-Mn-Ti based casting alloy, comprising the steps of:
(1) weighing: weighing corresponding raw materials according to the chemical components and the mass fraction of the alloy, wherein the raw materials comprise: 99.99% Al, Al-20Si, pure Mg blocks, Al-50Cu, Al-5Cr, Al-10Mn, Al-10Ti, Al-5Ti-1B and Al-10 Sr;
(2) smelting: putting the graphite crucible filled with the corresponding quality of pure aluminum into a resistance furnace for heating, sequentially adding an intermediate alloy, a refining agent and a slag removing agent after the graphite crucible is completely melted, removing slag, and finally casting into a water-cooled copper mold to obtain an aluminum alloy ingot;
(3) solution treatment: putting the aluminum alloy cast ingot into a medium temperature furnace at 540-550 ℃, preserving heat for 5-6 h, and then putting the aluminum alloy cast ingot into hot water at 70-90 ℃ for quenching;
(4) aging treatment: and (3) placing the quenched aluminum alloy ingot into an aging furnace at 170-180 ℃ for heat preservation for 2-4 h, and finally air cooling.
In the better disclosed example of the invention, the 99.99 percent of Al and the pure magnesium blocks are weighed in the step (1) and 5 percent of Al and pure magnesium blocks are additionally weighed to make up the burning loss of the melt.
In the preferred embodiment of the invention, the step (2) of smelting is to put a graphite crucible filled with pure aluminum with corresponding quality into a resistance furnace for heating, after the graphite crucible is completely melted and the temperature of the molten aluminum reaches 720-740 ℃, add intermediate alloy of Al-20Si, Al-50Cu, Al-10Mn, Al-10Ti and Al-5Cr, keep the temperature for 15-20 min, then cool the temperature to 700-720 ℃, add pure Mg blocks, when the temperature of the melt is returned to 710-720 ℃, keep the temperature for 10min, then add refining agent and slag-removing agent, the adding amount of the refining agent and the slag-removing agent is 0.4% and 0.35% of the mass of the melt respectively, keep the temperature for 10-15 min, then remove the slag, add 0.2% Al-5Ti-1B and 0.2% Al-10Sr, control the temperature of the melt at 700-710 ℃ after stirring, keep the temperature for 10-15 min, and then cast the melt into a water-cooled copper mold, thus obtaining the aluminum alloy ingot.
In the preferred embodiment of the invention, when the refining agent is added in the step (2), the refining agent is pressed into the bottom of the crucible by the graphite rod, so that the gas in the melt is fully escaped; when the slag removing agent is added, the slag removing agent is uniformly scattered on the surface of the melt, the mixture is fully stirred, the lumps on the melt are broken as much as possible, and then slag is removed.
In the alloy composition disclosed by the invention, the addition of the Cu element can reduce the Secondary Dendritic Arm Spacing (SDAS) of alpha-Al, and the reduction of the SDAS can effectively improve the mechanical property of the alloy; the Cu element can also form a plurality of precipitated phases (Al2Cu and Al-Si-Mg-Cu) in the Al-Si-Mg alloy, and the existence of the precipitated phases can block dislocation movement, improve the alloy strength and reduce the elongation of the alloy after fracture; meanwhile, the addition of Cu can achieve the effect of refining alloy grains to a certain extent. According to the invention, the content of Cu element is controlled to be 0.5-1.0%, so that the tensile strength is improved to the maximum extent, and the damage to plasticity is reduced.
In the alloy composition disclosed by the invention, the addition of Mn and Cr elements can improve the appearance of an iron-rich phase in the alloy, so that a needle-shaped Al-Fe-Si ternary phase in the alloy is changed into a blocky or Chinese character-shaped Al-Si- (Cr, Fe) or Al-Si- (Mn, Fe) quaternary phase, and the strength and the elongation of the alloy are improved; mn and Cr elements react with Al to form MnAl6 and CrAl7 dispersed phases which become heterogeneous nucleation points during solidification, thereby playing a role in refining grains to a certain extent, and the improvement effect of the Mn-Cr dispersed phases is better than the effect of separately adding Mn and Cr. Excessive Mn and Cr elements can form coarse second phases, and the mechanical property of the alloy is reduced. The content of Cr and Mn in the alloy is 0.1-0.3% and 0.1-0.2% respectively, so that the appearance of an iron-rich phase can be improved, and a coarse second phase can be prevented from being formed.
In the alloy composition disclosed by the invention, Ti element reacts with Al melt to form fine and dispersed Al3Ti particles, the fine and dispersed Al3Ti particles become heterogeneous nucleation points during solidification to refine grains, and meanwhile, an Al matrix is converted from long columnar dendrites into an approximate sphere, so that the hardness, tensile strength and elongation of the alloy are improved. Excessive Ti element can also form coarse second phases, and the mechanical property of the alloy is reduced. The Ti content in the alloy is 0.1-0.15%, the effect of refining crystal grains is achieved, and the mechanical property of the alloy is improved.
In the alloy composition disclosed by the invention, after T6 heat treatment, Si and Mg elements can form an Mg2Si phase, so that dislocation movement can be hindered, internal stress can be generated in the alloy, the alloy is one of main strengthening phases of the alloy, the content of the Mg2Si phase of the alloy is increased along with the increase of the content of the Si and Mg elements, and the tensile strength of the alloy is increased along with the increase of the content of the Mg2Si phase.
The invention has the characteristics that:
(1) the Cu element is added on the basis of the A356.2 alloy, so that the Secondary Dendritic Arm Spacing (SDAS) of alpha-Al can be reduced, and the reduction of the SDAS can effectively improve the mechanical property of the alloy; and a plurality of precipitated phases (Al2Cu and Al-Si-Mg-Cu) can be formed in the alloy matrix, the variety and the number of the precipitated phases can be controlled by controlling the Cu content, meanwhile, the addition of the Cu can play a role in refining alloy grains to a certain extent, and the proper Cu content can effectively improve the mechanical property of the alloy.
(2) The addition of Mn and Cr elements can improve the appearance of an iron-rich phase in the alloy, so that a needle-shaped Al-Fe-Si ternary phase in the alloy is changed into a blocky or Chinese character-shaped Al-Si- (Cr, Fe) or Al-Si- (Mn, Fe) quaternary phase, and the strength and the elongation of the alloy are improved; mn and Cr elements react with Al to form MnAl6 and CrAl7 dispersed phases which become heterogeneous nucleation points during solidification, thereby playing a role in refining grains to a certain extent, and the improvement effect of the Mn-Cr dispersed phases is better than the effect of separately adding Mn and Cr.
(3) Ti element reacts with Al melt to form fine and dispersed Al3Ti particles, which become heterogeneous nucleation points during solidification to refine grains, and simultaneously, the Al matrix is changed from long columnar dendrite into approximate sphere, so that the hardness, tensile strength and elongation of the alloy are improved.
(4) The mechanical property of the alloy can be obviously improved by controlling the composite addition of Cu, Cr, Mn and Ti.
Advantageous effects
The invention discloses a high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti series casting alloy, which is cast by adopting a water-cooling copper mold metal mold, the alloy is strengthened by adding a Cu element through regulating and controlling the types and the content of alloy elements and a heat treatment process, the Ti element refines crystal grains, the Mn element and the Cr element improve the appearance of an iron-rich phase, the mechanical property of the alloy is greatly improved, the tensile strength is 330-355 MPa, the yield strength is 210-275 MPa, and the elongation after fracture is 7-13%. The manufacturing process disclosed by the invention is simple and feasible, the raw materials are easy to obtain, the production cost is low, the mechanical property of the alloy can be improved by regulating and controlling the element content and the heat treatment process, and the method has a very large application prospect in the automobile hub manufacturing industry.
Drawings
FIG. 1 is an SEM image of a conventional A356.2 and Al-Si-Cu-Mg-Cr-Mn-Ti alloy with different Si and Cr contents;
FIG. 2 TEM image of conventional A356.2 and Al-Si-Cu-Mg-Cr-Mn-Ti alloy of different Si, Cr contents, wherein: (a) is a conventional a356.2 alloy, (b) is example 1, (c) is example 4;
FIG. 3. mechanical properties (tensile strength, yield strength and elongation after fracture) of example 4 as a function of aging time.
Detailed Description
The present invention will be described in detail below with reference to examples to enable those skilled in the art to better understand the present invention, but the present invention is not limited to the following examples.
Example 1
A high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti series casting alloy comprises the following components in percentage by mass: 7.4 percent of Si, 0.6 percent of Cu, 0.45 percent of Mg, 0.2 percent of Cr, 0.15 percent of Mn, 0.1 percent of Ti, 0.02 percent of Sr and the balance of Al.
The preparation method of the high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti series casting alloy comprises the following steps:
(1) weighing: weighing corresponding raw materials according to the chemical components and mass fractions of the prefabricated casting alloy, wherein the raw materials comprise the following components in percentage by mass: 99.99% Al, Al-20Si, pure Mg, Al-50Cu, Al-5Cr, Al-10Mn, Al-10Ti, Al-5Ti-1B and Al-10 Sr;
(2) smelting: putting a graphite crucible filled with corresponding mass of pure aluminum into a resistance furnace for heating, after the graphite crucible is completely melted and the temperature of molten aluminum reaches 720-740 ℃, adding intermediate alloy of Al-20Si, Al-50Cu, Al-10Ti, Al-10Mn and Al-2Cr, cooling to 700-720 ℃ after heat preservation for 15-20 min, adding a pure Mg block, when the temperature of a melt is returned to 710-720 ℃, adding a refining agent and a slagging agent after heat preservation for 10min, wherein the adding amounts of the refining agent and the slagging agent are respectively 0.4% and 0.35% of the mass of the melt, preserving heat for 10-15 min, then slagging, adding 0.2% of Al-5Ti-1B and 0.2% of Al-10Sr, controlling the temperature of the melt to 700-710 ℃ after stirring, preserving heat for 10-15 min, and casting into a water-cooled copper mold to obtain an aluminum alloy ingot;
(3) solution treatment: putting the alloy into a 540 ℃ medium temperature furnace, preserving heat for 5 hours, and then putting the alloy into hot water at 70-90 ℃ for quenching;
(4) aging treatment: and (3) putting the quenched alloy into an aging furnace at 180 ℃ for heat preservation for 2h, and finally air cooling.
The tensile strength of the aluminum alloy cast by the embodiment reaches 354.7MPa, the yield strength reaches 274.3MPa, and the elongation after fracture reaches 9.6%.
Example 2
The alloy components and their corresponding mass fractions of this example are the same as in example 1.
The preparation process of the alloy comprises the following steps:
(1) the weighing procedure was the same as in example 1.
(2) The melting process was the same as in example 1.
(3) The solution treatment process was the same as in example 1.
(4) Aging treatment: and (3) placing the quenched alloy into an aging furnace at 190 ℃ for heat preservation for 2 hours, and finally air cooling.
The tensile strength of the aluminum alloy cast by the embodiment reaches 338.5MPa, the yield strength reaches 281.5MPa, and the elongation after fracture reaches 7.0%.
Example 3
The alloy components and their corresponding mass fractions of this example are the same as in example 1.
The preparation process of the alloy comprises the following steps:
(1) the weighing procedure was the same as in example 1.
(2) The melting process was the same as in example 1.
(3) The solution treatment process was the same as in example 1.
(4) Aging treatment: and (3) placing the quenched alloy into an aging furnace at 200 ℃ for heat preservation for 2 hours, and finally air cooling.
The tensile strength of the aluminum alloy cast by the embodiment reaches 344.6MPa, the yield strength reaches 272.2MPa, and the elongation after fracture reaches 7.6%.
Example 4
The alloy components of example 4 and their corresponding mass fractions are respectively: 8.3 percent of Si, 0.6 percent of Cu, 0.45 percent of Mg, 0.3 percent of Cr, 0.15 percent of Mn, 0.1 percent of Ti, 0.02 percent of Sr and the balance of Al.
The preparation process of the alloy comprises the following steps:
(1) the weighing procedure was the same as in example 1.
(2) The melting process was the same as in example 1.
(3) The solution treatment process was the same as in example 1.
(4) Aging treatment: and (3) putting the quenched alloy into an aging furnace at 180 ℃ for heat preservation for 4 hours, and finally air cooling.
The tensile strength of the aluminum alloy cast by the embodiment reaches 333.2MPa, the yield strength reaches 247.0MPa, and the elongation after fracture reaches 11.1%.
Example 5
The alloy components and their corresponding mass fractions of this example are the same as in example 1.
The preparation process of the alloy comprises the following steps:
(1) the weighing procedure was the same as in example 1.
(2) The melting process was the same as in example 1.
(3) The solution treatment process was the same as in example 1.
(4) Aging treatment: and (3) placing the quenched alloy into an aging furnace at 200 ℃ for heat preservation for 4 hours, and finally air cooling.
The tensile strength of the aluminum alloy cast by the embodiment reaches 332.2MPa, the yield strength reaches 253.4MPa, and the elongation after fracture reaches 8.7%.
TABLE 1 summary of mechanical Properties of conventional A356.2 and novel Al-Si-Cu-Mg-Cr-Mn-Ti alloys with different Si, Cr contents and ageing temperatures
| Alloy (I) | Tensile strength/MPa | Yield strength/MPa | Elongation after break/% |
| A356.2 | 269.8 | 185.4 | 12.8 |
| Example 1 | 354.7 | 274.3 | 9.6 |
| Example 2 | 338.5 | 218.5 | 7.0 |
| Example 3 | 334.6 | 272.2 | 7.6 |
| Example 4 | 333.2 | 247.0 | 11.1 |
| Example 5 | 332.2 | 253.4 | 8.7 |
Although the embodiments of the present invention have been described above, it should be noted that the above-mentioned embodiments are exemplary only, and are intended to facilitate understanding and use of the invention, and not to limit the invention, and that those skilled in the art, on the basis of the description of the invention, will make equivalent changes, modifications, variations and substitutions within the scope of the claims of the present application.
Claims (7)
1. The high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti cast alloy is characterized by comprising the following components in percentage by mass: 7.0-8.5% of Si, 0.5-1.0% of Cu, 0.35-0.5% of Mg, 0.1-0.3% of Cr, 0.1-0.2% of Mn, 0.1-0.15% of Ti, 0.015-0.025% of Sr, less than or equal to 0.15% of the total amount of other impurities and the balance of Al.
2. The high-strength and high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti cast alloy as claimed in claim 1, wherein the alloy comprises the following components in percentage by mass: 7.4% of Si, 0.6% of Cu, 0.45% of Mg, 0.2% of Cr, 0.15% of Mn, 0.1% of Ti, 0.02% of Sr and the balance of Al.
3. The high strength and toughness Al-Si-Cu-Mg-Cr-Mn-Ti based casting alloy according to claim 1 or 2, wherein: according to the national standard GB/T228.1-2010, a tensile sample is taken from a casting, the tensile strength is 330-355 MPa, the yield strength is 210-275 MPa, and the elongation after fracture is 7-13% under the T6 state.
4. Method for the preparation of a high strength and high toughness Al-Si-Cu-Mg-Cr-Mn-Ti based cast alloy according to any of the preceding claims 1 to 3, characterized in that it comprises the following steps:
(1) weighing: weighing corresponding raw materials according to the chemical components and the mass fraction of the alloy, wherein the raw materials comprise: 99.99% Al, Al-20Si, pure Mg blocks, Al-50Cu, Al-5Cr, Al-10Mn, Al-10Ti, Al-5Ti-1B and Al-10 Sr;
(2) smelting: putting the graphite crucible filled with the corresponding quality of pure aluminum into a resistance furnace for heating, sequentially adding an intermediate alloy, a refining agent and a slag removing agent after the graphite crucible is completely melted, removing slag, and finally casting into a water-cooled copper mold to obtain an aluminum alloy ingot;
(3) solution treatment: putting the aluminum alloy cast ingot into a medium temperature furnace at 540-550 ℃, preserving heat for 5-6 h, and then putting the aluminum alloy cast ingot into hot water at 70-90 ℃ for quenching;
(4) aging treatment: and (3) placing the quenched aluminum alloy ingot into an aging furnace at 170-180 ℃ for heat preservation for 2-4 h, and finally air cooling.
5. The method for preparing the high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti cast alloy according to claim 4, wherein the method comprises the following steps: weighing in the step (1), and additionally weighing 5% of 99.99% of Al and pure magnesium blocks to make up for the burning loss of the melt.
6. The method for preparing the high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti cast alloy according to claim 4, wherein the method comprises the following steps: and (2) smelting, namely putting the graphite crucible filled with pure aluminum with corresponding quality into a resistance furnace for heating, after the graphite crucible is completely melted and the temperature of the molten aluminum reaches 720-740 ℃, adding Al-20Si, Al-50Cu, Al-10Mn, Al-10Ti and Al-5Cr, preserving heat for 15-20 min, cooling to 700-720 ℃, adding a pure Mg block, after the melt is warmed to 710-720 ℃, adding a refining agent and a slagging agent after 10min of heat preservation, wherein the adding amounts of the refining agent and the slagging agent are 0.4% and 0.35% of the mass of the melt respectively, preserving heat for 10-15 min, slagging, adding 0.2% of Al-5Ti-1B and 0.2% of Al-10Sr, controlling the melt temperature to 700-710 ℃ after stirring, preserving heat for 10-15 min, and casting into a water-cooled copper mold to obtain the aluminum alloy ingot.
7. The method for preparing the high-strength high-toughness Al-Si-Cu-Mg-Cr-Mn-Ti cast alloy according to claim 4, wherein the method comprises the following steps: when the refining agent is added in the step (2), pressing the refining agent into the bottom of the crucible by using a graphite rod to enable gas in the melt to fully escape; when the slag removing agent is added, the slag removing agent is uniformly scattered on the surface of the melt, the mixture is fully stirred, the lumps on the melt are broken as much as possible, and then slag is removed.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
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| WO2023015578A1 (en) * | 2021-08-11 | 2023-02-16 | 江苏大学 | Al-si-cu-fe-mn alloy and preparation method therefor |
| CN114672674B (en) * | 2022-02-28 | 2024-03-15 | 中国第一汽车股份有限公司 | Casting-rolling high-strength high-toughness aluminum-silicon alloy and preparation method thereof |
| CN114672674A (en) * | 2022-02-28 | 2022-06-28 | 中国第一汽车股份有限公司 | Cast-rolled high-strength high-toughness aluminum-silicon alloy and preparation method thereof |
| CN114774741B (en) * | 2022-04-21 | 2023-11-24 | 中铝材料应用研究院有限公司 | Heat-resistant high-strength cast aluminum alloy and manufacturing method thereof |
| CN114774741A (en) * | 2022-04-21 | 2022-07-22 | 中铝材料应用研究院有限公司 | Heat-resistant high-strength cast aluminum alloy and manufacturing method thereof |
| CN115044810A (en) * | 2022-06-17 | 2022-09-13 | 大连科天新材料有限公司 | Aluminum alloy, preparation method thereof and automobile material |
| CN115141960A (en) * | 2022-06-17 | 2022-10-04 | 中南大学 | High-strength and high-toughness cast aluminum alloy with low Si content and preparation method thereof |
| CN115305392B (en) * | 2022-08-12 | 2024-02-06 | 清华大学 | High-strength and high-toughness die-casting aluminum-silicon alloy and preparation method and application thereof |
| CN115305392A (en) * | 2022-08-12 | 2022-11-08 | 清华大学 | High-strength and high-toughness die-casting aluminum-silicon alloy and preparation method and application thereof |
| WO2024036672A1 (en) * | 2022-08-15 | 2024-02-22 | 保定市立中车轮制造有限公司 | High toughness, high casting performance, heat treatment-free aluminum alloy stressed member material and preparation method therefor |
| CN115786784A (en) * | 2022-11-17 | 2023-03-14 | 大连科天新材料有限公司 | High-strength and high-toughness cast aluminum-silicon-copper-magnesium alloy, and preparation method and application thereof |
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| CN116657005B (en) * | 2023-06-01 | 2023-12-12 | 保定市立中车轮制造有限公司 | Regenerated aluminum alloy material and preparation method thereof |
| CN116970847A (en) * | 2023-07-24 | 2023-10-31 | 东莞理工学院 | High-strength low-defect Al-Si alloy and preparation method and application thereof |
| CN116970847B (en) * | 2023-07-24 | 2024-05-28 | 东莞理工学院 | High-strength low-defect Al-Si alloy and preparation method and application thereof |
| CN117488148A (en) * | 2024-01-03 | 2024-02-02 | 魏桥(苏州)轻量化研究院有限公司 | Cast aluminum alloy and preparation method and application thereof |
| CN117488148B (en) * | 2024-01-03 | 2024-04-02 | 魏桥(苏州)轻量化研究院有限公司 | Cast aluminum alloy and preparation method and application thereof |
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Application publication date: 20210702 |