CN109797326B - High-strength heat-resistant aluminum alloy and preparation method thereof - Google Patents
High-strength heat-resistant aluminum alloy and preparation method thereof Download PDFInfo
- Publication number
- CN109797326B CN109797326B CN201910193124.9A CN201910193124A CN109797326B CN 109797326 B CN109797326 B CN 109797326B CN 201910193124 A CN201910193124 A CN 201910193124A CN 109797326 B CN109797326 B CN 109797326B
- Authority
- CN
- China
- Prior art keywords
- alloy
- less
- heat
- phase
- resistant
- 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
Images
Landscapes
- Conductive Materials (AREA)
- Continuous Casting (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
Abstract
Disclosure of the inventionA high-strength heat-resistant aluminum alloy and a preparation method thereof are disclosed, wherein the expression of the weight percentage of alloy elements is as follows: al (Al)aCubMncCedNieZrfWherein a is not less than 83.75 and not more than 89.9, b is not less than 7.0 and not more than 9.0, c is not less than 0.5 and not more than 2.0, d is not less than 1.0 and not more than 2.5, e is not less than 1.5 and not more than 2.5, f is not less than 0.1 and not more than 0.25, and a + b + c + d + e + f = 100. The method comprises the following steps: selecting a heat-resistant aluminum alloy system, adjusting alloy components according to an alloy solidification path, preparing an alloy ingot, freely forging the alloy ingot, and carrying out solid solution and aging heat treatment on a forging stock to obtain a heterogeneous cross-scale reinforced structural structure, namely, a nanoscale intermetallic compound heat-resistant phase is uniformly precipitated in crystal grains to reinforce a matrix, a micron-scale heat-resistant intermetallic compound is continuously and uniformly distributed on the crystal grain boundary to stabilize the crystal grain boundary, and the material has excellent high-temperature tensile strength and elongation. The alloy material has the tensile strength of 116MPa at 400 ℃ and the elongation of 37.5 percent, and compared with the prior ZL208 alloy (T6), the tensile strength of the alloy material is improved by 31.8 percent and the elongation of the alloy material is improved by 2.5 times.
Description
Technical Field
The invention belongs to the technology of heat-resistant aluminum alloy materials, and particularly relates to a high-strength heat-resistant aluminum alloy material and a preparation method thereof.
Background
Under the severe challenge of resources, energy and environment, the requirements of high performance and light weight of structural member materials for reducing energy consumption, saving resources and protecting environment in the manufacturing industries of airplanes, automobiles and the like are more and more urgent. Aluminum and aluminum alloys have many advantages of low density, high strength, good processability, corrosion resistance, etc., and have been widely used as excellent structural materials in the fields of aerospace, construction of bridges, automobiles, ships, mechanical equipment, etc. Among them, the heat-resistant aluminum alloy has excellent high-temperature oxidation resistance and better plastic deformation resistance and yield strength under the long-time action of temperature and dynamic and static loads, and has been widely applied to engine pistons, cylinder sleeves and box bodies of weapons, aerospace and ships, particularly tanks, shells of missiles, cylinders of aeroengines, blades, aircraft skins and the like. With the development of aerospace and weapon armors, higher requirements are put forward on the high-temperature performance of heat-resistant aluminum alloy, however, the thermal fatigue, high-temperature resistance and other performances of the existing aluminum alloy casting material approach the limit state, and the development requirements of equipment are difficult to adapt. For example, a piston of an engine, which is one of key components of a combustion chamber of the engine, is exposed to a high-temperature gas environment at 350-400 ℃ during working, and is also subjected to a thermal mechanical fatigue effect. The volume fraction of heat-resistant phase in the heat-resistant aluminum alloy such as ZL208 and the like which is widely applied in the ingot production method is less, the strengthening effect is insufficient, and the alloy can only be used at the temperature below 350 ℃. Although the service temperature of the ZL207 alloy reaches 400 ℃, the brittleness caused by a large amount of fine-meshed heat-resistant phases at the crystal boundary of the material is low, so that the plasticity of the material is too low at 350-400 ℃, the material cannot replace titanium alloy at the temperature of 350-400 ℃, and the development requirement of light weight cannot be met. In addition, the composite material is limited in interfacial bonding strength, which tends to result in a material with low plasticity.
Disclosure of Invention
The invention aims to provide a high-strength heat-resistant aluminum alloy material. The material has high tensile strength and excellent plasticity at high temperature. The material has simple preparation process and low cost, and is easy to popularize.
The technical solution for realizing the purpose of the invention is as follows: high-strength heat-resistant aluminum alloy material and alloy element thereof
The expression of the weight percentage of the elements is as follows: al (Al)aCubMncCedNieZrfWherein a is not less than 83.75 and not more than 89.9, b is not less than 7.0 and not more than 9.0, c is not less than 0.5 and not more than 2.0, d is not less than 1.0 and not more than 2.5, e is not less than 1.5 and not more than 2.5, f is not less than 0.1 and not more than 0.25, and a + b + c + d + e + f = 100.
Furthermore, the structure of the high-strength heat-resistant aluminum alloy material is characterized in that: the nano-scale intermetallic compound Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2Cu heat-resistant phase, precipitation of continuous and uniform distribution micron-sized heat-resistant intermetallic compound Al on grain boundary16Cu4Mn2Ce、Al7Cu4Ni, which has a structural organization with heterodomain cross-scale reinforcement.
Furthermore, the material has excellent tensile strength of 105-117 MPa at 400 ℃ and elongation of 29-38%.
The method for preparing the heat-resistant high-strength aluminum alloy material comprises the following steps:
the first step is as follows: selecting heat-resistant aluminum alloy system, and according to a solidification phase diagram, Ala1Cub1Mnc1Ced1The quaternary alloy is rich in aluminum end, wherein a is more than or equal to 81.01≤94.0，5.0≤b1≤14.0，0.5≤c1≤2.0，0.5≤d1Less than or equal to 3.0, precipitating Al16Cu4Mn2Ce、Al20Cu2Mn3、Al2Cu phase, Ala2Cub2Nic2The aluminum-rich end of the ternary alloy is 78.0-a2<96.0，4.0≤b2≤12.0，0＜c2Less than or equal to 10.0, precipitating Al7Cu4Ni phase, adjusting the alloy component Al according to the quaternary alloy aluminum-rich end and the ternary alloy aluminum-rich endaCubMncCedNieZrfWherein a is not less than 83.75 and not more than 89.9, b is not less than 7.0 and not more than 9.0, c is not less than 0.5 and not more than 2.0, d is not less than 1.0 and not more than 2.5, e is not less than 1.5 and not more than 2.5, f is not less than 0.1 and not more than 0.25, and a + b + c + d + e + f =100, so that micron-scale Al is uniformly precipitated from grain boundaries in the solidification process16Cu4Mn2Ce、Al7Cu4Ni intermetallic compound phase, nano-scale intermetallic compound Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase;
the second step is that: mechanically polishing the surface of a metal raw material to remove oxide skin on the surface, and preparing the material according to the component proportion in the first step;
the third step: sequentially adding high-purity Al, Cu, Ni, Mn, Zr, Al-10% Ce and Al into a water-cooled copper crucible, covering a furnace cover, and vacuumizing to 2 x 10-2Pa, filling high-purity argon (99.99%) with the pressure of 0.4-0.6 MPa into the furnace, and smelting an alloy ingot by adopting a water-cooled copper crucible suspension smelting furnace;
the fourth step: smelting the alloy for 3-4 times to obtain an alloy ingot which is uniformly mixed;
the fifth step: freely forging the alloy ingot, wherein the initial forging temperature is 500 ℃, the final forging temperature is 400 ℃, the deformation amount of each time is 20-30%, the total deformation amount is 60-70%, and crushing coarse precipitated phases to obtain a uniform structure;
and a sixth step: solid dissolving the forged blank at 540 +/-5 ℃ for 12 hours, and quenching the forged blank into water at 25 ℃;
the seventh step: aging at 175 + -5 deg.C for 5 hr, and air cooling.
Furthermore, in the second step, the purity of the metal raw material is more than 99.5 percent.
Furthermore, in the fourth step, the smelting power is 18-22 KW.
Compared with the prior art, the invention has the following remarkable advantages: (1) the invention designs a structure with different domains and cross-scale reinforcement, namely, a micron-scale intermetallic compound phase is precipitated on a crystal boundary to form a continuous network structure to stabilize the crystal boundary, and a nano-scale intermetallic compound phase is uniformly precipitated in the crystal grain to stabilize a matrix, so that the high-temperature mechanical property of the material is obviously improved, and the material meets the high-temperature service condition. (2) The material has excellent plasticity at high temperature. The heat-resistant aluminum alloy of the invention introduces intermetallic compound phases which are continuously and uniformly distributed, thereby being beneficial to the coordinated deformation and leading the material to have excellent plasticity.
Drawings
FIG. 1 is a flow chart of the heat-resistant aluminum alloy material of the present invention.
FIG. 2 is a macroscopic view of the heat-resistant aluminum alloy material of example 1.
FIG. 3 is a microstructure diagram of the heat-resistant aluminum alloy material of example 1 (a is a continuous uniform distribution of micrometer-scale Al on grain boundaries)7Cu4Ni phase and Al16Cu4Mn2Ce phase and b is nanoscale Al uniformly distributed in crystal grains20Cu2Mn3Phase c is nano-scale Al uniformly distributed in the crystal grains2A Cu phase).
FIG. 4 is a high temperature (400 ℃) tensile diagram of the heat-resistant aluminum alloy material of example 1.
Detailed Description
The preparation steps of the following examples are shown in the schematic flow chart of fig. 1.
Example 1
(1) Selection of alloy composition
Selecting heat-resistant aluminum alloy system, and according to a solidification phase diagram, Ala1Cub1Mnc1Ced1Quaternary alloy aluminum-rich end (81.0 ≤ a)1≤94.0，5.0≤b1≤14.0，0.5≤c1≤2.0，0.5≤d1Less than or equal to 3.0) precipitation of Al16Cu4Mn2Ce、Al20Cu2Mn3、Al2Cu phase, Ala2Cub2Nic2Ternary alloy Al-rich end (78.0 ≤ a)2<96.0，4.0≤b2≤12.0，0＜c2Less than or equal to 10.0) precipitation of Al7Cu4Ni phase, thereby adjusting the alloy composition Al86.1Cu8.3Mn1.0Ce2.4Ni2.0Zr0.2；
(2) Selection of raw materials
The purity of each metal component selected for preparing the alloy ingot is shown in table 1, and the alloy component is Al86.1Cu8.3Mn1.0Ce2.4Ni2.0Zr0.2(weight percent);
TABLE 1 purity (%)
| Alloy element | Al | Cu | Mn | Zr | Ni | Al-10%Ce |
| Purity/%) | 99.9 | 99.99 | 99.9 | 99.9 | 99.9 | 99.5 |
(3) Preparation of the alloy
A water-cooled copper crucible suspension smelting furnace is adopted to smelt alloy ingots, and the specific procedures are as follows:
a. mechanically polishing the surface of a metal raw material to remove oxide skin on the surface, and preparing the material according to a designed component proportion; the prepared materials are put into a water-cooled copper crucible in a smelting furnace according to the weight of about 60g per ingot, and the furnace cover is covered for vacuumizing to 2 multiplied by 10-2Pa; filling a certain amount of high-purity argon (99.99%) with pressure, wherein the pressure range of the argon is 0.4 MPa;
b. and smelting the alloy ingot for multiple times to obtain the alloy ingot which is uniformly mixed. The power adopted during smelting is 20 KW;
(4) free forging of alloy ingot
Freely forging the alloy ingot, wherein the initial forging temperature is 500 +/-5 ℃, the final forging temperature is 400 +/-10 ℃, the deformation amount of each time is controlled to be 20-30%, and the total deformation amount is 60-70%;
(5) heat treatment of forged stock
a. Carrying out solid solution on the alloy at 540 +/-5 ℃ for 12 hours, and quenching the alloy into water at 25 ℃;
b. aging the alloy at 170 +/-5 ℃ for 5 hours, and air cooling;
(6) texture, Performance testing
The physical diagram of the prepared material is shown in figure 2. The microstructure of the material is shown in fig. 3: the structure with the strengthened cross-scale structure of the different domains is obtained, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
FIG. 4 is a tensile stress-strain curve of a heat-resistant aluminum alloy material at 400 ℃, and the mechanical property test result shows that: the tensile strength of the prepared material reaches 116MPa, is increased by 31.8 percent compared with that of ZL208 alloy, and the plasticity reaches 37.5 percent, which is 3.5 times of that of the ZL208 alloy.
Example 2
(1) Selection of alloy composition
Selecting heat-resistant aluminum alloy system, and according to a solidification phase diagram, Ala1Cub1Mnc1Ced1Quaternary alloy aluminum-rich end (81.0 ≤ a)1≤94.0，5.0≤b1≤14.0，0.5≤c1≤2.0，0.5≤d1Less than or equal to 3.0) precipitation of Al16Cu4Mn2Ce、Al20Cu2Mn3、Al2Cu phase, Ala2Cub2Nic2Ternary alloy Al-rich end (78.0 ≤ a)2<96.0，4.0≤b2≤12.0，0＜c2Less than or equal to 10.0) precipitation of Al7Cu4Ni phase, adjusting the alloy composition Al86.4Cu8.4Mn1.2Ce2.3Ni1.5Zr0.2；
(2) Selection of raw materials
The purity of each metal component selected for preparing the alloy ingot is shown in table 1, and the alloy component is Al86.4Cu8.4Mn1.2Ce2.3Ni1.5Zr0.2(weight percent);
TABLE 1 purity (%)
| Alloy element | Al | Cu | Mn | Zr | Ni | Al-10%Ce |
| Purity/%) | 99.9 | 99.99 | 99.9 | 99.9 | 99.9 | 99.5 |
(3) Preparation of the alloy
A water-cooled copper crucible suspension smelting furnace is adopted to smelt alloy ingots, and the specific procedures are as follows:
a. mechanically polishing the surface of a metal raw material to remove oxide skin on the surface, and preparing the material according to a designed component proportion; the prepared materials are put into a water-cooled copper crucible in a smelting furnace according to the weight of about 60g per ingot, and the furnace cover is covered for vacuumizing to 2 multiplied by 10-2Pa; filling a certain amount of high-purity argon (99.99%) with pressure, wherein the pressure range of the argon is 0.4 MPa;
b. and smelting the alloy ingot for multiple times to obtain the alloy ingot which is uniformly mixed. The power adopted during smelting is 19 kW;
(4) free forging of alloy ingot
Freely forging the alloy ingot, wherein the initial forging temperature is 500 +/-5 ℃, the final forging temperature is 400 +/-10 ℃, the deformation amount of each time is controlled to be 20-30%, and the total deformation amount is 60-70%;
(5) heat treatment of forged stock
a. Carrying out solid solution on the alloy at 540 +/-5 ℃ for 12 hours, and quenching the alloy into water at 25 ℃;
b. aging the alloy at 175 +/-5 ℃ for 5 hours, and air cooling;
(6) texture, Performance testing
The structure with the strengthened cross-scale structure of the different domains is obtained, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 114MPa, is improved by 29.5 percent compared with that of ZL208 alloy, and the plasticity reaches 38.0 percent, which is 3.6 times of that of the ZL208 alloy.
Example 3
(1) Selection of alloy composition
Selecting heat-resistant aluminum alloy system, and according to a solidification phase diagram, Ala1Cub1Mnc1Ced1Quaternary alloy aluminum-rich end (81.0 ≤ a)1≤94.0，5.0≤b1≤14.0，0.5≤c1≤2.0，0.5≤d1Less than or equal to 3.0) precipitation of Al16Cu4Mn2Ce、Al20Cu2Mn3、Al2Cu phase, Ala2Cub2Nic2Ternary alloy Al-rich end (78.0 ≤ a)2<96.0，4.0≤b2≤12.0，0＜c2Less than or equal to 10.0) precipitation of Al7Cu4Ni phase, adjusting the alloy composition Al83.75Cu9.0Mn2.0Ce2.5Ni2.5Zr0.25；
(2) Selection of raw materials
The purity of each metal component selected for preparing the alloy ingot is shown in table 1, and the alloy component is Al83.75Cu9.0Mn2.0Ce2.5Ni2.5Zr0.25(weight percent);
TABLE 1 purity (%)
| Alloy element | Al | Cu | Mn | Zr | Ni | Al-10%Ce |
| Purity/%) | 99.9 | 99.99 | 99.9 | 99.9 | 99.9 | 99.5 |
(3) Preparation of the alloy
A water-cooled copper crucible suspension smelting furnace is adopted to smelt alloy ingots, and the specific procedures are as follows:
a. mechanically polishing the surface of a metal raw material to remove oxide skin on the surface, and preparing the material according to a designed component proportion; the prepared materials are put into a water-cooled copper crucible in a smelting furnace according to the weight of about 60g per ingot, and the furnace cover is covered for vacuumizing to 2 multiplied by 10-2Pa; filling a certain amount of high-purity argon (99.99%) with pressure, wherein the pressure range of the argon is 0.6 MPa;
b. and smelting the alloy ingot for multiple times to obtain the alloy ingot which is uniformly mixed. The power adopted during smelting is 22 KW;
(4) free forging of alloy ingot
Freely forging the alloy ingot, wherein the initial forging temperature is 500 +/-5 ℃, the final forging temperature is 400 +/-10 ℃, the deformation amount of each time is controlled to be 20-30%, and the total deformation amount is 60-70%;
(5) heat treatment of forged stock
a. Carrying out solid solution on the alloy at 540 +/-5 ℃ for 12 hours, and quenching the alloy into water at 25 ℃;
b. aging the alloy at 175 +/-5 ℃ for 5 hours, and air cooling;
(6) texture, Performance testing
The structure with the strengthened cross-scale structure of the different domains is obtained, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 117MPa, which is improved by 33.0 percent compared with ZL208 alloy, and the plasticity reaches 32.5 percent, which is 3.0 times of that of ZL208 alloy.
Example 4
The invention prepares the master alloy with Al as the component85.9Cu8.0Mn1.0Ce2.5Ni2.5Zr0.1(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 113MPa, which is 28.4% higher than that of ZL208 alloy, and the plasticity reaches 36.5%, which is 3.4 times of that of ZL208 alloy.
Example 5
The invention prepares the master alloy with Al as the component88.75Cu7.0Mn1.0Ce1.0Ni2.1Zr0.15(weight percent) obtaining a cross-scale of different domainsStrengthened structural organization, i.e. continuous and uniform distribution of micrometer-scale Al at grain boundaries of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 109MPa, which is 23.9% higher than that of ZL208 alloy, and the plasticity reaches 35.8%, which is 3.3 times of that of ZL208 alloy.
Example 6
The invention prepares the master alloy with Al as the component89.9Cu7.0Mn0.5Ce1.0Ni1.5Zr0.1(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 105MPa, is improved by 19.3 percent compared with that of ZL208 alloy, and the plasticity reaches 37.0 percent, which is 3.5 times of that of the ZL208 alloy.
Example 7
The invention prepares the master alloy with Al as the component86.7Cu8.0Mn1.5Ce1.5Ni2.2Zr0.1(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 113MPa, which is 28.4% higher than that of ZL208 alloy, and the plasticity reaches 35.2%, which is 3.3 times of that of ZL208 alloy.
Example 8
The invention prepares the master alloy componentIs Al85.55Cu8.5Mn1.5Ce2.0Ni2.3Zr0.15(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 115MPa, is improved by 30.7 percent compared with that of ZL208 alloy, and the plasticity reaches 32.1 percent, which is 3.0 times of that of the ZL208 alloy.
Example 9
The invention prepares the master alloy with Al as the component85.2Cu8.6Mn2.0Ce2.0Ni2.0Zr0.2(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 116MPa, is increased by 31.8 percent compared with that of ZL208 alloy, and the plasticity reaches 29.1 percent, which is 2.7 times of that of the ZL208 alloy.
Example 10
The invention prepares the master alloy with Al as the component84.4Cu9.0Mn2.0Ce2.5Ni2.0Zr0.2(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 112MPa, is improved by 27.3 percent compared with that of ZL208 alloy, and the plasticity reaches 30.5 percent, which is 2.85 times of that of the ZL208 alloy.
Example 11
The invention prepares the master alloy with Al as the component87.8Cu7.5Mn1.0Ce1.5Ni2.0Zr0.2(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 110MPa, is improved by 25.0 percent compared with that of ZL208 alloy, and the plasticity reaches 30.1 percent, which is 2.8 times of that of the ZL208 alloy.
Example 12
The invention prepares the master alloy with Al as the component86.8Cu8.0Mn1.0Ce2.0Ni2.0Zr0.2(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 112MPa, is improved by 27.3 percent compared with that of ZL208 alloy, and the plasticity reaches 31.3 percent, which is 2.9 times of that of the ZL208 alloy.
Example 13
The invention prepares the master alloy with Al as the component86.8Cu7.5Mn1.5Ce2.0Ni2.0Zr0.2(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 109MPa, which is 23.9% higher than that of ZL208 alloy, and the plasticity reaches 29.3%, which is 2.7 times of that of ZL208 alloy.
Example 14
The invention prepares the master alloy with Al as the component84.8Cu8.8Mn1.5Ce2.2Ni2.5Zr0.2(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 115MPa, is improved by 30.7 percent compared with that of ZL208 alloy, and the plasticity reaches 30.8 percent, which is 2.8 times of that of the ZL208 alloy.
Example 15
The invention prepares the master alloy with Al as the component86.8Cu7.5Mn1.5Ce2.0Ni2.0Zr0.2(weight percentage) obtains a structural structure with the structure that the heterodomains are strengthened in a cross-scale mode, namely, micrometer-scale Al is continuously and uniformly distributed at the grain boundary of the material7Cu4Ni and Al16Cu4Mn2Ce phase, nano-sized Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2A Cu phase.
The mechanical property test result shows that: the tensile strength of the prepared material at 400 ℃ reaches 114MPa, is improved by 29.5 percent compared with that of ZL208 alloy, and the plasticity reaches 31.2 percent, which is 2.9 times of that of the ZL208 alloy.
Claims (8)
1. The high-strength heat-resistant aluminum alloy material is characterized in that the expression of the weight percentage of alloy elements is as follows: al (Al)aCubMncCedNieZrfWherein a is not less than 83.75 and not more than 89.9, b is not less than 7.0 and not more than 9.0, c is not less than 0.5 and not more than 2.0, d is not less than 1.0 and not more than 2.5, e is not less than 1.5 and not more than 2.5, f is not less than 0.1 and not more than 0.25, a +b+c+d+e+f=100。
2. A high strength heat resistant aluminium alloy material according to claim 1, wherein the aluminium alloy material has a delocalized, cross-dimensionally strengthened structural structure, the aluminium alloy material having a structure characterized by: the nano-scale intermetallic compound Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2Cu heat-resistant phase, precipitation of continuous and uniform distribution micron-sized heat-resistant intermetallic compound Al on grain boundary16Cu4Mn2Ce、Al7Cu4Ni。
3. The high-strength heat-resistant aluminum alloy material as claimed in claim 1 or 2, wherein the material has excellent tensile strength at 400 ℃ of 105-117 MPa and elongation of 29-38%.
4. A method for preparing a heat-resistant high-strength aluminum alloy material comprises the following steps:
the first step is as follows: selecting a heat-resistant aluminum alloy system, and adjusting the alloy component Al according to the quaternary alloy aluminum-rich end and the ternary alloy aluminum-rich endaCubMncCedNieZrfA is not less than 83.75 and not more than 89.9, b is not less than 7.0 and not more than 9.0, c is not less than 0.5 and not more than 2.0, d is not less than 1.0 and not more than 2.5, e is not less than 1.5 and not more than 2.5, f is not less than 0.1 and not more than 0.25, and a + b + c + d + e + f =100, so that micron-scale Al can be uniformly precipitated from grain boundaries in the solidification process16Cu4Mn2Ce、Al7Cu4Ni intermetallic compound phase, nano-scale intermetallic compound Al is uniformly precipitated in the crystal grains20Cu2Mn3、Al2Cu phase, wherein, according to a solidification phase diagram, Ala1Cub1Mnc1Ced1A is more than or equal to 81.0 at the aluminum-rich end of the quaternary alloy1≤94.0，5.0≤b1≤14.0，0.5≤c1≤2.0，0.5≤d1Less than or equal to 3.0, precipitating Al16Cu4Mn2Ce、Al20Cu2Mn3、Al2Cu phase, Ala2Cub2Nic2Ternary alloy Al-rich end, 78.0-a2<96.0，4.0≤b2≤12.0，0＜c2Less than or equal to 10.0, precipitating Al7Cu4A Ni phase;
the second step is that: mechanically polishing the surface of a metal raw material to remove oxide skin on the surface, and preparing the material according to the component proportion in the first step;
the third step: sequentially adding high-purity Al, Cu, Ni, Mn, Zr, Al-10% Ce and Al into a water-cooled copper crucible, covering a furnace cover, and vacuumizing to 2 x 10-2Pa, filling high-purity argon gas of 0.4-0.6 MPa into the furnace, and smelting an alloy ingot by adopting a water-cooled copper crucible suspension smelting furnace;
the fourth step: smelting the alloy for 3-4 times to obtain an alloy ingot which is uniformly mixed;
the fifth step: freely forging the alloy ingot, wherein the initial forging temperature is 500 ℃, the final forging temperature is 400 ℃, the deformation amount of each time is 20-30%, the total deformation amount is 60-70%, and crushing coarse precipitated phases to obtain a uniform structure;
and a sixth step: solid dissolving the forged blank at 540 +/-5 ℃ for 12 hours, and quenching the forged blank into water at 25 ℃;
the seventh step: aging at 175 + -5 deg.C for 5 hr, and air cooling.
5. The method of claim 4, wherein in the second step, the metal feedstock is greater than 99.5% pure.
6. The method of claim 4 wherein the high purity argon gas has a purity of not less than 99.99%.
7. The method as claimed in claim 4, characterized in that in the fourth step the smelting power is 18-22 kW.
8. The method of claim 4, wherein the material has excellent 400 ℃ tensile strength of 105 to 117MPa and elongation of 29 to 38%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910193124.9A CN109797326B (en) | 2019-03-14 | 2019-03-14 | High-strength heat-resistant aluminum alloy and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201910193124.9A CN109797326B (en) | 2019-03-14 | 2019-03-14 | High-strength heat-resistant aluminum alloy and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN109797326A CN109797326A (en) | 2019-05-24 |
| CN109797326B true CN109797326B (en) | 2020-10-20 |
Family
ID=66563496
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201910193124.9A Active CN109797326B (en) | 2019-03-14 | 2019-03-14 | High-strength heat-resistant aluminum alloy and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN109797326B (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20210130934A1 (en) * | 2019-10-30 | 2021-05-06 | Sumit Bahl | Aluminum-cerium-copper alloys for metal additive manufacturing |
| US11986904B2 (en) | 2019-10-30 | 2024-05-21 | Ut-Battelle, Llc | Aluminum-cerium-nickel alloys for additive manufacturing |
| CN114438383A (en) * | 2022-01-21 | 2022-05-06 | 常州工学院 | Multistage intermetallic compound reinforced heat-resistant alloy and preparation method thereof |
| CN115094277B (en) * | 2022-07-11 | 2023-01-24 | 上海交通大学 | Mixed crystal structure aluminum alloy and preparation method and application thereof |
| CN115323230B (en) * | 2022-07-29 | 2023-05-16 | 西安交通大学 | Aluminum-copper-cerium series heat-resistant aluminum alloy and preparation method thereof |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB596178A (en) * | 1945-07-24 | 1947-12-30 | Tennyson Fraser Bradbury | Aluminium base alloys |
| SU387018A1 (en) * | 1970-12-18 | 1973-06-21 | ALLOY BASED ON ALUMINUM | |
| CN101363092B (en) * | 2008-07-09 | 2011-01-12 | 贵州大学 | High-strength cast aluminium alloy material |
| CN102758109B (en) * | 2012-08-07 | 2014-09-24 | 曾琦 | High-strength wear-resisting heat-resisting aluminium alloy material and preparation process thereof |
| CN104372219A (en) * | 2013-08-16 | 2015-02-25 | 镇江忆诺唯记忆合金有限公司 | Method for increasing Al-Cu-Mn-Ti alloy thermal fatigue performance by adding Ce |
| CN104313418A (en) * | 2014-11-07 | 2015-01-28 | 安徽瑞研新材料技术研究院有限公司 | High-performance heat-resistant aluminum alloy material |
| RU2604084C1 (en) * | 2015-09-02 | 2016-12-10 | Федеральное государственное унитарное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" (ФГУП "ВИАМ") | Aluminium-based filler material, alloyed with rare-earth metals |
-
2019
- 2019-03-14 CN CN201910193124.9A patent/CN109797326B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN109797326A (en) | 2019-05-24 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109797326B (en) | High-strength heat-resistant aluminum alloy and preparation method thereof | |
| CN108823472B (en) | High-strength and high-toughness Al-Zn-Mg-Cu aluminum alloy and heat treatment method thereof | |
| CN1325683C (en) | Al-Cu-Mg-Si alloy and method for producing the same | |
| CN101476061B (en) | High temperature resistant titanium and aluminum based alloy and manufacturing method thereof | |
| CN106756319A (en) | A kind of aluminium alloy and aluminum matrix composite for preparing high-strength high-plastic aluminum matrix composite | |
| CN111455241B (en) | High-strength heat-resistant low-scandium composite microalloyed Al-Cu alloy and heat treatment process thereof | |
| CN101509091A (en) | High-strength high-ductility Al-Zn-Mg-Cu-Sr alloy and production method | |
| CN104611617B (en) | A kind of liquid forging Al-Cu-Zn aluminium alloy and preparation method thereof | |
| CN113667912B (en) | Large-size aluminum alloy plate and preparation method thereof | |
| CN110373574A (en) | A kind of nearly cocrystallizing type high-strength temperature-resistant Al-Ce line aluminium alloy and preparation method | |
| CN113444903A (en) | High-gadolinium rare earth magnesium alloy bar and preparation method thereof | |
| CN111057924A (en) | High-plasticity low-rare earth magnesium alloy and preparation method thereof | |
| CN109536776B (en) | Heat-resistant titanium alloy and preparation method thereof | |
| CN114438383A (en) | Multistage intermetallic compound reinforced heat-resistant alloy and preparation method thereof | |
| CN113737065B (en) | Aluminum alloy, preparation method and application | |
| CN112646997B (en) | Scandium-containing ultrahigh-strength aluminum alloy for aerospace and manufacturing method thereof | |
| CN114535478A (en) | Rotary die forging preparation method of ultralight high-strength magnesium-lithium alloy | |
| CN103225028A (en) | Al-Er-Zr-Si heat-resistant aluminum alloy and its heat treatment technology | |
| CN114592147A (en) | Aluminum alloy profile and preparation method thereof | |
| CN114369776A (en) | Method for improving strength of (Ce + Yb) composite modified hypoeutectic Al-Si-Mg-Cu-Cr alloy | |
| CN112063885B (en) | Ruthenium-containing multi-component TiAl alloy suitable for 800 DEG C | |
| CN109913731B (en) | High-strength and high-toughness Ti-Al intermetallic compound and preparation method thereof | |
| CN113430428A (en) | Al-Mg-Si aluminum alloy and preparation method thereof | |
| CN115786788B (en) | Heat-resistant corrosion-resistant Al-Cu-Mg alloy and preparation method and application thereof | |
| CN106929724B (en) | AQ80M magnesium alloy Wide and Thick Slab hot extrusion techniques |
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 |