CN113293342A - Enhancement of in situ TiB2Composite deformation method for mechanical property of Al-Cu composite material - Google Patents
Enhancement of in situ TiB2Composite deformation method for mechanical property of Al-Cu composite material Download PDFInfo
- Publication number
- CN113293342A CN113293342A CN202110532271.1A CN202110532271A CN113293342A CN 113293342 A CN113293342 A CN 113293342A CN 202110532271 A CN202110532271 A CN 202110532271A CN 113293342 A CN113293342 A CN 113293342A
- Authority
- CN
- China
- Prior art keywords
- deformation
- temperature
- tib
- composite material
- follows
- 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.)
- Pending
Links
- 238000000034 method Methods 0.000 title claims abstract description 86
- 239000002131 composite material Substances 0.000 title claims abstract description 72
- 229910018182 Al—Cu Inorganic materials 0.000 title claims abstract description 40
- 238000011065 in-situ storage Methods 0.000 title claims abstract description 37
- 230000032683 aging Effects 0.000 claims abstract description 13
- 229910033181 TiB2 Inorganic materials 0.000 claims description 27
- 238000005096 rolling process Methods 0.000 claims description 11
- 239000006104 solid solution Substances 0.000 claims description 9
- 238000010791 quenching Methods 0.000 claims description 8
- 230000000171 quenching effect Effects 0.000 claims description 8
- 238000005266 casting Methods 0.000 claims description 7
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 7
- 238000004321 preservation Methods 0.000 claims description 4
- 239000000243 solution Substances 0.000 claims description 3
- 238000005242 forging Methods 0.000 claims description 2
- 238000000265 homogenisation Methods 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims 1
- 239000002245 particle Substances 0.000 abstract description 15
- 239000011159 matrix material Substances 0.000 abstract description 8
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract description 7
- 229910052782 aluminium Inorganic materials 0.000 abstract description 7
- 229910000838 Al alloy Inorganic materials 0.000 abstract description 5
- 229910045601 alloy Inorganic materials 0.000 abstract description 3
- 239000000956 alloy Substances 0.000 abstract description 3
- 238000002360 preparation method Methods 0.000 abstract description 3
- 230000015572 biosynthetic process Effects 0.000 abstract description 2
- 239000013078 crystal Substances 0.000 abstract description 2
- 230000000052 comparative effect Effects 0.000 description 6
- 239000000463 material Substances 0.000 description 5
- 230000002776 aggregation Effects 0.000 description 4
- 238000000137 annealing Methods 0.000 description 4
- 238000009826 distribution Methods 0.000 description 3
- 238000005054 agglomeration Methods 0.000 description 2
- 238000004220 aggregation Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 230000002787 reinforcement Effects 0.000 description 2
- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 230000003014 reinforcing effect Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Images
Classifications
-
- 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
- C22F1/057—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 copper as the next major constituent
-
- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
-
- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
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
一种提高原位增强TiB2/Al‑Cu铝合金复合材料力学性能的复合强变形方法，是将原位自生法制备的TiB2/Al‑Cu复合材料铸坯均匀化处理后进行变温强变形、固溶处理、室温变形和人工时效；所述变温强变形由高温变形与中低温变形两部分组成；高温变形温度400‑450℃，变形量60％‑70％；中低温变形温度室温‑300℃，变形量20‑30％；室温变形变形量3‑50％。与常规塑性成形工艺相比,本发明引入复合强变形工艺，促进形成均匀分散的TiB2粒子并细化晶粒，保持高强度的同时具有较好的塑性。本发明工艺方法简单、操作方便，可显著提高合金的强度和塑性。适于工业化应用。对提高航空航天、交通运输等领域应用的原位增强铝基复合材料的性能具有重要作用。对制备大规格高综合性能原位增强TiB2/Al‑Cu铝基复合材料和构件以及应用具有重要意义。
A composite strong deformation method for improving the mechanical properties of an in-situ reinforced TiB 2 /Al-Cu aluminum alloy composite material is that the TiB 2 /Al-Cu composite material prepared by the in-situ autogenous method is homogenized and then subjected to variable temperature and strong deformation. , solution treatment, room temperature deformation and artificial aging; the variable temperature deformation is composed of high temperature deformation and medium and low temperature deformation; the high temperature deformation temperature is 400-450 ℃, and the deformation amount is 60%-70%; ℃, the deformation amount is 20‑30%; the room temperature deformation amount is 3‑50%. Compared with the conventional plastic forming process, the present invention introduces a composite strong deformation process, which promotes the formation of uniformly dispersed TiB 2 particles and refines the crystal grains, and has good plasticity while maintaining high strength. The invention has the advantages of simple process method and convenient operation, and can significantly improve the strength and plasticity of the alloy. Suitable for industrial applications. It plays an important role in improving the performance of in-situ reinforced aluminum matrix composites used in aerospace, transportation and other fields. It is of great significance for the preparation and application of in-situ reinforced TiB 2 /Al-Cu aluminum matrix composites and components with large size and high comprehensive performance.
Description
Technical Field
The invention relates to the technical field of aluminum-based composite material forming, in particular to a method for improving in-situ reinforced TiB2A composite deformation method for mechanical property of Al-Cu composite material.
Background
The particle aluminum alloy composite material has the characteristics of high strength, high elastic modulus and the like, has wide application prospect in the fields of aerospace, automobiles, electronics, advanced weapon systems and the like, and is a new generation structural material with wide application prospect. In situ enhanced TiB2The Al-Cu composite material has the characteristics of high strength and elastic modulus, good thermal stability and the like, and is a new generation structural material which needs to be developed urgently for high-end equipment such as aerospace and the like. The particle reinforced aluminum matrix composite material prepared by the in-situ self-generation method has the following advantages: (1) the in-situ synthesized reinforced particles have good thermodynamic stability in the matrix, and slow down the softening of the material in the high-temperature service process; (2) the reinforcement is directly generated in the matrix, the problem of interface wettability does not exist, the contact interface between the reinforcement and the matrix is neat and clean, and the interface combination is more stable. (3) Under the proper preparation conditions, the size, the quantity and the distribution of the reinforcing body particles can be controlled by reasonably designing the reaction process, and better comprehensive performance is obtained. But TiB2The particles are seriously agglomerated, and the prior art strengthens TiB2The preparation process of the/Al-Cu composite material is generally that a casting is subjected to solution treatment after being rolled at normal temperature, and TiB can be improved to a certain extent2Particle agglomeration, but the effect is extremely limited, leading to TiB prepared by in situ autobiogenesis2The elongation of the particle in-situ reinforced aluminum matrix composite is extremely low and the difference is large. Restricting the application thereof. Therefore, an effective reduction of TiB was investigated2Method for particle agglomeration to improve in-situ enhanced TiB2Mechanical property of Al-Cu composite material, and in-situ enhanced TiB with high comprehensive performance for preparing large specification2The Al-Cu composite material and the component and the application have important significance.
Disclosure of Invention
Aiming at the problems in the prior art, the invention aims to provide a method for improving in-situ enhanced TiB2Mechanical property of/Al-Cu composite materialEnergy composite strong deformation method. By adopting the method of the invention, TiB in the composite material matrix can be effectively improved2The aggregation state of the particles improves the mechanical property of the composite material, and the composite material has better plasticity while keeping high strength.
The invention is realized by the following scheme:
in-situ enhanced TiB2The composite strong deformation method of the mechanical property of the Al-Cu composite material is to prepare TiB by an in-situ self-generation method2Carrying out variable temperature strong deformation, solid solution treatment, room temperature deformation and artificial aging after homogenizing treatment on the/Al-Cu composite casting blank;
the variable-temperature strong deformation consists of high-temperature deformation and medium-low temperature deformation;
the variable-temperature strong deformation consists of high-temperature deformation and medium-low temperature deformation;
the high-temperature deformation process parameters are as follows:
temperature: 400-500 ℃, deformation: more than or equal to 60 percent; deforming for one or more times;
the medium-low temperature deformation process parameters are as follows:
temperature: the temperature is between room temperature and 300 ℃, and the deformation is more than or equal to 10 percent;
the room temperature deformation process parameters are as follows:
temperature: at room temperature, the deformation is more than or equal to 3 percent.
The invention relates to a method for improving in-situ reinforced TiB2The composite strong deformation method of the mechanical property of the Al-Cu composite material comprises a high-temperature deformation process, a medium-low temperature deformation process and a room-temperature deformation process, wherein the high-temperature deformation process, the medium-low temperature deformation process and the room-temperature deformation process are selected from one of rolling, forging and extruding.
The invention relates to a method for improving in-situ reinforced TiB2A composite strong deformation method of mechanical property of Al-Cu composite material,
the high-temperature deformation process parameters are as follows:
temperature: 400-450 ℃, deformation: 65 to 80 percent;
the medium-low temperature deformation process parameters are as follows:
temperature: the temperature is between room temperature and 300 ℃, and the deformation is 15-30%;
the room temperature deformation process parameters are as follows:
temperature: and (3) deformation of 3-50% at room temperature.
The invention relates to a method for improving in-situ reinforced TiB2The composite strong deformation method of the mechanical property of the Al-Cu composite material comprises the following high-temperature deformation process parameters:
temperature: the deformation is 70-80% at 400-450 ℃;
the medium-low temperature deformation process parameters are as follows:
temperature: deformation at 100-200 ℃: 20 to 30 percent;
the room temperature deformation process parameters are as follows:
temperature: room temperature, deformation amount: 30 to 50 percent.
The medium-low temperature deformation process parameters are as follows:
temperature: the temperature is between room temperature and 300 ℃, and the deformation is more than or equal to 20 percent;
the room temperature deformation process parameters are as follows:
temperature: at room temperature, the deformation is more than or equal to 3 percent.
The invention relates to a method for improving in-situ reinforced TiB2The composite strong deformation method of the mechanical property of the Al-Cu composite material comprises the following casting blank homogenization treatment process parameters: 500-550 ℃.
The invention relates to a method for improving in-situ reinforced TiB2The composite strong deformation method of the mechanical property of the Al-Cu composite material comprises the following solid solution treatment process parameters: the temperature is 500-540 ℃, and the heat preservation time is as follows: and water quenching for 0.5-10 h.
The invention relates to a method for improving in-situ reinforced TiB2The composite strong deformation method of the mechanical property of the Al-Cu composite material comprises the following artificial aging process parameters: the temperature is 150-200 ℃, and the heat preservation time is as follows: 1-50 h.
The invention relates to a method for improving in-situ reinforced TiB2A composite strong deformation method of the mechanical property of the Al-Cu composite material, namely the TiB2The Al-Cu composite material comprises the following components in percentage by mass:
compared with the conventional plastic forming process, the invention introduces a composite strong deformation method process to promote the formation of uniformly dispersed TiB2The grains are refined, and the high strength and good plasticity are realized. According to the invention, the uniform casting blank is subjected to variable-temperature strong deformation treatment, so that the dispersion of agglomerated particles is effectively promoted, and the recrystallization is induced to occur, so that the aggregation state of particles is effectively improved; meanwhile, the material subjected to solution quenching treatment is subjected to low-temperature strong deformation, so that the dislocation density is improved, and the TiB is further improved2The distribution state of the particles is regulated and controlled through artificial aging, and the aging precipitated phase state is finally realized while the high strength of the composite material is maintained.
The invention has simple process and convenient operation, and can obviously improve the strength and the plasticity of the alloy. Is suitable for industrial application. The method plays an important role in improving the performance of the in-situ reinforced aluminum-based composite material applied in the fields of aerospace, transportation and the like. For preparing large-specification high-comprehensive-performance in-situ enhanced TiB2The Al-Cu aluminum-based composite material, the component and the application have important significance.
Drawings
FIG. 1 is a metallographic photograph of an alloy in an aged state by conventional plastic deformation in comparative example 1;
FIG. 2 is a metallographic photograph of a composite strong deformation sample obtained by applying the present invention in example 1;
it can be seen from the metallographic picture of fig. 1: TiB2Uneven particle distribution and coarse grains
As can be seen from the metallographic picture of fig. 2: TiB2The particles are dispersed and distributed and the crystal grains are fine
The specific implementation mode is as follows:
comparative example 1 and examples 1-4 are homogenized TiB2a/Al-Cu composite material.
(5wt.TiB2Al-6.3Cu-0.3Mn-0.10Zr (mass fraction)) aluminum alloy casting blanks are formed by adopting the process flow of the invention, and the conditions of deformation temperature, solid solution, aging heat treatment and the like are shown in the comparative example and the embodiment.
TiB prepared by comparative example 1 and examples 1 to 4 was used2The strength and elongation of the/Al-Cu composite are shown in Table 1. The mechanical tensile test is referred to GB/T228.
Comparative example 1:
TiB2preheating a/Al-Cu series composite material homogenized cast ingot at 450 ℃ for 4 hours, and rolling the ingot, wherein the total deformation is 93%; solid solution is carried out for 2h at 540 ℃, water quenching is carried out at room temperature, cold deformation is carried out for 3 percent, and aging is carried out at 155 ℃/23 h.
Example 1:
TiB2preheating a homogenized ingot made of the Al-Cu composite material at 450 ℃ for 4h, rolling at 450 ℃ for 73%, annealing at 450 ℃ for 1h, and then rolling at 300 ℃ for 20%, wherein the total deformation is 93%; solid solution is carried out for 2h at 540 ℃, water quenching is carried out at room temperature, cold deformation is carried out for 3 percent, and aging is carried out at 155 ℃/23 h.
Example 2:
TiB2preheating a homogenized ingot of the Al-Cu composite material at 450 ℃ for 4h, rolling at 450 ℃ for 73%, annealing at 450 ℃ for 1h, and rolling at room temperature for 20%; solid solution is carried out for 2h at 540 ℃, water quenching is carried out at room temperature, cold deformation is carried out for 3 percent, and aging is carried out at 155 ℃/23 h.
Example 3:
preheating an Al-Cu aluminum alloy homogenized ingot at 450 ℃ for 4 hours, rolling at 450 ℃ for 73 percent, annealing at 450 ℃ for 1 hour, rolling at 300 ℃ for 20 percent, and keeping the total deformation amount at 93 percent; solid solution is carried out for 2h at 540 ℃, water quenching is carried out at room temperature, 30 percent cold deformation and aging is carried out at 155 ℃/23 h.
Example 4:
preheating an Al-Cu aluminum alloy homogenized ingot at 450 ℃ for 4 hours, rolling at 450 ℃ for 73 percent, annealing at 450 ℃ for 1 hour, rolling at 300 ℃ for 20 percent, and keeping the total deformation amount at 93 percent; solid solution is carried out for 2h at 540 ℃, water quenching is carried out at room temperature, cold deformation is carried out by 50 percent, and aging is carried out at 155 ℃/23 h.
TABLE 1 in-situ reinforced mechanical properties of TiB2/2219 composite material
| Examples of the invention | Heat treatment method | σb/MPa | σ0.2/MPa | δ/％ |
| Comparative example 1 | The invention | 474.2±2 | 400.6±1 | 4.7±0.1 |
| Example 1 | The invention | 480.7±2 | 404.6±1 | 5.5±0.1 |
| Example 2 | The invention | 489.6±2 | 414.3±1 | 6±0.1 |
| Example 3 | The invention | 480.9±2 | 427.2±3 | 5.6±0.1 |
| Example 4 | The invention | 498.7±2 | 446.7±4 | 5.7±0.1 |
The results in Table 1 show that TiB is enhanced in situ using the present invention as compared to conventional plastic deformation2The Al-Cu composite material has strong composite deformation of mechanical property, and the tensile strength and yield strength of the material are obviously improved.
Claims (8)
1. In-situ enhanced TiB2The composite strong deformation method of the mechanical property of the Al-Cu composite material is to prepare TiB by an in-situ self-generation method2Carrying out variable temperature strong deformation, solid solution treatment, room temperature deformation and artificial aging after homogenizing treatment on the/Al-Cu composite casting blank;
the variable-temperature strong deformation consists of high-temperature deformation and medium-low temperature deformation;
the high-temperature deformation process parameters are as follows:
temperature: 400-500 ℃, deformation: more than or equal to 60 percent; deforming for one or more times;
the medium-low temperature deformation process parameters are as follows:
temperature: the temperature is between room temperature and 300 ℃, and the deformation is more than or equal to 10 percent;
the room temperature deformation process parameters are as follows:
temperature: at room temperature, the deformation is more than or equal to 3 percent.
2. The method of claim 1, wherein the TiB is enhanced in situ2The composite strong deformation method of the mechanical property of the Al-Cu composite material is characterized by comprising the following steps: the high-temperature deformation process, the medium-low temperature deformation process and the room-temperature deformation process are selected from one of rolling, forging and extruding.
3. The method of claim 1, wherein the TiB is enhanced in situ2The composite strong deformation method of the mechanical property of the Al-Cu composite material is characterized by comprising the following steps:
the high-temperature deformation process parameters are as follows:
temperature: 400-450 ℃, deformation: 65 to 80 percent;
the medium-low temperature deformation process parameters are as follows:
temperature: the temperature is between room temperature and 300 ℃, and the deformation is 15-30%;
the room temperature deformation process parameters are as follows:
temperature: and (3) deformation of 3-50% at room temperature.
4. The method of claim 3, wherein the TiB is enhanced in situ2The composite strong deformation method of the mechanical property of the Al-Cu composite material is characterized by comprising the following steps:
the high-temperature deformation process parameters are as follows:
temperature: the deformation is 70-80% at 400-450 ℃;
the medium-low temperature deformation process parameters are as follows:
temperature: deformation at 100-200 ℃: 20 to 30 percent;
the room temperature deformation process parameters are as follows:
temperature: room temperature, deformation amount: 30 to 50 percent.
5. The method of claim 1, wherein the TiB is enhanced in situ2The composite strong deformation method of the mechanical property of the Al-Cu composite material is characterized by comprising the following steps: the casting blank homogenization treatment process parameters are as follows: 500-550 ℃.
6. The method of claim 1, wherein the TiB is enhanced in situ2The composite strong deformation method of the mechanical property of the Al-Cu composite material is characterized by comprising the following steps: the technological parameters of the solution treatment are as follows: the temperature is 500-540 ℃, and the heat preservation time is as follows: and water quenching for 0.5-10 h.
7. The method of claim 1, wherein the TiB is enhanced in situ2The composite strong deformation method of the mechanical property of the Al-Cu composite material is characterized by comprising the following steps: the artificial aging process parameters are as follows: the temperature is 150-200 ℃, and the heat preservation time is as follows: 1-50 h.
8. An enhanced in situ TiB as claimed in any one of claims 1 to 72A composite strong deformation method of the mechanical property of the Al-Cu composite material, namely the TiB2The Al-Cu composite material comprises the following components in percentage by mass:
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110532271.1A CN113293342A (en) | 2021-05-17 | 2021-05-17 | Enhancement of in situ TiB2Composite deformation method for mechanical property of Al-Cu composite material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110532271.1A CN113293342A (en) | 2021-05-17 | 2021-05-17 | Enhancement of in situ TiB2Composite deformation method for mechanical property of Al-Cu composite material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN113293342A true CN113293342A (en) | 2021-08-24 |
Family
ID=77322498
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202110532271.1A Pending CN113293342A (en) | 2021-05-17 | 2021-05-17 | Enhancement of in situ TiB2Composite deformation method for mechanical property of Al-Cu composite material |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN113293342A (en) |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101168809A (en) * | 2007-11-21 | 2008-04-30 | 苏州有色金属研究院有限公司 | Endogenesis sub-micron TiB2 particle enhanced aluminum-base composite material and preparing technique thereof |
| CN106119629A (en) * | 2016-08-25 | 2016-11-16 | 上海交通大学 | Cutting free particle enhanced aluminum-based composite material and preparation method thereof |
| CN106498318A (en) * | 2016-10-13 | 2017-03-15 | 中南大学 | Improve the process of 2219 aluminium alloy rings comprehensive mechanical properties |
| CN109628787A (en) * | 2018-12-27 | 2019-04-16 | 吉林大学 | Molten internal in-situ micro-nano granules strengthen the preparation method of Al-Cu-Mg-Si sheet alloy |
-
2021
- 2021-05-17 CN CN202110532271.1A patent/CN113293342A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101168809A (en) * | 2007-11-21 | 2008-04-30 | 苏州有色金属研究院有限公司 | Endogenesis sub-micron TiB2 particle enhanced aluminum-base composite material and preparing technique thereof |
| CN106119629A (en) * | 2016-08-25 | 2016-11-16 | 上海交通大学 | Cutting free particle enhanced aluminum-based composite material and preparation method thereof |
| CN106498318A (en) * | 2016-10-13 | 2017-03-15 | 中南大学 | Improve the process of 2219 aluminium alloy rings comprehensive mechanical properties |
| CN109628787A (en) * | 2018-12-27 | 2019-04-16 | 吉林大学 | Molten internal in-situ micro-nano granules strengthen the preparation method of Al-Cu-Mg-Si sheet alloy |
Non-Patent Citations (2)
| Title |
|---|
| JAMES MATHEW,ET AL.: "Effect of semi-solid forging on microstructure and mechanical properties of in-situ cast Al-Cu-TiB2 composites", 《JOURNAL OF ALLOYS AND COMPOUNDS》 * |
| JUNHUI TANG，ET AL.: "Superior Strength and Ductility of In Situ Nano TiB2/Al–Cu–Mg Composites by Cold Rolling and Post-Aging Treatment", 《MATERIALS》 * |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN109355538B (en) | Production process of high-strength 7-series aluminum alloy pipe | |
| CN110983131B (en) | 7-series aluminum alloy section and manufacturing method thereof | |
| JP6406971B2 (en) | Method for producing aluminum alloy member | |
| CN111593239B (en) | Low-cost and high-formability aluminum alloy sheet for vehicle body structure and preparation method thereof | |
| JP2017538861A5 (en) | ||
| CN106498318A (en) | Improve the process of 2219 aluminium alloy rings comprehensive mechanical properties | |
| CN109371266B (en) | Production method of high-strength corrosion-resistant weldable Al-Mg-Si series alloy extrusion material | |
| CN104651683A (en) | Aluminum alloy subjected to composite microalloying of Sc and Zr and preparation method thereof | |
| CN114369776B (en) | Method for improving strength of (Ce + Yb) composite modified hypoeutectic Al-Si-Mg-Cu-Cr alloy | |
| CN108048716A (en) | High-strength creep resistant Al-Cu containing scandium line aluminium alloys and casting and heat treatment process | |
| CN110195178B (en) | A kind of high-strength, high-plasticity, heat-resistant and flame-resistant magnesium alloy and its manufacturing method | |
| CN107488800B (en) | Al-Zn alloy containing precipitates with improved strength and elongation and method for producing same | |
| CN109023183B (en) | Heat treatment process for rare earth magnesium alloy ingot | |
| CN113293342A (en) | Enhancement of in situ TiB2Composite deformation method for mechanical property of Al-Cu composite material | |
| CN106367700B (en) | Eutectic Silicon in Al-Si Cast Alloys nodularization heat treatment method in a kind of cocrystallized Al-Si alloy | |
| CN117845105B (en) | A high-strength and tough cast aluminum alloy and its preparation method and application | |
| CN110093538B (en) | A kind of heat-resistant, corrosion-resistant aluminum alloy and its preparation method and application | |
| CN108130466A (en) | A kind of multielement complex intensifying high-strength and low-cost magnesium alloy and preparation method thereof | |
| CN116926390A (en) | Aluminum-based composite material plate and preparation method thereof | |
| CN113755769B (en) | A kind of high strength and high toughness aluminum matrix composite material and heat treatment method | |
| CN113322401B (en) | A kind of (TiB2/Al-Cu)/Al-Cu series aluminum matrix composite material and preparation method | |
| CN110184499A (en) | A kind of microalloying method improving TC4 titanium alloy strength level | |
| CN113136512B (en) | Processing method for improving high-temperature creep property of magnesium alloy by rolling and pre-compression | |
| CN114686735A (en) | Wrought aluminum alloy with gradient structure and preparation method thereof | |
| CN113718140A (en) | Ultrahigh-performance spray-formed aluminum-silicon-iron-nickel-vanadium alloy and preparation method thereof |
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 | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20210824 |
|
| RJ01 | Rejection of invention patent application after publication |