CN110714176B - Heat treatment method capable of realizing rapid aging of aluminum alloy - Google Patents
Heat treatment method capable of realizing rapid aging of aluminum alloy Download PDFInfo
- Publication number
- CN110714176B CN110714176B CN201911077772.4A CN201911077772A CN110714176B CN 110714176 B CN110714176 B CN 110714176B CN 201911077772 A CN201911077772 A CN 201911077772A CN 110714176 B CN110714176 B CN 110714176B
- Authority
- CN
- China
- Prior art keywords
- aging
- magnetic field
- treatment
- sample
- aluminum alloy
- 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
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
- C22F1/047—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 magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/04—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering with simultaneous application of supersonic waves, magnetic or electric fields
-
- 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
- C22F3/00—Changing the physical structure of non-ferrous metals or alloys by special physical methods, e.g. treatment with neutrons
Abstract
The invention provides a rapid aging heat treatment of aluminum alloyTreatment methods, i.e. ageing heat treatment methods in which the alloy to be subjected to ageing treatment is subjected to predeformation and magnetic field effects, are suitable for Al-Mg2Si series aluminum alloy, belonging to the field of metal material heat treatment. Firstly Al-Mg2The Si-based aluminum alloy is subjected to solution treatment, the solution treatment is carried out at 500-540 ℃ for 5-15 h, then water quenching is carried out, the water quenched sample is subjected to 0.5-5% tensile plastic deformation, then magnetic field aging treatment is carried out, the aging treatment is carried out at 180-210 ℃ for 0-24 h, and air cooling is carried out. Compared with the conventional aging heat treatment, the heat treatment process has the advantages of obvious effect of improving the structure performance of the alloy, simple process, reasonable working procedures, convenient operation and suitability for industrial production.
Description
Technical Field
The invention relates to the field of heat treatment of metal materials, in particular to the field of heat treatment of aluminum alloys, and specifically relates to Al-Mg2The rapid aging method of the Si-based alloy is realized under the synergistic effect of pre-deformation and a magnetic field.
Background
Since pure aluminum itself has many disadvantages of low strength, low hardness, etc., it cannot be directly applied to industry, and its properties can be improved by alloying. After Mg and Si elements are added into the Al matrix, a large amount of dispersed and uniformly distributed Mg can be generated2A Si phase. Mg (magnesium)2Si has excellent properties such as high melting point, low density, low thermal expansion coefficient, high elastic modulus, high hardness and the like. Mg (magnesium)2The Si phase is a stable strengthening phase thermodynamically and is generated in situ as Mg2The interface of the Si phase and the matrix is clean and firm, and has higher thermal stability, formability and processability. Mg in aluminum alloy2The Si phase can be precipitated from the alloy in two forms of primary phase and eutectic phase, and plays a role in strengthening the matrix. For nascent Mg2Modification of Si by refiningTreatment, effective control of its morphology and size, nascent Mg2Si is converted from a coarse dendritic shape into a fine polygonal shape, so that the mechanical property of the alloy is obviously improved. In order to further increase the strength of the alloy and improve the eutectic structure morphology, it is usually heat treated. The heat treatment is generally solid solution and aging treatment, and eutectic Mg is obtained by solid solution treatment2Si is dissolved in the matrix in a solid manner, and a fine strengthening phase is uniformly precipitated in the subsequent aging treatment, so that the strengthening effect is achieved.
The traditional heat treatment refers to a heat processing technology for changing the structure and the performance of a metal material through solid-state phase transition in the heating and cooling processes. This process is primarily related to the temperature field. In recent years, more and more research has found that the application of strong magnetic fields, stress fields and pulsed electric fields, in addition to temperature fields, can alter the progress of the heat treatment of materials and the final products. The magnetic field is used as a cold physical field, more and more scholars at home and abroad apply the magnetic field means to the field of materials, and research the change behavior of the metal material under the action of the magnetic field is carried out, and certain results are obtained. Experiments show that the magnetic field has great influence on the structure and performance of the metal material, and the application range of the static magnetic field is expanded from the traditional ferromagnetic material to the whole material field. On the other hand, the deformation also has an important influence on the precipitation of precipitation strengthening phases during the aging of the alloy. After the alloy is pre-deformed, a large amount of dislocations are formed in a matrix, and the dislocations formed in the pre-deformation process not only can generate work hardening, but also have very important influence on precipitation in the subsequent aging process of the alloy.
Disclosure of Invention
For the current Al-Mg2The invention aims to improve the aging hardness of the alloy, shorten the time of the appearance of an aging hardening peak value, fully utilize the action of pre-deformation and a magnetic field, improve the dissolution and precipitation rate of a precipitation phase, accelerate the aging hardening process, effectively improve the strength of the alloy peak value, provide a heat treatment process with simple process and convenient implementation, improve the alloy structure and performance and facilitate the realization of industrial production.
In order to achieve the purpose, the invention provides the following specific scheme:
the method comprises the following steps: selecting a proper aluminum alloy sample on the ingot for solution treatment and water quenching;
step two: carrying out tensile plastic deformation treatment on the aluminum alloy sample subjected to the solution treatment;
step three: and carrying out magnetic field aging treatment on the pre-deformed aluminum alloy, and then air-cooling to room temperature.
Further, step two is about 10-3The strain rate/s applies tensile plastic deformation to the sample until 0.5% to 5% plastic strain.
Furthermore, the solid solution temperature range is 500-540 ℃, and the solid solution heat preservation time is 5-15 h.
Further, after the solution treatment in the step one, rapid water quenching is carried out.
Furthermore, the aging temperature range is 180-210 ℃, the aging heat preservation time is 0-24 h, and the magnetic induction intensity UOH is more than or equal to 1T.
Further, the transfer time of quenching should be less than 5 s.
Further, magnetic field aging is carried out in a magnetic field high-temperature box furnace, the magnetic induction intensity UOH of the magnetic field high-temperature box furnace is more than or equal to 1T, and the permanent magnet is communicated with a water cooler to reduce the temperature all the time during the operation of the instrument, so that the magnetism of the magnet is prevented from being influenced by high temperature; during operation, a sample is firstly placed into a hearth, when the temperature is raised to the required temperature, the permanent magnet is moved to the position above the hearth to apply a magnetic field, and after the aging is finished, the sample is taken out of the hearth, and then the permanent magnet is moved back to the position far away from the hearth.
Further, the Al-Mg2The Si-based aluminum alloy is Al-x% Mg2Si, wherein x is 5-20 wt.%.
Further, an aluminum alloy prepared by the method is provided.
Compared with the prior art, the invention has the following advantages:
the invention realizes Al-x% Mg2The age hardening strengthening effect of the Si alloy and the time to the age hardness peak is shortened. Alloy (I)After the pre-deformation treatment, a large amount of dislocation is formed in the matrix, which has important influence on the precipitation of a precipitation strengthening phase in the aging process of the alloy, and then the aging treatment is carried out by applying a magnetic field, so that the dissolution and precipitation of the precipitated phase are accelerated, and the effect of accelerating the aging hardening is realized, compared with the sample which is not subjected to the pre-deformation and non-magnetic field heat treatment, the sample which is subjected to the pre-deformation and magnetic field heat treatment reaches the peak hardness from about 10 hours (the magnetic field heat treatment without the pre-deformation is applied), and is shortened to about 6 hours to reach the peak hardness, which is accelerated by about 40%. On the other hand, the application of the pre-deformation can influence the movement of vacancies and dislocations in the alloy and influence the distribution of precipitated phases, so that the phenomenon of strength enhancement is shown no matter alpha-Al or eutectic structures, and the peak age hardness is improved by about 8 percent.
The method has the advantages of simple process, reasonable working procedures, convenient operation, energy conservation and low consumption, can effectively improve the peak hardness of the alloy, and effectively shortens the time for reaching the peak hardness. Has great advantages and is suitable for industrial production.
Drawings
FIG. 1: strong magnetic field high temperature box furnace schematic diagram, wherein: 1-permanent magnet, 2-insulating sleeve, 3-heating furnace tube;
FIG. 2: al-7% Mg2Age hardening curve of magnetic field heat treatment with or without pre-deformation of Si alloy.
Detailed Description
The technical solutions in the embodiments of the present invention will be described clearly and completely with reference to the accompanying drawings, and it is obvious that the described embodiments are some, but not all embodiments of the present invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
According to a feature of the invention, the examples use Al-Mg of different compositions2The Si alloy is tested, the samples in the examples are smelted and cast, the heat treatment process without pre-deformation and magnetic field is compared with the heat treatment process applying pre-deformation, and the performance of the experimental sample is evaluated by adopting a hardness test. Bottom surface cleaning deviceThe features of the present invention are further described by way of examples, but the present invention is not limited to the following examples.
FIG. 1 is a schematic view of a high-temperature box-type furnace with a strong magnetic field, wherein the permanent magnet and the heat-insulating sleeve are both hollow cylinders and can axially slide along the heating furnace tube. And (3) putting the sample into the central position of the heating furnace tube, sliding the permanent magnet to the central position of the heating furnace tube when the magnetic field is required to be added for treatment, and sliding the heat insulation sleeve to the central position of the heating furnace tube when the magnetic field is not required to be added for treatment. In order to prevent the magnetic property of the permanent magnet from being damaged by high temperature, the permanent magnet is communicated with a water cooling machine all the time to be cooled.
Selecting casting alloy Al-x% Mg with small number of pores and uniform distribution of structure2And Si (x is 5-20 wt.%) is subjected to heat treatment, and is divided into two groups, one group is a pre-deformation magnetic field heat treatment process, and the other group is a non-pre-deformation magnetic field treatment process. Wherein the first group of pre-deformation and magnetic field heat treatment is experimental group, the ingot is subjected to solution treatment in a box type resistance furnace, then water quenching is carried out, and then pre-deformation (deformation amount is 0.5-5%) is carried out to about 10 percent-3And (3) applying tensile plastic deformation to the sample at the strain rate of/s, and then placing the sample into a magnetic field high-temperature box type furnace for aging treatment. The second group has no pre-deformation and no magnetic field heat treatment as the control group, the ingot is treated with solid solution treatment in a box type resistance furnace, then water quenched, and the sample is directly put into a magnetic field high temperature box type furnace for aging treatment. Comparisons of sample organization and performance testing are then performed.
The detailed steps are as follows:
(1) taking Al-x% Mg with small number of pores and uniform tissue distribution on the cast ingot2Si alloy, cutting a plurality of small cylindrical samples with the diameter of 10mm multiplied by 6 mm.
(2) Ultrasonically cleaning the sample with methanol solution for 1min, ultrasonically cleaning with alcohol solution for 1min, and oven drying.
(3) And (3) carrying out solid solution treatment on the sample in a box type resistance furnace at the temperature of 500-540 ℃ for 5-15 h, then rapidly quenching with water, cleaning and drying.
(4) And for the magnetic field heat treatment process for applying the pre-deformation, the sample is subjected to tensile deformation with the deformation amount of 0.5-5%, then the sample is placed into a magnetic field box type furnace for aging treatment, the aging temperature range is 180-210 ℃, the aging heat preservation time is 0-24 h, and the sample is air-cooled to the room temperature. And for the magnetic field heat treatment process without pre-deformation, directly putting the sample into a magnetic field box type furnace without pre-deformation for aging treatment, wherein the aging temperature range is 180-210 ℃, the aging heat preservation time is 0-24 h, and air cooling to room temperature.
(5) Respectively measuring Al-x% Mg by using Vickers hardness tester2Eutectic structure in the Si alloy and hardness of α -Al.
In the step (4), the magnetic induction UOH of a high-intensity magnetic field high-temperature box furnace used for magnetic field aging is more than or equal to 1T, and the permanent magnet is communicated with a water cooler to reduce the temperature all the time during the operation of the instrument, so that the magnetism of the magnet is prevented from being influenced by high temperature; during operation, a sample is firstly placed into a hearth, when the temperature is raised to the required temperature, the permanent magnet is moved to the position above the hearth to apply a magnetic field, and after the aging is finished, the sample is taken out of the hearth, and then the permanent magnet is moved back to the position far away from the hearth.
In the step (5), when the hardness is measured by a Vickers hardness tester, the pressure is 200gf, and the pressure is maintained for 10 s.
Example 1
The alloy comprises the following chemical components: al-7% Mg2Si。
(1) And (3) carrying out solution treatment on the sample in a box type resistance furnace, wherein the temperature is 500 ℃, the solution heat preservation time is 15h, the water quenching is carried out, and the quenching transfer time is less than 5 s.
(2) At 10-3And (2) applying tensile force plastic deformation to the sample at a strain rate/s, wherein the pre-deformation amount is 3%, then carrying out aging treatment in a magnetic field high-temperature box furnace, wherein the aging temperature is 200 ℃, the aging heat preservation time is 0h, 1h, 6h, 10h, 12h, 15h and 24h respectively, and air cooling to room temperature.
(3) Finally, respectively measuring Al-7% Mg by using a Vickers hardness tester2Eutectic structure and hardness of primary alpha-Al in Si alloy. The results are shown in Table 1.
Comparative example 1
The alloy comprises the following chemical components: al-7% Mg2Si。
(1) And (3) carrying out solution treatment on the sample in a box type resistance furnace, wherein the temperature is 500 ℃, the solution heat preservation time is 15h, the water quenching is carried out, and the quenching transfer time is less than 5 s.
(2) And then carrying out aging treatment in a magnetic field high-temperature box furnace, wherein the aging temperature is 200 ℃, the aging heat preservation time is 0h, 1h, 6h, 10h, 12h, 15h and 24h respectively, and air cooling to room temperature.
(3) Finally, respectively measuring Al-7% Mg by using a Vickers hardness tester2Eutectic structure and hardness of primary alpha-Al in Si alloy. The results are shown in Table 1.
FIG. 2 is Al-7% Mg2The Si alloy has an age hardening curve after the pre-deformation and magnetic field-free heat treatment. It can be seen that the age hardening curve without pre-deformation reaches the age hardness peak around 10h, while the age hardening curve with pre-deformation reaches the age hardness peak around 6h, and the peak strength of the latter is higher than that of the former, which is obvious in comparison.
Example 2
The alloy comprises the following chemical components: al-10% Mg2Si。
(1) And (3) carrying out solution treatment on the sample in a box type resistance furnace, wherein the temperature is 510 ℃, the solution heat preservation time is 10h, the water quenching is carried out, and the quenching transfer time is less than 5 s.
(2) At 10-3And (2) applying tensile plastic deformation to the sample at a strain rate of/s, then performing aging treatment in a magnetic field high-temperature box furnace at the aging temperature of 180 ℃ for 0h, 1h, 6h, 10h, 12h, 15h and 24h, and air-cooling to room temperature.
(3) Finally, respectively measuring Al-10% Mg by using a Vickers hardness tester2Eutectic structure and hardness of primary alpha-Al in Si alloy. The results are shown in Table 1.
Comparative example 2
The alloy comprises the following chemical components: al-10% Mg2Si。
(1) And (3) carrying out solution treatment on the sample in a box type resistance furnace, wherein the temperature is 510 ℃, the solution heat preservation time is 10h, the water quenching is carried out, and the quenching transfer time is less than 5 s.
(2) And then carrying out aging treatment in a magnetic field high-temperature box furnace, wherein the aging temperature is 180 ℃, the aging heat preservation time is 0h, 1h, 6h, 10h, 12h, 15h and 24h respectively, and air cooling to room temperature.
(3) Finally, respectively measuring Al-10% Mg by using a Vickers hardness tester2Eutectic structure and hardness of primary alpha-Al in Si alloy. The results are shown in Table 1.
Example 3
The alloy comprises the following chemical components: al-15% Mg2Si。
(1) And (3) carrying out solution treatment on the sample in a box type resistance furnace, wherein the temperature is 520 ℃, the solution heat preservation time is 5h, the water quenching is carried out, and the quenching transfer time is less than 5 s.
(2) At 10-3And (2) applying tensile force plastic deformation to the sample at a strain rate/s, wherein the pre-deformation amount is 1%, then carrying out aging treatment in a magnetic field high-temperature box furnace, wherein the aging temperature is 210 ℃, the aging heat preservation time is 0h, 1h, 6h, 10h, 12h, 15h and 24h respectively, and air cooling to room temperature.
(3) Finally, respectively measuring Al-15% Mg by using a Vickers hardness tester2Hardness of eutectic structure in Si alloy. The results are shown in Table 1.
Comparative example 3
The alloy comprises the following chemical components: al-15% Mg2Si。
(1) And (3) carrying out solution treatment on the sample in a box type resistance furnace, wherein the temperature is 520 ℃, the solution heat preservation time is 5h, the water quenching is carried out, and the quenching transfer time is less than 5 s.
(2) And then carrying out aging treatment in a magnetic field high-temperature box furnace, wherein the aging temperature is 210 ℃, the aging heat preservation time is 0h, 1h, 6h, 10h, 12h, 15h and 24h respectively, and air cooling to room temperature.
(3) Finally, respectively measuring Al-15% Mg by using a Vickers hardness tester2Hardness of eutectic structure in Si alloy. The results are shown in Table 1.
TABLE 1
As can be seen from the data in table 1: for Al-7% Mg2Si、Al-10％Mg2Si、Al-15％Mg2The three alloys of Si, the non-predeformation magnetic field heat treatment sample reaches the peak hardness in about 10h, the predeformation magnetic field heat treatment sample can be advanced to about 6h, and the eutectic structure hardness is respectively improved by about 7.69%, 8.28% and 8.34%. Due to Al-15% Mg2Presence of nascent Mg in Si alloys2Si, primary α -Al is not present, and thus only the Vickers hardness of the eutectic structure is measured for evaluation. Al-7% Mg2Si、Al-10％Mg2The alpha-Al hardness of the Si alloy is respectively improved by about 8.83 percent and 7.28 percent.
While the present invention has been described with reference to the embodiments shown in the drawings, the present invention is not limited to the embodiments, which are illustrative and not restrictive, and it will be apparent to those skilled in the art that many more modifications and variations can be made without departing from the spirit and scope of the invention as claimed.
Claims (4)
1. Al-Mg2The heat treatment method for the rapid aging of the Si series aluminum alloy is characterized by comprising the following steps: the Al-Mg2The Si-based aluminum alloy is Al-x% Mg2Si, wherein x =5-7wt.% comprises the steps of:
the method comprises the following steps: selecting a proper aluminum alloy sample on the ingot to carry out solution treatment, water quenching, wherein the solution temperature range is 500-540 ℃, and the solution heat preservation time is 5-15 h;
step two: subjecting the aluminum alloy sample subjected to solution treatment to tensile plastic deformation treatment to obtain a tensile plastic deformation value of 10−3The strain rate of/s applies tensile plastic deformation to the sample until 0.5% plastic strain;
step three: and (3) carrying out magnetic field aging treatment on the pre-deformed aluminum alloy, and then air-cooling to room temperature, wherein the aging temperature range is 210 ℃, the aging heat preservation time is 0-24 h, and the magnetic induction intensity UOH is more than or equal to 1T.
2. The method of claim 1, wherein the transfer time for quenching is less than 5 seconds.
3. The method as claimed in claim 2, wherein the magnetic field aging is carried out in a magnetic field high temperature box furnace, the magnetic induction UOH of the magnetic field high temperature box furnace is more than or equal to 1T, and the permanent magnet is communicated with a water cooling machine to cool down at any time during the operation of the instrument, so as to prevent the magnetism of the magnet from being influenced by high temperature; during operation, a sample is firstly placed into a hearth, when the temperature is raised to the required temperature, the permanent magnet is moved to the position above the hearth to apply a magnetic field, and after the aging is finished, the sample is taken out of the hearth, and then the permanent magnet is moved back to the position far away from the hearth.
4. An aluminium alloy produced by the method of any one of claims 1 to 3.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201911077772.4A CN110714176B (en) | 2019-11-06 | 2019-11-06 | Heat treatment method capable of realizing rapid aging of aluminum alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201911077772.4A CN110714176B (en) | 2019-11-06 | 2019-11-06 | Heat treatment method capable of realizing rapid aging of aluminum alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN110714176A CN110714176A (en) | 2020-01-21 |
| CN110714176B true CN110714176B (en) | 2020-12-29 |
Family
ID=69213773
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201911077772.4A Active CN110714176B (en) | 2019-11-06 | 2019-11-06 | Heat treatment method capable of realizing rapid aging of aluminum alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN110714176B (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113981281B (en) * | 2021-10-15 | 2022-08-09 | 华峰铝业有限公司 | High-strength rapid aging aluminum alloy and preparation method thereof |
| CN114350932B (en) * | 2022-01-11 | 2023-03-10 | 西安交通大学 | Post-treatment method for solid solution-free precipitation-strengthened metal additive manufacturing thin-wall component |
| CN114381676A (en) * | 2022-01-19 | 2022-04-22 | 内蒙古科技大学 | Two-stage aging treatment method for 7-series aluminum alloy, 7-series aluminum alloy and preparation method thereof |
Family Cites Families (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2652016B2 (en) * | 1987-04-15 | 1997-09-10 | スカイアルミニウム株式会社 | Method for producing aluminum alloy material having fine crystal grains |
| CN1077672C (en) * | 1997-11-03 | 2002-01-09 | 中国科学院金属研究所 | Particle-reinforced aluminum-base wear-resisting pipe and its production |
| CN100406598C (en) * | 2003-09-12 | 2008-07-30 | 吉林大学 | Composite material for automobile brake disc and its preparing method |
| DE102005045340B4 (en) * | 2004-10-05 | 2010-08-26 | Aleris Aluminum Koblenz Gmbh | Process for heat treating an aluminum alloy element |
| CN101514409B (en) * | 2009-03-31 | 2012-05-09 | 南昌大学 | A method for preparing in situ MgSi particle reinforced metal matrix composite |
| CN102108463B (en) * | 2010-01-29 | 2012-09-05 | 北京有色金属研究总院 | Aluminium alloy product suitable for manufacturing structures and preparation method |
| CN103233148B (en) * | 2012-08-23 | 2016-01-20 | 北京有色金属研究总院 | One is applicable to structure-function integration Al-alloy products and preparation method |
| CN103614673B (en) * | 2013-04-11 | 2016-08-17 | 中南大学 | One can realize aluminium alloy quick aging heat treatment method |
| CN103643192B (en) * | 2013-12-17 | 2015-12-09 | 江苏大学 | A kind of electromagnetic coupling method improving plastic deformation capacity of aluminum matrix composite |
| CN103789583B (en) * | 2014-01-22 | 2016-06-08 | 北京科技大学 | Quick aging response type Al-Mg-Si-Cu-Zn system Alloy And Preparation Method |
| CN104264088B (en) * | 2014-10-16 | 2017-03-01 | 中南大学 | A kind of method of utilization electromagnetic field ageing strengthening aluminium alloy |
| CN105441759A (en) * | 2015-11-27 | 2016-03-30 | 天津大学 | Sc-containing high-strength Al-Cu-Mg-Mn-Zr alloy and preparation method thereof |
| CN108642331B (en) * | 2018-05-30 | 2020-03-31 | 乳源东阳光优艾希杰精箔有限公司 | 6181 aluminum alloy for automobile plate and preparation method thereof |
| CN108531702A (en) * | 2018-07-02 | 2018-09-14 | 内蒙古科技大学 | Annealing device, method and system for the quick timeliness of aluminium alloy electric magnetic energy |
-
2019
- 2019-11-06 CN CN201911077772.4A patent/CN110714176B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN110714176A (en) | 2020-01-21 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110714176B (en) | Heat treatment method capable of realizing rapid aging of aluminum alloy | |
| CN105970132B (en) | Regulate and control AlxThe method of CoCrFeNi two-phase high-entropy alloy tissues | |
| CN108220851B (en) | A kind of hardware and its processing method | |
| CN110804707B (en) | High-strength high-plasticity zirconium alloy and preparation method and application thereof | |
| CN105039758A (en) | Precipitation strengthening type high-strength and high-conductivity CuZr alloy and preparing method thereof | |
| CN101880844A (en) | Heat treatment process for ZL101A aluminium alloy for automobile wheel hub | |
| Fakioglu et al. | Effects of different heat treatment conditions on fatigue behavior of AA7075 alloy | |
| CN110438422B (en) | Heat treatment method for additive manufacturing of 2219 aluminum alloy | |
| CN103320730B (en) | Magnesium alloy heat treatment method combined with high-energy ultrasonic processing | |
| CN104264088B (en) | A kind of method of utilization electromagnetic field ageing strengthening aluminium alloy | |
| Wang et al. | Rapid annealing effects on microstructure, texture, and magnetic properties of non-oriented electrical steel | |
| CN108385046A (en) | A kind of heat treatment method of TiAl-V alloys | |
| CN107475649A (en) | Improve the heat treatment method of the superpower Alcoa rolled plate performance of isotropism | |
| CN104711498A (en) | Control method of surface orange peel effect in second tension forming of high strength aluminium alloy | |
| CN108941197B (en) | Preparation method of high-thermal-conductivity aluminum-silicon alloy plate | |
| CN112281092B (en) | Heat treatment method for preaging, re-solid solution and re-aging of Al-Cu-Li alloy | |
| CN113265602A (en) | Heat treatment method for rapidly improving strength of aluminum alloy | |
| CN113373388B (en) | Method for improving plasticity and toughness of boron-containing eutectic alloy by utilizing double-structure | |
| CN113981349A (en) | Annealing process of high-grain-size spinning cathode roller titanium cylinder | |
| Hai et al. | Influence of rolling on internal friction peak of Mg-3Cu-1Mn alloy | |
| CN108396214A (en) | A kind of bimodal tissue Mg-6Zn-0.45Zr alloy preparation methods | |
| CN104674141A (en) | Heat treatment method for controlling orange peel effect of drawn surface of aluminum alloy | |
| CN112324892B (en) | Secondary peak value aging method for high-vacuum die-casting high-speed reduction gearbox shell containing rare earth aluminum silicon alloy | |
| Garba et al. | EFFECT OF THERMAL AGEING TREATMENT ON THE HARDNESS CHARACTERISTICS OF A356 TYPE AL-SI-MG ALLOY | |
| Górny et al. | The effect of toughening combined with microjet cooling during quenching (solution heat treatment) of calcium carbide-modified CuAl10Fe4Ni4 alloy on its mechanical properties |
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 |