CN105239029A - Thermal treatment method for controlling uniform dispersion precipitation of Mn-containing phase in Al-Cu-Mg-Mn alloy - Google Patents
Thermal treatment method for controlling uniform dispersion precipitation of Mn-containing phase in Al-Cu-Mg-Mn alloy Download PDFInfo
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Abstract
The invention relates to a thermal treatment method for controlling uniform dispersion precipitation of the Mn-containing phase in Al-Cu-Mg-Mn alloy. The thermal treatment method is characterized in that the thermal treatment method includes the following steps that firstly, the temperature of an Al-Cu-Mg-Mn alloy cast into is raised to 410-470 DEG C from the room temperature at the average temperature rise rate of 10-400 DEG C per hour or in 1 h to 40 h , and heat preservation is conducted for 0-30 h; secondly, the temperature of the Al-Cu-Mg-Mn alloy cast into is raised to 470-530 DEG C at the average temperature rise rate of 2.5-400 DEG C per hour or in 0.25-40 h , and heat preservation is conducted for 1-60 h; and thirdly, the Al-Cu-Mg-Mn alloy cast is cooled to the room temperature after homogenization. By means of the thermal treatment method, precipitation of the Mn-containing dispersion phase in Al-Cu-Mg-Mn alloy can be well controlled, and the Mn dispersion phase can be uniformly distributed in the structure. The thermal treatment method is wide in application range, can be applied to aeronautical materials, and can be applied to thermal treatment processing of panels, profiles, 2XXX system alloy parts and the like.
Description
Technical field
The invention belongs to non-ferrous metal technical field, be specifically related in a kind of control Al-Cu-Mg-Mn alloy containing the heat treating method that Mn phase even dispersion is separated out.
Background technology
Aluminium alloy has the features such as low density, high specific strength, good toughness and solidity to corrosion and is widely used in the fields such as Aeronautics and Astronautics, communications and transportation and machinery, electronics, building, in national economy and national defense construction, have irreplaceable effect.Al-Cu-Mg-Mn alloy belongs to 2XXX system alloy category, is the Typical Representative of Ultra-High Strength Aluminum Alloys, is all with a wide range of applications in the field such as Aeronautics and Astronautics, communications and transportation.How to improve the performance of Al-Cu-Mg-Mn system alloy further as fatigue property etc., have great importance.
The domestic thermal treatment process research about this alloy, major part works and concentrates on how to regulate and control in the precipitation of main strengthening precipitated phase and Grain Boundary Precipitates distribution, for how regulating and controlling containing the distribution of Mn disperse phase and to follow-up alloy property, the affecting laws research as fatigue property is few.Therefore, how obtaining containing the equally distributed matrix of Mn disperse phase, is the significant technical task of tool.
Summary of the invention
The heat treating method of separating out containing Mn phase even dispersion in the control Al-Cu-Mg-Mn alloy that the present invention proposes, to be intended to by the regulation and control of suitable homogenization heat treatment method containing the distribution in the base of Mn disperse phase, finally obtain a kind of containing Mn disperse phase in the base evenly, the tissue of Dispersed precipitate.
Containing the heat treating method that Mn phase even dispersion is separated out in control Al-Cu-Mg-Mn alloy proposed by the invention, comprise the following steps: (1) casts to Al-Cu-Mg-Mn alloy melting the Al-Cu-Mg-Mn alloy cast ingot obtained and processes, Al-Cu-Mg-Mn alloy cast ingot is warming up to 410 ~ 470 DEG C from room temperature with the average heating rate of 10 ~ 400 DEG C/h or through 1 ~ 40h, and is incubated 0 ~ 30h; (2) then Al-Cu-Mg-Mn alloy cast ingot is warming up to 470 ~ 530 DEG C with the average heating rate of 2.5 ~ 400 DEG C/h or through 0.25 ~ 40h, and is incubated 1 ~ 60h; (3) room temperature is cooled to after homogenizing.
Further, containing the heat treating method that Mn phase even dispersion is separated out in above-mentioned control Al-Cu-Mg-Mn alloy, wherein: described Al-Cu-Mg-Mn alloy comprises AA2524, AA2024 and other 2XXX system alloy containing Mn element.
Further, containing the heat treating method that Mn phase even dispersion is separated out in above-mentioned control Al-Cu-Mg-Mn alloy, wherein: the type of cooling in described step (3) is water cooling or air cooling.
Again further, containing the heat treating method that Mn phase even dispersion is separated out in above-mentioned control Al-Cu-Mg-Mn alloy, wherein: rate of cooling >5 DEG C/h in described step (3).
The heat treating method of separating out containing Mn phase even dispersion in the control Al-Cu-Mg-Mn alloy that the present invention proposes, by the regulation and control of suitable homogenization heat treatment method containing the distribution in the base of Mn disperse phase, finally obtain a kind of containing Mn disperse phase in the base evenly, the tissue of Dispersed precipitate.This tissue is conducive to the recrystallized structure controlling alloy, is conducive to the fatigue property etc. improving alloy.And heat treating method of the present invention is widely used, not only can be applied to aeronautical material, can be applicable to the heat treatment process of sheet material, section bar and 2XXX system alloyed components etc. simultaneously.
Accompanying drawing explanation
Fig. 1 is after alloy carries out 450 DEG C × 5h+498 DEG C × 30h Water Quenching, i.e. the scanning electron microscopy of embodiment 1;
Fig. 2 is after alloy carries out 450 DEG C × 10h+498 DEG C × 30h Water Quenching, i.e. the scanning electron microscopy of embodiment 2;
Fig. 3 is after alloy carries out 460 DEG C × 5h+498 DEG C × 30h Water Quenching, i.e. the scanning electron microscopy of embodiment 3;
Fig. 4 is after alloy carries out 498 DEG C × 30h Water Quenching, i.e. the scanning electron microscopy of comparative example 1;
Fig. 5 is after alloy carries out 400 DEG C × 5h+498 DEG C × 30h Water Quenching, i.e. the EDAX results of comparative example 2;
Fig. 6 is after alloy carries out 400 DEG C × 5h+498 DEG C × 30h Water Quenching, i.e. the scanning electron microscopy of comparative example 2.
Embodiment
Below in conjunction with accompanying drawing, specific embodiment and comparative example, be described in further detail the specific embodiment of the present invention, is easier to understand and grasp to make technical solution of the present invention.
Containing the heat treating method that Mn phase even dispersion is separated out in the present invention's control Al-Cu-Mg-Mn alloy, first batching melting is carried out according to alloy component range before heat-treating, casting obtains required ingot casting, comprise the following steps: (1) casts to Al-Cu-Mg-Mn alloy melting the Al-Cu-Mg-Mn alloy cast ingot obtained and processes, Al-Cu-Mg-Mn alloy cast ingot is warming up to 410 ~ 470 DEG C from room temperature with the average heating rate of 10 ~ 400 DEG C/h or through 1 ~ 40h, and is incubated 0 ~ 30h; (2) then Al-Cu-Mg-Mn alloy cast ingot is warming up to 470 ~ 530 DEG C with the average heating rate of 2.5 ~ 400 DEG C/h or through 0.25 ~ 40h, and is incubated 1 ~ 60h; (3) room temperature is cooled to after homogenizing.Described Al-Cu-Mg-Mn alloys range includes AA2524, AA2024 and other 2XXX system alloy containing Mn element, and namely the present invention is applicable to all Al-Cu-Mg-Mn alloys.In the Al-Cu-Mg-Mn alloy structure obtained after step (2) containing Mn phase can evenly, the distribution of disperse.The type of cooling in described step (3) is water cooling or air cooling, rate of cooling >5 DEG C/h.
embodiment 1
1) al alloy component is by percentage to the quality: Cu4.28wt.%, Mg1.25wt.%, Mn0.57wt.%, Ti0.03wt.%, Fe≤0.08wt.%, Si≤0.08wt.%, and surplus is Al.
2) according to 1) interalloy element proportioning carries out batching melting, casting obtains required ingot casting, homogenizing thermal treatment is carried out to ingot casting: be warming up to 450 DEG C of insulation 5h from room temperature with the average heating rate of 40 DEG C/h or through about 10.6h, then continue to be warming up to 498 DEG C of insulation 30h with the average heating rate of 40 DEG C/h or through about 1.2h, water-cooled is to room temperature.
embodiment 2
1) al alloy component is by percentage to the quality: Cu4.28wt.%, Mg1.25wt.%, Mn0.57wt.%, Ti0.03wt.%, Fe≤0.08wt.%, Si≤0.08wt.%, and surplus is Al.
2) according to 1) interalloy element proportioning carries out batching melting, casting obtains required ingot casting, homogenizing thermal treatment is carried out to ingot casting: be warming up to 450 DEG C of insulation 10h from room temperature with the average heating rate of 30 DEG C/h or through about 14.2h, then continue to be warming up to 498 DEG C of insulation 30h with the average heating rate of 30 DEG C/h or through about 1.6h, water-cooled is to room temperature.
embodiment 3
1) al alloy component is by percentage to the quality: Cu4.28wt.%, Mg1.25wt.%, Mn0.57wt.%, Ti0.03wt.%, Fe≤0.08wt.%, Si≤0.08wt.%, and surplus is Al.
2) according to 1) interalloy element proportioning carries out batching melting, casting obtains required ingot casting, homogenizing thermal treatment is carried out to ingot casting: be warming up to 460 DEG C of insulation 5h from room temperature with the average heating rate of 40 DEG C/h or through about 11h, then continue to be warming up to 498 DEG C of insulation 30h with the average heating rate of 40 DEG C/h or through about 1h, water-cooled is to room temperature.
comparative example 1
1) al alloy component is by percentage to the quality: Cu4.28wt.%, Mg1.25wt.%, Mn0.57wt.%, Ti0.03wt.%, Fe≤0.08wt.%, Si≤0.08wt.%, and surplus is Al.
2) according to 1) interalloy element proportioning carries out batching melting, and casting obtains required ingot casting, carries out homogenizing thermal treatment to ingot casting: be warming up to 498 DEG C of insulation 30h from room temperature with the average heating rate of 40 DEG C/h or through about 11.8h, water-cooled is to room temperature.
comparative example 2
1) al alloy component is by percentage to the quality: Cu4.28wt.%, Mg1.25wt.%, Mn0.57wt.%, Ti0.03wt.%, Fe≤0.08wt.%, Si≤0.08wt.%, and surplus is Al.
2) according to 1) interalloy element proportioning carries out batching melting, casting obtains required ingot casting, homogenizing thermal treatment is carried out to ingot casting: be warming up to 400 DEG C of insulation 5h from room temperature with the average heating rate of 40 DEG C/h or through about 9.4h, then continue to be warming up to 498 DEG C of insulation 30h with the average heating rate of 40 DEG C/h or through about 2.5h, water-cooled is to room temperature.
Table 1 illustrates the measurements resistivity of embodiment and comparative example interalloy, table 2 illustrates in embodiment and comparative example and is uniformly distributed region containing Mn disperse phase and contains Mn disperse phase distributed pole non-uniform areas area fraction statistics, and table 3 illustrates the molecular fraction of A, B, C 3 each material compositions in Fig. 5.Fig. 5 illustrates disperse phase EDAX results in comparative example 2, and Fig. 1, Fig. 2, Fig. 3, Fig. 4, Fig. 6 illustrate in embodiment and comparative example containing Mn disperse phase distribution SEM organization chart.
Experimental result is as shown in table 2, embodiment 1, example 2, do not exist containing Mn disperse phase distributed pole non-uniform areas in example 3, its area fraction is 0%, containing Mn disperse phase distributed pole non-uniform areas area fraction in comparative example 1 is then 14.2%, containing Mn disperse phase distributed pole non-uniform areas area fraction in comparative example 2 is 14.9%, it can thus be appreciated that, the present invention is by conservative control temperature rise rate, first step homogenizing holding temperature and soaking time, second stage homogenizing holding temperature and soaking time, effectively can regulate and control the distribution containing Mn phase in Al-Cu-Mg-Mn alloy, make containing Mn phase even in the tissue, the distribution of disperse.Simultaneously, as shown in Table 1, under embodiment 1, embodiment 2, embodiment 3 treated state, resistance alloys rate value is respectively 5.9,6.0,6.0 μ Ω × cm, under comparative example 1 treated state, resistance alloys rate value is 5.9 μ Ω × cm, under comparative example 2 treated state, resistance alloys rate value is 6.0 μ Ω × cm, it can thus be appreciated that, resistance alloys rate change after heat treating method process of the present invention is minimum, namely heat treating method of the present invention affects less for each alloying element solid solution capacity in the base and amount of precipitation, has has just regulated and controled containing Mn disperse phase distributional pattern in the tissue.
Experimental result as shown in Figure 1, Figure 2, Figure 3 shows, after alloy carries out 450 DEG C × 5h+498 DEG C × 30h, 450 DEG C × 10h+498 DEG C × 30h, 460 DEG C × 5h+498 DEG C × 30h Water Quenching, namely, after embodiment 1, embodiment 2, embodiment 3 process, each region of alloy is uniformly distributed containing Mn disperse phase; As shown in Figure 4, after alloy carries out 498 DEG C × 30h Water Quenching, namely after comparative example 1 processes, alloy had both existed and to be evenly distributed region containing Mn disperse phase, also existed containing Mn disperse phase skewness region; As shown in Figure 6, after alloy carries out 400 DEG C × 5h+498 DEG C × 30h Water Quenching, namely after comparative example 2 processes, alloy had both existed and to be evenly distributed region containing Mn disperse phase, also existed containing Mn disperse phase skewness region.In comparative example 2, be evenly distributed shown in its energy spectrum analysis of region figure as left in Fig. 5 containing Mn disperse phase, the visible Mn disperse phase that contains is evenly distributed; In comparative example 2, shown in its energy spectrum analysis of Mn disperse phase skewness region figure as right in Fig. 5, visible containing Mn disperse phase skewness.In Fig. 5, the molecular fraction of A point, B point, each material composition of C point is as shown in table 3, the molecular fraction of A point Mn element is 1.5%, the molecular fraction of B point Mn element is the molecular fraction of 0.8%, C point Mn element is 1.9%, the molecular fraction difference to some extent of each Mn element.In summary, by the precipitation containing Mn disperse phase of this Al-4.28Cu-1.25Mg-0.57Mn-0.03Ti alloy of the equal controllable of heat treating method of embodiment 1, embodiment 2, embodiment 3, to make containing Mn disperse phase in the tissue evenly, the precipitation of disperse.
Certainly, above is only embody rule example of the present invention, does not constitute any limitation protection scope of the present invention.The technical scheme that all employing equivalents or equivalence are replaced and formed, all drops within rights protection scope of the present invention.
Resistance alloys rate value under table 1 embodiment and comparative example treated state
| State | Resistivity, μ Ω × cm |
| Embodiment 1 | 5.9 |
| Embodiment 2 | 6.0 |
| Embodiment 3 | 6.0 |
| Comparative example 1 | 5.9 |
| Comparative example 2 | 6.0 |
Table 2 is uniformly distributed region containing Mn disperse phase and contains Mn disperse phase distributed pole non-uniform areas area fraction statistics
| State | Region area mark/% is uniformly distributed containing Mn disperse phase | Containing Mn disperse phase distributed pole non-uniform areas area fraction/% |
| Embodiment 1 | 100 | 0 |
| Embodiment 2 | 100 | 0 |
| Embodiment 3 | 100 | 0 |
| Comparative example 1 | 85.8 | 14.2 |
| Comparative example 2 | 85.1 | 14.9 |
The molecular fraction of A, B, C 3 each material compositions in table 3 Fig. 5
Claims (4)
1. in control Al-Cu-Mg-Mn alloy, contain the heat treating method that Mn phase even dispersion is separated out, it is characterized in that comprising the following steps: (1) casts to Al-Cu-Mg-Mn alloy melting the Al-Cu-Mg-Mn alloy cast ingot obtained and processes, Al-Cu-Mg-Mn alloy cast ingot is warming up to 410 ~ 470 DEG C from room temperature with the average heating rate of 10 ~ 400 DEG C/h or through 1 ~ 40h, and is incubated 0 ~ 30h; (2) then Al-Cu-Mg-Mn alloy cast ingot is warming up to 470 ~ 530 DEG C with the average heating rate of 2.5 ~ 400 DEG C/h or through 0.25 ~ 40h, and is incubated 1 ~ 60h; (3) room temperature is cooled to after homogenizing.
2. the heat treating method of separating out containing Mn phase even dispersion in control Al-Cu-Mg-Mn alloy as claimed in claim 1, is characterized in that: described Al-Cu-Mg-Mn alloy comprises AA2524, AA2024 and other 2XXX system alloy containing Mn element.
3. the heat treating method of separating out containing Mn phase even dispersion in control Al-Cu-Mg-Mn alloy as claimed in claim 1, is characterized in that: the type of cooling in described step (3) is water cooling or air cooling.
4. the heat treating method of separating out containing Mn phase even dispersion in control Al-Cu-Mg-Mn alloy as claimed in claim 4, is characterized in that: rate of cooling >5 DEG C/h in described step (3).
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| CN109136506A (en) * | 2018-08-24 | 2019-01-04 | 山东南山铝业股份有限公司 | It is a kind of for inhibiting the processing method and aluminium alloy extrusions of aluminium alloy extrusions coarse grain ring |
| CN109266923A (en) * | 2018-11-28 | 2019-01-25 | 中铝材料应用研究院有限公司 | A kind of high-intensitive, high fatigue life Al-Cu-Mg-Si-Mn line aluminium alloy and its processing method |
| CN111097911A (en) * | 2019-12-12 | 2020-05-05 | 南方科技大学 | Ceramic-metal composite foam material and preparation method thereof |
| CN111690887A (en) * | 2020-06-28 | 2020-09-22 | 山东南山铝业股份有限公司 | Preparation method for preparing 2-series aluminum alloy annealed fine-grain thin plate |
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| CN109136506A (en) * | 2018-08-24 | 2019-01-04 | 山东南山铝业股份有限公司 | It is a kind of for inhibiting the processing method and aluminium alloy extrusions of aluminium alloy extrusions coarse grain ring |
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| CN111097911A (en) * | 2019-12-12 | 2020-05-05 | 南方科技大学 | Ceramic-metal composite foam material and preparation method thereof |
| CN111097911B (en) * | 2019-12-12 | 2022-04-26 | 南方科技大学 | Ceramic-metal composite foam material and preparation method thereof |
| CN111690887A (en) * | 2020-06-28 | 2020-09-22 | 山东南山铝业股份有限公司 | Preparation method for preparing 2-series aluminum alloy annealed fine-grain thin plate |
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