CN104561669B - Heat treatment process of Al-Er-Zr-Si alloy - Google Patents
Heat treatment process of Al-Er-Zr-Si alloy Download PDFInfo
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Abstract
The invention discloses a heat treatment process of Al-Er-Zr-Si alloy, and belongs to the technical field of alloys. The heat treatment process comprises the following steps: firstly, at 760 DEG C, smelting Al-Er-Zr-Si alloy comprising 0.29wt% of Er, 0.30wt% of Zr, 0.20wt% of Si and the balance of Al; after melting alloy elements, stirring and casting to obtain as-cast alloy; performing sufficient solid solution at 640 DEG C and quenching by using water to room temperature; performing cold rolling deformation by 20-90%, and then performing equal-time aging for 3 hours once every 25 DEG C from 150 DEG C to 600 DEG C; or performing cold rolling deformation by 90% by using a rolling machine, and then performing equal-temperature aging from 250 DEG C to 400 DEG C, wherein the optimal equal-time aging cold rolling deformation amount is 60% and the optimal aging temperature interval is 150-425 DEG C; the optimal equal-temperature aging temperature is 350 DEG C and the optimal equal-temperature aging time is 100 hours. The heat treatment process adopts a method of combining Er and Zr composite micro-alloying and after-cold-rolling annealing, so that the alloy acquires high conductivity on the premise of keeping relatively stable hardness; by the heat treatment process, the Al-Er-Zr-Si alloy with high strength and high conductivity is obtained.
Description
Technical field：
The invention belongs to field of metal alloy technology, is related to a kind of thermomechanical treatment process of Al-Er-Zr-Si alloys.
Background technology：
High-strength temperature-resistant Aluminum conductor has higher tensile strength, while having good heat resistance, makes wire
Have the advantages that heat-resist, current-carrying capacity is big, tensile strength is high, the arc property that hangs down is good, light weight afterwards, using height on transmission line of electricity
Strong heat-resisting aluminium alloy twisted wire can dramatically increase multi-line power transmission amount, therefore be subject to common concern in the world.But according to
IEC62004 standards, the intensity for using at present is only in the conductivity of the high strength heat resistant alloy wire AT2 of more than 220MPa
55%IACS, and two kind heat-resisting aluminium alloy AT1 and AT3 intensity of the conductivity more than 60%IACS only have 170MPa or so, lack
A kind of existing high intensity and thermostability, and while the aluminium alloy conductor material with high conductivity.Therefore research high-strength temperature-resistant and
The aluminum alloy materials and its preparation technology of high conductivity are particularly significant.
Research and development Heat-resistant aluminum alloy a kind of method be so that alloy can disperse educt have hyperpyrexia steady
Qualitatively Second Phase Particle, strengthens matrix and hinders recrystallization as hardening constituent.But improve intensity and improve between conductivity
Exist conflicting, improving intensity must improve the content of alloying element or improve machining deformation amount, and alloying element content
Raising with machining deformation amount will decline all will electrical conductivity.Therefore need adding minimal amount of alloying element (the high conductance of guarantee
Rate) under conditions of can separate out a large amount of Dispersed precipitates (high intensity) and the hardening constituent (high-fire resistance) with high thermal stability.Grind
Study carefully discovery, the Sc of 0.1at.% is added in aluminum can produce significant ageing strengthening effect, and the Al for separating out3Sc dispersion-strengthernings
Can exist steadily in the long term below 300 DEG C.But the price of Sc is prohibitively expensive, and add the aluminum of relatively inexpensive Er elements
Alloy has and precipitation process as Al-Sc alloy types, can be formed with aluminum substrate coherence with L12The Al of structure3Er phases,
And impact very little of the addition of Er to electrical conductivity.The micro Zr of addition can play certain ageing strengthening and act on and improve resistance to
It is hot, but the electrical conductivity of alloy is remarkably decreased.The research work of early stage shows that compound addition Er and Zr can produce collaboration and make
With, formed a large amount of disperses it is tiny and with the Al of aluminum substrate coherence3(Er, Zr) complex precipitates, effectively improve microalloying effect,
And electrical conductivity can reach 59%IACS.
Thermomechanical treatment is the method in combination with the phase transformation strengthening by working hardening during plastic deformation when the heat treatment.If closing
Gold undergoes phase transition during deforming or after deformation, then deform the Precipitation Kinetics of a large amount of dislocations meeting appreciable impact precipitated phase of introducing
And distribution；And precipitated phase also can On Dislocation Motion produce pinning, retardation, so as to steady-state deformation tissue.The present invention is by cold
The thermomechanical treatment of rear timeliness is rolled, compared with without the state deformed after direct aging, is shown on the premise of alloy rigidity is ensured
Work improves electrical conductivity.
The content of the invention：
It is an object of the invention to provide a kind of thermomechanical treatment process of Al-Er-Zr-Si alloys.By cold rolling retrogressing
The method of fire so that alloy aging separates out a large amount of Al3(Er, Zr) complex precipitates, can obtain ageing strengthening and due to analysis
The partial deformation reinforcing for go out phase pinning, blocking dislocation motion and retaining, it is ensured that enough mechanical properties, and can be introduced by deforming
A large amount of dislocations promote to separate out, obtain apparently higher than the static electrical conductivity for separating out.A kind of Al-Er-Zr-Si that the present invention is provided is closed
The thermomechanical treatment process of gold, concrete technical scheme is as follows：
1) the melting Al-Er-Zr-Si alloys at 760 DEG C, alloying component is Er：0.29wt%, Zr：0.30wt%, Si：
0.20wt%, balance of Al.It is sufficiently stirred for after each alloying element fusing, casting obtains cast alloy；
2) to step 1) gained alloy carries out heat treatment, and first in 640 DEG C of abundant solid solutions, simultaneously water quenching, to room temperature, is then used
Milling train carry out 20% to 90% it is cold roller and deformed, and between 150～600 DEG C when 25 DEG C etc. timeliness 3 hours；Or use
Milling train carries out 90% cold roller and deformed, then any one temperature 100 hours between 250～400 DEG C；
As currently preferred technical scheme, step 2) in by alloy carry out 60% it is cold roller and deformed after 150～425
Between DEG C when waiting for 25 DEG C timeliness 3 hours, or carry out 90% it is cold roller and deformed after be incubated 100 hours at 350 DEG C.
Advantages of the present invention and good effect：
The strain induced precipitate that thermomechanical treatment process provided by the present invention is produced by cold rolling after annealing, and without change
The alloy of shape direct aging is compared, and on the premise of the enough mechanical properties of alloy are ensured, promotes the precipitation of precipitated phase, so as to
The electrical conductivity of alloy is significantly improved, the contradiction existed between alloy strength and conductivity raising is solved, actual production is had very
Big directive significance.
Description of the drawings
Fig. 1：Timeliness (is protected at a temperature of each when waiting Jing after different distortion amount rolling process after Al-Er-Zr-Si alloy solid solutions
Temperature 3 hours) firmness change curve；
Fig. 2：Timeliness (is protected at a temperature of each when waiting Jing after different distortion amount rolling process after Al-Er-Zr-Si alloy solid solutions
Temperature 3 hours) conductivity variations curve；
Fig. 3：Isothermal aging firmness change after Al-Er-Zr-Si alloy solid solutions Jing after 90% is cold roller and deformed under different temperatures
Curve；
Fig. 4：Not deformed and Jing after 90% is cold roller and deformed under different temperatures isothermal aging after Al-Er-Zr-Si alloy solid solutions
Conductivity variations curve comparison：(a)250℃；(b)300℃；(c)350℃；(d)400℃
Specific embodiment：
Embodiment 1：The chemical composition of alloy is Er：0.29wt%, Zr：0.30wt%, Si：0.20wt%, balance of Al.
It is sufficiently stirred for after each alloying element fusing, casting obtains cast alloy, then carries out heat treatment to alloy, fills at 640 DEG C
Point solid solution and water quenching to room temperature, carry out afterwards 20% it is cold roller and deformed, and between 150～600 DEG C when 25 DEG C etc. timeliness 3
Hour.As can be seen from Figure 1 variation tendency of the hardness number of alloy before 425 DEG C is to gradually rise, and to 425 DEG C hardness is reached
Peak value 49.2HV, afterwards hardness number with temperature raise be gradually reduced, show alloy occur overaging.Alloy as can be seen from Figure 2
Electrical conductivity gradually rose in the past at 475 DEG C, show Al3The precipitation of (Er, Zr) precipitated phase, to 475 DEG C peak value 59.3% is reached
IACS, afterwards with the rising of temperature, because precipitated phase produces back dissolving, electrical conductivity is gradually lowered.
Embodiment 2：The chemical composition of alloy is Er：0.29wt%, Zr：0.30wt%, Si：0.20wt%, balance of Al.
It is sufficiently stirred for after each alloying element fusing, casting obtains cast alloy, then carries out heat treatment to alloy, fills at 640 DEG C
Point solid solution and water quenching to room temperature, carry out afterwards 60% it is cold roller and deformed, and between 150～600 DEG C when 25 DEG C etc. timeliness 3
Hour.As can be seen from Figure 1 variation tendency of the hardness number of alloy before 400 DEG C is to gradually rise, and to 400 DEG C hardness is reached
Peak value 51.0HV, afterwards hardness number be gradually reduced with the rising of temperature, alloy there occurs overaging.Alloy as can be seen from Figure 2
Electrical conductivity gradually rose in the past at 450 DEG C, peak value 59.7%IACS is reached to 450 DEG C, afterwards with the rising of temperature, electrical conductivity
It is gradually lowered.
Embodiment 3：The chemical composition of alloy is Er：0.29wt%, Zr：0.30wt%, Si：0.20wt%, balance of Al.
It is sufficiently stirred for after each alloying element fusing, casting obtains cast alloy, then carries out heat treatment to alloy, fills at 640 DEG C
Point solid solution and water quenching to room temperature, carry out afterwards 90% it is cold roller and deformed, and between 150～600 DEG C when 25 DEG C etc. timeliness 3
Hour.As can be seen from Figure 1 the variation tendency of the hardness number of alloy is gradually lowered with the rising of temperature, and 425 DEG C with
Front fluctuation is very big.As can be seen from Figure 2 the electrical conductivity of alloy gradually rose in the past at 475 DEG C, and to 475 DEG C peak value 60.3% is reached
IACS, afterwards with the rising of temperature, electrical conductivity is gradually lowered.
Comparative example 1：The chemical composition of alloy is Er：0.29wt%, Zr：0.30wt%, Si：0.20wt%, balance of Al.
It is sufficiently stirred for after each alloying element fusing, casting obtains cast alloy, then carries out heat treatment to alloy, fills at 640 DEG C
Point solid solution and water quenching is to room temperature, be not added with afterwards deformation directly between 150～600 DEG C when waiting for 25 DEG C timeliness 3 hours.From figure
1 can be seen that variation tendency of the hardness number of alloy before 400 DEG C is to gradually rise, and to 400 DEG C peak value of hardness is reached
49.0HV, afterwards hardness number be gradually reduced with the rising of temperature, alloy there occurs overaging.The electricity of alloy as can be seen from Figure 2
Conductance gradually rose in the past at 450 DEG C, and to 450 DEG C peak value 58.6%IACS is reached, and afterwards with the rising of temperature, electrical conductivity is gradually
Reduce.The peak value of hardness of alloy is close with the peak value of hardness of not deformed alloy Jing after 20% is cold roller and deformed, and the cold rolling changes of Jing 60%
Peak value of hardness of the peak value of hardness of alloy apparently higher than not deformed alloy after shape.The electrical conductivity peak value of alloy is bright Jing after cold roller and deformed
Aobvious is higher than not deformed alloy, illustrates that strain induced precipitate promotes Al3The precipitation of (Er, Zr) precipitated phase, so as to improve alloy
Electrical conductivity.
For the alloy Jing after 90% is cold roller and deformed, although its electrical conductivity peak value highest, but its hardness is with the liter of temperature
Height is presented downward trend；For the alloy Jing after 60% is cold roller and deformed, it is cold rolling that its hardness and electrical conductivity peak value are above Jing 20%
Alloy after deformation, it is advantageous to technical scheme be 60% it is cold roller and deformed after wait when timeliness to 425 DEG C.
Embodiment 4：The chemical composition of alloy is Er：0.29wt%, Zr：0.30wt%, Si：0.20wt%, balance of Al.
It is sufficiently stirred for after each alloying element fusing, casting obtains cast alloy, then carries out heat treatment to alloy, fills at 640 DEG C
Point solid solution and water quenching is to room temperature, then carry out it is 90% cold roller and deformed, and in 250 DEG C of insulations.From figure 3, it can be seen that alloy is 100
Hardness is always held at 55HV or so in hour insulating process, does not occur being decreased obviously, and shows the Al of strain induced precipitate3(Er,
Zr) precipitated phase effectively hinders recrystallization.From Fig. 4 (a) as can be seen that compared with when not deformed, the electrical conductivity of alloy slightly rises
Height, at 100 hours 55.6%IACS was reached.
Embodiment 5：The chemical composition of alloy is Er：0.29wt%, Zr：0.30wt%, Si：0.20wt%, balance of Al.
It is sufficiently stirred for after each alloying element fusing, casting obtains cast alloy, then carries out heat treatment to alloy, fills at 640 DEG C
Point solid solution and water quenching is to room temperature, then carry out it is 90% cold roller and deformed, and in 300 DEG C of insulations.From figure 3, it can be seen that alloy is 100
Hardness is always held at 53HV or so, slightly below embodiment 4 in hour insulating process, and does not occur being decreased obviously.From Fig. 4 (b)
As can be seen that compared with when not deformed, the electrical conductivity of alloy is increased significantly, at 100 hours 57.5%IACS was reached.
Embodiment 6：The chemical composition of alloy is Er：0.29wt%, Zr：0.30wt%, Si：0.20wt%, balance of Al.
It is sufficiently stirred for after each alloying element fusing, casting obtains cast alloy, then carries out heat treatment to alloy, fills at 640 DEG C
Point solid solution and water quenching is to room temperature, then carry out it is 90% cold roller and deformed, and in 350 DEG C of insulations.From figure 3, it can be seen that alloy is 100
Hardness is always held at 51HV or so, slightly below embodiment 5 in hour insulating process, and does not occur being decreased obviously.From Fig. 4 (c)
As can be seen that after 100 hours the electrical conductivity of not deformed alloy can reach 59.1%IACS, and the electrical conductivity of cold rolling rear alloy
Apparently higher than not deformed alloy, 59.8%IACS is reached.
Embodiment 7：The chemical composition of alloy is Er：0.29wt%, Zr：0.30wt%, Si：0.20wt%, balance of Al.
It is sufficiently stirred for after each alloying element fusing, casting obtains cast alloy, then carries out heat treatment to alloy, fills at 640 DEG C
Point solid solution and water quenching is to room temperature, then carry out it is 90% cold roller and deformed, and in 400 DEG C of insulations.From figure 3, it can be seen that alloy is being protected
Temperature after 8 minutes hardness number occur being decreased obviously, hardness number reaches minimum after insulation 30 minutes, shows, because temperature is too high, to cause
The Al of strain induced precipitate3(Er, Zr) precipitated phase fails effectively to hinder recrystallization.Although from 30 minutes start alloy hardness by
It is gradually increasing in the lasting precipitation of precipitated phase, but 37.2HV is only reached after 100 hours, far below 4～embodiment of embodiment
6.From Fig. 4 (d) as can be seen that the electrical conductivity of not deformed alloy after 100 hours can reach 58.8%IACS, and it is cold rolling after close
The electrical conductivity of gold reaches 59.8%IACS apparently higher than not deformed alloy.
For embodiment 4 and embodiment 5, although hardness number is not apparent from reducing in the insulating process of 100 hours, but conductance
Rate peak value is relatively low；For embodiment 7, although electrical conductivity reaches 59.8%IACS after being incubated 100 hours, but hardness number fails to keep
It is relatively stable.For embodiment 6, hardness number remains at 51HV or so after being incubated 100 hours, and electrical conductivity also can reach
To 59.8%IACS.It is advantageous to technical scheme be to be incubated 100 hours at 350 DEG C after 90% cold roller and deformed.
Claims (3)
1. a kind of thermomechanical treatment process of Al-Er-Zr-Si alloys, the composition of alloy is Er：0.29wt%, Zr：
0.30wt%, Si：0.20wt%, balance of Al, it is characterised in that comprise the following steps：
1) the melting Al-Er-Zr-Si alloys at 760 DEG C, are sufficiently stirred for after each alloying element fusing, and casting obtains as cast condition
Alloy；
2) to step 1) gained alloy carries out heat treatment, first 640 DEG C of abundant solid solutions simultaneously water quenching to room temperature, then using milling train
Carry out 20% to 90% it is cold roller and deformed, and between 150～600 DEG C when 25 DEG C etc. timeliness 3 hours；Or use milling train
Carry out 90% it is cold roller and deformed, then at any one temperature between 250～400 DEG C be incubated 100 hours.
2. Technology for Heating Processing according to claim 1, it is characterised in that timeliness cold rolling reduction is 60% when waiting, and
Between 150～425 DEG C when waiting for 25 DEG C timeliness 3 hours.
3. Technology for Heating Processing according to claim 1, it is characterised in that using milling train carry out 90% it is cold roller and deformed, etc.
Warm hardening temperature and time is to be incubated 100 hours at 350 DEG C.
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| CN105925924A (en) * | 2016-06-11 | 2016-09-07 | 江苏迅达电磁线有限公司 | Thermomechanical treatment method capable of improving performance of end ring for high-speed rail |
| CN110241317A (en) * | 2019-06-20 | 2019-09-17 | 西安理工大学 | A kind of hard bar of high-performance aluminium sheet of preparation method |
| CN110987695B (en) * | 2019-12-19 | 2020-12-04 | 中南大学 | Method for measuring quenching sensitive temperature range of heat-treatable strengthened aluminum alloy |
| CN112095038B (en) * | 2020-09-27 | 2022-03-22 | 北京工业大学 | Method for increasing number of disperse phases in aluminum alloy |
| CN114606414B (en) * | 2022-03-11 | 2022-12-02 | 北京理工大学 | High-conductivity regenerated aluminum alloy conductor and preparation method thereof |
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| JPS5864363A (en) * | 1981-10-14 | 1983-04-16 | Hitachi Cable Ltd | Manufacture of heat resistant aluminum alloy with high electric conductivity |
| JPS5964753A (en) * | 1982-09-30 | 1984-04-12 | Dainichi Nippon Cables Ltd | Manufacture of heat-resistant aluminium alloy wire for conducting electricity |
| JPS6123752A (en) * | 1984-07-12 | 1986-02-01 | Furukawa Electric Co Ltd:The | Manufacture of high strength and heat resistant aluminum alloy conductor |
| JPH11350093A (en) * | 1998-06-04 | 1999-12-21 | Mitsubishi Cable Ind Ltd | Manufacture of heat resistant aluminum alloy conducting wire |
| KR100755130B1 (en) * | 2006-01-31 | 2007-09-04 | 엘에스전선 주식회사 | Method of manufacturing aluminum alloy having high electro-conductivity and heat resistance, Aluminum alloy wire and Overhead transmission line manufactured using the same |
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| CN103225028A (en) * | 2013-03-15 | 2013-07-31 | 北京工业大学 | Al-Er-Zr-Si heat-resistant aluminum alloy and its heat treatment technology |
| CN103184372B (en) * | 2013-04-01 | 2015-05-06 | 北京工业大学 | Electrochemical corrosion-resistant reinforced Al-Zr-Er alloy material and preparation method thereof |
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