CN103014391B - The alloy preparation method of a kind of improvement 2618 aluminium alloy micostructure - Google Patents
The alloy preparation method of a kind of improvement 2618 aluminium alloy micostructure Download PDFInfo
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- CN103014391B CN103014391B CN201210567413.9A CN201210567413A CN103014391B CN 103014391 B CN103014391 B CN 103014391B CN 201210567413 A CN201210567413 A CN 201210567413A CN 103014391 B CN103014391 B CN 103014391B
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- 239000000956 alloy Substances 0.000 title claims abstract description 91
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 89
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 58
- 238000002360 preparation method Methods 0.000 title claims abstract description 16
- 230000006872 improvement Effects 0.000 title claims abstract description 11
- 239000000843 powder Substances 0.000 claims abstract description 23
- 238000000034 method Methods 0.000 claims abstract description 14
- 229910052802 copper Inorganic materials 0.000 claims abstract description 11
- 229910052782 aluminium Inorganic materials 0.000 claims description 14
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 10
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 7
- 241000209456 Plumbago Species 0.000 claims description 7
- 239000010439 graphite Substances 0.000 claims description 7
- 239000002245 particle Substances 0.000 claims description 7
- 238000003756 stirring Methods 0.000 claims description 7
- 239000004411 aluminium Substances 0.000 claims description 6
- 229910052759 nickel Inorganic materials 0.000 claims description 6
- 238000010792 warming Methods 0.000 claims description 5
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 claims description 4
- 239000003795 chemical substances by application Substances 0.000 claims description 4
- 238000007254 oxidation reaction Methods 0.000 claims description 4
- 150000003839 salts Chemical class 0.000 claims description 4
- 229910000881 Cu alloy Inorganic materials 0.000 claims description 2
- 238000000889 atomisation Methods 0.000 claims description 2
- 150000001875 compounds Chemical class 0.000 claims description 2
- 238000000113 differential scanning calorimetry Methods 0.000 claims description 2
- 238000000746 purification Methods 0.000 claims description 2
- 239000011780 sodium chloride Substances 0.000 claims description 2
- 239000008247 solid mixture Substances 0.000 claims description 2
- 238000001179 sorption measurement Methods 0.000 claims description 2
- 239000013078 crystal Substances 0.000 abstract description 15
- 229910018182 Al—Cu Inorganic materials 0.000 abstract description 9
- 238000005266 casting Methods 0.000 abstract description 7
- 210000001787 dendrite Anatomy 0.000 abstract description 6
- 230000008569 process Effects 0.000 abstract description 4
- 239000000203 mixture Substances 0.000 description 10
- 239000011159 matrix material Substances 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 238000007670 refining Methods 0.000 description 5
- 230000015572 biosynthetic process Effects 0.000 description 4
- 238000000265 homogenisation Methods 0.000 description 4
- 238000011282 treatment Methods 0.000 description 4
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000004080 punching Methods 0.000 description 2
- 229910001030 Iron–nickel alloy Inorganic materials 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 229910001297 Zn alloy Inorganic materials 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000004581 coalescence Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000007771 core particle Substances 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000004512 die casting Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 230000005684 electric field Effects 0.000 description 1
- 230000005713 exacerbation Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 239000002667 nucleating agent Substances 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
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Abstract
The invention belongs to field of aluminium alloy material preparation, particularly the alloy preparation method of a kind of improvement 2618 aluminium alloy micostructure, comprises refinement 2618 aluminium alloy as-cast grain structure and improves as-cast structure pattern.The technical solution used in the present invention is: in aluminium alloy melt, add the good Al-90Cu(Al-90wt%Cu of a certain amount of wettability) powdered alloy is with the Al-Cu master alloy used in alternative conventional cast process, by strictly controlling aluminum alloy melt temperature and churning time, immediately Near-liquidus Casting is carried out to it when powder is just dissolved, to obtain 2618 aluminium alloys that crystal grain is tiny, dendrite reduces.
Description
Technical field
The invention belongs to field of aluminium alloy material preparation, particularly the alloy preparation method of a kind of improvement 2618 aluminium alloy micostructure, comprises refinement 2618 aluminium alloy as-cast grain structure and improves as-cast structure pattern.
Background technology
2618 aluminium alloys belong to the heat-resisting wrought aluminium of Al-Cu-Mg-Fe-Ni system, the S` (Al of half coherence that artificial aging process is separated out
2cuMg) be the main strengthening phase of this alloy mutually, adding of Fe, Ni in proportion can form intermetallic compound as Al on a small quantity
9feNi, controls the size of crystal grain and the motion of dislocation effectively, further increases room temperature and the high-temperature behavior of this alloy, is widely used in the field such as automobile industry and Aeronautics and Astronautics.
Along with science and technology and the structure and properties of development to 2618 aluminium alloys of aviation industry are had higher requirement, and the alloy that founding goes out to have fine isometric crystal grains tissue is one of key of use properties under this Alloy At Room Temperature of raising and comparatively high temps; The method of refining aluminum alloy matrix grain mainly can be divided into two kinds: one to be object and solidifying fine crystal by controlling and regulate alloying constituent, speed of cooling, teeming temperature to reach crystal grain thinning; Two is obtain tiny crystal grain i.e. rotten thin crystalline substance by a large amount of external heterogeneous forming core particle of method introducing of interpolation nucleating agent or microalloying; Solidifying fine crystal usually will by means of the effect of necessarily additional electric field, magnetic field, mechanical field, and higher to equipment requirements, cost increases; And the rotten thin brilliant add-on to alterant, melt temperature has strict requirement and control usually, not only increases cost and complex process, even can because of bringing inclusion particle adding of external particle, if control improper for the performance of severe exacerbation alloy; Al-90Cu alloy powder once added in zinc die casting alloys and formed wild phase by patent applicant, thus prepared the Zinc alloy based matrix material with good over-all properties.
When adopting fusion casting to prepare aluminium alloy, traditional method adds required alloying element with the form of various master alloy; Because intermetallic compound in master alloy is in thicker form, and have larger component segregation, bad tissue heredity will be produced when therefore adopting this master alloy to found aluminium alloy, make in the aluminum alloy organization obtained that dendrite is more flourishing, crystal grain is thicker; For this reason, the Adding Way finding a kind of new master alloy replaces traditional master alloy Adding Way, on the main component basis of guarantee 2618 aluminium alloy, prepare 2618 tiny aluminium alloys of as-cast grain structure, having very important actual application value, is also an important innovations on aluminum alloy Preparation Method.
Summary of the invention
It is thick to there is intermetallic compound in the common Al-Cu master alloy used in 2618 aluminum alloy melt casting processes, the problem that component segregation is larger; Therefore, bad tissue heredity will be produced when adopting this master alloy to found 2618 aluminium alloy, make that this aluminium alloy as-cast structure dendrite is flourishing, crystal grain is thicker.
Use Al-90Cu alloy powder for the common Al-Cu master alloy used during conventional cast in the present invention, because powdered alloy adopts the method for powder by atomization to prepare, therefore master alloy is organized very tiny, composition is very even, adopts this master alloy to prepare 2618 alloys and will obtain good effect.
The particle size of the made of Al-Cu alloy powder that the present invention adopts is 100 orders, controls its add-on and makes the content of Cu element in 2618 alloys be 1.9-2.5wt.%; After alloy powder being added aluminum alloy melt, the strict churning time that controls is within 60S, just cast at the liquidus temperature of 2618 alloys above 20-40 DEG C when making it just melt, 2618 alloy matrix aluminum grain-sizes can be made to control at 15-20um, and its cast structure becomes the uniform formation of axles such as being tending towards from original large dendritic crystal, most of dendrite disappears.
The principle of this invention is: adopt Al-90Cu powdered alloy substitute for Al-Cu intermediate alloy ingot to add in aluminium alloy melt, guarantee 2618 al alloy component constant basis on, introduce the effect that a large amount of micro-powders plays miniature chill; Because the miniature chill of powder causes larger undulating composition and temperature fluctuation in dissolution process, the formation of mass crystallization core can be promoted, reduce the formation of dentrite, finally reach the object of refining aluminum alloy Solidification Microstructure of Castings.
The object of the invention is, the unnecessary foreing impuritys particle issues brought is added to the dependence of impressed field and alterant when the alloy preparation method proposing a kind of improvement 2618 aluminium alloy micostructure is to solve tradition thin brilliant casting, also can avoid adopting common master alloy problem, the problem includes: the bad heredity problem of thick microstructure and composition segregation, aim to provide the alloy preparation method that a kind of grain refining effect is good, act on fast, easy to operate improvement 2618 aluminium alloy micostructure.
The technical solution used in the present invention is: in aluminium alloy melt, add the good Al-90Cu(Al-90wt%Cu of a certain amount of wettability) powdered alloy is with the Al-Cu master alloy used in alternative conventional cast process, by strictly controlling aluminum alloy melt temperature and churning time, immediately Near-liquidus Casting is carried out to it when powder is just dissolved, to obtain 2618 aluminium alloys that crystal grain is tiny, dendrite reduces.
Improve an alloy preparation method for 2618 aluminium alloy micostructure, comprise the steps:
A. adopt crucible electrical resistance furnace preheating plumbago crucible to red heat state, be then warming up to 720-750 DEG C and commercial-purity aluminium, Al-10wt.%Fe, Al-10wt.%Ni and Al-25wt.%Mg master alloy are melted completely.
B. stir aluminium alloy and add salt insulating covering agent on aluminium alloy surface and prevent oxidization burning loss, purefying melt, to leave standstill, until control melt temperature at the above 30-50 DEG C of liquidus line.
C. in melt, add Al-90Cu alloy powder equably, the strict churning time that controls, within 60S, stirs rapidly and powder has just been dissolved just cast immediately, make the pouring temperature of aluminum alloy melt remain on the above 20-40 DEG C of liquidus line.
In described step A, preheating plumbago crucible is 540 ~ 560 DEG C to the temperature of red heat state.
Salt insulating covering agent in described step B is 30wt%%NaCl+47 wt%%KCl+23 wt%Na
3alF
6solid mixture, for preventing the air-breathing oxidization burning loss of melt, oxide compound in Al adsorption melt purification melt.
In described step B, liquidus temperature adopts DSC(differential scanning calorimetry) be determined as 638 DEG C, control melt temperature at the above 30-50 DEG C of liquidus line, even if melt temperature controls at 668-688 DEG C.
Al-90Cu alloy powder particle size in described step C be 100 orders with the Al-Cu master alloy used during alternative conventional cast, pouring temperature to control at liquidus temperature above 20-40 DEG C: 658 DEG C-678 DEG C.
In described step C, the strict churning time that controls is in 60S, uneven components after increase powdered alloy is dissolved by aluminum alloy melt, keep having larger undulating composition and concentration fluctuations in aluminium alloy, give full play to the miniature chill effect of powdered alloy, increase the quantity of solidifying nucleus, thus the grain structure of refining aluminum alloy.
In the present invention, Al-90wt.%Cu powdered alloy add-on is 2.11 wt% ~ .2.78 of 2618 aluminium alloy total amounts
Wt%, thus make the content of Cu element in 2618 alloys be 1.9-2.5wt.%.
Advantage of the present invention is: adopt Al-90wt.%Cu alloy powder to replace Al-Cu master alloy and prepare 2618 aluminium alloys, the formation of thick dentrite in alloy can be reduced, obtain the grain structure of the evenly tiny axle such as approximate, this alloy structure still can keep preferably after the Homogenization Treatments of 480 DEG C of+24h, and this cold and hot working performance to improvement 2618 aluminium alloy, final product quality and use properties thereof are all very important.
Accompanying drawing explanation
The SEM photo of Fig. 1 to be granularity be 100 object Al-90Cu alloy powders, as can be seen from the figure powder is all exist with form that is granular or strip, mean particle size the chances are 100 μm.
Fig. 2 adopts the melting of traditional Al-50wt.%Cu master alloy, to cast under differing temps the microstructure picture of 2618 aluminum alloy specimens obtained, along with pouring temperature drops to 660 DEG C from 720 DEG C, the refinement to some extent of alloy matrix aluminum grain structure, but thinning effect is not obvious, along with the reduction of pouring temperature, in cast structure, large dendritic crystal obviously reduces, and average grain size is about 30um.
Fig. 3 is the microstructure picture of 2618 aluminum alloy specimens of the different Cu content adopting the inventive method to prepare, and the pouring temperature of employing is 660 DEG C; Along with the increase alloy matrix aluminum crystal grain of Cu content has the trend reduced gradually, to cast at the same temperature prepared alloy compared with embodiment one, matrix grain organizes obvious refinement, and average grain size, at 15-20um, only has a small amount of dentrite to retain.
Fig. 4 is the microstructure picture of 2618 aluminum alloy specimens of the different Cu content adopting the inventive method to prepare, but its teeming temperature is 720 DEG C, the impact of the alloy of experimental study teeming temperature as a comparison solidified structure; Along with the increase of Cu content, alloy matrix aluminum crystal grain has the trend reduced gradually, and cast prepared alloy ratio at the same temperature comparatively with embodiment one, matrix grain organizes obvious refinement; But with embodiment two compares, grain-size is slightly grown up and mostly is columnar dendrite.
Fig. 5 is the SEM photo of alloy sample after the Homogenization Treatments of 480 DEG C of+24h adopting embodiment one, two, three to prepare; Sample after homogenizing annealing grain boundaries second-phase compared with original as cast condition obviously reduces, Al more stable under only leaving high temperature
9feNi phase, crystal boundary becomes intermittent, and due to atomic diffusion under high temperature very fast, small grains coalescence makes the grain-size of alloy increase to some extent; Compare with 2618 aluminium alloys prepared by traditional method, under identical pouring temperature, 2618 alloys adopting the inventive method to prepare still maintain the advantage of small grains tissue after Homogenization Treatments, and along with the increase of powdered alloy amount, the degree increase of grain refining.
Fig. 5 (a) 660 DEG C, master alloy, 4.6% represent that its teeming temperature is 660 DEG C, and the add-on of employing Al-Cu master alloy preparation method, master alloy is massfraction 4.6%; The method for expressing of other (b)-(h) figure is identical with (a) indicates its teeming temperature respectively, casting mode and master alloy or powdered alloy add massfraction.
Embodiment
Embodiment one: adopt the melting of traditional Al-50wt%Cu master alloy to prepare 2618 aluminium alloys, design mix is 2.3Cu-1.6Mg-1.1Fe-1.1Ni-Bal.Al (massfraction), then the add-on of master alloy is 4.6wt.%; First adopt crucible electrical resistance furnace preheating plumbago crucible to red heat state (550 DEG C), then be warming up to 720-750 DEG C commercial-purity aluminium (99.7wt.%Al), Al-50wt.%Cu, Al-10wt.%Fe, Al-10wt.%Ni and Al-25wt.%Mg master alloy are melted completely, stirring makes it mix, and leaves standstill the temperature controlling alloy melt and casts 660 DEG C and 720 DEG C respectively.
Embodiment two: adopt Al-90Cu(Al-90wt%Cu) powdered alloy is as the source of Cu element in 2618 aluminium alloys, design mix is that 1.9-2.5Cu-1.6Mg-1.1Fe-1.1Ni-Bal.Al, Cu content is respectively 1.9%, 2.3%, 2.5% (massfraction), first adopt crucible electrical resistance furnace preheating plumbago crucible to red heat state (540 DEG C), then 720-750 DEG C is warming up to by commercial-purity aluminium, Al-10wt.%Fe, Al-10wt.%Ni and Al-25wt.%Mg master alloy melts completely, stirring makes it mix, leave standstill the temperature of control alloy melt at 668-688 DEG C, add 2.11 wt.% respectively, 2.56, the alloy powder of 2.78wt.%, be stirred to rapidly powder melt completely and strictly control churning time within 60S, be cast to immediately and be preheating to hole, 150 DEG C of chambeies and be of a size of in the punching block of φ 12 × 120mm, teeming temperature is 660 DEG C.
Embodiment three: the program be as a comparison and adopt scheme.Adopting Al-90Cu(Al-90wt%Cu) powdered alloy is as the source of Cu element in 2618 aluminium alloys, and design mix is 1.9-2.5Cu-1.6Mg-1.1Fe
-1.1Ni-Bal.Al, Cu content is respectively 1.9%, 2.3%, 2.5% (massfraction), first adopt crucible electrical resistance furnace preheating plumbago crucible to red heat state (560), then 720-750 DEG C is warming up to by commercial-purity aluminium (99.7wt.%Al), Al-10wt.%Fe, Al-10wt.%Ni and Al-25wt.%Mg master alloy melts completely, stirring makes it mix, leave standstill the temperature of control alloy melt at 730-750 DEG C, add 2.11 wt.% respectively, 2.56, 2.78wt.% alloy powder, be stirred to rapidly powder melt completely and strictly control churning time within 60S, be cast to immediately and be preheating to hole, 150 DEG C of chambeies and be of a size of in the punching block of φ 12 × 120mm, teeming temperature is 720 DEG C.
Embodiment four: the whole alloy cast ingots prepared by embodiment one, two, three, cut in the water of one group of sample Homogenization Treatments direct input room temperature after 24 hours at 480 DEG C and quench, the tissue of homogenizing is remained into the observation that room temperature carries out microstructure.
Claims (5)
1. improve an alloy preparation method for 2618 aluminium alloy micostructure, comprise the steps:
(A) adopt crucible electrical resistance furnace preheating plumbago crucible to red heat state, be then warming up to 720-750 DEG C and commercial-purity aluminium, Al-10wt%Fe, Al-10wt%Ni and Al-25wt.%Mg master alloy are melted completely;
(B) stir aluminium alloy and add salt insulating covering agent on aluminium alloy surface and prevent oxidization burning loss, purefying melt, to leave standstill, until control melt temperature at the above 30-50 DEG C of liquidus line;
(C) in melt, add the Al-90 wt%Cu alloy powder adopting the method for powder by atomization to prepare equably, strict control churning time is within 60s, rapid stirring makes powder just dissolve just to cast immediately, make the pouring temperature of aluminum alloy melt remain on the above 20-40 DEG C of liquidus line;
In described step C, Al-90wt.%Cu powdered alloy add-on is 2.11 wt% ~ 2.78wt% of 2618 aluminium alloy total amounts, makes the content of Cu element in 2618 alloys be 1.9-2.5wt%.
2. the alloy preparation method of a kind of improvement as claimed in claim 1 2618 aluminium alloy micostructure, is characterized in that: in described step A, preheating plumbago crucible is 540 ~ 560 DEG C to the temperature of red heat state.
3. the alloy preparation method of a kind of improvement as claimed in claim 1 2618 aluminium alloy micostructure, is characterized in that: the salt insulating covering agent in described step B is 30wt%NaCl+47 wt%KCl+23 wt%Na
3alF
6solid mixture, for preventing the air-breathing oxidization burning loss of melt, oxide compound in Al adsorption melt purification melt.
4. the alloy preparation method of a kind of improvement as claimed in claim 1 2618 aluminium alloy micostructure, is characterized in that: in described step B, liquidus temperature adopts differential scanning calorimetry to measure.
5. the alloy preparation method of a kind of improvement as claimed in claim 1 2618 aluminium alloy micostructure, is characterized in that: the Al-90Cu alloy powder particle size in described step C is 100 orders.
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| CN113737037A (en) * | 2021-09-17 | 2021-12-03 | 苏州明志科技股份有限公司 | Method for refining aluminum alloy grains |
| CN113862534B (en) * | 2021-10-08 | 2022-07-29 | 上海交通大学 | Method for regulating and controlling tissue inheritance of aluminum alloy material and method for preparing 7085 aluminum alloy thick plate |
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Non-Patent Citations (2)
| Title |
|---|
| 2618耐热铝合金的组织与力学性能的研究;王建华;《中国博士学位论文全文数据库 工程科技I辑》;20041215(第4期);第21页第2.1.2部分第2段 * |
| 王金华.《悬浮铸造》.《悬浮铸造》.国防工业出版社,1982,第128-129页. * |
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