CN107052282B - A kind of preparation method of the twin dendrite of Al-40%Zn alloy - Google Patents
A kind of preparation method of the twin dendrite of Al-40%Zn alloy Download PDFInfo
- Publication number
- CN107052282B CN107052282B CN201710281993.8A CN201710281993A CN107052282B CN 107052282 B CN107052282 B CN 107052282B CN 201710281993 A CN201710281993 A CN 201710281993A CN 107052282 B CN107052282 B CN 107052282B
- Authority
- CN
- China
- Prior art keywords
- heating
- alloy
- dendrite
- thermal insulation
- twin
- 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.)
- Expired - Fee Related
Links
- 210000001787 dendrite Anatomy 0.000 title claims abstract description 70
- 238000002360 preparation method Methods 0.000 title claims abstract description 26
- 229910001297 Zn alloy Inorganic materials 0.000 title claims abstract description 23
- 238000007711 solidification Methods 0.000 claims abstract description 19
- 230000008023 solidification Effects 0.000 claims abstract description 19
- 238000010438 heat treatment Methods 0.000 claims description 38
- 238000005086 pumping Methods 0.000 claims description 35
- 238000009413 insulation Methods 0.000 claims description 28
- 230000006698 induction Effects 0.000 claims description 25
- 229910000838 Al alloy Inorganic materials 0.000 claims description 17
- 229910002804 graphite Inorganic materials 0.000 claims description 17
- 239000010439 graphite Substances 0.000 claims description 17
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 16
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 12
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 claims description 6
- 244000137852 Petrea volubilis Species 0.000 claims description 3
- 238000004140 cleaning Methods 0.000 claims description 3
- 238000005498 polishing Methods 0.000 claims description 3
- 238000007789 sealing Methods 0.000 claims description 3
- 238000004321 preservation Methods 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 abstract description 18
- 239000000956 alloy Substances 0.000 abstract description 18
- 229910018137 Al-Zn Inorganic materials 0.000 abstract description 13
- 229910018573 Al—Zn Inorganic materials 0.000 abstract description 13
- 238000000034 method Methods 0.000 abstract description 11
- 230000008569 process Effects 0.000 abstract description 5
- 229910052725 zinc Inorganic materials 0.000 abstract description 5
- 238000005516 engineering process Methods 0.000 abstract description 3
- 238000013461 design Methods 0.000 abstract description 2
- 239000004615 ingredient Substances 0.000 abstract description 2
- 239000007769 metal material Substances 0.000 abstract description 2
- 239000013078 crystal Substances 0.000 description 10
- 238000001887 electron backscatter diffraction Methods 0.000 description 9
- 238000011160 research Methods 0.000 description 8
- 239000000126 substance Substances 0.000 description 8
- 238000004458 analytical method Methods 0.000 description 7
- 239000007788 liquid Substances 0.000 description 4
- 229910052782 aluminium Inorganic materials 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 230000015271 coagulation Effects 0.000 description 3
- 238000005345 coagulation Methods 0.000 description 3
- 230000008859 change Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000002425 crystallisation Methods 0.000 description 2
- 230000008025 crystallization Effects 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 230000001681 protective effect Effects 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 229910001128 Sn alloy Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 208000016253 exhaustion Diseases 0.000 description 1
- 210000003746 feather Anatomy 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 230000008014 freezing Effects 0.000 description 1
- 238000007710 freezing Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/049—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds for direct chill casting, e.g. electromagnetic casting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
- B22D11/003—Aluminium alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/10—Supplying or treating molten metal
- B22D11/11—Treating the molten metal
- B22D11/112—Treating the molten metal by accelerated cooling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
Abstract
The invention belongs to the preparation fields of metal material, and in particular to a kind of preparation method of the twin dendrite of Al-40%Zn alloy.The preparation method selects the ingredient design of high Zn content Al-Zn alloy (40%Zn), using directional solidification technique, high directional solidification withdrawing rate (900 ~ 1100 μm/s) are chosen, intracorporal convection current is melted using being formed in directional solidification process, is successfully prepared the twin dendrite of Al-40%Zn alloy.The present invention choose Al-40%Zn alloy be used as the alloy system for prepare twin dendrite, be different from study report in low content Zn(30%Zn or less) Al-Zn alloy system, this is not reported at component selections, overcomes technology prejudice.
Description
Technical field
The invention belongs to the preparation fields of metal material, and in particular to a kind of preparation side of the twin dendrite of Al-40%Zn alloy
Method.
Background technique
Twin dendrite, also known as Feather-like Crystal (Feathery grains), also referred to as twin crystal, twin, basaltiform are brilliant
Deng belonging to one kind (Growth twin) of twin.Be originally found in semi-continuous casting aluminium alloy, be totally different from it is common
A kind of abnormal grain of column crystal and dendrite, referred to as the third class dendrite in casting.It is twin why it is referred to as featheriness
Dendrite is that its pattern is similar to feather in two-dimentional microstructure due to this kind of dendrite.Research shows that twin dendrite is certain
Under the conditions of a kind of obtained cast sturcture, the speed of maximum growth axially carries out, has with axial parallel twin dendrite
There is strongest competitiveness, so the dendrite in other directions is easy to be suppressed.Thus, the direction of growth is substantially parallel with axial direction,
It with strong anisotropy, and is not susceptible to deform in pressing process and be crushed, so its microcosmic group to alloy
It knits and plays the role of optimization with mechanical property.Zhou Yao and et al. it is brilliant to single Shu Yuzhuan crystalline substance and multi beam pinniform in last century the eighties
Mechanical property did the work of more system, and analyze influence of the pinniform crystal layer piece spacing to mechanical property, they have found
The reticular structure that multi beam pinniform crystalline substance is formed when intersecting strengthens the continuity of sample in the stretching direction, so that mechanical property
It significantly improves.Therefore in alloy casting process obtain the twin dendrite of large area become improve alloy property key, to it
Research has important value in solidification theory research and industrial application.
And found in the research of the Forming Mechanism in twin dendrite, since twin dendrite is the temperature in crystallization front liquid
It is generated in the case that degree gradient is very precipitous, to cross cold belt extremely narrow.Therefore, when the overtemperature of melt is very high, ingot casting
Cooling velocity is exceedingly fast, hot-fluid from crystallization be diffused towards single direction and melt in effective active particle it is few when, it is twin
Raw dendrite is easy to generate.Based on this, it is that twin dendrite generates that generally high temperature gradient and strong convection are thought in research at present
Necessary condition.Since Al has weak anisotropy such as in Al-Zn alloy, coarse boundary is easily formed during conventional coagulation
Face is unfavorable for the formation of twin dendrite there is no strong growth competitiveness, but passes through the study found that under certain specific condition,
In high-temperature gradient and strong convection environment, certain twin dendrite can also be formed.Directional solidification technique is as special
Nonequilibrium freezing technology, temperature gradient, cooling rate and convection environment with higher in process of setting are Al-Zn alloy
The formation of twin dendrite provides preparation condition.However, current study show that in Al-Zn alloy when Zn content reaches 40%, it is twin
Raw dendrite does not re-form, this becomes the bottleneck of the twin dendrite preparation process of Al-Zn alloy.It therefore, can be in high Zn content Al-Zn
Twin dendrite is prepared in alloy becomes the research emphasis of material preparation.
Summary of the invention
The purpose of the present invention is to provide a kind of preparation methods of twin dendrite of Al-40%Zn alloy.
To achieve the above object, the technical solution adopted by the present invention is as follows:
A kind of preparation method of the twin dendrite of Al-40%Zn alloy, the preparation method use a device for directionally solidifying, this is fixed
It include pumping rod, heating and thermal insulation furnace and induction coil, inverted trapezoidal graphite cannula, cylinder among its inner cavity to coagulation system
Crucible, "convex" shaped connecting tube, collet, the small end of connecting tube is adapted with crucible, big end is adapted with pumping rod, and heating is protected
The side wall of warm furnace and its inner cavity are respectively communicated with equipped with Ar tracheae and vacuum tube, and Ar tracheae is connected with Ar gas tank, and vacuum tube successively connects
It is connected to molecular pump, mechanical pump, the bottom of heating and thermal insulation furnace is sealedly connected with crystallizer with it, and Ga-In-Sn conjunction is filled in crystallizer
Golden liquid, crystallizer top is located among heating and thermal insulation furnace chamber, remainder is then located at heating and thermal insulation furnace exterior, and collet is located at
On crystallizer, graphite cannula is located on collet, and induction coil is adding around graphite cannula surrounding, induction coil is located at setting
Induction power supply except hot holding furnace is connected, and crucible is located among graphite cannula, the small end that crucible and pumping rod pass through connecting tube
Be plugged in the lower end of the crucible, big end cap pumping rod upper end realize connection, pumping rod from top to bottom successively sealing through collet,
Crystallizer, pumping rod bottom are connected with drawing device；
Preparation step is as follows:
(1), cylinder Al-40%Zn alloy sample compatible with crucible shape is prepared；
(2), sand paper polishing, acetone cleaning sample, to remove the oxide layer and impurity on surface；Sample is put into crucible,
Move down pumping rod by drawing device until the small end of connecting tube bottom is just concordant with the top of collet, big end then
It stretches out collet and immerses in the Ga-In-Sn aluminium alloy in crystallizer；
(3), it is vacuumized respectively using mechanical pump and molecular pump, until the vacuum degree of heating and thermal insulation furnace is to 7 × 10-3Pa with
On, it is then filled with Ar gas into heating and thermal insulation furnace and forms protective gas environment, fills the vacuum degree after Ar gas in heating and thermal insulation furnace and protects
It holds in 350 ~ 400 Pa；
(4), induction power supply is opened, is heated by induction coil, is heated to above 80 ~ 150 DEG C of sample fusing point, locates at this time
Sample in induction coil effective heating area melts, and the sample except induction coil effective heating area does not melt
Change, keep the temperature (30 ~ 60min), keeps melt temperature uniform, stable；
(5), the drawing velocity for adjusting pumping rod is 900 ~ 1100 μm/s, starts pull and is oriented solidification experiments, will melt
Body draws in Ga-In-Sn aluminium alloy from top to bottom and realizes directional solidification；
(6), after melt directional solidification, then adjusting the drawing velocity of pumping rod is 90 ~ 110 mm/s, and entire sample is complete
It draws in Ga-In-Sn aluminium alloy and is quenched entirely, simultaneously close off heating and thermal insulation furnace, open fire door, the furnace in holding furnace to be heated
After temperature naturally cools to room temperature, pumping rod is moved up by drawing device, entire sample is ejected into Ga-In-Sn alloy completely
Liquid takes out to get the twin dendrite of Al-40%Zn alloy.
Preferably, the drawing velocity for adjusting pumping rod is preferably 1000 μm/s
Preferably, the preferably high-purity (99.9%Al of the crucible2O3) aluminium oxide alundum tube.
The utility model has the advantages that
1, the present invention chooses Al-40%Zn alloy as the alloy system for preparing twin dendrite, contains different from low in research report
Measure Zn(30%Zn or less) Al-Zn alloy system, this is not reported at component selections.And existing research before making the present invention
(in Yang Luyan, Li Shuanming, Gao Ka, Zhong Hong, Fu Heng will aluminium alloy progress [J] the Rare Metals Materials of twin dendrite with
Engineering, 2015,44 (07): 001809-1814) think that Al-Zn alloy can not be prepared twin when Zn content is greater than 40%
The alloying component of raw dendrite, therefore the present invention overcomes technology prejudice；
2, the ingredient design that high Zn content Al-Zn alloy (40%Zn) is selected in the present invention, uses directional solidification technique,
High directional solidification withdrawing rate (900 ~ 1100 μm/s) are chosen, melt intracorporal convection current using being formed in directional solidification process, at
Function is prepared for the twin dendrite of high Zn content Al-Zn alloy, provides test basis for the extensive preparation of the twin dendrite of Al-Zn alloy.
In addition, Hirschfeld-Klinger reaction only occurs for twin dendrite obtained, organization internal by the method for the invention, precipitated phase is simple, and entire behaviour
It is simple to make process, experimental expenses is lower.
Detailed description of the invention
Fig. 1: oriented coagulation forming device: 1- heating and thermal insulation furnace, 2- induction coil, 3- graphite cannula, 4- crucible, 5- connection
Pipe, 6- collet, 7-Ar tracheae, 8- vacuum tube, 9- crystallizer, 10-Ga-In-Sn aluminium alloy, 11- pumping rod, 12- sample.
Fig. 2: the longitudinal section analysis of the twin dendrite of Al-40%Zn alloy made from embodiment 1 :(a) micro-organization chart；(b) it is
(a) solid-line rectangle frame region enlarged drawing in；(c) the EBSD pole figure tested for dashed rectangle frame region in (b).
Fig. 3: the longitudinal section analysis of Al-40%Zn alloy plain cylindrical crystalline substance made from reference examples 1 :(a) micro-organization chart；(b)
The EBSD pole figure tested for dashed rectangle frame region in (a).
Fig. 4: the longitudinal section analysis of Al-40%Zn alloy plain cylindrical crystalline substance made from reference examples 2 :(a) micro-organization chart；(b)
For solid-line rectangle frame region enlarged drawing in (a)；(c) the EBSD pole figure tested for dashed rectangle frame region in (b).
Specific embodiment
The present invention is further elaborated combined with specific embodiments below, and used raw material is in following embodiment
This field general chemical.
Embodiment 1
A kind of preparation method of the twin dendrite of Al-40%Zn alloy, the preparation method use a device for directionally solidifying, such as Fig. 1
Shown, which includes pumping rod 11, heating and thermal insulation furnace 1 and the induction coil 2 among its inner cavity, inverted trapezoidal
Graphite cannula 3, the high-purity (99.9%Al of cylinder crucible 4(2O3) aluminium oxide alundum tube), "convex" shaped connecting tube 5, collet 6, connection
The small end of pipe 5 is adapted with crucible 4, big end is adapted with pumping rod 11, and the side wall of heating and thermal insulation furnace 1 is respectively communicated with its inner cavity
Equipped with Ar tracheae 7 and vacuum tube 8, Ar tracheae 7 is connected with Ar gas tank, and vacuum tube 8 is connected with molecular pump, mechanical pump in turn, heating
The bottom of holding furnace 1 is sealedly connected with crystallizer 9 with it, and Ga-In-Sn aluminium alloy 10,9 top of crystallizer are filled in crystallizer 9
Among 1 inner cavity of heating and thermal insulation furnace, remainder be then located at outside heating and thermal insulation furnace 1, collet 6 is located on crystallizer 9,
Graphite cannula 3 is located on collet 6, and induction coil 2 is around 3 surrounding of graphite cannula is located at, and induction coil 2 and setting are in heating and thermal insulation
Induction power supply except furnace 1 is connected, and crucible 4 is located among graphite cannula 3, the small end that crucible 4 and pumping rod 11 pass through connecting tube 5
Be plugged in 4 lower end of crucible, big end cap pumping rod 11 upper end realize connection, pumping rod 11 from top to bottom successively sealing through every
Hot jacket 6, crystallizer 9,11 bottom of pumping rod are connected with drawing device；
Preparation step is as follows:
(1), high-purity (99.99%) Al and Zn metal is weighed by 60: 40 mass ratio, is melted by high-frequency induction heating and matches, cuts
It is cut into cylinder Al-40%Zn alloy sample 12 compatible with 4 shape of crucible；
(2), sand paper polishing, acetone cleaning sample 12, to remove the oxide layer and impurity on surface；Sample 12 is put into crucible
In 4, top flat of the pumping rod 11 up to the bottom of the small end of connecting tube 5 just with collet 6 is moved down by drawing device
Together, big end then stretches out collet 6 and immerses the (mass percentage composition: Ga 10%, In of the Ga-In-Sn aluminium alloy in crystallizer 9
45%, Sn 45%) in 10；
(3), it is vacuumized respectively using mechanical pump and molecular pump, until the vacuum degree of heating and thermal insulation furnace 1 is to 7 × 10-3Pa,
Then it is filled with Ar gas into heating and thermal insulation furnace 1 and forms protective gas environment, fills the vacuum degree after Ar gas in heating and thermal insulation furnace 1 and keeps
In 400 Pa；
(4), induction power supply is opened, is heated by induction coil 2, is heated to above 80 DEG C of 12 fusing point of sample, is now in
The sample 12 of 2 effective heating area of induction coil melts, and the sample 12 except 2 effective heating area of induction coil is not sent out
Raw fusing, keeps the temperature 30min, keeps melt temperature uniform, stable；
(5), the drawing velocity for adjusting pumping rod 11 is 1000 μm/s, starts pull and is oriented solidification experiments, by melt
It is drawn in Ga-In-Sn aluminium alloy 10 from top to bottom and realizes directional solidification；
(6), after melt directional solidification, then adjusting the drawing velocity of pumping rod 11 is 100mm/s, and entire sample 12 is complete
It draws in Ga-In-Sn aluminium alloy 10 and is quenched entirely, simultaneously close off heating and thermal insulation furnace 1, open fire door, in holding furnace 1 to be heated
Furnace temperature naturally cool to room temperature after, pumping rod 11 is moved up by drawing device, by the ejection Ga- completely of entire sample 12
In-Sn aluminium alloy 10 takes out to get the twin dendrite of Al-40%Zn alloy.
Fig. 2 is the longitudinal section analysis of the twin dendrite of Al-40%Zn alloy :(a) micro-organization chart；It (b) is solid line square in (a)
Shape frame region enlarged drawing；(c) the EBSD pole figure tested for dashed rectangle frame region in (b).Fig. 2 (a) is it can be seen that in sample
Portion forms flourishing Feather-like Crystal tissue, and twin dendritic growth consistency is obvious.In Fig. 2 (b), a dendrite of twin dendrite
Do now apparent symmetrical interface, as shown by the solid line, dendrite two sides about this Twin Interface symmetric growth, secondary dendrite with it is twin
About 60 ° of angles are presented in interface.In addition, dendrite has apparent crystal boundary in Fig. 2 (b).It is analyzed by further EBSD, such as Fig. 2
(c) shown in, it may be determined that gained arborescent structure is twin dendrite, and twin plane is (111) face, the dry main shaft of dendrite of dendrite and secondary
The dendritic arm direction of growth is<110>direction, the increase meeting of this and Zn constituent content in Gonzales and Rappaz discovery aluminium alloy
Change the anisotropy of solid liquid interface energy, so that the direction of growth of conventional dendrite becomes<110>from<100>, is conducive to<110>side
To the formation of twin dendrite, this conclusion is consistent.
Reference examples 1
The difference from embodiment 1 is that: inverted trapezoidal graphite cannula is saved in device for directionally solidifying, and in preparation step (5),
The drawing velocity for adjusting pumping rod 11 is 800 μm/s, other with embodiment 1.
The longitudinal section analysis of product made from the reference examples is as shown in Figure 3 :(a) micro-organization chart；It (b) is dotted line in (a)
The EBSD pole figure that rectangle frame region is tested.Fig. 3 (a) is it can be seen that sample inside and not formed Feather-like Crystal tissue, Al-40%
Zn alloy microstructure is conventional plain cylindrical crystalline substance tissue, and dendrite is dry and a dendrite does not have the feature of the twin dendrite of featheriness.
And it, cannot due to there is no the drawing velocity (lower than the drawing velocity in the present invention) using inverted trapezoidal graphite cannula and 800 μm/s
Generate strong convection environment inside melt, column crystal each along solidification direction of heat flow perpendicular to quenching interface growth, without Fig. 2
The twin dendrite of middle lateral growth occurs, and the secondary dendrite of plain cylindrical crystalline substance and dendrite are done and 60 ° of angles is not presented, such as Fig. 3 (a)
It is shown.It is analyzed by further EBSD, as shown in Fig. 3 (b), it may be determined that gained arborescent structure is common dendrite, not twin
Interface occurs, and it is not<110>direction that the dry main shaft direction of growth of dendrite of dendrite, which is<100>direction,.It can illustrate institute in Fig. 3
It is shown as conventional common dendrite, is not twin dendrite.
Reference examples 2
The difference from embodiment 1 is that: inverted trapezoidal graphite cannula is saved in device for directionally solidifying, and in preparation step (5),
The drawing velocity for adjusting pumping rod 11 is 1500 μm/s, other with embodiment 1.
The longitudinal section analysis of product made from the reference examples is as shown in Figure 4 :(a) micro-organization chart；It (b) is solid line in (a)
Rectangle frame regional enlarged drawing；(c) the EBSD pole figure tested for dashed rectangle frame region in (b).In this reference examples experimentation
It does not use inverted trapezoidal graphite cannula, and uses the pull degree of hastening of 1500 μm/s (higher than the drawing velocity in the present invention).Fig. 4
(a) it can be seen that sample interior tissue is Al-Zn alloy routine plain cylindrical crystalline substance tissue, dendrite is dry and a dendrite does not have plumage
The shape characteristic of hairy twin dendrite, column crystal each along solidification direction of heat flow perpendicular to quenching interface growth, the two of column crystal
Secondary dendrite and the dry angle of dendrite are not 60 °, as shown in Figure 4 (b).EBSD analysis the result shows that: the dry main shaft of dendrite of dendrite is raw
Length direction is<100>direction, is not<110>direction, is occurred without Twin Interface, as shown in Fig. 4 (c), it may be determined that this reference examples
Resulting arborescent structure is common dendrite.
From it was found from embodiment 1 and reference examples 1-2: only using drawing velocity and preparation method in the present invention that could make
The standby twin dendrite of Al-40%Zn alloy out.Described herein to be: inventor is finally determined of the invention by creative work
Technical solution, the present invention also only enumerate the representational reference examples of two of them and are explained, but are not exhaustions.
Claims (3)
1. a kind of preparation method of the twin dendrite of Al-40%Zn alloy, it is characterised in that: the preparation method uses a directional solidification
Device, the device for directionally solidifying include pumping rod, heating and thermal insulation furnace and induction coil, inverted trapezoidal graphite among its inner cavity
Set, cylindrical crucible, "convex" shaped connecting tube, collet, the small end of connecting tube is adapted with crucible, big end and pumping rod are mutually fitted
Match, the side wall of heating and thermal insulation furnace is respectively equipped with Ar tracheae and vacuum tube and is connected to the inner cavity of heating and thermal insulation furnace, and Ar tracheae is connected with
Ar gas tank, vacuum tube are connected with molecular pump, mechanical pump in turn, and the bottom of heating and thermal insulation furnace is sealedly connected with crystallizer with it, knot
Ga-In-Sn aluminium alloy is filled in brilliant device, crystallizer top is located among heating and thermal insulation furnace chamber, remainder is then located at heating
Outside holding furnace, collet is located on crystallizer, and graphite cannula is located on collet, and induction coil surrounds and is located at graphite cannula four
Week, induction coil are connected with the induction power supply being arranged in except heating and thermal insulation furnace, and crucible is located among graphite cannula, crucible and pumping
Pull rod by the small end of connecting tube be plugged in the lower end of the crucible, big end cap pumping rod upper end realize connection, pumping rod from up to
Under successively sealing run through collet, crystallizer, pumping rod bottom is connected with drawing device；
Preparation step is as follows:
(1), cylinder Al-40%Zn alloy sample compatible with crucible shape is prepared；
(2), sand paper polishing, acetone cleaning sample；Sample is put into crucible, by drawing device move down pumping rod until
The bottom of the small end of connecting tube is just concordant with the top of collet, big end then stretches out collet and immerses the Ga- in crystallizer
In In-Sn aluminium alloy；
(3), it is vacuumized respectively using mechanical pump and molecular pump, until the vacuum degree of heating and thermal insulation furnace is to 7 × 10-3Pa or more, so
It is filled with Ar gas in backward heating and thermal insulation furnace, the vacuum degree after Ar gas in heating and thermal insulation furnace is filled and is maintained at 350 ~ 400 Pa；
(4), induction power supply is opened, is heated by induction coil, is heated to above 80 ~ 150 DEG C of sample fusing point, is now in sense
The sample of coil effective heating area is answered to melt, and the sample except induction coil effective heating area does not melt,
Heat preservation keeps melt temperature uniform, stable；
(5), the drawing velocity for adjusting pumping rod is 900 ~ 1100 μm/s, and melt is drawn in Ga-In-Sn aluminium alloy from top to bottom
Middle realization directional solidification；
(6), after melt directional solidification, then adjusting the drawing velocity of pumping rod is 90 ~ 110 mm/s, and entire sample is drawn completely
Into being quenched in Ga-In-Sn aluminium alloy, simultaneously closes off heating and thermal insulation furnace, opens fire door, the furnace temperature in holding furnace to be heated is certainly
After being so cooled to room temperature, pumping rod is moved up by drawing device, entire sample is ejected into Ga-In-Sn aluminium alloy completely, is taken
Out to get the twin dendrite of Al-40%Zn alloy.
2. preparation method as described in claim 1, it is characterised in that: in step (5), the drawing velocity for adjusting pumping rod is
1000 μm/s。
3. preparation method as claimed in claim 1 or 2, it is characterised in that: the crucible is high purity aluminium oxide alundum tube.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710281993.8A CN107052282B (en) | 2017-04-26 | 2017-04-26 | A kind of preparation method of the twin dendrite of Al-40%Zn alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710281993.8A CN107052282B (en) | 2017-04-26 | 2017-04-26 | A kind of preparation method of the twin dendrite of Al-40%Zn alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107052282A CN107052282A (en) | 2017-08-18 |
| CN107052282B true CN107052282B (en) | 2018-12-04 |
Family
ID=59604699
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201710281993.8A Expired - Fee Related CN107052282B (en) | 2017-04-26 | 2017-04-26 | A kind of preparation method of the twin dendrite of Al-40%Zn alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN107052282B (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN111570515A (en) * | 2020-05-20 | 2020-08-25 | 中国科学院上海应用物理研究所 | Metal composite plate rolling process optimization method and design method |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3485289A (en) * | 1966-02-01 | 1969-12-23 | Mitsubishi Chem Ind | Method for the manufacture of aluminum or aluminum alloy castings |
| RU2040362C1 (en) * | 1992-01-09 | 1995-07-25 | Рыбинский Авиационный Технологический Институт | Method of guided cast hardening |
| CN1184036C (en) * | 2002-02-28 | 2005-01-12 | 李碚 | Prepn process of TbDyFe-base directionally solidified alloy crystal |
| CN101875106B (en) * | 2009-11-20 | 2011-12-28 | 北京科技大学 | Preparation method of directional solidification high-niobium TiAl-base alloy |
| CN102206785B (en) * | 2011-04-23 | 2012-10-03 | 中国科学院合肥物质科学研究院 | Twinning induced plasticity alloy steel with columnar crystal structure and preparation method thereof |
-
2017
- 2017-04-26 CN CN201710281993.8A patent/CN107052282B/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| CN107052282A (en) | 2017-08-18 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102011195B (en) | Preparation method of directional solidification high-Nb TiAl alloy single crystal | |
| CN104278173B (en) | A kind of high-strength high-ductility TiAl alloy material and preparation method thereof | |
| CN102618766B (en) | Preparation method of quasi-crystal enhanced high-strength magnesium-zinc-yttrium (Mg-Zn-Y) alloy | |
| CN104328501B (en) | Fully controllable TiAl single crystal alloys of a kind of lamellar orientation and preparation method thereof | |
| CN110218897A (en) | A kind of preparation method of aeroengine combustor buring chamber liner high temperature resistant Cu-Cr-Nb-Ce alloy | |
| CN103382536A (en) | Fourth-generation single-crystal high temperature alloy with high strength and stable structure and preparation method thereof | |
| WO2016055013A1 (en) | Tial intermetallic compound single crystal material and preparation method therefor | |
| CN104947194A (en) | Magnetostrictive material and preparation method thereof | |
| CN104878452A (en) | High-temperature high-strength TiAl-Nb monocrystal and preparation method thereof | |
| CN104451314B (en) | A kind of high-strength temperature-resistant cast magnesium alloy and preparation method | |
| CN102672150A (en) | Direct control method for titanium-aluminum-niobium alloy lamellar structure | |
| CN107052282B (en) | A kind of preparation method of the twin dendrite of Al-40%Zn alloy | |
| Zheng et al. | The interdendritic-melt solidification control (IMSC) and its effects on the porosity and phase change of a Ni-based superalloy | |
| CN108555297B (en) | Method for eliminating primary β grain boundary of TC4 alloy by adding B induction heating during laser additive manufacturing | |
| CN104233029B (en) | A kind of high-strength degradable magnesium alloy and preparation method | |
| CN104388714A (en) | Smelting preparation method of large-sized titanium-aluminum intermetallic ingot | |
| CN114247857A (en) | Magnesium and magnesium alloy casting device and method based on melt controlled-speed drop casting | |
| CN106480351B (en) | A kind of method for preparing the excellent nickel Al-Cr-Mo eutectic alloy of thermal structure stability | |
| CN204491024U (en) | A kind of device controlling superalloy oriented freezing organization | |
| CN101476095B (en) | Heat working technological process for high strength deformed magnesium alloy | |
| CN103060660B (en) | Method for preparing Fe-Ga-In-Tb alloy by double-feeding vacuum induction smelting | |
| CN108998703B (en) | Self-inoculating rod, preparation method thereof and preparation method of hypoeutectic aluminum-silicon alloy semi-solid slurry | |
| CN102888649B (en) | Method for preparing Si-TaSi2 eutectic in-situ composite material | |
| CN109943760A (en) | High-strength high-plastic magnesium-rare earth of one kind and preparation method thereof | |
| CN107354331B (en) | The method for controlling TiAl-base alloy oriented freezing organization lamellar orientation as substrate seed crystal using refractory metal |
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 | ||
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20181204 Termination date: 20190426 |