CN107052282A - A kind of preparation method of the twin dendrite of Al 40%Zn alloys - Google Patents
A kind of preparation method of the twin dendrite of Al 40%Zn alloys Download PDFInfo
- Publication number
- CN107052282A CN107052282A CN201710281993.8A CN201710281993A CN107052282A CN 107052282 A CN107052282 A CN 107052282A CN 201710281993 A CN201710281993 A CN 201710281993A CN 107052282 A CN107052282 A CN 107052282A
- Authority
- CN
- China
- Prior art keywords
- dendrite
- heating
- pumping rod
- thermal insulation
- alloys
- 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.)
- Granted
Links
- 210000001787 dendrite Anatomy 0.000 title claims abstract description 70
- 229910001297 Zn alloy Inorganic materials 0.000 title claims abstract description 25
- 238000002360 preparation method Methods 0.000 title claims abstract description 25
- 238000007711 solidification Methods 0.000 claims abstract description 18
- 230000008023 solidification Effects 0.000 claims abstract description 18
- 238000010438 heat treatment Methods 0.000 claims description 38
- 238000005086 pumping Methods 0.000 claims description 35
- 238000009413 insulation Methods 0.000 claims description 31
- 230000006698 induction Effects 0.000 claims description 23
- 229910000838 Al alloy Inorganic materials 0.000 claims description 18
- 229910002804 graphite Inorganic materials 0.000 claims description 15
- 239000010439 graphite Substances 0.000 claims description 15
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 14
- PNEYBMLMFCGWSK-UHFFFAOYSA-N Alumina Chemical compound [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 8
- 241000486406 Trachea Species 0.000 claims description 7
- 210000003437 trachea Anatomy 0.000 claims description 7
- 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
- 229910045601 alloy Inorganic materials 0.000 abstract description 16
- 239000000956 alloy Substances 0.000 abstract description 16
- 238000000034 method Methods 0.000 abstract description 10
- 238000011160 research Methods 0.000 abstract description 8
- 229910052725 zinc Inorganic materials 0.000 abstract description 5
- 238000005516 engineering process Methods 0.000 abstract description 4
- 238000013461 design Methods 0.000 abstract description 2
- 239000007769 metal material Substances 0.000 abstract description 2
- 239000000203 mixture Substances 0.000 abstract description 2
- 229910018137 Al-Zn Inorganic materials 0.000 description 11
- 229910018573 Al—Zn Inorganic materials 0.000 description 11
- 239000013078 crystal Substances 0.000 description 10
- 238000001887 electron backscatter diffraction Methods 0.000 description 9
- 238000004458 analytical method Methods 0.000 description 7
- 230000015572 biosynthetic process Effects 0.000 description 5
- 239000000126 substance Substances 0.000 description 4
- 238000005266 casting Methods 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 230000015271 coagulation Effects 0.000 description 2
- 238000005345 coagulation Methods 0.000 description 2
- 229910052593 corundum Inorganic materials 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
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- TWNQGVIAIRXVLR-UHFFFAOYSA-N oxo(oxoalumanyloxy)alumane Chemical compound O=[Al]O[Al]=O TWNQGVIAIRXVLR-UHFFFAOYSA-N 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
- 239000004575 stone Substances 0.000 description 2
- 229910001845 yogo sapphire Inorganic materials 0.000 description 2
- 241001631457 Cannula Species 0.000 description 1
- 229910001128 Sn alloy Inorganic materials 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910052571 earthenware Inorganic materials 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
- 239000000155 melt 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
- 239000011435 rock 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 field of metal material, and in particular to a kind of preparation method of the twin dendrite of Al 40%Zn alloys.The preparation method selects high Zn content Al Zn alloys（40%Zn）Composition design, using directional solidification technique, choose high directional solidification withdrawing rate（900~1100μm/s）, using the convection current formed in directional solidification process in melt, it is successfully prepared the twin dendrite of Al 40%Zn alloys.The present invention chooses Al 40%Zn alloys as the alloy system for preparing twin dendrite, different from low content Zn in research report（Below 30%Zn）Al Zn alloy systems, this is not reported into component selections, overcomes technology prejudice.
Description
Technical field
The invention belongs to the preparation field of metal material, and in particular to a kind of preparation side of the twin dendrite of Al-40%Zn alloys
Method.
Background technology
Twin dendrite, also known as Feather-like Crystal（Feathery grains）, also referred to as twin crystal, twin, basaltiform be brilliant
Deng belonging to one kind of twin（Growth 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, is referred to as the 3rd class dendrite in casting.It is twin why it is referred to as featheriness
Dendrite, is due to that this kind of dendrite its pattern in two-dimentional microstructure is similar to feather.Research shows that twin dendrite is certain
Under the conditions of a kind of obtained cast sturcture, the speed of its maximum growth axially carries out, has with axially in parallel twin dendrite
There is most strong competitiveness, so the dendrite in other directions is easy to be suppressed.Thus, its direction of growth substantially with it is axially in parallel,
With strong anisotropy, and it is not susceptible to deform in pressing process and crushes, so its microcosmic group to alloy
Knit and play a part of optimization with mechanical property.Zhou Yao and et al. it is brilliant to single Shu Yuzhuan brilliant with 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 network structure that multi beam pinniform crystalline substance is formed when intersecting strengthens the continuity of sample in the stretching direction so that mechanical property
Significantly improve.Therefore large area twin dendrite being obtained in alloy casting process and turning into improves the key of alloy property, to it
Research has important value in solidification theory research and commercial Application.
And found in the research of the Forming Mechanism in twin dendrite, because twin dendrite is the temperature in crystallization front liquid
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 produce.Based on this, the thermograde for thinking high and strong convection are generally studied at present, are that twin dendrite is produced
Necessary condition.Because Al has weak anisotropy such as in Al-Zn alloys, coarse boundary is easily formed during conventional coagulation
Face, in the absence of strong growth competitiveness, is unfavorable for the formation of twin dendrite, but is found by studying, under certain specific condition,
As in high-temperature gradient and strong convection environment, certain twin dendrite can also be formed.Directional solidification technique is as special
There is higher thermograde, cooldown rate and convection environment in nonequilibrium freezing technology, its process of setting, be Al-Zn alloys
The formation of twin dendrite provides preparation condition.However, current study show that in Al-Zn alloys when Zn contents reach 40%, it is twin
Raw dendrite is not re-formed, and this turns into the bottleneck of the twin dendrite preparation process of Al-Zn alloys.Accordingly, it is capable to no in high Zn content Al-Zn
Twin dendrite is prepared in alloy turns into research emphasis prepared by material.
The content of the invention
It is an object of the invention to provide a kind of preparation method of the twin dendrite of Al-40%Zn alloys.
To achieve the above object, the technical scheme that the present invention takes is as follows：
A kind of preparation method of the twin dendrite of Al-40%Zn alloys, the preparation method uses a device for directionally solidifying, and the orientation is coagulated
It is fixedly mounted with induction coil, inverted trapezoidal graphite cannula, the cylindrical earthenware put including pumping rod, heating and thermal insulation stove and among its inner chamber
Crucible, "convex" shaped connecting tube, collet, the small end of connecting tube is adapted with crucible, end greatly is adapted with pumping rod, heating and thermal insulation
The side wall of stove is respectively communicated with provided with Ar tracheaes and vacuum tube with its inner chamber, and Ar tracheaes are connected with Ar gas tanks, and vacuum tube is sequentially connected
There are molecular pump, mechanical pump, the bottom of heating and thermal insulation stove, which is sealed against, is connected with crystallizer, and Ga-In-Sn alloys are filled with crystallizer
Liquid, crystallizer top is among heating and thermal insulation furnace chamber, remainder is then located at outside heating and thermal insulation stove, and collet is located at knot
On brilliant device, graphite cannula is located on collet, and induction coil is around graphite cannula surrounding is located at, and induction coil is with being arranged on heating
Induction power supply outside holding furnace is connected, and crucible is located among graphite cannula, and crucible and pumping rod are inserted by the small end of connecting tube
The upper end realization connection that crucible lower end, big end are enclosed on pumping rod is located at, pumping rod is sealed through collet, knot successively from top to bottom
Brilliant device, pumping rod bottom is connected with drawing device；
Preparation process is as follows：
（1）, prepare the cylindrical Al-40%Zn alloy samples that are adapted with crucible shape；
（2）, sand paper polishing, acetone cleaning sample, to remove the oxide layer and impurity on surface；Sample is put into crucible, passed through
Drawing device moves down pumping rod until the bottom of the small end of connecting tube is just concordant with the top of collet, hold then stretch out greatly
Collet is simultaneously immersed in the Ga-In-Sn aluminium alloys in crystallizer；
（3）, respectively vacuumized using mechanical pump and molecular pump, until the vacuum of heating and thermal insulation stove is to 7 × 10-3 More than Pa, so
Ar gas formation protective gas environment is filled with backward heating and thermal insulation stove, the vacuum after Ar gas in heating and thermal insulation stove is filled and is maintained at
350~400 Pa；
（4）, open induction power supply, heated by induction coil, be heated to above 80 ~ 150 DEG C of sample fusing point, be now in sense
The sample of coil effective heating area is answered to melt, and the sample outside induction coil effective heating area does not melt,
Insulation（30 ~60min）, make melt temperature uniformly, stably；
（5）, adjustment pumping rod drawing velocity be 900 ~ 1100 μm/s, start pull be oriented solidification experiments, by melt from
Drawn under above in Ga-In-Sn aluminium alloys and realize directional solidification；
（6）, after after melt directional solidification, then it is 90 ~ 110 mm/s to adjust the drawing velocity of pumping rod, and whole sample is drawn completely
Enter and quenched in Ga-In-Sn aluminium alloys, simultaneously close off heating and thermal insulation stove, open fire door, the furnace temperature in holding furnace to be heated from
So it is cooled to after room temperature, pumping rod is moved up by drawing device, whole sample is ejected into Ga-In-Sn aluminium alloys completely, taken
Go out, produce the twin dendrite of Al-40%Zn alloys.
Preferably, the drawing velocity of adjustment pumping rod is preferably 1000 μm/s
Preferably, the crucible is preferably high-purity（99.9%Al2O3）Aluminum oxide alundum tube.
Beneficial effect：
1st, the present invention chooses Al-40%Zn alloys as the alloy system for preparing twin dendrite, different from low content Zn in research report
（Below 30%Zn）Al-Zn alloy systems, this is not reported into component selections.And existing research before making the present invention（Yang Lu
Progress [J] the Rare Metals Materials and engineering of twin dendrite in rock, Li Shuanming, Gao Ka, Zhong Hong, Fu Heng will aluminium alloys,
2015, 44(07): 001809-1814）Think that Al-Zn alloys can not possibly prepare twin dendrite when Zn contents are more than 40%
Alloying component, therefore instant invention overcomes technology prejudice；
2nd, high Zn content Al-Zn alloys are selected in the present invention（40%Zn）Composition design, employ directional solidification technique, choose
High directional solidification withdrawing rate（900~1100μm/s）, using the convection current formed in directional solidification process in melt, successfully make
For the twin dendrite of high Zn content Al-Zn alloys, the extensive preparation for the twin dendrite of Al-Zn alloys provides test basis.In addition,
By twin dendrite made from the inventive method, Hirschfeld-Klinger reaction only occurs for organization internal, and precipitated phase is simple, and whole operation process
Simply, experimental expenses is relatively low.
Brief description of the drawings
Fig. 1：Oriented coagulation forming device：1- heating and thermal insulation stoves, 2- induction coils, 3- graphite cannulas, 4- crucibles, 5- connections
Pipe, 6- collets, 7-Ar tracheaes, 8- vacuum tubes, 9- crystallizers, 10-Ga-In-Sn aluminium alloys, 11- pumping rods, 12- samples.
Fig. 2：The longitudinal section analysis of the twin dendrite of Al-40%Zn alloys made from embodiment 1：（a）Micro-organization chart；（b）For
（a）Middle solid-line rectangle frame regional enlarged drawing；（c）For（b）The EBSD pole figures that middle dotted rectangle region is tested.
Fig. 3：The brilliant longitudinal section analysis of Al-40%Zn alloys plain cylindrical made from reference examples 1：（a）Micro-organization chart；（b）
For（a）The EBSD pole figures that middle dotted rectangle region is tested.
Fig. 4：The brilliant longitudinal section analysis of Al-40%Zn alloys plain cylindrical made from reference examples 2：（a）Micro-organization chart；（b）
For（a）Middle solid-line rectangle frame regional enlarged drawing；（c）For（b）The EBSD pole figures that middle dotted rectangle region is tested.
Embodiment
With reference to specific embodiment, the present invention is further elaborated, and used raw material is in following examples
This area general chemical.
Embodiment 1
A kind of preparation method of the twin dendrite of Al-40%Zn alloys, the preparation method uses a device for directionally solidifying, such as Fig. 1 institutes
Show, the device for directionally solidifying includes pumping rod 11, heating and thermal insulation stove 1 and induction coil 2, inverted trapezoidal stone among its inner chamber
Ink set 3, cylindrical crucible 4（It is high-purity（99.9%Al2O3）Aluminum oxide alundum tube）, "convex" shaped connecting tube 5, collet 6, connecting tube
5 small end is adapted with crucible 4, end greatly is adapted with pumping rod 11, and the side wall of heating and thermal insulation stove 1 is respectively communicated with its inner chamber to be set
There are Ar tracheaes 7 and vacuum tube 8, Ar tracheaes 7 are connected with Ar gas tanks, and vacuum tube 8 is connected with molecular pump, mechanical pump in turn, and heating is protected
The bottom of warm stove 1, which is sealed against, is connected with crystallizer 9, and Ga-In-Sn aluminium alloys 10, the upper bit of crystallizer 9 are filled with crystallizer 9
Among the inner chamber of heating and thermal insulation stove 1, remainder then be located at heating and thermal insulation stove 1 outside, collet 6 be located at crystallizer 9 on, stone
Ink set 3 is located on collet 6, and induction coil 2 is around the surrounding of graphite cannula 3 is located at, and induction coil 2 is with being arranged on heating and thermal insulation stove
Induction power supply outside 1 is connected, and crucible 4 is located among graphite cannula 3, and crucible 4 and pumping rod 11 are inserted by the small end of connecting tube 5
The upper end realization connection that the lower end of crucible 4, big end are enclosed on pumping rod 11 is located at, pumping rod 11 is sealed through heat-insulated successively from top to bottom
Set 6, crystallizer 9, the bottom of pumping rod 11 is connected with drawing device；
Preparation process is as follows：
（1）, by 60: 40 mass ratio weigh high-purity (99.99%) Al and Zn metals, match somebody with somebody, cut into by the way that high-frequency induction heating is molten
The cylindrical Al-40%Zn alloy samples 12 being adapted with the shape of crucible 4；
（2）, sand paper polishing, acetone cleaning sample 12, to remove the oxide layer and impurity on surface；Sample 12 is put into crucible 4,
Pumping rod 11 is moved down by drawing device until the bottom of the small end of connecting tube 5 is just concordant with the top of collet 6, big
Collet 6 and the Ga-In-Sn aluminium alloys immersed in crystallizer 9 are then stretched out in end（Mass percent is constituted：Ga 10%、In 45%、
Sn 45%）In 10；
（3）, respectively vacuumized using mechanical pump and molecular pump, until the vacuum of heating and thermal insulation stove 1 is to 7 × 10-3 Pa, then
Ar gas formation protective gas environment is filled with into heating and thermal insulation stove 1, the vacuum after Ar gas in heating and thermal insulation stove 1 is filled and is maintained at
400 Pa；
（4）, open induction power supply, heated by induction coil 2, be heated to above 80 DEG C of 12 fusing point of sample, be now in sensing
The sample 12 of the effective heating area of coil 2 melts, and the sample 12 outside the effective heating area of induction coil 2 does not melt
Change, be incubated 30min, make melt temperature uniformly, stably；
（5）, adjustment pumping rod 11 drawing velocity be 1000 μm/s, start pull and be oriented solidification experiments, by melt from upper
And under draw in Ga-In-Sn aluminium alloys 10 and realize directional solidification；
（6）, after after melt directional solidification, then it is 100mm/s to adjust the drawing velocity of pumping rod 11, and whole sample 12 is drawn completely
Enter and quenched in Ga-In-Sn aluminium alloys 10, simultaneously close off heating and thermal insulation stove 1, the stove opened in fire door, holding furnace 1 to be heated
Temperature is naturally cooled to after room temperature, and pumping rod 11 is moved up by drawing device, by whole sample 12 ejection Ga-In-Sn completely
Aluminium alloy 10, takes out, produces the twin dendrite of Al-40%Zn alloys.
Fig. 2 is the longitudinal section analysis of the twin dendrite of Al-40%Zn alloys：（a）Micro-organization chart；（b）For（a）Middle solid line square
Shape frame regional enlarged drawing；（c）For（b）The EBSD pole figures that middle dotted rectangle region is tested.Fig. 2（a）It can be seen that：In sample
Portion forms the Feather-like Crystal tissue of prosperity, and twin dendritic growth uniformity is obvious.In Fig. 2 (b), a dendrite of twin dendrite
Do now obvious symmetrical interface, as shown by the solid line, dendrite both sides on this Twin Interface symmetric growth, secondary dendrite with it is twin
About 60 ° of angles are presented in interface.In addition, dendrite has obvious crystal boundary in Fig. 2 (b).Analyzed by further EBSD, such as Fig. 2
(c) shown in, it may be determined that gained arborescent structure is twin dendrite, twin plane is（111）Face, dry main shaft of dendrite of dendrite and secondary
The dendritic arm direction of growth is<110>Direction, this finds the increase meeting of Zn constituent contents in aluminium alloy with Gonzales and Rappaz
Change solid liquid interface can anisotropy so that the direction of growth of conventional dendrite by<100>It is changed into<110>, be conducive to<110>Side
To the formation of twin dendrite, this conclusion is consistent.
Reference examples 1
Difference with embodiment 1 is：Inverted trapezoidal graphite cannula, and preparation process are saved in device for directionally solidifying（5）In, adjustment
The drawing velocity of pumping rod 11 is 800 μm/s, other equal be the same as Examples 1.
The longitudinal section analysis of product made from the reference examples is as shown in Figure 3：（a）Micro-organization chart；（b）For（a）Middle dotted line
The EBSD pole figures that rectangle frame region is tested.Fig. 3（a）It can be seen that：Feather-like Crystal tissue, Al-40% are not formed inside sample
Zn alloys 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 due to the drawing velocity without use inverted trapezoidal graphite cannula and 800 μm/s（Less than the drawing velocity in the present invention）, it is impossible to
Convection environment strong inside melt is produced, column crystal is each along direction of heat flow is solidified perpendicular to quenching interface growth, without Fig. 2
The twin dendrite of middle lateral growth occurs, and the brilliant secondary dendrite of plain cylindrical is done with dendrite and 60 ° of angles, such as Fig. 3 are not presented（a）
It is shown.Analyzed by further EBSD, shown in such as Fig. 3 (b), it may be determined that gained arborescent structure is common dendrite, not twin
Interface occurs, and the dry main shaft direction of growth of dendrite of dendrite is<100>Direction, be not<110>Direction.Institute in Fig. 3 can be illustrated
Conventional common dendrite is shown as, is not twin dendrite.
Reference examples 2
Difference with embodiment 1 is：Inverted trapezoidal graphite cannula, and preparation process are saved in device for directionally solidifying（5）In, adjustment
The drawing velocity of pumping rod 11 is 1500 μm/s, other equal be the same as Examples 1.
The longitudinal section analysis of product made from the reference examples is as shown in Figure 4：（a）Micro-organization chart；（b）For（a）Middle solid line
Rectangle frame regional enlarged drawing；（c）For（b）The EBSD pole figures that middle dotted rectangle region is tested.In this reference examples experimentation
Inverted trapezoidal graphite cannula is not used, and uses 1500 μm/s pull degree of hastening（Higher than the drawing velocity in the present invention）.Fig. 4
（a）It can be seen that：Sample interior tissue is the conventional plain cylindrical crystalline substance tissue of Al-Zn alloys, and dendrite is dry and a dendrite does not have plumage
The shape characteristic of the twin dendrite of hairy, column crystal is 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 °, such as Fig. 4（b）It is shown.EBSD analysis results show：The dry main shaft life of dendrite of dendrite
Length direction is<100>Direction, be not<110>Direction, occurs without Twin Interface, shown in such as Fig. 4 (c), it may be determined that this reference examples
The arborescent structure of gained is common dendrite.
It was found from embodiment 1 and reference examples 1-2：It could only be made using the drawing velocity and preparation scheme in the present invention
It is standby go out the twin dendrite of Al-40%Zn alloys.It is described herein to be：Inventor finally determines the present invention's by creative work
Technical scheme, the present invention also simply enumerates the representational reference examples of two of which and is explained, but is not exhaustive.
Claims (3)
1. a kind of preparation method of the twin dendrite of Al-40%Zn alloys, it is characterised in that：The preparation method uses a directional solidification
Device, the device for directionally solidifying includes pumping rod, heating and thermal insulation stove and induction coil, inverted trapezoidal graphite among its inner chamber
Set, cylindrical crucible, "convex" shaped connecting tube, collet, the small end of connecting tube are adapted with crucible, hold mutually fitted with pumping rod greatly
Match somebody with somebody, side wall and its inner chamber of heating and thermal insulation stove are respectively communicated with provided with Ar tracheaes and vacuum tube, and Ar tracheaes are connected with Ar gas tanks, vacuum
Pipe is connected with molecular pump, mechanical pump in turn, and the bottom of heating and thermal insulation stove, which is sealed against, is connected with crystallizer, is filled with crystallizer
Ga-In-Sn aluminium alloys, crystallizer top is among heating and thermal insulation furnace chamber, remainder is then located at outside heating and thermal insulation stove,
Collet is located on crystallizer, and graphite cannula is located on collet, and induction coil surrounds and is located at graphite cannula surrounding, induction coil
It is connected with the induction power supply being arranged on outside heating and thermal insulation stove, crucible is located among graphite cannula, crucible and pumping rod pass through even
The small end of adapter is plugged in the upper end realization connection that crucible lower end, big end are enclosed on pumping rod, and pumping rod is sealed successively from top to bottom
Through collet, crystallizer, pumping rod bottom is connected with drawing device；
Preparation process is as follows：
（1）, prepare the cylindrical Al-40%Zn alloy samples that are adapted with crucible shape；
（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, collet and the Ga- immersed in crystallizer are then stretched out in big end
In In-Sn aluminium alloys；
（3）, respectively vacuumized using mechanical pump and molecular pump, until the vacuum of heating and thermal insulation stove is to 7 × 10-3 More than Pa, so
Ar gas is filled with backward heating and thermal insulation stove, the vacuum after Ar gas in heating and thermal insulation stove is filled and is maintained at 350 ~ 400 Pa；
（4）, open induction power supply, heated by induction coil, be heated to above 80 ~ 150 DEG C of sample fusing point, be now in sense
The sample of coil effective heating area is answered to melt, and the sample outside induction coil effective heating area does not melt,
Insulation, makes melt temperature uniformly, stably；
（5）, adjustment pumping rod drawing velocity be 900 ~ 1100 μm/s, melt is drawn in Ga-In-Sn aluminium alloys from top to bottom
In realize directional solidification；
（6）, after after melt directional solidification, then it is 90 ~ 110 mm/s to adjust the drawing velocity of pumping rod, and whole sample is drawn completely
Enter and quenched in Ga-In-Sn aluminium alloys, simultaneously close off heating and thermal insulation stove, open fire door, the furnace temperature in holding furnace to be heated from
So it is cooled to after room temperature, pumping rod is moved up by drawing device, whole sample is ejected into Ga-In-Sn aluminium alloys completely, taken
Go out, produce the twin dendrite of Al-40%Zn alloys.
2. preparation method as claimed in claim 1, it is characterised in that：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 true CN107052282A (en) | 2017-08-18 |
| CN107052282B 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) |
Cited By (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 |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB1142098A (en) * | 1966-02-01 | 1969-02-05 | 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 |
| CN1440848A (en) * | 2002-02-28 | 2003-09-10 | 李碚 | Prepn process of TbDyFe-base directionally solidified alloy crystal |
| CN101875106A (en) * | 2009-11-20 | 2010-11-03 | 北京科技大学 | Preparation method of directional solidification high-niobium TiAl-base alloy |
| CN102206785A (en) * | 2011-04-23 | 2011-10-05 | 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
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB1142098A (en) * | 1966-02-01 | 1969-02-05 | 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 |
| CN1440848A (en) * | 2002-02-28 | 2003-09-10 | 李碚 | Prepn process of TbDyFe-base directionally solidified alloy crystal |
| CN101875106A (en) * | 2009-11-20 | 2010-11-03 | 北京科技大学 | Preparation method of directional solidification high-niobium TiAl-base alloy |
| CN102206785A (en) * | 2011-04-23 | 2011-10-05 | 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 |
Non-Patent Citations (3)
| Title |
|---|
| 冯坚等: "Al-0.53Zn合金近快速定向凝固条件下的胞晶间距选择", 《金属学报》 * |
| 杨鲁岩等: "铝合金中孪生枝晶的研究进展", 《稀有金属材料与工程》 * |
| 马颖等: "Zn-Al合金热型连铸定向凝固的晶体生长机理", 《金属学报》 * |
Cited By (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 |
Also Published As
| Publication number | Publication date |
|---|---|
| CN107052282B (en) | 2018-12-04 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5344919B2 (en) | Apparatus and method for crystal growth | |
| CN102927815B (en) | Suspension type cold crucible continuous melting and casting and directional solidification device | |
| CN102011195B (en) | Preparation method of directional solidification high-Nb TiAl alloy single crystal | |
| CN101875106A (en) | Preparation method of directional solidification high-niobium TiAl-base alloy | |
| CN104947194A (en) | Magnetostrictive material and preparation method thereof | |
| CN104278173B (en) | A kind of high-strength high-ductility TiAl alloy material and preparation method thereof | |
| CN109396400B (en) | Large complex thin-wall fine-grain casting integrated forming method and device | |
| CN104328501B (en) | Fully controllable TiAl single crystal alloys of a kind of lamellar orientation and preparation method thereof | |
| WO2016055013A1 (en) | Tial intermetallic compound single crystal material and preparation method therefor | |
| MA | DEVELOPMENT OF SINGLE CRYSTAL SOLIDIFICA-TION TECHNOLOGY FOR PRODUCTION OF SUPERALLOY TURBINE BLADES | |
| CN104878452A (en) | High-temperature high-strength TiAl-Nb monocrystal and preparation method thereof | |
| Ma et al. | Innovations in casting techniques for single crystal turbine blades of superalloys | |
| CN104353795A (en) | Continuous directional solidification technology adopting temperature gradient crystallizer | |
| CN106319621A (en) | Large-size czochralski silicon single crystal growth method | |
| CN111230078A (en) | Directional solidification method for metal material | |
| CN107052282A (en) | A kind of preparation method of the twin dendrite of Al 40%Zn alloys | |
| CN104562181A (en) | Device and method for controlling directionally solidified structures of high-temperature alloy | |
| Wang et al. | Effect of melt thermal history on solidification behavior and microstructural characteristics of a third-generation Ni-based single crystal superalloy | |
| CN114101613A (en) | Method and device for preparing homogeneous immiscible alloy continuous casting billet through high-intensity magnetic field composite melt overheating treatment | |
| CN102888649B (en) | Method for preparing Si-TaSi2 eutectic in-situ composite material | |
| CN204491024U (en) | A kind of device controlling superalloy oriented freezing organization | |
| CN114833326B (en) | Device and method for preparing eutectic superalloy directional solidification by magnetic control electric arc | |
| CN103949599B (en) | A kind of bar-like silicon cast mould and casting method thereof | |
| CN114703436B (en) | Alloying method for improving high-temperature performance of directional solidification titanium aluminum alloy and prepared titanium aluminum alloy | |
| CN107677126B (en) | Electromagnetic suspension water-cooled copper crucible |
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 |