CN116837236A - Method for improving plasticity of Ni-Mn-Ga alloy - Google Patents
Method for improving plasticity of Ni-Mn-Ga alloy Download PDFInfo
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- 238000000034 method Methods 0.000 title claims abstract description 40
- 229910000807 Ga alloy Inorganic materials 0.000 title claims abstract description 30
- 239000000956 alloy Substances 0.000 claims abstract description 86
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 84
- 238000007711 solidification Methods 0.000 claims abstract description 30
- 230000008023 solidification Effects 0.000 claims abstract description 30
- 239000013078 crystal Substances 0.000 claims abstract description 25
- 238000003723 Smelting Methods 0.000 claims abstract description 23
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 19
- 229910001339 C alloy Inorganic materials 0.000 claims abstract description 17
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 17
- 229910052733 gallium Inorganic materials 0.000 claims abstract description 17
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 14
- 238000005520 cutting process Methods 0.000 claims abstract description 6
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 5
- 238000002844 melting Methods 0.000 claims description 26
- 230000008018 melting Effects 0.000 claims description 26
- 238000005266 casting Methods 0.000 claims description 17
- 239000012535 impurity Substances 0.000 claims description 16
- 238000010438 heat treatment Methods 0.000 claims description 12
- 238000001035 drying Methods 0.000 claims description 7
- 230000006698 induction Effects 0.000 claims description 7
- 239000002184 metal Substances 0.000 claims description 7
- 229910052751 metal Inorganic materials 0.000 claims description 7
- KRHYYFGTRYWZRS-UHFFFAOYSA-N Fluorane Chemical compound F KRHYYFGTRYWZRS-UHFFFAOYSA-N 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 4
- 238000004321 preservation Methods 0.000 claims description 4
- 239000002994 raw material Substances 0.000 claims description 4
- 238000005303 weighing Methods 0.000 claims description 4
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 3
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 claims description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 3
- 238000004140 cleaning Methods 0.000 claims description 3
- 229910017604 nitric acid Inorganic materials 0.000 claims description 3
- 229910052760 oxygen Inorganic materials 0.000 claims description 3
- 239000001301 oxygen Substances 0.000 claims description 3
- 238000005498 polishing Methods 0.000 claims description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 241001062472 Stokellia anisodon Species 0.000 claims 1
- 238000010309 melting process Methods 0.000 claims 1
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 42
- 238000011084 recovery Methods 0.000 description 7
- 229910001285 shape-memory alloy Inorganic materials 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 230000003446 memory effect Effects 0.000 description 4
- 238000002360 preparation method Methods 0.000 description 4
- 238000010586 diagram Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 230000007547 defect Effects 0.000 description 2
- 230000005294 ferromagnetic effect Effects 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical compound [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 1
- 230000008878 coupling Effects 0.000 description 1
- 238000010168 coupling process Methods 0.000 description 1
- 238000005859 coupling reaction Methods 0.000 description 1
- 239000003814 drug Substances 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000003203 everyday effect Effects 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 description 1
- 239000010931 gold Substances 0.000 description 1
- 229910052737 gold Inorganic materials 0.000 description 1
- 238000003384 imaging method Methods 0.000 description 1
- 230000005291 magnetic effect Effects 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 230000001012 protector Effects 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 238000001228 spectrum Methods 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B11/00—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method
- C30B11/14—Single-crystal growth by normal freezing or freezing under temperature gradient, e.g. Bridgman-Stockbarger method characterised by the seed, e.g. its crystallographic orientation
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- Engineering & Computer Science (AREA)
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- Metallurgy (AREA)
- Organic Chemistry (AREA)
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- Crystallography & Structural Chemistry (AREA)
- Crystals, And After-Treatments Of Crystals (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention discloses a method for improving the plasticity of Ni-Mn-Ga alloy, and relates to the technical field of alloys. Smelting Ni and Ga to obtain Ni-Ga alloy; then adding Mn and carbon for smelting treatment to obtain a Ni-Mn-Ga-C alloy rod; finally cutting the Ni-Mn-Ga-C alloy rod and directionally solidifying by a seed crystal method to obtain the strong plasticity Ni-Mn-Ga-C alloy. The invention adopts the orientation to be austenite through carbon doping treatment<110> A The directional seed crystal is subjected to seed crystal directional solidification treatment, so that the Ni-Mn-Ga alloy strong plasticity is remarkably improved.
Description
Technical Field
The invention belongs to the technical field of alloys, and particularly relates to a method for improving the plasticity of Ni-Mn-Ga alloy.
Background
Shape memory alloy (shape memory alloy), i.e. an alloy with a "memory" effect, has a shape memory effect (shape memory effect) and is widely used in the fields of clinical medicine, vehicle engineering, aerospace, etc., such as artificial joints, endoscopes, satellite antennas, automatic dryers, steam drain valves, and overcurrent protectors. Shape memory alloys are also applicable to everyday life such as electronic cookers, eyeglass frames, and mobile phone antennas. Along with the appearance of shape memory alloy materials and the continuous development and utilization, the shape memory alloy materials are highly valued in an intelligent material system, and have wide application prospect.
The Ni-Mn-Ga shape memory alloy is used as a novel ferromagnetic memory alloy, is a novel intelligent material with thermoelastic martensitic transformation and ferromagnetic transformation, has the advantage of larger output strain (about 10%) of the traditional alloy, has higher magnetostriction response frequency (about KHz), and is a perfect fusion of a magnetic field driving mechanism and a shape memory effect. Thus making it widely used as a sensor-driving material.
The prior Ni-Mn-Ga alloy has the defects of large brittleness, low strength and the like, so that the application and development of the alloy are greatly limited, and the main direction of Ni-Mn-Ga alloy research is realized by how to improve the strength of the Ni-Mn-Ga alloy, reduce the brittleness of the Ni-Mn-Ga alloy and simultaneously maintain or even improve the heat recovery property of the alloy.
Disclosure of Invention
Aiming at the defects of the prior art, the invention provides a method for improving the plasticity of Ni-Mn-Ga alloy, which is realized according to the following technical scheme:
a method for improving the plasticity of a Ni-Mn-Ga alloy, comprising the steps of:
step 1, removing impurities from Ni, mn and Ga metal raw materials, and drying for later use;
step 2, according to Ni 54 Mn 26 Ga 20 Weighing Ni, mn and Ga according to the atomic ratio in the alloy, putting the weighed Ni and Ga into a crucible and putting into a smelting furnace, and then carrying out vacuum arc smelting to obtain a smelted Ni-Ga alloy;
step 3, adding weighed Mn into the Ni-Ga alloy, adding carbon blocks, smelting in an induction smelting furnace, and carrying out suction casting on the smelted alloy to obtain a Ni-Mn-Ga-C alloy rod, wherein the atomic ratio of carbon in the alloy rod is 0.1%;
step 4, cutting the Ni-Mn-Ga-C alloy rod, and then carrying out seed crystal method directional solidification treatment to obtain the strong plasticity Ni-Mn-Ga-C alloy, wherein the orientation of the seed crystal is austenite<110> A Direction.
Preferably, the impurity removing method of Ni and Ga in the step 1 is to remove oxide layers and impurities on the metal surface by using a mechanical polishing method;
the impurity removal method of Mn comprises the steps of firstly cleaning Mn by using a solution formed by nitric acid, hydrofluoric acid and water in a volume ratio of 20:5:75 so as to remove an oxide layer on the surface of Mn; then placing the mixture in absolute ethyl alcohol for ultrasonic impurity removal, and finally drying.
Preferably, in the vacuum arc melting in the step 2, the vacuumizing treatment is performed first so that the vacuum degree is-0.05 MPa, then the melting current is adjusted to 200A after arc striking, the melting is performed to remove residual oxygen, and then the current is adjusted to 270A-300A for repeated melting treatment.
Preferably, in the vacuum arc melting in the step 2, four times of melting treatment are performed under the current of 270A-300A, the melting time is 1min each time, and the turning-over treatment is required to be performed on the alloy ingot after the single melting is finished.
Preferably, in the step S3, alloy ingots which are repeatedly smelted in the induction smelting furnace until no carbon residues exist on the surfaces are subjected to suction casting treatment, wherein the arc current is 350A during the suction casting treatment, a suction casting switch is opened to perform suction casting by utilizing pressure difference after the alloy ingots are completely melted, and the alloy is sucked and cast into alloy rods with the diameter of 8 mm.
Preferably, step 4 is cutting the Ni-Mn-Ga-C alloy rod into an alloy rod having a diameter of 3 mm.
Preferably, step 4 is to physically bond the cut alloy rod with a seed crystal with the same diameter and length of 3-4mm, wherein the seed crystal is positioned at the bottom of the alloy rod, and then placing the alloy rod in a heating furnace for heating and melting treatment, wherein the heating temperature is not lower than 1450 ℃, and the heat preservation time is not lower than 30min; starting a directional solidification drawing device, carrying out directional solidification at the directional solidification growth rate of 10 mu m/s, and naturally cooling to room temperature after 120mm of directional solidification.
Compared with the prior art, the invention has the following beneficial effects:
smelting Ni and Ga to obtain Ni-Ga alloy; then adding Mn and carbon for smelting treatment to obtain a Ni-Mn-Ga-C alloy rod; finally cutting the Ni-Mn-Ga-C alloy rod and directionally solidifying by a seed crystal method to obtain the strong plasticity Ni-Mn-Ga-C alloy. The invention adopts the process of doping carbon and the orientation to be austenite<110> A The directional seed crystal is subjected to seed crystal directional solidification treatment, so that the Ni-Mn-Ga alloy strong plasticity is remarkably improved. The strong plasticity Ni-Mn-Ga-C alloy prepared by the invention not only maintains the phase structure and heat recovery of the original alloy, but also improves the mechanical property of the alloy. The compressive fracture strength of the strong plasticity Ni-Mn-Ga-C alloy is increased by nearly two times, and the strain is increased by three times.
Drawings
FIG. 1 is a process flow diagram of the present invention;
FIG. 2 is a schematic diagram of directional solidification according to the present invention;
FIG. 3 is comparative example 1 (Ni 54 Mn 26 Ga 20 ) 99.9 C 0.1 Alloy and comparative example 2Ni 54 Mn 26 Ga 20 XRD spectrum of alloy;
FIG. 4 is (Ni 54 Mn 26 Ga 20 ) 99.9 C 0.1 -<110> A Alloy (Ni) 54 Mn 26 Ga 20 ) 99.9 C 0.1 Alloy, ni 54 Mn 26 Ga 20 -<110> A Alloy and Ni 54 Mn 26 Ga 20 Compressive stress-strain curve of the alloy;
in FIG. 5, (a) is Ni 54 Mn 26 Ga 20 The alloy has heat recovery after twinning (b) of (Ni 54 Mn 26 Ga 20 ) 99.9 C 0.1 -<110> A The alloy has thermal recovery after twinning, (c) Ni 54 Mn 26 Ga 20 The alloy has a heat recovery at a compressive strain of 10% (d) of (Ni 54 Mn 26 Ga 20 ) 99.9 C 0.1 -<110> A The alloy has a heat recovery at a compressive strain of 10%;
FIG. 6 is (Ni 54 Mn 26 Ga 20 ) 99.9 C 0.1 -<110>Aalloy cross-sectional orientation imaging (a) and enlargement (b), and (Ni 54 Mn 26 Ga 20 ) 99.9 C 0.1 -<110>An A alloy gold phase diagram (c) and an enlarged diagram (d).
Detailed Description
The invention will be further illustrated with reference to specific examples.
Example 1
A kind of (Ni 54 Mn 26 Ga 20 ) 99.9 C 0.1 -<110>The preparation method of the alloy A comprises the following specific steps:
step 1, removing impurities from Ni, mn and Ga metal raw materials, and drying for later use;
step 2, according to Ni 54 Mn 26 Ga 20 Weighing Ni, mn and Ga according to the atomic ratio in the alloy, putting the weighed Ni and Ga into a crucible and putting into a smelting furnace, and then carrying out vacuum arc smelting to obtain a smelted Ni-Ga alloy;
step 3, adding weighed Mn into the Ni-Ga alloy, adding carbon blocks, smelting in an induction smelting furnace, and carrying out suction casting on the smelted alloy to obtain the alloy (Ni with the diameter of 8mm 54 Mn 26 Ga 20 ) 99.9 C 0.1 An alloy rod;
step 4, step (Ni) 54 Mn 26 Ga 20 ) 99.9 C 0.1 The alloy rod is cut into alloy rods with the diameter of 3mm, and then seed crystal method directional solidification treatment is carried out to obtain the strong plasticity (Ni 54 Mn 26 Ga 20 ) 99.9 C 0.1 -<110>An alloy A, the orientation of the seed crystal is austenite<110> A Direction.
The impurity removing method of Ni and Ga in the step 1 is to remove oxide layers and impurities on the surface of metal by using a mechanical polishing method;
the impurity removal method of Mn comprises the steps of firstly cleaning Mn by using a solution formed by nitric acid, hydrofluoric acid and water in a volume ratio of 20:5:75 so as to remove an oxide layer on the surface of Mn; then placing the mixture in absolute ethyl alcohol for ultrasonic impurity removal, and finally drying.
In the vacuum arc melting in the step 2, vacuumizing treatment is firstly carried out to ensure that the vacuum degree is minus 0.05MPa, then, after striking an arc, the melting current is adjusted to 200A, melting is carried out to remove residual oxygen, and then, the current is adjusted to 280A for repeated melting treatment.
The vacuum arc melting in the step 2 is performed for four times under the current of 280A, the melting time is 1min each time, and the turning-over treatment is required to be performed on the alloy ingot after the single melting is finished.
In the invention, step S3, alloy ingots which are repeatedly smelted in an induction smelting furnace until no carbon residue exists on the surfaces are subjected to suction casting treatment, wherein the arc current is 350A during the suction casting treatment, a suction casting switch is opened to perform suction casting by utilizing pressure difference after the alloy ingots are completely melted, and the alloy is sucked and cast into alloy rods with the diameter of 8 mm.
Step 4 of the invention is to physically bond the cut alloy rod with seed crystals with the same diameter and 3mm length, wherein the seed crystals are positioned at the bottom of the alloy rod, and then the alloy rod is placed in a heating furnace for heating and melting treatment, wherein the heating temperature is 1450 ℃, and the heat preservation time is 60min; starting a directional solidification drawing device, carrying out directional solidification at the directional solidification growth rate of 10 mu m/s, and naturally cooling to room temperature after 120mm of directional solidification.
Comparative example 1
A kind of (Ni 54 Mn 26 Ga 20 ) 99.9 C 0.1 The preparation method of the alloy comprises the following specific steps:
step 1, (Ni) having a diameter of 8mm was prepared according to the procedure 1-3 of example 1 54 Mn 26 Ga 20 ) 99.9 C 0.1 An alloy rod;
step 2, step (2) of subjecting the (Ni 54 Mn 26 Ga 20 ) 99.9 C 0.1 The alloy rod was cut into an alloy rod having a diameter of 3mm, and then subjected to directional solidification treatment to obtain a (Ni) 54 Mn 26 Ga 20 ) 99.9 C 0.1 The method of directional solidification of the alloy comprises the steps of placing the cut alloy rod into a heating furnace for heating and melting treatment, wherein the heating temperature is 1450 ℃, and the heat preservation time is 60min; starting a directional solidification drawing device, carrying out directional solidification at the directional solidification growth rate of 10 mu m/s, and naturally cooling to room temperature after 120mm of directional solidification.
Comparative example 2
Ni (nickel) 54 Mn 26 Ga 20 The preparation method of the alloy comprises the following specific steps:
step 1, removing impurities from Ni, mn and Ga metal raw materials, and drying for later use;
step 2, according to Ni 54 Mn 26 Ga 20 Weighing Ni, mn and Ga according to the atomic ratio in the alloy, putting the weighed Ni and Ga into a crucible and putting into a smelting furnace, and then carrying out vacuum arc smelting to obtain a smelted Ni-Ga alloy;
step 3, adding weighed Mn into the Ni-Ga alloy, smelting in an induction smelting furnace, and carrying out suction casting on the smelted alloy (wherein the suction casting method is the same as that of the embodiment 1) to obtain Ni with the diameter of 8mm 54 Mn 26 Ga 20 An alloy rod;
step 4, ni to be prepared 54 Mn 26 Ga 20 The alloy rod was directionally solidified according to the method of example 1, step 2 to obtain Ni 54 Mn 26 Ga 20 And (3) alloy.
Comparative example 3
Ni (nickel) 54 Mn 26 Ga 20 -<110> A The preparation method of the alloy comprises the following specific steps:
step 1, ni with a diameter of 8mm was obtained according to comparative example 1, steps 1-3 54 Mn 26 Ga 20 An alloy rod;
step 2, ni is added 54 Mn 26 Ga 20 The alloy rod is subjected to seed crystal method directional solidification treatment according to the step 4 of the embodiment 1 to obtain Ni 54 Mn 26 Ga 20 -<110> A And (3) alloy.
As can be seen from FIGS. 1-6, the invention carries out carbon doping and seed crystal method directional solidification treatment on Ni-Mn-Ga alloy, does not change the phase composition of the alloy, is a non-modulated tetragonal martensite phase, does not damage the thermal recovery property of the alloy, and well retains the shape memory effect of the alloy.
Compared with the prior art, the invention can find that the Ni-Mn-Ga directional solidification alloy prepared by carbon doping has better plasticity than the Ni-Mn-Ga master alloy without carbon doping, and the alloy prepared by adopting the seed crystal with <110> A orientation for seed crystal method directional solidification has better plasticity than the directional solidification alloy prepared by not adopting the seed crystal method. The Ni-Mn-Ga-C alloy prepared by coupling carbon doping and a seed crystal method has higher strong plasticity than Ni-Mn-Ga directional solidification alloy without carbon doping and without using the seed crystal method, and improves the strong plasticity of the alloy.
It should be noted that the above-mentioned embodiments are only a few specific embodiments of the present invention, and it is obvious that the present invention is not limited to the above embodiments, but other modifications are possible. All modifications directly or indirectly derived from the disclosure of the present invention will be considered to be within the scope of the present invention.
Claims (7)
1. A method for improving the plasticity of a Ni-Mn-Ga alloy, comprising the steps of:
step 1, removing impurities from Ni, mn and Ga metal raw materials, and drying for later use;
step 2, according to Ni 54 Mn 26 Ga 20 Weighing Ni, mn and Ga according to the atomic ratio in the alloy, putting the weighed Ni and Ga into a crucible and putting into a smelting furnace, and then carrying out vacuum arc smelting to obtain a smelted Ni-Ga alloy;
step 3, adding weighed Mn into the Ni-Ga alloy, adding carbon blocks, smelting in an induction smelting furnace, and carrying out suction casting on the smelted alloy to obtain a Ni-Mn-Ga-C alloy rod, wherein the atomic ratio of carbon in the alloy rod is 0.1%;
step 4, cutting the Ni-Mn-Ga-C alloy rod, and then carrying out seed crystal method directional solidification treatment to obtain the strong plasticity Ni-Mn-Ga-C alloy, wherein the orientation of the seed crystal is austenite<110> A Direction.
2. The method for improving the plasticity of the Ni-Mn-Ga alloy according to claim 1, wherein the impurity removal method for Ni and Ga in the step 1 is a method for removing oxide layers and impurities on the metal surface by using a mechanical polishing method;
the impurity removal method of Mn comprises the steps of firstly cleaning Mn by using a solution formed by nitric acid, hydrofluoric acid and water in a volume ratio of 20:5:75 so as to remove an oxide layer on the surface of Mn; then placing the mixture in absolute ethyl alcohol for ultrasonic impurity removal, and finally drying.
3. The method for improving the plasticity of the Ni-Mn-Ga alloy according to claim 1, wherein in the step 2, the vacuum arc melting is performed by vacuumizing so that the vacuum degree is-0.05 MPa, then adjusting the melting current to 200A after striking an arc, melting to remove residual oxygen, and then adjusting the current to 270A-300A, and repeating the melting process.
4. The method for improving the plasticity of the Ni-Mn-Ga alloy according to claim 3, wherein in the step 2, the vacuum arc melting is performed four times of melting treatment under the current of 270A-300A, the melting time is 1min each time, and the turning treatment is required to be performed on the alloy ingot after the single melting is finished.
5. The method for improving the plasticity of the Ni-Mn-Ga alloy according to claim 1, wherein the step S3 is to repeatedly smelt the alloy ingot with no carbon residue on the surface in an induction smelting furnace for suction casting treatment, wherein the arc current is 350A during the suction casting treatment, the suction casting switch is opened to perform suction casting by utilizing pressure difference after the alloy ingot is completely melted, and the alloy is sucked and cast into an alloy rod with the diameter of 8 mm.
6. The method for improving the plasticity of a Ni-Mn-Ga alloy according to claim 1, wherein step 4 is cutting the Ni-Mn-Ga-C alloy rod into alloy rods having a diameter of 3 mm.
7. The method for improving the plasticity of the Ni-Mn-Ga alloy according to claim 1, wherein the step 4 is to physically bond the cut alloy rod with a seed crystal with the same diameter and the length of 3-4mm, wherein the seed crystal is positioned at the bottom of the alloy rod, and then placing the alloy rod in a heating furnace for heating and melting treatment, wherein the heating temperature is not lower than 1450 ℃, and the heat preservation time is not lower than 30min; starting a directional solidification drawing device, carrying out directional solidification at the directional solidification growth rate of 10 mu m/s, and naturally cooling to room temperature after 120mm of directional solidification.
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