CN113088850A - Preparation method of large reversible magnetic strain NiCoMnSn alloy - Google Patents
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Abstract
The invention provides a preparation method of a large reversible magnetic strain NiCoMnSn alloy, belonging to the technical field of metamagnetic shape memory alloys. The invention carries out electron irradiation modification on the NiCoMnSn alloy to obtain the NiCoMnSn alloy with large reversible magnetic strain. The preparation method provided by the invention adopts electron radiation modification to the NiCoMnSn alloy, and irradiates the surface of the NiCoMnSn alloy to generate vacancies; due to the strong dependence of the magnetic exchange interaction on the Mn-Mn distance, the lattice contraction leads to the reduction of the Mn-Mn distance, so that the magnetization difference (delta M) between two phases (parent phase austenite and martensite) before and after the phase transformation is increased, and meanwhile, the 3d orbital hybridization is enhanced, so that the driving force of a magnetic field on the movement of the parent phase and the martensite interface is increased, and the change is favorable for obtaining large magnetic induction strain under a lower field.
Description
Technical Field
The invention relates to the technical field of metamagnetic shape memory alloys, in particular to a preparation method of a large reversible magnetostriction NiCoMnSn alloy.
Background
When an external magnetic field is applied to the novel metamagnetic shape memory alloy Ni-Co-Mn-X (X ═ Sn, In and Sb), the magnetization intensity between two phases is remarkably changed, so that the Zeeman can be differentiated, and the field martensite phase transformation from low-symmetry martensite to high-symmetry austenite is caused, and the crystallography of the metamagnetic shape memory alloy at a microscopic level is changed along with the field martensite phase transformation, so that macroscopic magnetic strain is generated, and the metamagnetic shape memory alloy has potential application In new-generation sensors and brakes. However, the large magnetic induction strain which can be obtained at present is obtained in a single-variant state in a single crystal or a polycrystal after cyclic training, the preparation process is complex, the mechanical processing is difficult, and the large-scale practical production is difficult to realize.
Disclosure of Invention
In view of the above, the present invention aims to provide a method for preparing a NiCoMnSn alloy with large reversible magnetic strain. The invention provides a new method for obtaining large reversible magnetic induced strain under polycrystalline condition by carrying out electron irradiation on NiCoMnSn alloy.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a preparation method of a large reversible magnetostriction NiCoMnSn alloy, which comprises the following steps:
and carrying out electron irradiation modification on the NiCoMnSn alloy to obtain the NiCoMnSn alloy with the large reversible magnetic strain.
Preferably, the irradiation energy of the electron irradiation modification is 60 KeV-1.2 MeV, and the irradiation fluence rate is 1 x 1012e/cm2·S-1The irradiation fluence is (1-3) x 1017e/cm2。
Preferably, the NiCoMnSn alloy is Ni47-xCoxMn43Sn10And x is an integer of 4-7.
Preferably, the Ni47-xCoxMn43Sn10Alloy of Ni41Co6Mn43Sn10And (3) alloying.
Preferably, the Ni47-xCoxMn43Sn10The alloy is prepared by a method comprising the following steps:
mixing Ni, Mn, Co and Sn, and then sequentially carrying out smelting, ingot casting molding and cutting to obtain a block sample;
sequentially carrying out mechanical polishing and absolute ethyl alcohol cleaning on the block sample to obtain a cleaned sample;
sequentially carrying out solution annealing, ice water quenching, polishing and annealing stress relief on the cleaned sample to obtain the Ni47-xCoxMn43Sn10And (3) alloying.
Preferably, the vacuum degree of the solution annealing is 10-4Pa, the temperature is 950-1000 ℃, and the time is 24 hours.
Preferably, the vacuum degree of the electron irradiation modification is 10-4Pa。
The invention provides a preparation method of a large reversible magnetostriction NiCoMnSn alloy, which comprises the following steps: and carrying out electron irradiation modification on the NiCoMnSn alloy to obtain the NiCoMnSn alloy with the large reversible magnetic strain.
The preparation method provided by the invention adopts electron radiation modification to the NiCoMnSn alloy, and irradiates the surface of the NiCoMnSn alloy to generate vacancies; due to the strong dependence of the magnetic exchange interaction on the Mn-Mn distance, the lattice contraction leads to the reduction of the Mn-Mn distance, so that the magnetization difference (delta M) between two phases (parent phase austenite and martensite) before and after the phase transformation is increased, and meanwhile, the 3d orbital hybridization is enhanced, so that the driving force of a magnetic field on the movement of the parent phase and the martensite interface is increased, and the change is favorable for obtaining large magnetic induced strain under a lower magnetic field. The invention provides a novel method for obtaining large reversible magnetic induction strain under a polycrystalline condition by carrying out electron irradiation on NiCoMnSn alloy, solves the problem of low strain under most of traditional Ni-Mn-based polycrystal conditions, simplifies the preparation process, and obtains 0.22 percent of maximum completely reversible magnetic induction strain under a 4.5T magnetic field under the condition of no pre-deformation of Ni-Co-Mn-Sn polycrystal.
Drawings
FIG. 1 is a graph showing the simulation of 1.2MeV electrons in Ni by CASNO in example 141Co6Mn43Sn10Electron path diagram in alloys;
FIG. 2 is the simulation of 1.2MeV electrons in Ni using CASNO in example 141Co6Mn43Sn10Energy loss profile in the alloy;
FIG. 3 shows Ni before and after electron irradiation in example 141Co6Mn43Sn10An X-ray diffraction pattern of the sample;
FIG. 4 shows Ni before and after electron irradiation in example 141Co6Mn43Sn10Magnetization curves of samples in which (a) is a magnetization-temperature dependence curve at low field (M-T curve), (b) and (c) are Ni, respectively41Co6Mn43Sn10A magnetic field dependence curve (M-H curve) of the magnetization before and after irradiation of the alloy;
FIG. 5 shows Ni before and after electron irradiation in example 141Co6Mn43Sn10Isothermal magnetic strain curve of sample measured in the direction perpendicular to the magnetic field test direction, wherein (a) is Ni before electron irradiation41Co6Mn43Sn10Isothermal magnetic strain curve of sample, (b) is Ni after electron irradiation41Co6Mn43Sn10Isothermal magnetic strain curve of the sample.
Detailed Description
The invention provides a preparation method of a large reversible magnetic strain NiCoMnSn alloy, which comprises the following steps;
and carrying out electron irradiation modification on the NiCoMnSn alloy to obtain the NiCoMnSn alloy with the large reversible magnetic strain.
In the invention, the irradiation energy of the electron irradiation modification is preferably 60 KeV-1.2 MeV, and the irradiation fluence rate is preferably 1 x 1012e/cm2·S-1The irradiation fluence is preferably (1-3). times.1017e/cm2More preferably 2X 1017e/cm2。
In the invention, the vacuum degree of the electron irradiation modification is 10-4Pa。
In the present invention, the temperature of the electron irradiation modification is preferably room temperature, and more preferably room temperature is maintained using a cooling water circulation.
In the present invention, the NiCoMnSn alloy is preferably Ni47-xCoxMn43Sn10In the alloy, x is preferably an integer of 4 to 7, and more preferably 6.
In the present invention, the Ni47-xCoxMn43Sn10The alloy is preferably Ni41Co6Mn43Sn10And (3) alloying.
In the present invention, the Ni47-xCoxMn43Sn10The alloy is preferably made by a process comprising the steps of:
mixing Ni, Mn, Co and Sn, and then sequentially carrying out smelting, ingot casting molding and cutting to obtain a block sample;
sequentially carrying out mechanical polishing and absolute ethyl alcohol cleaning on the block sample to obtain a cleaned sample;
sequentially carrying out solution annealing, ice water quenching, polishing and annealing stress relief on the cleaned sample to obtain the Ni47-xCoxMn43Sn10And (3) alloying.
According to the invention, Ni, Mn, Co and Sn are mixed and then sequentially subjected to smelting, ingot casting forming and cutting to obtain a block sample. In the present invention, the Ni is preferably Ni having a purity of 99.99 wt.%, the Mn is preferably Mn having a purity of 99.99 wt.%, the Co is preferably Co having a purity of 99.99 wt.%, and the Sn is preferably Sn having a purity of 99.99 wt.%. The invention has no special limit on the dosage of the Ni, the Mn, the Co and the Sn, and can ensure that the NiCoMnSn alloy is obtained.
In the present invention, the melting is preferably performed in a water-cooled copper crucible arc melting furnace.
The present invention is not particularly limited with respect to the specific manner of shaping and cutting the ingot, and may be implemented in a manner known to those skilled in the art.
After the block sample is obtained, the cleaned sample is obtained after the block sample is sequentially subjected to mechanical polishing and absolute ethyl alcohol cleaning. In the present invention, the mechanical polishing functions to remove surface scale.
In the invention, the absolute ethyl alcohol washing is preferably carried out in ultrasonic, and the number of times of the absolute ethyl alcohol washing is preferably 3-5 times.
After a cleaned sample is obtained, the cleaned sample is sequentially subjected to solution annealing, ice water quenching, polishing and annealing stress relief to obtain the Ni47-xCoxMn43Sn10And (3) alloying.
In the present invention, the degree of vacuum of the solution treatment is 10-4Pa, the temperature is 950-1000 ℃, and the time is 24 hours. In the present invention, the solution annealing is preferably performed in a quartz tube.
The specific modes of quenching water, polishing and annealing for stress relief are not particularly limited in the present invention, and can be any modes known to those skilled in the art.
In order to further illustrate the present invention, the following examples are given to describe the highly reversible magnetostriction NiCoMnSn alloy and the preparation method and application thereof in detail, but they should not be construed as limiting the scope of the present invention.
Example 1
The test material was Ni41Co6Mn43Sn10The alloy is prepared by using 99.99 wt% -Ni, 99.95 wt% -Mn, 99.99 wt% -Co and 99.99 wt% -Sn as raw materials, smelting the raw materials into ingots by a water-cooled copper crucible arc melting furnace, then obtaining block samples with corresponding sizes by a wire cut electrical discharge machining method, then removing surface oxide scales by a mechanical polishing method, ultrasonically cleaning the samples in absolute ethyl alcohol for 5 times, and sealing the cleaned samples in vacuum degree of 10-4And (3) carrying out solution annealing on the Pa quartz tube at 1000 ℃ for 24 hours, and then quenching the quartz tube into ice water. And polishing the obtained sample, annealing and removing stress, and then carrying out an electron irradiation test.
The electron irradiation experiment is completed by space comprehensive irradiation simulation equipment of the physical research institute of Heilongjiang. Maintaining vacuum 10 in the target chamber during irradiation-4Pa, cooling water is circulated to keep the room temperature. Irradiation experiment parameters: the irradiation energy range is 1.2MeV, and the fluence rate is 1X 1012e/cm2·S-1The irradiation fluence is 2X 1017e/cm2。
Simulation of 1.2MeV electrons in Ni by CASNO41Co6Mn43Sn10The paths and energy loss distributions in the alloy are shown in fig. 1-2, wherein fig. 1 is an electron path diagram, and fig. 2 is an energy loss distribution diagram, it can be seen that the energy loss of electrons is not uniformly distributed along with the incident depth in the propagation process, and the path distribution of electrons shows that the path distribution is wide.
For Ni after electron irradiation41Co6Mn43Sn10The sample was subjected to X-ray diffraction analysis, and as a result, as shown in fig. 3, the diffraction characteristic peaks of the sample before and after irradiation were the same as the standard pattern of the L21Heusler type crystal structure, and no characteristic peak of the second phase was found in the range tested. Calculating the lattice constant a of the sample before and after irradiation according to the X-ray diffraction diagram
Down to
This is due to the creation of vacancies caused by the electron irradiation process. Due to the strong dependence of the magnetic exchange interaction on the Mn-Mn distance, the lattice contraction can cause the reduction of the Mn-Mn distance, so that the magnetization difference (delta M) between two phases before and after phase change is increased, and meanwhile, the enhancement of 3d orbital hybridization can cause the increase of the driving force of a magnetic field on the movement of a parent phase and a martensite interface, and the change is beneficial to obtaining large magnetic induction strain under a lower field.
FIG. 4 shows Ni before and after electron irradiation41Co6Mn43Sn10The magnetization curve of the sample, wherein (a) is the magnetization versus temperature curve at low field (M-T curve), the temperature scale of the phase change characteristics is shown in (a). (b) And (c) are each Ni41Co6Mn43Sn10Magnetic field dependent bending of magnetization before and after alloy irradiationLine (M-H curve). The measuring process follows a Loop method, namely before each temperature test, the sample is cooled to 150K and is kept warm for 5 minutes, so that the sample is completely in a martensite state, and then the sample is heated to a test target temperature lifting magnetic field. The magnetization of the sample before and after electron irradiation increases linearly with the magnetic field lines at low temperature, and does not saturate even at 7T field. With a gradual increase in the test temperature, a sharp increase in magnetization up to saturation is observed As the temperature approaches the As temperature, and a hysteresis loop occurs, corresponding to a metamagnetic transition from antiferromagnetic martensite to ferromagnetic austenite. However, when the temperature is further raised above the Af temperature, the atomic magnetic moment orientation is broken, resulting in a gradual decrease in magnetization. In addition, the samples before and after irradiation are compared, and the magnetization intensity of the sample after electron irradiation is obviously enhanced.
FIG. 5 shows Ni in the reverse martensitic transformation temperature range41Co6Mn43Sn10Isothermal magnetic strain curves of the samples measured in a direction perpendicular to the magnetic field test direction. (a) Ni before electron irradiation41Co6Mn43Sn10The isothermal magnetic strain curve of the sample shows that the magnetic strain cannot be found in the range of the measured magnetic field until the temperature is raised to the temperature at which the electric field induced martensitic transformation occurs, i.e., 235K, because the anisotropic energy in the martensitic state is not significant. With further increase in temperature, the magnetic strain increases significantly due to the enhanced martensitic transformation. At 250K, the maximum reversible magnetic strain reaches 0.05% at a magnetic field of 5T. With further changes in temperature, reversible magnetic strains can also be observed, but with a significant reduction compared to the initial magnetic strain. This is due to the thermal hysteresis effect caused by the phase boundary friction, with the result that only a small amount of field-hindered austenite can be reduced to martensite. With further increase in temperature, the magnetic strain gradually decreases. (b) As Ni after electron irradiation41Co6Mn43Sn10The isothermal magnetic strain curve of the sample shows that the maximum reversible magnetic strain obtained at 240K temperature under-4.5T magnetic field is 0.22% which is 4.4 times that of the sample without irradiation. Taking into account the combined effects of the magnetic strain and the applied magnetic field,in the work, a sample subjected to electron irradiation can obtain large reversible magnetic strain without multiple mechanical cycle treatments under a polycrystalline condition.
The foregoing is merely a preferred embodiment of the invention and is not intended to limit the invention in any manner. It should be noted that, for those skilled in the art, without departing from the principle of the present invention, several improvements and modifications can be made, and these improvements and modifications should also be construed as the protection scope of the present invention.
Claims (7)
1. A preparation method of a large reversible magnetostriction NiCoMnSn alloy is characterized by comprising the following steps:
and carrying out electron irradiation modification on the NiCoMnSn alloy to obtain the NiCoMnSn alloy with the large reversible magnetic strain.
2. The method according to claim 1, wherein the electron irradiation modification has an irradiation energy of 60KeV to 1.2MeV and an irradiation fluence rate of 1 x 1012e/cm2·S-1The irradiation fluence is (1-3) x 1017e/cm2。
3. Method for the production according to claim 1 or 2, characterized in that the NiCoMnSn alloy is Ni47- xCoxMn43Sn10And x is an integer of 4-7.
4. The method of claim 3, wherein the Ni is47-xCoxMn43Sn10Alloy of Ni41Co6Mn43Sn10And (3) alloying.
5. The method of claim 3, wherein the Ni is47-xCoxMn43Sn10The alloy is prepared by a method comprising the following steps:
mixing Ni, Mn, Co and Sn, and then sequentially carrying out smelting, ingot casting molding and cutting to obtain a block sample;
sequentially carrying out mechanical polishing and absolute ethyl alcohol cleaning on the block sample to obtain a cleaned sample;
sequentially carrying out solution annealing, ice water quenching, polishing and annealing stress relief on the cleaned sample to obtain the Ni47- xCoxMn43Sn10And (3) alloying.
6. The production method according to claim 5, wherein the degree of vacuum of the solution annealing is 10-4Pa, the temperature is 950-1000 ℃, and the time is 24 hours.
7. The method according to claim 1 or 2, wherein the degree of vacuum of the electron irradiation modification is 10- 4Pa。
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Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02186605A (en) * | 1989-10-07 | 1990-07-20 | Res Inst Electric Magnetic Alloys | Wear-resistant high permeability magnetic recording and reproducing head |
| CN102115914A (en) * | 2010-12-15 | 2011-07-06 | 河北师范大学 | Mn50CoxNiySnz high-temperature ferromagnetic shape memory alloy material and preparation methods thereof |
| CN103074522A (en) * | 2013-01-10 | 2013-05-01 | 哈尔滨工业大学 | Poly-crystal Ni-Co-Mn-In-Gd alloy and preparation method thereof |
| CN105950916A (en) * | 2016-05-25 | 2016-09-21 | 北京科技大学 | Magnetic field driving torsional nickel-cobalt-manganese-tin alloy wire and preparation method |
| CN106119661A (en) * | 2016-07-29 | 2016-11-16 | 东北大学 | A kind of Mn Ni Sn Co alloy thin band and preparation method thereof |
| CN108330372A (en) * | 2018-02-28 | 2018-07-27 | 华南理工大学 | A kind of Ni-Co-Mn-Sn magnetic refrigerating materials and preparation method thereof |
| CN111304565A (en) * | 2020-02-28 | 2020-06-19 | 哈尔滨工业大学 | Ni-Co-Mn-In alloy magnetic refrigeration material and preparation method thereof |
-
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Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02186605A (en) * | 1989-10-07 | 1990-07-20 | Res Inst Electric Magnetic Alloys | Wear-resistant high permeability magnetic recording and reproducing head |
| CN102115914A (en) * | 2010-12-15 | 2011-07-06 | 河北师范大学 | Mn50CoxNiySnz high-temperature ferromagnetic shape memory alloy material and preparation methods thereof |
| CN103074522A (en) * | 2013-01-10 | 2013-05-01 | 哈尔滨工业大学 | Poly-crystal Ni-Co-Mn-In-Gd alloy and preparation method thereof |
| CN105950916A (en) * | 2016-05-25 | 2016-09-21 | 北京科技大学 | Magnetic field driving torsional nickel-cobalt-manganese-tin alloy wire and preparation method |
| CN106119661A (en) * | 2016-07-29 | 2016-11-16 | 东北大学 | A kind of Mn Ni Sn Co alloy thin band and preparation method thereof |
| CN108330372A (en) * | 2018-02-28 | 2018-07-27 | 华南理工大学 | A kind of Ni-Co-Mn-Sn magnetic refrigerating materials and preparation method thereof |
| CN111304565A (en) * | 2020-02-28 | 2020-06-19 | 哈尔滨工业大学 | Ni-Co-Mn-In alloy magnetic refrigeration material and preparation method thereof |
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| CN116005061A (en) * | 2023-02-07 | 2023-04-25 | 西北工业大学 | Magnetic control memory alloy with gradient tissue structure and controllable magnetic performance and preparation method thereof |
| CN116005061B (en) * | 2023-02-07 | 2023-09-12 | 西北工业大学 | Magnetic control memory alloy with gradient tissue structure and controllable magnetic performance and preparation method thereof |
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