CN113667934B - Magnetic controllable two-dimensional magnetic composite material and preparation method thereof - Google Patents

Magnetic controllable two-dimensional magnetic composite material and preparation method thereof Download PDF

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CN113667934B
CN113667934B CN202110816328.0A CN202110816328A CN113667934B CN 113667934 B CN113667934 B CN 113667934B CN 202110816328 A CN202110816328 A CN 202110816328A CN 113667934 B CN113667934 B CN 113667934B
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CN113667934A (en
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李领伟
周健
胡亮
杨秉璋
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Hangzhou Dianzi University
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    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
    • C23C14/24—Vacuum evaporation
    • C23C14/28—Vacuum evaporation by wave energy or particle radiation
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
    • C23C14/08—Oxides
    • C23C14/083—Oxides of refractory metals or yttrium
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/0036—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties showing low dimensional magnetism, i.e. spin rearrangements due to a restriction of dimensions, e.g. showing giant magnetoresistivity
    • H01F1/009—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties showing low dimensional magnetism, i.e. spin rearrangements due to a restriction of dimensions, e.g. showing giant magnetoresistivity bidimensional, e.g. nanoscale period nanomagnet arrays

Abstract

The invention relates to the field of magnetic materials, and discloses a magnetic controllable two-dimensional magnetic composite material and a preparation method thereof, aiming at overcoming the defects of low adjustable performance and poor magnetic adjustment repeatability of the conventional magnetic material. The bottom lining layer is connected with the magnetic layer through coupling acting force, when the temperature changes, the change of the internal state of the bottom lining layer can be influenced, the bottom lining layer is acted by internal force, and then stress can be applied to the magnetic layer, and the stress acts on the magnetic layer, so that the change of magnetic characteristics can be shown. The reversibility of the action process of the force can be achieved only by controlling the temperature, so that the magnetic strength of the magnetic layer is regulated and controlled from the angle of regulating and controlling the temperature.

Description

Magnetic controllable two-dimensional magnetic composite material and preparation method thereof
Technical Field
The invention relates to the field of magnetic materials, in particular to a magnetic controllable two-dimensional magnetic composite material and a preparation method thereof.
Background
The two-dimensional material is an ultrathin material with two dimensions belonging to macroscopic dimensions and the other dimension belonging to nanometer dimension range. Two-dimensional materials are novel materials which are born in the beginning of the twenty-first century and rapidly rise, and have wide application prospects in the fields of photoelectric converters, catalysis, sensing, medicine and the like because they show a series of special structures and performances, such as unique optical, mechanical, electromagnetic and gas-sensitive properties, compared with blocks.
One type of system with magnetic properties (i.e., two-dimensional magnetic materials) in the two-dimensional material family is receiving extensive academic and industrial attention. Such as two-dimensional Fe-Ge-Te material (Fe 3 GeTe 2 ) The material has the characteristics common to two-dimensional materials, and has a higher ferromagnetic phase transition Curie temperature (about 220K), so that the material is expected to be applied to the next-generation spintronics devices. Since 2018, magnetic regulation of iron-germanium-tellurium materials has been the hotspot of current research, and scientists have been led to a new search for the two-dimensional magnetic field from the experimental point of view. Regulation and controlThe methods currently comprise component regulation, doping regulation, strain regulation, electric field regulation, illumination regulation and the like, but the methods still have a plurality of defects, such as poor repeatability, magnetic second phase interference, insignificant curie temperature improvement and the like, so that development of novel methods for regulating magnetic characteristics is necessary.
Research on vanadium dioxide has never been discontinued since Morin found the phase change properties of vanadium dioxide in 1959. The vanadium dioxide film can generate phase change when reaching 68 ℃, the crystal structure can be changed from a low-temperature monoclinic phase structure to a high-temperature tetragonal phase structure, and the process can be reversibly carried out when the temperature is reduced below a phase change point along with the expansion of crystal lattices and the reduction of resistivity, so that the vanadium dioxide film is a phase change material with excellent performance.
Theoretical research shows that the strain can significantly improve the magnetic performance of the two-dimensional magnetic material, but repeated modulation is difficult to achieve by manually applying the strain, so that development of a new stress transmission mode is needed. The Fe-Ge-Te material is a two-dimensional layered ferromagnetic material formed by combining Van der Waals forces, so that the characteristics ensure that the Fe-Ge-Te and other materials can be coupled by the Van der Waals forces to generate strong neighbor interaction, and the effectiveness and controllability of the process are still needed to be explored.
Chinese patent publication No. CN111681691a discloses a phase-change auxiliary magnetic disk medium, magnetic disk, apparatus and method, which is characterized in that it comprises: a substrate; the phase change material layer is formed on the substrate and is subjected to phase change under preset conditions; the magnetic material layer is formed on the phase-change material layer, is in an unmagnetized state when the phase-change material layer is subjected to phase change, and has a first magnetization direction and a second magnetization direction under the magnetic field conditions of the first direction and the second direction when the phase-change material layer is not subjected to phase change; and a cladding layer formed on the magnetic material layer. The magnetic material has the defects that an external magnetic field is needed to obtain a first magnetization direction and a second magnetization direction, and the magnetic strength depends on the intensity of the external magnetic field; the magnetization state is changed in an on-off state when in strain, and the adjustable performance is low.
Disclosure of Invention
The invention discloses a magnetic controllable two-dimensional magnetic composite material with high regulation performance and strong repeatability and a preparation method thereof, and aims to overcome the defects of low regulation performance and poor magnetic regulation repeatability of the conventional magnetic material.
In order to achieve the above object, the present invention adopts the following technical scheme:
the magnetic controllable two-dimensional magnetic composite material is formed by coupling a bottom lining layer and a magnetic layer, and the magnetic controllable two-dimensional magnetic composite material changes magnetism by adjusting temperature.
The bottom lining layer is connected with the magnetic layer through coupling acting force, when the temperature changes, the change of the internal state of the bottom lining layer can be influenced, the bottom lining layer is acted by internal force, and then stress can be applied to the magnetic layer, and the stress acts on the magnetic layer, so that the change of magnetic characteristics can be shown. The reversibility of the action process of the force can be achieved only by controlling the temperature, so that the magnetic strength of the magnetic layer is regulated and controlled from the angle of regulating and controlling the temperature.
Further, the underlayer is a monoclinic crystalline vanadium dioxide film that is weakly ferromagnetic at room temperature.
The monoclinic vanadium dioxide is free of ferromagnetism or weak ferromagnetism at room temperature, can generate structural phase change at the temperature higher than 68 ℃ to form rutile tetragonal crystal, and can be converted into monoclinic crystal at the temperature lower than 68 ℃ to generate change of lattice constant.
Further, the thickness of the underlayer is 20-30 nm.
Further, the magnetic layer is an iron germanium tellurium nano-sheet.
The iron germanium tellurium nano-sheet is ferromagnetic at a low temperature, but the magnetism gradually weakens along with the temperature rise, and the magnetism can completely disappear when reaching 220K. The inventor finds that in the experimental process, when the iron germanium tellurium nanosheets are coupled with the weak ferromagnetism vanadium dioxide film at room temperature, a neighbor effect exists, namely, the vanadium element and the iron element in the iron germanium tellurium are coupled to generate spin-orbit, the weak ferromagnetism vanadium dioxide can induce the non-ferromagnetism iron germanium tellurium to display ferromagnetic characteristics, the vanadium dioxide crystal form is changed along with the rising of the temperature, and the ferromagnetic characteristics of the iron germanium tellurium are further influenced due to the transmission of stress on a contact surface, so that the magnetic characteristics of the iron germanium tellurium are gradually enhanced. The possibility of maintaining the magnetic properties and enhancing the magnetic properties of the iron germanium tellurium at normal temperature and even at higher temperature is realized. Because Van der Waals force belongs to intermolecular weak interaction, the force transfer effect on the iron germanium tellurium nanosheets can be guaranteed when the vanadium dioxide film changes phase, the iron germanium tellurium nanosheets cannot be excessively applied to force so as to damage the integral structure of the iron germanium tellurium nanosheets, and the practical value of the iron germanium tellurium is widened.
Further, the average thickness of the magnetic layer is 10-50 nm, and the transverse dimension is 1-20 μm.
A manufacturing method of a magnetic controllable two-dimensional magnetic composite material comprises the following steps:
(1) Depositing and preparing a bottom lining film on a substrate;
(2) Stripping the magnetic material crystal to obtain a magnetic layer nano sheet;
(3) Transferring the magnetic layer nano-sheet to the prepared underlayer film to form a two-dimensional magnetic composite material with the magnetic layer nano-sheet combined with the underlayer film;
(4) And (3) performing temperature regulation and control on the two-dimensional magnetic composite material obtained in the step (3), so as to regulate and control the magnetic properties of the two-dimensional magnetic composite material.
Further, in the step (1), the substrate is sapphire, and the thickness of the sapphire substrate is 1-2 mm.
Further, in the step (1), the deposition method is a pulse laser deposition PLD method, the film forming temperature of PLD is 500-700 ℃, the oxygen pressure is 5-15 mTorr, the pulse wavelength is 248nm, the pulse width is 10-30 ns, the pulse repetition frequency is 1-20 Hz, and the energy density is 2-4J/cm 2 The distance from the pulsed laser target to the substrate is 40-50 mm.
When the laser frequency is too high, particles deposited on the film do not move, and the next batch of particles fall down, so that accumulation is caused to form an uneven film; when the frequency is too low, the interval becomes long, and impurities enter the film, degrading the quality of the underlying film. The laser energy is too low to obtain a film or the deposition speed is slower, and as the energy increases, the film deposition speed, the average particle size and the spatial distribution of plasma plumes also change, but when the energy is too high, large particles appear, and the surface smoothness of the film also decreases. When the distance from the target to the substrate is too large, ions in the plume can be compounded into large particles; too small a distance Shi Yuhui can result in high ion energies and speeds that can affect film quality and even damage the substrate.
By adopting the technical scheme, the invention has the following beneficial effects: on the premise that coupling acting force exists between the bottom lining layer and the magnetic layer, the two-dimensional magnetic composite material enables the bottom lining layer to be structurally changed by changing the temperature, so that stress is applied to the magnetic layer, the magnetism of the magnetic layer is changed, and the controllable adjustment of the magnetism of the two-dimensional magnetic composite material is realized; in the process of magnetic adjustment, the change of influencing factors is reversible, so that the magnetic adjustment of the two-dimensional magnetic composite material has repeatability; in addition, the inventor finds that the ferromagnetism of the iron germanium tellurium is obviously improved after the phase change of the two-dimensional magnetic composite material in the process of adjusting the magnetism of the two-dimensional magnetic composite material; and the Curie temperature of the Fe-Ge-Te is improved, the applicable temperature range is improved, and the application prospect of the two-dimensional magnetic composite material is effectively expanded.
Drawings
FIG. 1 is a schematic diagram of the present invention in which the FeGeTe nanosheets are coupled to a vanadium dioxide thin film and are stressed by a temperature controlled process.
Fig. 2 is an optical micrograph of the vanadium dioxide film coupled iron germanium tellurium nanoplatelets of the present invention before and after.
FIG. 3 is a graph showing magnetization-temperature at 4 to 300K of the tellurium-germanium-iron single crystal of comparative example 1.
Fig. 4 is a graph of magnetization intensity versus temperature at 4-300 k for a target sample of iron germanium tellurium nanoplatelets of comparative example 2 composited on a silicon wafer with an oxide layer.
FIG. 5 is a graph of magnetization versus temperature for the vanadium dioxide film of comparative example 3 at 4-300K.
FIG. 6 is a plot of magnetization versus temperature for two-dimensional magnetic composites of the iron germanium tellurium nanoplatelets prepared in example 1 and comparative example 4, comparative example 5 coupled to vanadium dioxide thin films under an applied magnetic field of 1000 Oe.
FIG. 7 is a plot of magnetization versus magnetic field strength for the two-dimensional magnetic composite of example 1 at 300K and 340K.
Detailed Description
The invention is further described below with reference to the drawings and detailed description.
The two-dimensional magnetic composite material with controllable magnetism is formed by coupling a vanadium dioxide film on a bottom lining layer and a iron germanium tellurium nano-sheet on a magnetic layer, wherein the magnetism of the two-dimensional magnetic composite material with controllable magnetism is changed by adjusting temperature, as shown in fig. 1 (b), the iron germanium tellurium nano-sheet is coupled on the surface of the vanadium dioxide film, the crystal form of the vanadium dioxide film is changed along with the rise of temperature, so that phase change occurs, and the iron germanium tellurium nano-sheet is stretched by the neighbor effect due to the effect of the neighbor effect, so that the adjustment of the magnetism of the composite iron germanium tellurium nano-sheet is realized.
Example 1
(1) 10ml of methanol is added into 10g of analytically pure vanadium dioxide powder to prepare suspension, the suspension is taken out after being placed at the constant temperature of 80 ℃ for 30min, ground into powder, and then placed in a pressurizing machine for pressurizing, thus obtaining the vanadium dioxide target. And (3) putting the prepared target into a high-temperature furnace, and annealing for 4 hours in an argon atmosphere at 1000 ℃ to prepare the target for the test. Fixing a target for test in a PLD instrument, adopting sapphire with the thickness of 1mm as a substrate, adopting an excimer pulse laser with the film forming temperature of 600 ℃, the oxygen pressure of 10mTorr, the control wavelength of 248nm, the pulse width of 20ns, the pulse repetition frequency of 2Hz and the energy density of 3J/cm 2 The distance from the target to the substrate was controlled at 40mm. Depositing to obtain the vanadium dioxide film with the thickness of 20 nm.
(2) And mechanically stripping the tellurium-germanium-iron monocrystal by using a special mechanical stripping adhesive tape to obtain the tellurium-germanium-iron nanosheets with the thickness average of 40nm and the transverse dimension of 10 mu m.
(3) And transferring the stripped iron germanium tellurium nanosheets to a vanadium dioxide film, and coupling the two nanosheets together under the action of Van der Waals force to obtain the two-dimensional magnetic composite material. Fig. 2 shows optical micrographs of the iron germanium tellurium nanoplatelets before and after transfer to the vanadium dioxide thin film.
(4) And (3) putting the transferred two-dimensional magnetic composite material into a SQUID instrument of a superconducting quantum interferometer, measuring the external magnetic field to be 1000Oe, and changing the magnetism of the iron germanium tellurium nanosheets before and after the phase change of the vanadium dioxide film within the temperature range of 300-360K.
Comparative example 1
And mechanically stripping the iron germanium tellurium monocrystal by using a special mechanical stripping adhesive tape to obtain the thickness average value of the iron germanium tellurium nanosheets of 40nm and the transverse dimension of 10 mu m, putting the stripped iron germanium tellurium nanosheets into a SQUID instrument, and measuring the magnetic change of the iron germanium tellurium nanosheets in the temperature range of 4K-300K. As shown in fig. 3, the iron germanium tellurium has completely lost magnetism by the time the temperature reaches 300K.
Comparative example 2
Selecting a commercial silicon wafer with the surface oxide layer thickness of 300nm, mechanically stripping the iron germanium tellurium monocrystal by using a special mechanical stripping adhesive tape to obtain an iron germanium tellurium nanosheet with the thickness average value of 40nm and the transverse dimension of 10 mu m, transferring the stripped iron germanium tellurium nanosheets onto the surface oxidized silicon wafer to couple the surface oxidized silicon wafer and the surface oxidized silicon wafer together, placing a transferred experimental sample into a SQUID instrument, and measuring the magnetic change of the iron germanium tellurium nanosheets on the surface oxidized silicon wafer in the temperature range of 4K-300K.
As can be seen from FIG. 4, the surface oxidized silicon wafer and the FeGeTe nanosheet are combined, the variation trend of the magnetization-temperature curve is similar to that of the FeGeTe single crystal in FIG. 3, and the magnetization is reduced and the Curie transition temperature is slightly reduced because of the fewer nanosheets transferred onto the silicon wafer.
Comparative example 3
10ml of methanol is added into 10g of analytically pure vanadium dioxide powder to prepare suspension, the suspension is taken out after being placed at the constant temperature of 80 ℃ for 30min, ground into powder, and then placed in a pressurizing machine for pressurizing, thus obtaining the vanadium dioxide target. Placing the prepared target materialAnnealing in an argon atmosphere at 1000 ℃ for 4 hours in a high-temperature furnace to prepare the target material for the test. Fixing a target for test in a PLD instrument, adopting sapphire with the thickness of 1mm as a substrate, adopting an excimer pulse laser with the film forming temperature of 600 ℃, the oxygen pressure of 10mTorr, the control wavelength of 248nm, the pulse width of 20ns, the pulse repetition frequency of 2Hz and the energy density of 3J/cm 2 The distance from the target to the substrate was controlled at 40mm. Depositing to obtain the vanadium dioxide film with the thickness of 20 nm.
And putting the prepared vanadium dioxide film into a SQUID instrument, and measuring the change of magnetism of the vanadium dioxide film before and after phase change in a temperature range of 4-300K when an external magnetic field is 1000 Oe. As shown in fig. 5, the magnetization of vanadium dioxide gradually decreases as the temperature increases to 300K, but the curie transition point is not reached, so that the vanadium dioxide is weakly ferromagnetic at normal temperature.
Comparative example 4
(1) Uniformly mixing 10g of vanadium dioxide powder (analytically pure), adding into 10ml of methanol solution to prepare suspension, standing at the constant temperature of 80 ℃ for 30min, taking out, grinding into powder, and then placing into a pressurizing machine for pressurizing to obtain the vanadium dioxide target. And (3) putting the prepared target into a high-temperature furnace, and annealing for 4 hours in an argon atmosphere at 1000 ℃ to prepare the target for the test. Fixing a target for test in a PLD instrument, adopting sapphire with the thickness of 1mm as a substrate, adopting an excimer pulse laser with the film forming temperature of 600 ℃, the oxygen pressure of 15mTorr, the control wavelength of 248nm, the pulse width of 20ns, the pulse repetition frequency of 2Hz and the energy density of 3J/cm 2 The distance from the target to the substrate was controlled at 40mm. Depositing to obtain the vanadium dioxide film with the thickness of 20 nm.
(2) And mechanically stripping the tellurium-germanium-iron monocrystal by using a special mechanical stripping adhesive tape to obtain the tellurium-germanium-iron nanosheets with the thickness average of 30nm and the transverse dimension of 20 mu m.
(3) And transferring the stripped iron germanium tellurium nanosheets to a vanadium dioxide film, and coupling the two nanosheets together under the action of Van der Waals force to obtain the two-dimensional magnetic composite material.
(4) And (3) putting the transferred two-dimensional magnetic composite material into a SQUID instrument, measuring the external magnetic field to be 1000Oe, and changing the magnetism of the iron germanium tellurium nanosheets before and after the phase change of the vanadium dioxide film within the temperature range of 300K-360K.
Comparative example 5
(1) Uniformly mixing 10g of vanadium dioxide powder (analytically pure), adding into 10ml of methanol solution to prepare suspension, standing at the constant temperature of 80 ℃ for 30min, taking out, grinding into powder, and then placing into a pressurizing machine for pressurizing to obtain the vanadium dioxide target. And (3) putting the prepared target into a high-temperature furnace, and annealing for 4 hours in an argon atmosphere at 1000 ℃ to prepare the target for the test. Fixing a target for test in a PLD instrument, adopting sapphire with the thickness of 1mm as a substrate, adopting an excimer pulse laser with the film forming temperature of 500 ℃, the oxygen pressure of 10mTorr, the control wavelength of 248nm, the pulse width of 20ns, the pulse repetition frequency of 2Hz and the energy density of 3J/cm 2 The distance from the target to the substrate was controlled at 40mm. Depositing to obtain the vanadium dioxide film with the thickness of 20 nm.
(2) And mechanically stripping the tellurium-germanium-iron monocrystal by using a special mechanical stripping adhesive tape to obtain the tellurium-germanium-iron nanosheets with the thickness average of 30nm and the transverse dimension of 10 mu m.
(3) And transferring the stripped iron germanium tellurium nanosheets to a vanadium dioxide film, and coupling the two nanosheets together under the action of Van der Waals force to obtain the two-dimensional magnetic composite material.
(4) And (3) putting the transferred two-dimensional magnetic composite material into a SQUID instrument, measuring the external magnetic field to be 1000Oe, and measuring the magnetic change of the iron germanium tellurium nanosheets before and after the phase change of the vanadium dioxide film from the temperature range of 300K-360K.
As can be seen from comparative examples 1 and 3, the independent iron germanium tellurium nanoplatelets and the independent vanadium dioxide thin films have no magnetic properties or show weak ferromagnetism at room temperature; as is clear from comparative example 2, when the FeGeTe nanosheet is composited on the silicon oxide surface which cannot be spin-orbit coupled with FeGeTe, the magnetic properties of FeGeTe are not affected. After the iron germanium tellurium nanosheets are coupled with the vanadium dioxide film, as shown in fig. 6, the curve of the magnetization intensity of the two-dimensional magnetic composite material in the temperature range of 300-360K along with the temperature change can be seen, the Curie temperature of the iron germanium tellurium is effectively improved, the iron germanium tellurium shows stronger magnetic characteristics at room temperature and higher temperature, and the application prospect of the iron germanium tellurium material is widened. As shown in fig. 6 (a), in example 1, the magnetization of the two-dimensional magnetic composite material changes when the external magnetic field is 1000Oe and the temperature is 300-360K, and it can be seen that, at 300K, the ferrogermanium tellurium nanosheets without ferromagnetism and the weak ferromagnetic vanadium dioxide thin film are compounded to show a certain magnetization, and in the temperature range of 300-340K, the magnetization of the two-dimensional magnetic composite material shows an ascending trend, and keeps stable in the temperature range of 340-360K, and according to the trend that the magnetization of example 1 changes with the temperature, the regulation and control of the magnetism of the two-dimensional magnetic composite material can be realized by adjusting the temperature. As shown in fig. 6 (b), in the case of the two-dimensional magnetic composite material of comparative example 4, the magnetization intensity of the two-dimensional magnetic composite material was changed when the external magnetic field was 1000Oe and the temperature was 300 to 360K, and it was seen that the two-dimensional magnetic composite material of comparative example 4 had a certain magnetization intensity at the temperature of 300K, but the magnetization intensity was significantly lower than that of the two-dimensional magnetic composite material of example 1, and the magnetization intensity was decreased after the temperature was increased to more than 300K. This is because the oxygen pressure in the preparation of the vanadium dioxide thin film is relatively large and the oxygen vacancies in the formed vanadium dioxide thin film are relatively small in the preparation of the two-dimensional magnetic composite material of comparative example 4, which results in a decrease in the coupling capability of the vanadium dioxide thin film with the iron germanium tellurium nanoplatelets, a decrease in the spin coupling effect of the vanadium dioxide with the iron germanium tellurium, and the initial magnetic properties at 300K are correspondingly weaker than those of example 1. The stress effect on the surface iron germanium tellurium nanoplatelets is correspondingly reduced during the subsequent vanadium dioxide phase transition, and finally the neighbor effect is weakened, so that the magnetic property cannot be enhanced through phase transition stretching as in the embodiment 1. As shown in fig. 6 (c), in the case of the two-dimensional magnetic composite material of comparative example 5, the magnetization intensity of the two-dimensional magnetic composite material was changed when the applied magnetic field was 1000Oe and the temperature was 300 to 360K, it was found that the two-dimensional magnetic composite material of comparative example 5 had a certain magnetization intensity at the temperature of 300K, but the magnetization intensity was also significantly weaker than that of example 1, and the magnetization intensity showed a similar decrease trend to that of comparative example 4 after the temperature reached 300K or more. In the preparation process of the two-dimensional magnetic composite material of comparative example 5, the film forming temperature is relatively low, the formed vanadium dioxide film is poor in quality and uneven in thickness, which can cause the coupling capacity of the vanadium dioxide film to the surface iron germanium tellurium nano-sheets to be reduced, so that the initial magnetization intensity of the vanadium dioxide film at 300K is weaker than that of example 1, the stress effect of the vanadium dioxide film to the surface iron germanium tellurium nano-sheets during phase transition is reduced, the neighbor effect is weakened, the magnetic property is worse than that of example 1, and the magnetic property cannot be enhanced by phase transition stretching as in example 1. Meanwhile, when comparing example 1 with comparative examples 4 and 5, it was found that oxygen pressure and film forming temperature during the process of producing the vanadium dioxide film had a direct effect on the quality of the vanadium dioxide film, which determines the magnetic properties of the two-dimensional magnetic composite material. Among them, the film formation temperature of example 1 was 600℃and the oxygen pressure was 10mTorr. As shown in fig. 7, the magnetization-magnetic field strength plot at 300K and 340K was obtained for the two-dimensional magnetic composite of example 1. It can be seen that, compared with the curve of magnetization intensity along with temperature change at 300K, at 340K, namely, the phase transition temperature of vanadium dioxide from a monoclinic phase structure to a high-temperature tetragonal phase structure, the loop of the two-dimensional magnetic composite material along with the curve of temperature change is obviously increased, and hysteresis is obviously enhanced, namely, after vanadium dioxide is converted from monoclinic crystal to tetragonal crystal, the magnetization intensity of the iron-germanium-tellurium nanosheets is obviously increased under the stretching effect of neighbor effect, and magnetism is obviously enhanced.

Claims (5)

1. The magnetic controllable two-dimensional magnetic composite material is characterized by being formed by coupling a bottom lining layer and a magnetic layer, wherein the magnetic controllable two-dimensional magnetic composite material changes magnetism by adjusting temperature;
the magnetic layer is an iron germanium tellurium nanosheet;
the underlayer is a monoclinic crystal vanadium dioxide film which is weakly ferromagnetic at room temperature;
the manufacturing method of the two-dimensional magnetic composite material comprises the following steps:
(1) Depositing and preparing a bottom lining film on a substrate;
(2) Stripping the magnetic material crystal to obtain a magnetic layer nano sheet;
(3) Transferring the magnetic layer nano-sheet to the prepared underlayer film to form a two-dimensional magnetic composite material with the magnetic layer nano-sheet combined with the underlayer film;
the substrate in the step (1) is sapphire;
the underlayer film in the step (1) is obtained by a method of pulse laser deposition PLD, the film forming temperature of PLD is 600 ℃, and the oxygen pressure is 10mTorr.
2. The magnetically controllable two-dimensional magnetic composite of claim 1, wherein the underlayer has a thickness of 20-30 nm.
3. The magnetically controllable two-dimensional magnetic composite of claim 1, wherein the average thickness of the magnetic layer is 10-50 nm and the lateral dimension is 1-20 μm.
4. The magnetically controllable two-dimensional magnetic composite material according to claim 1, wherein in the step (1), the thickness of the sapphire substrate is 1-2 mm.
5. The magnetically controllable two-dimensional magnetic composite material according to claim 1, wherein in the step (1), the pulse wavelength is 248nm, the pulse width is 10-30 ns, the pulse repetition frequency is 1-20 hz, and the energy density is 2-4 j/cm 2 The distance from the pulsed laser target to the substrate is 40-50 mm.
CN202110816328.0A 2021-07-20 2021-07-20 Magnetic controllable two-dimensional magnetic composite material and preparation method thereof Active CN113667934B (en)

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