CN114551626A - Deep ultraviolet photoelectric detector and preparation method and application thereof - Google Patents
Deep ultraviolet photoelectric detector and preparation method and application thereof Download PDFInfo
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- boron nitride
- hexagonal boron
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- H01L31/09—Devices sensitive to infrared, visible or ultraviolet radiation
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Abstract
The invention provides a deep ultraviolet photoelectric detector and a preparation method and application thereof, belonging to the technical field of photoelectric detection. The deep ultraviolet photoelectric detector provided by the invention comprises a dielectric insulating substrate, a photosensitive layer arranged on the surface of the dielectric insulating substrate and two electrodes arranged at two opposite ends of the photosensitive layer; the photosensitive layer comprises a hexagonal boron nitride film and a surface plasmon structure attached to the surface of part of the hexagonal boron nitride film, the hexagonal boron nitride film is in contact with the dielectric insulating substrate, one electrode is arranged on the surface of the hexagonal boron nitride film to which the surface plasmon structure is not attached, and the other electrode is arranged on the surface of the hexagonal boron nitride film to which the surface plasmon structure is attached; the surface plasmon structure comprises a metal nanoparticle or a semiconductor nanostructure. The deep ultraviolet photoelectric detector provided by the invention has extremely low dark current and high responsivity to deep ultraviolet light.
Description
Technical Field
The invention relates to the technical field of photoelectric detection, in particular to a deep ultraviolet photoelectric detector and a preparation method and application thereof.
Background
Photon detection in a deep ultraviolet region (with the wavelength of 200-280 nm) is important in the fields of flame monitoring and detection, biomedicine, chemistry and environment monitoring, ultraviolet astronomy, inter-satellite communication and the like. The wide bandgap semiconductor material has excellent physicochemical properties, and thus has a wide prospect in high-frequency, high-temperature, high-power and short-wavelength applications. Hexagonal boron nitride is an ultra-wide bandgap semiconductor material, and has been proved to be an ideal candidate material for a deep ultraviolet photoelectric detector with daily blindness due to the characteristics of oxidation resistance, radiation resistance, capability of working at high temperature and in a severe environment, and difficulty in reaction with chemical substances. Furthermore, the wide band gap of hexagonal boron nitride (h-BN) greatly simplifies the design of the device by avoiding the sun suppression filter and additional cooling system, as compared to other conventional wide band gap semiconductors. In the current research, the deep ultraviolet photoelectric detector prepared based on the large-area high-quality hexagonal boron nitride two-dimensional atomic crystal film has good daily blindness, but the performance of most of the deep ultraviolet photoelectric detectors based on the hexagonal boron nitride film reported so far is still poor, and the problems of low deep ultraviolet responsivity and high dark current mainly exist.
Disclosure of Invention
The invention aims to provide a deep ultraviolet photoelectric detector, a preparation method and application thereof.
In order to achieve the above object, the present invention provides the following technical solutions:
the invention provides a deep ultraviolet photoelectric detector, which comprises a dielectric insulating substrate, a photosensitive layer arranged on the surface of the dielectric insulating substrate and two electrodes arranged at two opposite ends of the photosensitive layer;
the photosensitive layer comprises a hexagonal boron nitride film and a surface plasmon structure attached to the surface of part of the hexagonal boron nitride film, the hexagonal boron nitride film is in contact with the dielectric insulating substrate, one electrode is arranged on the surface of the hexagonal boron nitride film to which the surface plasmon structure is not attached, and the other electrode is arranged on the surface of the hexagonal boron nitride film to which the surface plasmon structure is attached;
the surface plasmon structure comprises a metal nanoparticle or a semiconductor nanostructure.
Preferably, the thickness of the hexagonal boron nitride film is 100-500 nm.
Preferably, the material of the metal nanoparticles comprises gold, aluminum, silver, copper or platinum.
Preferably, the particle size of the metal nanoparticles is 1-10 nm, and the distance between adjacent metal nanoparticles on the surface of the hexagonal boron nitride film is 25-150 nm.
Preferably, the semiconductor nanostructure comprises hexagonal boron nitride nanoplates.
Preferably, the lateral dimension of the hexagonal boron nitride nanosheet is 1-45 μm, and the thickness of the hexagonal boron nitride nanosheet is 0.3-2 μm; the distance between adjacent hexagonal boron nitride nanosheets on the surface of the hexagonal boron nitride film is 1-20 microns.
Preferably, the dielectric insulating substrate comprises a sapphire substrate, a quartz glass substrate or a silicon oxide substrate.
Preferably, the electrode is a metal electrode.
The invention provides a preparation method of the deep ultraviolet photoelectric detector in the technical scheme, which comprises the following steps:
depositing on the surface of a dielectric insulating substrate to obtain a hexagonal boron nitride film, preparing a surface plasmon structure on part of the surface of the hexagonal boron nitride film, and forming a photosensitive layer on the surface of the dielectric insulating substrate;
and arranging two electrodes at two opposite ends of the photosensitive layer, wherein one electrode is arranged on the surface of the hexagonal boron nitride film without the surface plasmon structure, and the other electrode is arranged on the surface of the hexagonal boron nitride film with the surface plasmon structure, so that the deep ultraviolet photoelectric detector is obtained.
The invention provides an application of the deep ultraviolet photoelectric detector in the technical scheme or the deep ultraviolet photoelectric detector prepared by the preparation method in the technical scheme in the fields of chemical environment monitoring, biological environment monitoring, missile plume, radiation detection, astronomical research or satellite communication.
The invention provides a deep ultraviolet photoelectric detector, which comprises a dielectric insulating substrate, a photosensitive layer arranged on the surface of the dielectric insulating substrate and two electrodes arranged at two opposite ends of the photosensitive layer; the photosensitive layer comprises a hexagonal boron nitride film and a surface plasmon structure attached to the surface of part of the hexagonal boron nitride film, the hexagonal boron nitride film is in contact with the dielectric insulating substrate, one electrode is arranged on the surface of the hexagonal boron nitride film to which the surface plasmon structure is not attached, and the other electrode is arranged on the surface of the hexagonal boron nitride film to which the surface plasmon structure is attached; the surface plasmon structure comprises a metal nanoparticle or a semiconductor nanostructure. According to the invention, metal nanoparticles or semiconductor nanostructures are used as surface plasmon structures, so that the surface plasmon structures have the characteristic of extremely strong local field enhancement, the surface plasmon structures and the hexagonal boron nitride film are compounded to be used as photosensitive layers, the deep ultraviolet photoelectric detector based on the photosensitive layers has extremely low dark current, high responsivity to deep ultraviolet light (especially extremely high responsivity to 205nm ultraviolet light), and excellent spectral selectivity to deep ultraviolet light, the light absorption in the wavelength range of the deep ultraviolet light (200-280 nm) is remarkably enhanced, and no light absorption exists in the visible light to near infrared region (400-800 nm), so that the problems of high dark current, low light absorption in the deep ultraviolet region and low responsivity of the traditional hexagonal boron nitride film deep ultraviolet photoelectric detector can be improved. In addition, the surface plasmon structure is only attached to part of the surface of the hexagonal boron nitride film, one electrode is arranged on the surface of the hexagonal boron nitride film without the surface plasmon structure, and the other electrode is arranged on the surface of the hexagonal boron nitride film with the surface plasmon structure, so that an asymmetric vertical structure is formed, and the photoelectric characteristic enhancement effect of the detector in a deep ultraviolet light region is favorably improved.
The invention adopts the hexagonal boron nitride film as the photosensitive material, compared with other traditional semiconductor (such as SiC) deep ultraviolet photoelectric detection devices, the device process is simplified, and additional filtering wave plates and cooling devices are not needed.
Drawings
Fig. 1 is a Scanning Electron Microscope (SEM) photograph of the photosensitive layer in the deep ultraviolet photodetector prepared in example 1;
fig. 2 is a schematic structural diagram of the deep ultraviolet photodetector prepared in example 1;
fig. 3 is a Scanning Electron Microscope (SEM) photograph of the photosensitive layer in the deep ultraviolet photodetector prepared in example 2;
fig. 4 is a schematic structural view of the deep ultraviolet photodetector manufactured in example 2;
FIG. 5 is an I-V plot of a deep UV photodetector of example 1 under dark conditions and 205nm UV illumination;
FIG. 6 is an I-V plot of a deep UV photodetector of example 2 under dark conditions and 205nm UV illumination;
FIG. 7 is an I-V plot of a deep UV photodetector of example 1 under dark conditions and 330nm UV illumination;
FIG. 8 is an I-V curve of the deep UV photodetector of example 2 under dark conditions and 330nm UV illumination;
FIG. 9 is a histogram of the responsivity of deep ultraviolet photodetectors prepared in example 1 and comparative example 1 under 205nm and 330nm ultraviolet light illumination;
FIG. 10 is a histogram of the responsivity of deep UV photodetectors prepared in example 2 and comparative example 1 under 205nm and 330nm UV illumination;
fig. 11 is a graph of the ultraviolet-visible absorption spectrum of the deep ultraviolet photodetectors prepared in examples 1 to 2 and comparative example 1 at room temperature.
Detailed Description
The invention provides a deep ultraviolet photoelectric detector, which comprises a dielectric insulating substrate, a photosensitive layer arranged on the surface of the dielectric insulating substrate and two electrodes arranged at two opposite ends of the photosensitive layer;
the photosensitive layer comprises a hexagonal boron nitride film and a surface plasmon structure attached to the surface of part of the hexagonal boron nitride film, the hexagonal boron nitride film is in contact with the dielectric insulating substrate, one electrode is arranged on the surface of the hexagonal boron nitride film to which the surface plasmon structure is not attached, and the other electrode is arranged on the surface of the hexagonal boron nitride film to which the surface plasmon structure is attached;
the surface plasmon structure comprises a metal nanoparticle or a semiconductor nanostructure.
The deep ultraviolet photoelectric detector provided by the invention comprises a dielectric insulating substrate. In the present invention, the dielectric insulating substrate preferably includes a sapphire substrate, a quartz glass substrate, or a silicon oxide substrate. In the invention, the thickness of the dielectric insulating substrate is preferably 300-700 μm, and more preferably 400-500 μm.
The deep ultraviolet photoelectric detector provided by the invention comprises a photosensitive layer arranged on the surface of a dielectric insulating substrate, wherein the photosensitive layer comprises a hexagonal boron nitride film and a surface plasmon structure attached to the surface of part of the hexagonal boron nitride film, and the hexagonal boron nitride film is in contact with the dielectric insulating substrate. In the invention, the thickness of the hexagonal boron nitride film is preferably 100-500 nm, and more preferably 100-200 nm. In the present invention, the surface plasmon structure includes a metal nanoparticle or a semiconductor nanostructure. In the present invention, the material of the metal nanoparticles preferably includes gold, aluminum, silver, copper or platinum, and more preferably gold; the particle size of the metal nanoparticles is preferably 1-10 nm, more preferably 6-10 nm, and further preferably 9-10 nm; the distance between adjacent metal nanoparticles on the surface of the hexagonal boron nitride film is preferably 25-150 nm, more preferably 30-50 nm, and further preferably 0-35 nm. In the invention, the semiconductor nano structure preferably comprises hexagonal boron nitride nano sheets, and the transverse size of the hexagonal boron nitride nano sheets is preferably 1-45 μm, and more preferably 1-5 μm; the thickness of the hexagonal boron nitride nanosheet is preferably 0.3-2 μm, and more preferably 0.3-1 μm; the distance between adjacent hexagonal boron nitride nanosheets on the surface of the hexagonal boron nitride film is preferably 1-20 microns, and more preferably 1-10 microns. In the present invention, the area of the hexagonal boron nitride film to which the surface plasmon structure is attached preferably accounts for at least 50% of the total area of the hexagonal boron nitride film.
The deep ultraviolet photoelectric detector provided by the invention comprises two electrodes arranged at two opposite ends of a photosensitive layer, wherein one electrode is arranged on the surface of the hexagonal boron nitride film without the surface plasmon structure, and the other electrode is arranged on the surface of the hexagonal boron nitride film with the surface plasmon structure, namely, the deep ultraviolet photoelectric detector provided by the invention is of an asymmetric structure. In the present invention, the electrodes are preferably strip-shaped electrodes. In the present invention, the electrode is preferably a metal electrode; the thickness of the metal electrode is preferably 80-120 nm, and more preferably 100-120 nm; the material of the metal electrode preferably comprises one or more of gold, silver, titanium, molybdenum and chromium, and the metal electrode more preferably is a gold/titanium electrode; the gold/titanium electrode preferably comprises a gold layer and a titanium layer which are arranged in a laminated mode, the thickness of the gold layer is 50-100 nm, the thickness of the titanium layer is preferably 10-20 nm, and the titanium layer is in contact with the photosensitive layer.
The invention provides a preparation method of the deep ultraviolet photoelectric detector in the technical scheme, which comprises the following steps:
depositing on the surface of a dielectric insulating substrate to obtain a hexagonal boron nitride film, preparing a surface plasmon structure on part of the surface of the hexagonal boron nitride film, and forming a photosensitive layer on the surface of the dielectric insulating substrate;
and arranging two electrodes at two opposite ends of the photosensitive layer, wherein one electrode is arranged on the surface of the hexagonal boron nitride film without the surface plasmon structure, and the other electrode is arranged on the surface of the hexagonal boron nitride film with the surface plasmon structure, so that the deep ultraviolet photoelectric detector is obtained.
According to the invention, a hexagonal boron nitride film is obtained by deposition on the surface of a dielectric insulating substrate, a surface plasmon structure is prepared on part of the surface of the hexagonal boron nitride film, and a photosensitive layer is formed on the surface of the dielectric insulating substrate. In the present invention, the dielectric insulating substrate is preferably subjected to a pretreatment before use, the pretreatment preferably comprising: and ultrasonic cleaning the dielectric insulating substrate by using acetone and deionized water in sequence, then soaking the dielectric insulating substrate in a mixed solution of hydrogen peroxide and sulfuric acid, taking out the dielectric insulating substrate, ultrasonic cleaning by using deionized water and ethanol in sequence, and finally drying by using nitrogen. In the invention, the time of ultrasonic cleaning for each time is preferably 5-8 min independently; the hydrogen peroxide is preferably analytically pure, the sulfuric acid is preferably analytically pure, and the volume ratio of the hydrogen peroxide to the sulfuric acid is preferably 1: 3; the soaking time is preferably 10-15 min.
In the invention, the preparation method of the hexagonal boron nitride film preferably comprises a chemical vapor deposition method or a physical vapor deposition method, the chemical vapor deposition method preferably comprises a radio frequency plasma chemical vapor deposition method, a microwave plasma enhanced chemical vapor deposition method or an induction coupled plasma chemical vapor deposition method, and the physical vapor deposition method preferably comprises a radio frequency magnetron sputtering method, an ion beam assisted sputtering deposition method or a laser deposition method. The invention preferably adopts an ion beam assisted sputtering deposition method to prepare the hexagonal boron nitride film, and the operation steps of the ion beam assisted sputtering deposition method preferably comprise: and (2) using a double-ion-beam auxiliary sputtering deposition system to vacuumize the film deposition chamber, heating the dielectric insulating substrate, then introducing a main ion source and an auxiliary ion source, adjusting the working pressure of the film deposition chamber, then opening a Kaufman ion source, adjusting the energy of the main ion source and the energy of the auxiliary ion source, performing deposition, and depositing on the surface of the dielectric insulating substrate to obtain the hexagonal boron nitride film. In the present invention, the evacuation treatment is preferably carried out by evacuating the thin film deposition chamber to a degree of vacuum of 2X 10-5Pa; the heating is preferably carried out to heat the temperature of the dielectric insulating substrate to 300-500 ℃; the main ion source is preferably argon, and the flow rate of the main ion source is preferably 6 sccm; the auxiliary ion source is preferably argon and nitrogen, the flow rate of the argon is preferably 2sccm, and the flow rate of the nitrogen is preferably 3 sccm; the working pressure of the film deposition chamber is preferably (3-5) multiplied by 10-2Pa; the main ion source energy is preferably 1250eV, and the auxiliary ion source energy is preferably 280 eV; the deposition time is preferably 2-8 h.
After the hexagonal boron nitride film is deposited on the surface of the dielectric insulating substrate, the surface plasmon structure is prepared on part of the surface of the hexagonal boron nitride film, and the photosensitive layer is formed on the surface of the dielectric insulating substrate. According to the invention, different preparation methods are preferably adopted according to different surface plasmon structures, and particularly, when the surface plasmon structure is a metal nanoparticle, the metal nanoparticle can be prepared by a self-assembly micelle method, a nanosphere photoetching method, a rapid thermal annealing method or a hydrothermal method; when the surface plasmon structure is a semiconductor nanostructure, such as further hexagonal boron nitride nanosheets, it may be prepared using a mechanical lift-off method, preferably including a tape lift-off method, a ball milling method, a plasma etching method or a fluid lift-off method, a chemical lift-off method, preferably including a liquid phase ultrasonic lift-off method, an ion insertion lift-off method or a chemical functionalization lift-off method, or a synthetic method, preferably including a chemical synthesis method, a hydrothermal synthesis method or a gas phase synthesis method. The following describes in detail the preparation methods of the gold nanoparticles, the hexagonal boron nitride nanosheets and the photosensitive layer, taking the surface plasmon structure as gold nanoparticles or hexagonal boron nitride nanosheets as an example.
In the present invention, when the surface plasmon structure is a gold nanoparticle, the method for preparing the gold nanoparticle and the photosensitive layer preferably includes the following steps:
dispersing a diblock copolymer, namely polystyrene-polyvinyl pyridine, in toluene to obtain a toluene solution of the polystyrene-polyvinyl pyridine; mixing gold-containing inorganic metal salt with the toluene solution of the polystyrene-polyvinyl pyridine to obtain a gold salt-loaded polystyrene-polyvinyl pyridine reverse micelle solution;
coating the gold salt-loaded polystyrene-polyvinyl pyridine reverse micelle solution on part of the surface of the hexagonal boron nitride film, reducing the gold salt-loaded polystyrene-polyvinyl pyridine reverse micelle solution in the gold salt-loaded polystyrene-polyvinyl pyridine reverse micelle solution to generate gold nanoparticles, and obtaining the photosensitive layer on the surface of the substrate.
The invention disperses diblock copolymer polystyrene-polyvinyl pyridine in toluene to obtain toluene solution of polystyrene-polyvinyl pyridine. In the present invention, the molecular weight of polystyrene in the diblock copolymer polystyrene-polyvinylpyridine is preferably 185000, and the molecular weight of polyvinylpyridine is preferably 90000; in the examples of the present invention, the purity of the diblock copolymer, polystyrene-polyvinylpyridine, was not less than 99.5%, and was purchased from Afahesa (China) chemical Co. In the invention, in the toluene solution of polystyrene-polyvinylpyridine, the concentration of polystyrene-polyvinylpyridine is preferably 5-25 mg/mL, and more preferably 5-10 mg/mL; the dispersing mode is preferably magnetic stirring, and the time of the magnetic stirring is preferably 3-7 days.
After the toluene solution of polystyrene-polyvinylpyridine is obtained, the gold-containing inorganic metal salt is mixed with the toluene solution of polystyrene-polyvinylpyridine to obtain the gold salt loaded polystyrene-polyvinylpyridine reverse micelle solution. In the present invention, the gold-containing inorganic metal salt is preferably HAuCl4The mass ratio of the gold-containing inorganic metal salt to the diblock copolymer polystyrene-polyvinyl pyridine is preferably (15-40): 50, more preferably (16-27): 50; the mixing mode is preferably magnetic stirring, and the time of the magnetic stirring is preferably 7-14 days.
After the gold salt-loaded polystyrene-polyvinyl pyridine reverse micelle solution is obtained, coating the gold salt-loaded polystyrene-polyvinyl pyridine reverse micelle solution on part of the surface of the hexagonal boron nitride film, reducing the gold salt-loaded polystyrene-polyvinyl pyridine reverse micelle solution in the gold salt-loaded polystyrene-polyvinyl pyridine reverse micelle solution to generate gold nanoparticles, and obtaining a photosensitive layer on the surface of the substrate; wherein the elements contained in the diblock copolymer polystyrene-polyvinylpyridine are C, H and N, and are reduced into corresponding gases in the reduction treatment process without remaining in the photosensitive layer; one end of the diblock copolymer polystyrene-polyvinyl pyridine is hydrophilic, and the other end of the diblock copolymer polystyrene-polyvinyl pyridine is hydrophobic, so that the polystyrene-polyvinyl pyridine reverse micelle solution loaded with the gold salt is ensured to be uniformly distributed on the surface of the substrate in the pulling process by utilizing the performance. In the present invention, the coating method preferably includes a drawing method, a spin coating method or a drop coating method, more preferably a drawing method; in the embodiment of the invention, a part of square boron nitride film is placed in the gold salt-loaded polystyrene-polyvinylpyridine reverse micelle solution, and the gold salt-loaded polystyrene-polyvinylpyridine reverse micelle solution is pulled on a part of hexagonal boron nitride film; the pulling speed is preferably 200-300 μm/s, and more preferably 234 μm/s. In the present invention, the method of reduction treatment preferably includes a hydrogen plasma treatment method, a hydrogen reduction method, or a high-temperature annealing method, more preferably a hydrogen reduction method; the operating conditions of the hydrogen reduction process include: the flow rate of the hydrogen is preferably 30-50 sccm, and more preferably 40-50 sccm; the temperature of the heat treatment is preferably 450-550 ℃, and more preferably 500 ℃; the time of the heat treatment is preferably 1 to 3 hours, and more preferably 2 hours.
In the present invention, when the surface plasmon structure is a hexagonal boron nitride nanosheet, the method for preparing the hexagonal boron nitride nanosheet and the photosensitive layer preferably includes the following steps:
mixing hexagonal boron nitride powder with potassium permanganate to obtain a solid mixed material; mixing sulfuric acid and phosphoric acid to obtain mixed acid; mixing the solid mixed material with mixed acid, and performing first chemical treatment under a heating condition to obtain a first chemical material; mixing the first chemical material with aqueous hydrogen peroxide, and performing second chemical treatment under the ice-water bath condition to obtain a second chemical material;
carrying out low-speed centrifugal separation on the second chemical material to obtain supernatant; alternately carrying out high-speed centrifugal washing on the supernatant by using deionized water and ethanol until the pH value is greater than 5, and drying a precipitate obtained after the high-speed centrifugal washing to obtain a hexagonal boron nitride nanosheet; the rotating speed of the low-speed centrifugal separation is 3000-5000 rpm, and the rotating speed of the high-speed centrifugal washing is 16000-20000 rpm;
dispersing the hexagonal boron nitride nanosheet in ethanol to obtain a hexagonal boron nitride nanosheet dispersion liquid; and coating the hexagonal boron nitride nanosheet dispersion liquid on part of the surface of the hexagonal boron nitride film, and volatilizing ethanol to obtain a photosensitive layer on the surface of the substrate.
According to the invention, hexagonal boron nitride powder and potassium permanganate are mixed to obtain a solid mixed material. In the invention, the granularity of the hexagonal boron nitride powder is preferably 1-45 μm; the mass ratio of the hexagonal boron nitride powder to the potassium permanganate is preferably 1: (2-6), more preferably 1: (5-6). In the examples of the present invention, the purity of the hexagonal boron nitride powder is not less than 99.5%, and is purchased from alfa aesar (china) chemical limited; the potassium permanganate is analytically pure and purchased from Beijing chemical reagent company.
The invention mixes sulfuric acid and phosphoric acid to obtain mixed acid. In the present invention, the sulfuric acid is preferably analytically pure, the phosphoric acid is preferably analytically pure, and the volume ratio of the sulfuric acid to the phosphoric acid is preferably 8: (1-2). In the examples of the present invention, the sulfuric acid and phosphoric acid are available from Beijing Chemicals, Inc.
After the solid mixed material and the mixed acid are obtained, the solid mixed material and the mixed acid are mixed, and first chemical treatment is carried out under the heating condition to obtain a first chemical material. In the invention, the dosage ratio of the solid mixed material to the mixed acid is preferably (3-7) g: (135-150) mL, more preferably (6-7) g: (135-140) mL. In the invention, the temperature of the first chemical treatment is preferably 70-78 ℃, and more preferably 74-75 ℃; the time is preferably 10-14 h, and more preferably 12 h; the first chemical treatment is preferably performed under stirring conditions. In the invention, in the first chemical treatment process, potassium permanganate reacts with sulfuric acid to generate manganese dioxide nanoparticles, and the manganese dioxide nanoparticles are inserted between boron nitride layers in hexagonal boron nitride powder (namely massive hexagonal boron nitride), so that the distance between the layers is increased, and stripping is conveniently carried out by the subsequent second chemical treatment.
After the first chemical material is obtained, the first chemical material is mixed with aqueous hydrogen peroxide, and second chemical treatment is carried out under the ice-water bath condition to obtain a second chemical material. In the invention, the aqueous hydrogen peroxide solution is preferably obtained by mixing analytically pure hydrogen peroxide and deionized water, and the volume ratio of the analytically pure hydrogen peroxide to the deionized water is preferably 1: (6-20), more preferably 1: (6-8). In the examples of the present invention, the analytically pure hydrogen peroxide is purchased from Beijing chemical reagent company. In the invention, the aqueous hydrogen peroxide solution is preferably subjected to refrigeration treatment before use, and the refrigeration temperature is preferably-5 ℃, and more preferably-5-0 ℃; the time is preferably 12 to 24 hours, and more preferably 12 to 15 hours. In the invention, the time of the second chemical treatment is preferably 1.5-2 h, and the second chemical treatment is preferably carried out under the condition of stirring. After the second chemical treatment, the present invention preferably cools the resulting suspension naturally to room temperature (25 ℃) to obtain a second chemical material. In the invention, in the second chemical treatment process, the manganese dioxide nanoparticles react with hydrogen peroxide to generate oxygen, and the release of the oxygen can realize the stripping of hexagonal boron nitride powder (i.e. blocky hexagonal boron nitride), so as to obtain the hexagonal boron nitride nanosheet.
Carrying out low-speed centrifugal separation on the second chemical material to obtain supernatant; alternately carrying out high-speed centrifugal washing on the supernatant by using deionized water and ethanol until the pH value is greater than 5, and drying a precipitate obtained after the high-speed centrifugal washing to obtain a hexagonal boron nitride nanosheet; the rotating speed of the low-speed centrifugal separation is 3000-5000 rpm, and the rotating speed of the high-speed centrifugal washing is 16000-20000 rpm. In the invention, the time of the low-speed centrifugal separation is preferably 10-15 min, and the time of each high-speed centrifugal washing is preferably 10-15 min.
After the hexagonal boron nitride nanosheet is obtained, dispersing the hexagonal boron nitride nanosheet in ethanol to obtain a hexagonal boron nitride nanosheet dispersion liquid; and coating the hexagonal boron nitride nanosheet dispersion liquid on part of the surface of the hexagonal boron nitride film, and volatilizing ethanol to obtain a photosensitive layer on the surface of the substrate. In the invention, the concentration of the hexagonal boron nitride nanosheet dispersion is preferably 0.01-0.05 mg/mL, and more preferably 0.01-0.03 mg/mL. In the present invention, the coating method preferably includes a drawing method, a spin coating method or a drop coating method, more preferably a drawing method; in the embodiment of the invention, a part of the hexagonal boron nitride film is placed in the hexagonal boron nitride nanosheet dispersion, and the hexagonal boron nitride nanosheet dispersion is pulled on the part of the hexagonal boron nitride film; the pulling rate is preferably 10 to 50 μm/s, and more preferably 15 to 20 μm/s.
After the photosensitive layer is obtained, two electrodes are arranged at two opposite ends of the photosensitive layer, wherein one electrode is arranged on the surface of the hexagonal boron nitride film without the surface plasmon structure, and the other electrode is arranged on the surface of the hexagonal boron nitride film with the surface plasmon structure, so that the deep ultraviolet photoelectric detector is obtained. The electrode is prepared by preferably adopting a magnetron sputtering method or an evaporation coating method; the specific operating conditions of the magnetron sputtering method and the evaporation coating method are not particularly limited, and the specific operation conditions can be selected according to the material and the thickness of the electrode.
The deep ultraviolet photoelectric detector provided by the invention is simple in preparation process, low in cost and suitable for large-scale production.
The invention provides an application of the deep ultraviolet photoelectric detector in the technical scheme or the deep ultraviolet photoelectric detector prepared by the preparation method in the technical scheme in the fields of chemical environment monitoring, biological environment monitoring, missile plume, radiation detection, astronomical research or satellite communication.
The technical solution of the present invention will be clearly and completely described below with reference to the embodiments of the present invention. It is to be understood that the described embodiments are merely exemplary of the invention, and not restrictive of the full scope of the invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
(1) Adding a mixture of massive hexagonal boron nitride bulk powder (granularity is 1-45 mu m, purity is more than or equal to 99.5%, Afahesa, 1g) and potassium permanganate (analytically pure, Beijing reagent, 6g) into an acidic mixture of sulfuric acid (analytically pure, Beijing reagent, 120mL) and phosphoric acid (analytically pure, Beijing reagent, 15mL), and stirring the obtained mixed material at 75 ℃ for 12h to obtain a first chemical material; mixing hydrogen peroxide (analytically pure, Beijing reagent, 18mL) and deionized water (120mL), refrigerating at-5 ℃ for 12h, mixing the obtained refrigerated solution with the first chemical material, stirring for 1.5h under the condition of ice-water bath, then removing the ice-water bath, and naturally cooling to room temperature (25 ℃) to obtain a second chemical material; and (3) carrying out centrifugal separation on the second chemical material for 15min at 3000rpm, alternately carrying out high-speed centrifugal washing on the obtained supernatant by using deionized water and ethanol at 20000rpm, wherein the time of each centrifugal washing is 15min until the pH value is more than 5, and then drying the precipitate obtained after the high-speed centrifugal washing to obtain hexagonal Boron Nitride Nanosheets (BNNSs), wherein the transverse dimension of the hexagonal boron nitride nanosheets is 1-5 microns, and the thickness of the hexagonal boron nitride nanosheets is 0.3-1 micron.
(2) Taking a quartz glass substrate (with the thickness of 400nm) as a dielectric insulating substrate, ultrasonically cleaning the quartz glass substrate for 5min by using acetone and deionized water in sequence, then soaking the quartz glass substrate in a mixed solution of hydrogen peroxide and sulfuric acid (the volume ratio of the hydrogen peroxide to the sulfuric acid is 1: 3) for 10min, then taking out the quartz glass substrate, ultrasonically cleaning the quartz glass substrate for 5min by using deionized water and ethanol in sequence, finally drying the quartz glass substrate by using nitrogen to obtain a pretreated substrate, and drying and storing the pretreated substrate;
the vacuum degree of the film deposition chamber is pumped to 2 multiplied by 10 by adopting a double ion beam auxiliary sputtering deposition system-5Pa, heating the pretreated substrate to 500 ℃, introducing 6sccm of argon gas of a main ion source, 2sccm of argon gas of an auxiliary ion source and 3sccm of nitrogen gas of the auxiliary ion source, and adjusting the working pressure of the thin film deposition chamber to 3 multiplied by 10-2Pa, then opening a Kaufman ion source, adjusting the energy of the main ion source to 1250eV, adjusting the energy of the auxiliary ion source to 280eV, depositing for 2h, and depositing on the surface of the substrate to obtain the hexagonal boron nitride film with the thickness of 200 nm.
(3) Uniformly dispersing the hexagonal boron nitride nanosheets into ethanol to enable the concentration of the hexagonal boron nitride nanosheets to be 0.01mg/mL, so as to obtain a hexagonal boron nitride nanosheet dispersion liquid; placing a part of the substrate deposited with the hexagonal boron nitride film in the hexagonal boron nitride nanosheet dispersion, pulling the hexagonal boron nitride nanosheet dispersion on the part of the hexagonal boron nitride film at a speed of 15 mu m/s, and obtaining a photosensitive layer on the surface of the substrate after ethanol is completely volatilized, wherein the photosensitive layer comprises the hexagonal boron nitride film and the hexagonal boron nitride nanosheets attached to the part of the surface of the hexagonal boron nitride film, the spacing distance between every two adjacent hexagonal boron nitride nanosheets is 1-10 mu m, and the area of the hexagonal boron nitride film attached with the hexagonal boron nitride nanosheets accounts for 50% of the total area of the hexagonal boron nitride film.
(4) And depositing at two opposite ends of the surface of the photosensitive layer by adopting a magnetron sputtering method to obtain two strip gold/titanium electrodes, wherein one strip gold/titanium electrode is deposited on the surface of the hexagonal boron nitride film without the hexagonal boron nitride nanosheets, the other strip gold/titanium electrode is deposited on the surface of the hexagonal boron nitride film with the hexagonal boron nitride nanosheets, the gold/titanium electrodes comprise a gold layer and a titanium layer which are arranged in a laminated manner, the thickness of the gold layer is 100nm, the thickness of the titanium layer is 20nm, and the titanium layer is in contact with the photosensitive layer to obtain the deep ultraviolet photoelectric detector (h-BN/BNNSs).
Fig. 1 is a Scanning Electron Microscope (SEM) photograph of the photosensitive layer in the deep ultraviolet photodetector prepared in example 1, and it can be seen that hexagonal boron nitride nanosheets have been composited on the hexagonal boron nitride thin film.
Fig. 2 is a schematic structural diagram of the deep ultraviolet photodetector prepared in embodiment 1, which includes a substrate, a photosensitive layer disposed on a surface of the substrate, and two strip-shaped gold/titanium electrodes disposed at two opposite ends of the photosensitive layer, where the photosensitive layer includes a hexagonal boron nitride thin film and a hexagonal boron nitride nanosheet attached to a partial surface of the hexagonal boron nitride thin film, one of the strip-shaped gold/titanium electrodes is disposed on a surface of the hexagonal boron nitride thin film to which the hexagonal boron nitride nanosheet is not attached, and the other strip-shaped gold/titanium electrode is disposed on a surface of the hexagonal boron nitride thin film to which the hexagonal boron nitride nanosheet is attached, that is, the deep ultraviolet photodetector provided by the present invention has an asymmetric structure.
Example 2
(1) Dispersing 50mg of diblock copolymer polystyrene-polyvinylpyridine (purity is more than or equal to 99.95 percent, alfa aesar; molecular weight of polystyrene in the diblock copolymer polystyrene-polyvinylpyridine is 185000, molecular weight of polyvinylpyridine is 90000) in 10mL of toluene, and magnetically stirring for 7 days to completely dissolve the polystyrene-polyvinylpyridine to obtain the polystyrene-polyvinylpyridine suspensionTo a toluene solution of polystyrene-polyvinylpyridine; 26mg of HAuCl4Adding the solution into a toluene solution of polystyrene-polyvinyl pyridine, and magnetically stirring for 7 days to obtain a gold salt-loaded polystyrene-polyvinyl pyridine reverse micelle solution.
(2) The quartz glass substrate was pretreated in the same manner as in the step (2) in example 1, and then deposited on the surface of the substrate to obtain a hexagonal boron nitride film having a thickness of 200 nm.
(3) Placing a part of the substrate deposited with the hexagonal boron nitride film in the polystyrene-polyvinyl pyridine reverse micelle solution loaded with the gold salt, pulling the gold salt-loaded polystyrene-polyvinyl pyridine reverse micelle solution on part of the hexagonal boron nitride film at the speed of 234 mu m/s, then heating for 2h in a hydrogen environment of 50sccm at 500 ℃, reducing the polystyrene-polyvinylpyridine reverse micelle loaded with the gold salt on the hexagonal boron nitride film to generate gold nanoparticles (AuNPs), obtaining a photosensitive layer on the surface of the substrate, wherein the photosensitive layer comprises a hexagonal boron nitride film and gold nanoparticles attached to the surface of part of the hexagonal boron nitride film, the particle size of the gold nanoparticles is 9-10 nm, the spacing distance between adjacent gold nanoparticles is 30-35 nm, and the area of the hexagonal boron nitride film attached with the gold nanoparticles accounts for 50% of the total area of the hexagonal boron nitride film.
(4) And depositing at two opposite ends of the surface of the photosensitive layer by adopting a magnetron sputtering method to obtain two strip gold/titanium electrodes, wherein one strip gold/titanium electrode is deposited on the surface of the hexagonal boron nitride film without the gold nanoparticles, the other strip gold/titanium electrode is deposited on the surface of the hexagonal boron nitride film with the gold nanoparticles, the gold/titanium electrodes comprise a gold layer and a titanium layer which are arranged in a laminated manner, the thickness of the gold layer is 100nm, the thickness of the titanium layer is 20nm, and the titanium layer is in contact with the photosensitive layer to obtain the deep ultraviolet photodetector (h-BN/AuNPs).
Fig. 3 is a Scanning Electron Microscope (SEM) photograph of the photosensitive layer in the deep ultraviolet photodetector prepared in example 2, which shows that the gold nanoparticles are uniformly compounded on the hexagonal boron nitride film.
Fig. 4 is a schematic structural diagram of the deep ultraviolet photodetector prepared in embodiment 2, which includes a substrate, a photosensitive layer disposed on a surface of the substrate, and two strip-shaped gold/titanium electrodes disposed at two opposite ends of the photosensitive layer, where the photosensitive layer includes a hexagonal boron nitride film and gold nanoparticles attached to a part of a surface of the hexagonal boron nitride film, one of the strip-shaped gold/titanium electrodes is disposed on a surface of the hexagonal boron nitride film to which no gold nanoparticles are attached, and the other strip-shaped gold/titanium electrode is disposed on a surface of the hexagonal boron nitride film to which gold nanoparticles are attached, that is, the deep ultraviolet photodetector provided in the present invention has an asymmetric structure.
Comparative example 1
Pretreating a quartz glass substrate according to the method in the step (2) in the embodiment 1, and then depositing on the surface of the substrate to obtain a hexagonal boron nitride film with the thickness of 200 nm;
and depositing two strip gold/titanium electrodes at two opposite ends of the surface of the hexagonal boron nitride film by adopting a magnetron sputtering method, wherein the gold/titanium electrodes comprise a gold layer and a titanium layer which are arranged in a laminated manner, the thickness of the gold layer is 100nm, the thickness of the titanium layer is 20nm, and the titanium layer is in contact with the hexagonal boron nitride film to obtain the deep ultraviolet photoelectric detector.
And (3) performance testing:
1. the performance of the deep ultraviolet photodetectors prepared in examples 1-2 was tested under dark conditions and 205nm ultraviolet irradiation, respectively, under ± 35V voltage conditions using a gishy 2450 digital source meter, and the obtained I-V curves are shown in fig. 5 and 6. FIG. 5 is an I-V plot of the deep UV photodetector of example 1 under dark conditions and 205nm UV illumination, showing that the device has a very low photoresponse when a forward voltage is applied; when a negative voltage is applied, the optical response of the device increases with the increase of the voltage, and when a voltage of-35V is applied, the dark current of the device is-8.87 multiplied by 10-8Ampere, current under 205nm excitation is-1.47X 10-7Ampere, indicating that the device has good photoresponse characteristics. FIG. 6 is an I-V plot of the deep UV photodetector of example 2 under dark conditions and 205nm UV illumination, showing that the device has a very small photoresponse when a negative voltage is applied; when a forward voltage is applied, the optical response of the device increases with the voltageLarge and increased, and dark current of the device is +7.06 × 10 when +35V voltage is applied-8Ampere, current at 205nm excitation + 1.77X 10-7Ampere, indicating that the device has good photoresponse characteristics.
2. The performance of the deep ultraviolet photodetectors prepared in examples 1-2 was tested under dark conditions and 330nm ultraviolet irradiation, respectively, under ± 35V voltage conditions using a gishy 2450 digital source meter, and the obtained I-V curves are shown in fig. 7 and 8. FIG. 7 is an I-V plot of the deep UV photodetector of example 1 under dark conditions and 330nm UV illumination, showing that the device has a very low photoresponse when a forward voltage is applied; when a negative voltage is applied, the optical response of the device increases with the increase of the voltage, and when a voltage of-35V is applied, the dark current of the device is-8.87 multiplied by 10-8Ampere, current under 330nm excitation is-1.55X 10-7Ampere, indicating that the device has good photoresponse characteristics. FIG. 8 is an I-V plot of the deep UV photodetector of example 2 under dark conditions and 330nm UV illumination, showing that the device has a very small photoresponse when a negative voltage is applied; when a forward voltage is applied, the optical response of the device increases with the increase of the voltage, and when a voltage of +35V is applied, the dark current of the device is +7.06 × 10-8Ampere, current at 330nm excitation + 1.19X 10-7Ampere, indicating that the device has good photoresponse characteristics.
3. The performance of the deep ultraviolet photodetectors prepared in examples 1-2 and comparative example 1 was tested under the conditions of 205nm (power density of 0.019 watt per square centimeter) and 330nm (power density of 0.044 watt per square centimeter) ultraviolet irradiation with an applied voltage of ± 35V and an illumination area of 0.25 square centimeter using a gicherie 2450 digital source meter, and the obtained responsivity histograms were shown in fig. 9 and 10. Fig. 9 is a histogram of responsivity of the deep ultraviolet photodetectors prepared in example 1 and comparative example 1 under the irradiation of ultraviolet light at 205nm and 330nm, and the specific data are shown in table 1. The results show that the photoresponse intensity of the device prepared in example 1 is 1.24 × 10 under 205nm uv irradiation-5Ampere/watt, much higher than the photoresponse intensity of the device in comparative example 1 (3.86X 10)-7Ampere/watt). Devices prepared in example 1 under 330nm UV irradiationHas a photoresponse intensity of 6.00X 10-6Ampere/watt which is less than the light response intensity under the irradiation of 205nm ultraviolet light, and indicates that the response wave band of the device is in a deep ultraviolet region; furthermore, the intensity of the photoresponse of the device of example 1 is much higher than that of the device of comparative example 1 (8.49X 10) at an excitation wavelength of 330nm-7Ampere/watt). Fig. 10 is a histogram of the responsivity of the deep ultraviolet photodetectors prepared in example 2 and comparative example 1 under the irradiation of ultraviolet light at 205nm and 330nm, and the specific data are shown in table 1. The results show that the photoresponse intensity of the device prepared in example 2 is 2.24X 10 under 205nm UV irradiation-5Ampere/watt, much higher than the photoresponse intensity of the device in comparative example 1 (3.86X 10)-7Ampere/watt). The photoresponse intensity of the device prepared in example 2 was 4.35X 10 under 330nm UV irradiation-6Ampere/watt which is less than the light response intensity under the irradiation of 205nm ultraviolet light, and indicates that the response wave band of the device is in a deep ultraviolet region; furthermore, the intensity of the photoresponse of the device of example 2 is much higher than that of the device of comparative example 1 at an excitation wavelength of 330nm (8.49X 10)-7Ampere/watt).
TABLE 1 photoresponse intensities of devices of examples 1-2 and comparative example 1 at different excitation wavelengths
As can be seen from fig. 9 and 10 and table 1, the dark current of the deep ultraviolet photodetector without the metal nanoparticles and the boron nitride nanosheets as the surface plasmon structure is large, and the responsivity to ultraviolet light is extremely low; the dark current of the deep ultraviolet photoelectric detector with the metal nano-particles and the boron nitride nano-sheets as the surface plasmon structure is reduced, and the responsivity is greatly improved.
4. The performance of the deep ultraviolet photodetectors prepared in examples 1-2 and comparative example 1 was tested at room temperature using a UNICO UV-2802S ultraviolet-visible absorption spectrometer, and fig. 11 is an ultraviolet-visible absorption spectrum diagram of the deep ultraviolet photodetectors prepared in examples 1-2 and comparative example 1 at room temperature, from fig. 11, it can be seen that the deep ultraviolet photodetectors prepared in examples 1-2 and comparative example 1 have excellent spectral selectivity to deep ultraviolet light, and do not absorb light in the visible to near infrared region (400-800 nm). Meanwhile, the light absorption of the deep ultraviolet photoelectric detector prepared in the embodiment 2 in the range of the deep ultraviolet wavelength (200-280 nm) is obviously enhanced.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
Claims (10)
1. A deep ultraviolet photoelectric detector comprises a dielectric insulating substrate, a photosensitive layer arranged on the surface of the dielectric insulating substrate, and two electrodes arranged at two opposite ends of the photosensitive layer;
the photosensitive layer comprises a hexagonal boron nitride film and a surface plasmon structure attached to the surface of part of the hexagonal boron nitride film, the hexagonal boron nitride film is in contact with the dielectric insulating substrate, one electrode is arranged on the surface of the hexagonal boron nitride film to which the surface plasmon structure is not attached, and the other electrode is arranged on the surface of the hexagonal boron nitride film to which the surface plasmon structure is attached;
the surface plasmon structure comprises a metal nanoparticle or a semiconductor nanostructure.
2. The deep ultraviolet photodetector of claim 1, wherein the hexagonal boron nitride film has a thickness of 100 to 500 nm.
3. The deep ultraviolet photodetector of claim 1, wherein the metal nanoparticles comprise gold, aluminum, silver, copper, or platinum.
4. The deep ultraviolet photodetector according to claim 1 or 3, wherein the metal nanoparticles have a particle size of 1 to 10nm, and the distance between adjacent metal nanoparticles on the surface of the hexagonal boron nitride thin film is 25 to 150 nm.
5. The deep ultraviolet photodetector of claim 1, wherein the semiconductor nanostructure comprises hexagonal boron nitride nanoplates.
6. The deep ultraviolet photodetector of claim 5, wherein the hexagonal boron nitride nanosheets have a lateral dimension of 1-45 μ ι η and a thickness of 0.3-2 μ ι η; the distance between adjacent hexagonal boron nitride nanosheets on the surface of the hexagonal boron nitride film is 1-20 microns.
7. The deep ultraviolet photodetector of claim 1, wherein the dielectric insulating substrate comprises a sapphire substrate, a quartz glass substrate, or a silicon oxide substrate.
8. The deep ultraviolet photodetector of claim 1, wherein the electrode is a metal electrode.
9. The method for preparing the deep ultraviolet photodetector as claimed in any one of claims 1 to 8, comprising the steps of:
depositing on the surface of a dielectric insulating substrate to obtain a hexagonal boron nitride film, preparing a surface plasmon structure on part of the surface of the hexagonal boron nitride film, and forming a photosensitive layer on the surface of the dielectric insulating substrate;
and arranging two electrodes at two opposite ends of the photosensitive layer, wherein one electrode is arranged on the surface of the hexagonal boron nitride film without the surface plasmon structure, and the other electrode is arranged on the surface of the hexagonal boron nitride film with the surface plasmon structure, so that the deep ultraviolet photoelectric detector is obtained.
10. The deep ultraviolet photodetector according to any one of claims 1 to 8 or the deep ultraviolet photodetector prepared by the preparation method according to claim 9 is applied to the fields of chemical environment monitoring, biological environment monitoring, missile plume, radiation detection, astronomical research or satellite communication.
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