WO2007148802A1 - 酸化亜鉛系半導体結晶の製造方法 - Google Patents
酸化亜鉛系半導体結晶の製造方法 Download PDFInfo
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- WO2007148802A1 WO2007148802A1 PCT/JP2007/062634 JP2007062634W WO2007148802A1 WO 2007148802 A1 WO2007148802 A1 WO 2007148802A1 JP 2007062634 W JP2007062634 W JP 2007062634W WO 2007148802 A1 WO2007148802 A1 WO 2007148802A1
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- Prior art keywords
- semiconductor crystal
- zno
- crystal
- based semiconductor
- zinc oxide
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- XLOMVQKBTHCTTD-UHFFFAOYSA-N Zinc monoxide Chemical compound [Zn]=O XLOMVQKBTHCTTD-UHFFFAOYSA-N 0.000 title claims abstract description 378
- 239000013078 crystal Substances 0.000 title claims abstract description 238
- 239000011787 zinc oxide Substances 0.000 title claims abstract description 189
- 239000004065 semiconductor Substances 0.000 title claims abstract description 76
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 45
- 239000000758 substrate Substances 0.000 claims abstract description 106
- 239000011701 zinc Substances 0.000 claims abstract description 98
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 20
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 16
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 4
- 239000001301 oxygen Substances 0.000 claims abstract description 4
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims abstract 6
- 229910052733 gallium Inorganic materials 0.000 claims description 8
- 239000011777 magnesium Substances 0.000 claims description 8
- 239000011734 sodium Substances 0.000 claims description 8
- 229910052782 aluminium Inorganic materials 0.000 claims description 7
- 229910052785 arsenic Inorganic materials 0.000 claims description 7
- 229910052793 cadmium Inorganic materials 0.000 claims description 7
- 229910052739 hydrogen Inorganic materials 0.000 claims description 7
- 229910052738 indium Inorganic materials 0.000 claims description 7
- 229910052744 lithium Inorganic materials 0.000 claims description 7
- 229910052749 magnesium Inorganic materials 0.000 claims description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims description 7
- 229910052700 potassium Inorganic materials 0.000 claims description 7
- 239000011669 selenium Substances 0.000 claims description 7
- 229910052708 sodium Inorganic materials 0.000 claims description 7
- 229910052717 sulfur Inorganic materials 0.000 claims description 7
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 6
- 229910052711 selenium Inorganic materials 0.000 claims description 6
- 229910052714 tellurium Inorganic materials 0.000 claims description 6
- 229910052796 boron Inorganic materials 0.000 claims description 5
- GYHNNYVSQQEPJS-UHFFFAOYSA-N Gallium Chemical compound [Ga] GYHNNYVSQQEPJS-UHFFFAOYSA-N 0.000 claims description 4
- DGAQECJNVWCQMB-PUAWFVPOSA-M Ilexoside XXIX Chemical compound C[C@@H]1CC[C@@]2(CC[C@@]3(C(=CC[C@H]4[C@]3(CC[C@@H]5[C@@]4(CC[C@@H](C5(C)C)OS(=O)(=O)[O-])C)C)[C@@H]2[C@]1(C)O)C)C(=O)O[C@H]6[C@@H]([C@H]([C@@H]([C@H](O6)CO)O)O)O.[Na+] DGAQECJNVWCQMB-PUAWFVPOSA-M 0.000 claims description 3
- WHXSMMKQMYFTQS-UHFFFAOYSA-N Lithium Chemical compound [Li] WHXSMMKQMYFTQS-UHFFFAOYSA-N 0.000 claims description 3
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 3
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 3
- ZLMJMSJWJFRBEC-UHFFFAOYSA-N Potassium Chemical compound [K] ZLMJMSJWJFRBEC-UHFFFAOYSA-N 0.000 claims description 3
- BUGBHKTXTAQXES-UHFFFAOYSA-N Selenium Chemical compound [Se] BUGBHKTXTAQXES-UHFFFAOYSA-N 0.000 claims description 3
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 claims description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 3
- RQNWIZPPADIBDY-UHFFFAOYSA-N arsenic atom Chemical compound [As] RQNWIZPPADIBDY-UHFFFAOYSA-N 0.000 claims description 3
- BDOSMKKIYDKNTQ-UHFFFAOYSA-N cadmium atom Chemical compound [Cd] BDOSMKKIYDKNTQ-UHFFFAOYSA-N 0.000 claims description 3
- 239000001257 hydrogen Substances 0.000 claims description 3
- APFVFJFRJDLVQX-UHFFFAOYSA-N indium atom Chemical compound [In] APFVFJFRJDLVQX-UHFFFAOYSA-N 0.000 claims description 3
- 239000011574 phosphorus Substances 0.000 claims description 3
- 239000011591 potassium Substances 0.000 claims description 3
- 239000011593 sulfur Substances 0.000 claims description 3
- PORWMNRCUJJQNO-UHFFFAOYSA-N tellurium atom Chemical compound [Te] PORWMNRCUJJQNO-UHFFFAOYSA-N 0.000 claims description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims 2
- 125000004435 hydrogen atom Chemical class [H]* 0.000 claims 2
- 238000000034 method Methods 0.000 abstract description 25
- 239000012535 impurity Substances 0.000 abstract description 12
- 230000004907 flux Effects 0.000 description 33
- 229910052594 sapphire Inorganic materials 0.000 description 31
- 239000010980 sapphire Substances 0.000 description 31
- 230000007246 mechanism Effects 0.000 description 21
- 239000007789 gas Substances 0.000 description 20
- 230000000052 comparative effect Effects 0.000 description 18
- 238000005259 measurement Methods 0.000 description 17
- 238000000151 deposition Methods 0.000 description 16
- 230000008021 deposition Effects 0.000 description 16
- 239000010408 film Substances 0.000 description 13
- 238000002441 X-ray diffraction Methods 0.000 description 10
- 238000004140 cleaning Methods 0.000 description 9
- 238000001451 molecular beam epitaxy Methods 0.000 description 8
- 238000010586 diagram Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 239000007787 solid Substances 0.000 description 7
- 230000001133 acceleration Effects 0.000 description 6
- 238000002109 crystal growth method Methods 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 5
- 230000008569 process Effects 0.000 description 5
- 239000002994 raw material Substances 0.000 description 5
- 230000005012 migration Effects 0.000 description 4
- 238000013508 migration Methods 0.000 description 4
- 239000010409 thin film Substances 0.000 description 3
- 125000004429 atom Chemical group 0.000 description 2
- 239000011521 glass Substances 0.000 description 2
- 239000012212 insulator Substances 0.000 description 2
- 150000002500 ions Chemical class 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 150000004767 nitrides Chemical class 0.000 description 2
- -1 scandium aluminum magnesium Chemical compound 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 238000005411 Van der Waals force Methods 0.000 description 1
- VZPPHXVFMVZRTE-UHFFFAOYSA-N [Kr]F Chemical compound [Kr]F VZPPHXVFMVZRTE-UHFFFAOYSA-N 0.000 description 1
- WTKQDILJIUYBGG-UHFFFAOYSA-N aluminum;magnesium;oxygen(2-);scandium(3+) Chemical compound [O-2].[O-2].[O-2].[O-2].[Mg+2].[Al+3].[Sc+3] WTKQDILJIUYBGG-UHFFFAOYSA-N 0.000 description 1
- UXGVVDQWNOCWMA-UHFFFAOYSA-N aluminum;oxygen(2-);scandium(3+) Chemical compound [O-2].[O-2].[O-2].[Al+3].[Sc+3] UXGVVDQWNOCWMA-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 125000005842 heteroatom Chemical group 0.000 description 1
- 238000010884 ion-beam technique Methods 0.000 description 1
- PNHVEGMHOXTHMW-UHFFFAOYSA-N magnesium;zinc;oxygen(2-) Chemical compound [O-2].[O-2].[Mg+2].[Zn+2] PNHVEGMHOXTHMW-UHFFFAOYSA-N 0.000 description 1
- 238000005036 potential barrier Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- JBQYATWDVHIOAR-UHFFFAOYSA-N tellanylidenegermanium Chemical compound [Te]=[Ge] JBQYATWDVHIOAR-UHFFFAOYSA-N 0.000 description 1
- UMJICYDOGPFMOB-UHFFFAOYSA-N zinc;cadmium(2+);oxygen(2-) Chemical compound [O-2].[O-2].[Zn+2].[Cd+2] UMJICYDOGPFMOB-UHFFFAOYSA-N 0.000 description 1
Classifications
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L21/00—Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
- H01L21/04—Manufacture or treatment of semiconductor devices or of parts thereof the devices having potential barriers, e.g. a PN junction, depletion layer or carrier concentration layer
- H01L21/34—Manufacture or treatment of semiconductor devices or of parts thereof the devices having potential barriers, e.g. a PN junction, depletion layer or carrier concentration layer the devices having semiconductor bodies not provided for in groups H01L21/0405, H01L21/0445, H01L21/06, H01L21/16 and H01L21/18 with or without impurities, e.g. doping materials
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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
- C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
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- C23C14/086—Oxides of zinc, germanium, cadmium, indium, tin, thallium or bismuth
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- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
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- C23C14/08—Oxides
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- 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
- C23C14/32—Vacuum evaporation by explosion; by evaporation and subsequent ionisation of the vapours, e.g. ion-plating
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- 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
- C23C14/34—Sputtering
- C23C14/46—Sputtering by ion beam produced by an external ion source
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- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B23/00—Single-crystal growth by condensing evaporated or sublimed materials
- C30B23/02—Epitaxial-layer growth
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- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B23/00—Single-crystal growth by condensing evaporated or sublimed materials
- C30B23/02—Epitaxial-layer growth
- C30B23/08—Epitaxial-layer growth by condensing ionised vapours
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- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/10—Inorganic compounds or compositions
- C30B29/16—Oxides
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- H01L21/02365—Forming inorganic semiconducting materials on a substrate
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- H01L21/0237—Materials
- H01L21/024—Group 12/16 materials
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- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
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- H01L21/02365—Forming inorganic semiconducting materials on a substrate
- H01L21/02367—Substrates
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- H01L21/0242—Crystalline insulating materials
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- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
- H01L21/02104—Forming layers
- H01L21/02365—Forming inorganic semiconducting materials on a substrate
- H01L21/02436—Intermediate layers between substrates and deposited layers
- H01L21/02439—Materials
- H01L21/02469—Group 12/16 materials
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- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
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- H01L21/02365—Forming inorganic semiconducting materials on a substrate
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- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
- H01L21/02104—Forming layers
- H01L21/02365—Forming inorganic semiconducting materials on a substrate
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- H01L21/02565—Oxide semiconducting materials not being Group 12/16 materials, e.g. ternary compounds
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- H01L21/02365—Forming inorganic semiconducting materials on a substrate
- H01L21/02612—Formation types
- H01L21/02617—Deposition types
- H01L21/02631—Physical deposition at reduced pressure, e.g. MBE, sputtering, evaporation
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Definitions
- the present invention relates to an acid-zinc-based semiconductor capable of growing an acid-zinc-based semiconductor crystal having excellent surface flatness and crystallinity with a high crystal growth rate and extremely low impurities in the crystal.
- the present invention relates to a method for manufacturing a semiconductor crystal.
- Oxide-zinc (hereinafter referred to as ZnO) -based semiconductor crystals are attracting attention as a new crystal material that can be substituted for a V-group nitride semiconductor crystal used for blue light-emitting elements and ultraviolet light-emitting elements.
- ZnO-based semiconductor crystals are doped with non-doped ZnO, mixed crystals based on ZnO such as zinc magnesium oxide (ZnMgO) and zinc cadmium oxide (ZnCdO), and gallium (Ga) Nitride (N). ZnO having a specific conductivity or a mixed crystal based on ZnO is included.
- the ZnO-based semiconductor crystal is required to have excellent surface flatness and crystallinity.
- Non-Patent Document 1 a laser molecular beam epitaxy (laser MBE) apparatus is used and a non-doped ZnO semiconductor crystal (hereinafter simply abbreviated as ZnO crystal) at a very high V and crystal growth temperature (substrate temperature). Is described as growing. More specifically, the raw material ZnO sintered body was ablated with a krypton fluoride (KrF) excimer laser and reached the surface of a substrate heated to 800 ° C (in non-patent document 1, scandium aluminum magnesium oxide substrate). As a result, a ZnO crystal with excellent surface flatness and crystallinity has been realized.
- KrF krypton fluoride
- Non-Patent Document 2 A general ZnO crystal growth method by the MBE method is disclosed in Non-Patent Document 2, for example.
- a Knudsen cell filled with solid zinc (Zn) by heating a Knudsen cell filled with solid zinc (Zn), a part of the solid Zn is vaporized to reach the surface of the substrate (in the non-patent document 2, the sapphire substrate).
- This MBE method uses extremely high purity solid Zn and O gas as raw materials.
- a ZnO crystal is generally grown at a crystal growth temperature of about 600 to 700 ° C. (600 ° C. in Non-Patent Document 2).
- Non-Patent Document 3 A general ZnO crystal growth method by the R-ICB method is disclosed in Non-Patent Document 3, for example.
- the solid Zn filled in the crucible is heated to vaporize a part of the solid Zn to form a Zn cluster (a state in which a plurality of Zns are combined by van der Waals force).
- Part or all of the Zn clusters are ionized (Zn +) to reach the surface of the substrate (in Non-Patent Document 3, a glass substrate or a sapphire substrate), and O gas is supplied through a path for ionizing the Zn clusters. , A part of this O gas
- the ZnO crystal is grown by allowing Zn (Zn + ) clusters to react with 0 (0_) on the substrate surface by being turned on (0_) and reaching the substrate surface.
- Zn clusters and O are ionized to reach the substrate surface, thereby improving their surface migration (migration) effect. Therefore, the R-ICB method has relatively low crystallinity even at low crystal growth temperatures. Good, it can grow ZnO crystal.
- Non-patent literature 1 A. Tsukaza i et al., 'Layer-by-layer growth of high-optical-quality ZnO film on atomically smooth and lattice relaxed ZnO buffer layer Appl. Phys. Lett., 83 (2003), pp. 2784-2786
- Non-Patent Document 2 K. Nakahara et al., "Growth of Undoped ZnO Films with Improved Electrical Properties by Radical Source Molecular Beam Epitaxy" jpn. J. Appl. Phys., 4 0 (2001), pp. 250-254
- Non-Patent Document 3 K. Matsubara et al, "PROPERTIES OF ZnO FILMS PREPARED BY REACTIVE IONIZED CLUSTER BEAM DEPOSITION" Surface Science, 86 (1979), pp. 290-299
- Non-Patent Document 1 in the method of growing ZnO crystals, the impurity force contained in the ZnO sintered body as a raw material is almost directly incorporated into the grown ZnO crystals. If the grown ZnO crystal contains many impurities, there is a problem.
- the crystal growth temperature is relatively low at 600 to 700 ° C, so that a table of levels required for realizing a light-emitting element is obtained. It is difficult to obtain surface flatness and crystallinity.
- the crystal growth temperature is low !, the Zn that has reached the substrate surface is not sufficiently migrated, and as a result, the crystal tends to grow three-dimensionally. Since the crystal grown three-dimensionally in this way is an aggregate of grains (grains), the flatness of the crystal surface is rough. In addition, such crystals generally have low crystallinity.
- As a method for improving surface flatness and crystallinity in this MBE method as disclosed in Non-Patent Document 1, it is possible to easily grow at a high crystal growth temperature. Because the vapor pressure of the raw materials Zn and O (O) is high,
- Non-Patent Document 3 since the crystal growth temperature force is very low, S300 ° C or less, the surface flatness of the level required for realizing the light emitting device is obtained. It is extremely difficult to obtain properties and crystallinity. According to Non-Patent Document 3, the crystallinity of ZnO depends on the crystal growth temperature, and it is concluded that it is optimal to grow at 230 ° C for sapphire substrates and 300 ° C for glass substrates. In other words, it is considered that the surface flatness and crystallinity required to achieve a light emitting device by growing at a high temperature of about 800 ° C cannot be obtained.
- Non-Patent Document 3 describes that the vapor pressure of Zn supplied from the crucible is in the range of 0.1 to 1 Torr, and the O partial pressure in the chamber is 5 ⁇ 10 _4 Torr or less. In other words, in Non-Patent Document 3, since crystal growth is performed in a low vacuum atmosphere of about 0.1 to LTorr, there is a problem that impurities are very much mixed.
- the present invention has been made in view of the above circumstances, and an object thereof is to provide a method for producing a ZnO-based semiconductor crystal, which is excellent in surface flatness and crystallinity in which the crystal growth rate is high and has very few impurities in the crystal. To do.
- the present invention is a method for producing a ZnO-based semiconductor crystal, wherein at least Zn and O reach a substrate surface to grow a ZnO-based semiconductor crystal on the substrate, wherein 1 X 10
- a method for producing a ZnO-based semiconductor crystal is provided in which a part or all of Zn is ionized in a vacuum atmosphere of _4 Torr or less to reach the surface of the substrate to grow a ZnO-based semiconductor crystal.
- Zn for growing the ZnO-based semiconductor crystal is supplied in a monoatomic form, and a part or all of the monoatomic Zn is ionized. Furthermore, it is preferable that acceleration energy is given by applying a voltage to reach the substrate surface.
- the crystal growth temperature is 400 to 1200.
- the crystal growth temperature is 600 to 1200.
- the ZnO-based semiconductor crystal is preferably a non-doped ZnO crystal.
- the ZnO-based semiconductor crystal is selected from the group consisting of magnesium (Mg), cadmium (Cd), sulfur (S), selenium (Se), and tellurium (Te). It may contain at least one element for controlling the band gap selected from the above.
- the ZnO-based semiconductor crystal includes: poron (B), aluminum (A1), gallium (Ga), indium (In), nitrogen (N), phosphorus (P ), Arsenic (As), hydrogen (H), lithium (Li), sodium (Na), potassium (K), and may contain at least one element for conductivity control. Absent.
- the ZnO-based semiconductor crystal includes at least one element for band gap control selected from the group consisting of Mg, Cd, S, Se, and Te. And may contain at least one element for conductivity control selected from the group consisting of B, Al, Ga, In, N, P, As, H, Li, Na, and K. .
- element for band gap control selected from the group consisting of Mg, Cd, S, Se, and Te.
- element for conductivity control selected from the group consisting of B, Al, Ga, In, N, P, As, H, Li, Na, and K.
- the method for producing a ZnO-based semiconductor crystal of the present invention 1 X 10 _4 ⁇ : following some or all of ⁇ Te vacuum atmosphere allowed to reach Ioni spoon to the substrate surface formed the ZnO-based semiconductor crystal Make it long. Therefore, it is possible to provide a ZnO-based semiconductor crystal that has excellent surface flatness and crystallinity with a high crystal growth rate, and extremely few impurities in the crystal.
- Zn for growing the ZnO-based semiconductor crystal is supplied in a monoatomic state, part or all of the monoatomic Zn is ionized and further accelerated by applying voltage.
- the above-mentioned effect can be obtained more reliably by providing the surface of the substrate with the above.
- a part or all of O for growing the ZnO-based semiconductor crystal is radicalized to reach the substrate surface, thereby further improving the growth rate of the ZnO-based semiconductor crystal. it can.
- the crystal growth temperature by limiting the crystal growth temperature to 400 to 1200 ° C., more preferably 600 to 1200 ° C., it is possible to provide a ZnO-based semiconductor crystal having excellent surface flatness and crystallinity. it can.
- the ZnO-based semiconductor crystal to be grown is a non-doped ZnO crystal, the above effect can be obtained more reliably.
- the ZnO-based semiconductor crystal to be grown is Mg, Cd, S, Se, T
- the effect can be obtained even if at least one element for band gap control, which is selected from the group force consisting of e, is included.
- the ZnO-based semiconductor crystal to be grown has an element for conductivity control in which a group force consisting of B, Al, Ga, In, N, P, As, H, Li, Na, and K is also selected. The effect can be obtained even if at least one is included.
- the ZnO-based semiconductor crystal to be grown contains at least one element for bandgap control in which a group force consisting of Mg, Cd, S, Se, Te is also selected, and B,
- a group force consisting of Mg, Cd, S, Se, Te is also selected, and B,
- the above-mentioned effect can be obtained even if at least one element for conductivity control selected from the group consisting of Al, Ga, In, N, P, As, H, Li, Na, K is included.
- FIG. 1 is a configuration diagram showing an example of a crystal growth apparatus suitable for carrying out the production method of the present invention.
- FIG. 2 is a configuration diagram showing an example of the manufacturing method of the present invention.
- FIG. 3 is a configuration diagram showing a manufacturing method of Example 1.
- FIG. 4 is a configuration diagram showing details of an ionization mechanism of Example 1.
- FIG. 5 is a perspective view schematically showing the principle of the ionization mechanism of Example 1.
- FIG. 6 is a surface morphology of the ZnO crystal of Example 1.
- FIG. 7 is a surface morphology of the ZnO crystal of Comparative Example 1.
- FIG. 8 is a graph comparing the growth rate of Z ⁇ crystal with and without Zn + flux in the crystal growth temperature range of 600-1000 ° C.
- Growth chamber 23 ... Substrate holder, 24 "Manipulator, 25 ... Vacuum exhaust port, 26" Vacuum pump system, 27 ... Knudsen cell, 28 ... Ionization mechanism, 29 "RF radical Cell, 30 • 0 gas supply system, 31 ”RF power supply, 32a... sapphire substrate, 33 ⁇ DC stable Power supply, 43 ... high voltage power supply, 44 high voltage power supply, 51 ... filament, 52 ... collector, 53 ... dalid.
- FIG. 1 is a schematic configuration diagram of a crystal growth apparatus for carrying out an embodiment of a method for producing a ZnO-based semiconductor crystal of the present invention.
- This crystal growth apparatus 1 includes a growth chamber 2, a substrate holder 3 disposed in the growth chamber 2, a manipulator 4 for holding the substrate holder 3, and a substrate heating mechanism (not shown).
- the vacuum pump system 6 connected to the vacuum exhaust port 5 provided in the growth chamber 2, the Knudsen cell 7, the ionization mechanism 8, the radio frequency (RF) radical cell 9, the O gas supply system 10, and the RF power source 11 and.
- RF radio frequency
- the substrate heating mechanism heats the substrate (not shown) placed on the substrate holder 3 to a predetermined crystal growth temperature.
- the vacuum pump system 6 exhausts the gas in the growth chamber 2 through the vacuum exhaust port 5 to create an ultra-high vacuum atmosphere.
- the Knudsen cell 7 is inserted into the growth chamber 2 so as to face the substrate, and the solid Zn filled in the Knudsen cell 7 is vaporized.
- the ionization mechanism 8 ionizes a part or all of vaporized Zn provided between the Knudsen cell 7 and the substrate holder 3.
- the RF radical cell 9 radically oxidizes O gas provided by inserting the tip into the growth channel 2 so as to face the substrate.
- O gas supply system 10
- the substrate 12 First, placing the substrate 12 on the substrate holder 3, the inside of the growth chamber 2 1 X 10 _7 Torr or less, after evacuated to less ultra-high vacuum atmosphere good Mashiku is 1 X 10 _9 T OTr, the substrate 12 Heat in the range of 600 to 1200 ° C by the substrate heating mechanism.
- the substrate 12 placed on the substrate holder 3 is physically and chemically relatively stable at a crystal growth temperature of 600 to 1200 ° C, and a ZnO-based semiconductor crystal is grown on the surface. Anything can be used as long as it is obtained. Especially, ZnO substrate, sapphire substrate, scandium aluminum magnesium substrate, etc. It is preferable to use a material having a lattice constant that has a lattice constant within ⁇ 20% of a force having a lattice constant of ⁇ 20% or less.
- the Knudsen cell 7 is heated to vaporize a desired amount of solid Zn filled in the Knudsen cell 7 to form a monoatomic Zn (unlike clustered Zn, vaporized Zn is not bonded to each other).
- a Zn flux beam is generated.
- the monoatomic Zn is partially or entirely force ionized to become a Zn + flux beam, and further, voltage is applied.
- acceleration energy is applied to reach the surface of the substrate 12.
- High-purity O gas is supplied from the gas supply system 10 to the RF radical cell 9 and is used as an O gas beam.
- power may be supplied to the RF power source 11 to radicalize high-purity O gas in the radical cell 9 and reach the surface of the substrate 12 as an O radical beam.
- the inside of the growth chamber 2 is also in a state where Zn + flux and O or O radicals are introduced.
- FIG. 3 is a schematic configuration diagram of a crystal growth apparatus for carrying out the first embodiment. The configuration of such an apparatus will be described in detail below, but portions that overlap with the description of FIG. 1 are omitted.
- This crystal growth apparatus 21 includes a growth chamber 22, a substrate holder 23, a manipulator 24, a substrate heating mechanism (not shown), a vacuum exhaust port 25, a vacuum pump system 26, a Knudsen cell 27, a It consists of an ON mechanism 28, an RF radical cell 29, an O gas supply system 30, and an RF power source 31.
- an insulator 33 for insulating the substrate holder 23 and the growth channel 22 is inserted into the manipulator 24, and the substrate is driven by a high-voltage power source 41 provided outside the growth chamber 22.
- a voltage can be applied to the holder 23.
- FIG. 4 is a detailed configuration diagram of the ionization mechanism 28.
- the ionization mechanism 28 includes a filament 51 for emitting thermoelectrons, a collector (anode) 52 for attracting thermoelectrons, and a grid (cathode) for extracting Zn (Zn +) ionized by thermionic collisions 53 , A DC stabilized power supply 42 for supplying current to the filament, a high voltage power supply 43 for applying a positive potential to the collector 52, and a high voltage power supply 44 for applying a single potential to the grid 53.
- the filament 51, the collector 52, and the grid 53 are inserted with insulators at predetermined positions, and are insulated from the growth chamber 22. Further, the direct current stabilizing power source 42 and the high voltage power sources 43 and 44 are arranged outside the growth chamber 22 and are connected to the filament 51, the collector 52, and the grid 53 in the growth chamber 22 via a pressure-resistant connector (not shown).
- the direct current stabilizing power source 42 and the high voltage power sources 43 and 44 are arranged outside the growth chamber 22 and are connected to the filament 51, the collector 52, and the grid 53 in the growth chamber 22 via a pressure-resistant connector (not shown).
- the 10mm square sapphire substrate 32a having a thickness of 0. 35 mm was prepared, placing the substrate to the substrate holder 23, the growth chamber 22 in a 5 X 10 _1 ⁇ : was evacuated to ultrahigh vacuum atmosphere.
- the crystal plane orientation of the sapphire substrate 32a is (0001), and all the sapphire substrates described later have this crystal plane orientation.
- the sapphire substrate was heated to 770 ° C. in an ultra-high vacuum atmosphere of l X 10 _9 Torr, and thermal cleaning was performed for 30 minutes.
- a ZnO low temperature deposition buffer layer was grown on the surface of the sapphire substrate 32a.
- the growth time was 12 minutes.
- the process vacuum in the growth chamber 22 is 1.0 X 10 Torr.
- a ZnO crystal layer is grown on the sapphire substrate 32a on which the ZnO low-temperature deposition buffer layer is grown.
- current and voltage are applied to the filament 51, the collector 52, the grid 53, and the substrate holder 23 constituting the ionization mechanism 28 to generate a Zn + flux beam and reach the surface of the sapphire substrate 32a.
- Fig. 5 shows a form in which a Zn flux beam composed of monoatomic Zn generated from Knudsen cell 27 is partially or entirely ionized by an ionic mechanism 28 to form a Zn + flux beam and reaches the surface of the sapphire substrate 32a. It is a perspective view. Thermoelectrons are emitted from the filament 51, and the thermoelectrons are attracted while being accelerated to the collector 52 which is an anode.
- the Zn flux beam generated from the Knudsen cell 27 collides with the accelerated thermoelectrons when passing between the filament 51 and the collector 52, and a part or all of the monoatomic Zn contained in the flux beam. Emits one or more electrons in the outermost shell to become Zn + or Zn n + (hereinafter collectively referred to as Zn +). Since this Zn + has a positive potential, it is attracted to the grid 53 which is a cathode, and is further accelerated by the potential difference between the substrate holder 23 and the grid 53.
- the monoatomic Zn vaporized from the Knudsen cell 27 based on the above principle is partially or entirely force ionized, and is further given acceleration energy by voltage application to reach the surface of the sapphire substrate 32a.
- the growth time was 180 minutes. At this time, the degree of process vacuum in the growth chamber 22 was 2.0 ⁇ 10 _5 Torr.
- the sapphire substrate 32a was taken out from the crystal growth apparatus 21.
- a 10 mm square sapphire substrate 32b having a thickness of 0.35 mm was prepared, and thermal cleaning, ZnO low temperature deposition buffer layer growth, and ZnO crystal layer growth were performed in the same manner as in Example 1. However, a normal Zn flux beam was used without generating a Zn + flux beam during the growth of the ZnO crystal layer. The other growth conditions were the same as in Example 1.
- the crystal grown on the sapphire substrate 32b was confirmed to be ZnO by XRD measurement.
- the crystal growth rate was estimated to be 72 nm Zh from the results of film thickness measurement by cross-sectional SEM observation.
- Example 1 can improve the growth rate of ZnO crystals.
- Fig. 6 shows the results of Example 1
- Fig. 7 shows the results of Comparative Example 1. This is the surface morphology of ZnO crystal grown on the sapphire substrate 32b.
- the grain boundary region of the ZnO crystal of Example 1 is smaller than that of the ZnO crystal of Comparative Example 1 in which the density of the dahrain as a ZnO force is high.
- the ZnO crystal of Example 1 has higher continuity in the in-plane direction of the thin film than the ZnO crystal of Comparative Example 1, that is, excellent surface flatness. .
- Table 3 shows the residual carrier concentration of ZnO crystals measured by Hall measurement.
- Comparative Example 1 l .17 l 0 " 17 cm 3 [0047] As shown in Table 3, the ZnO crystal of Example 1 showed a lower residual carrier concentration than the ZnO crystal of Comparative Example 1, although slightly. That is, the ZnO crystal of Example 1 has better crystallinity than the ZnO crystal of Comparative Example 1.
- Example 1 Zn ionized by the ionization mechanism reaches the substrate surface when an acceleration voltage of about several eV to IkeV is applied. Therefore, the ionized Zn actively migrates on the substrate surface.
- migration is activated, the chance of overcoming the reaction potential barrier for ZnO formation through reaction of Zn (Zn +) and O increases, resulting in a faster crystal growth rate. it is conceivable that.
- the fact that migration is activated means that Zn (Zn +) can easily move to the kink position, which is the growth front. As a result, the continuity in the in-plane direction of the thin film is increased (grain boundary region force is reduced), and the surface flatness is improved. And as a result, it is thought that crystallinity also improves.
- the crystal obtained on the substrate according to Example 2 was confirmed to be ZnO by XRD measurement.
- the crystal growth rate is 160 nm from the film thickness measurement result by cross-sectional SEM
- a 10 mm square sapphire substrate 32d having a thickness of 0.35 mm was prepared, and thermal cleaning, ZnO low temperature deposition buffer layer growth, and ZnO crystal layer growth were performed.
- a normal Zn flux beam was used without generating a Zn + flux beam during the growth of the ZnO crystal layer, and the other growth conditions were the same as in Example 2.
- the crystal obtained on the substrate according to Comparative Example 2 was confirmed to be ZnO by XRD measurement.
- the crystal growth rate is 143 nm from the results of film thickness measurement by cross-sectional SEM observation. Estimated as Zh.
- the crystal obtained on the substrate according to Example 3 was confirmed to be ZnO by XRD measurement.
- the crystal growth rate was estimated to be 27 nmZh from the results of film thickness measurement by cross-sectional SEM observation.
- a 10 mm square sapphire substrate 32f with a thickness of 0.35 mm was prepared, and thermal cleaning, ZnO low temperature deposition buffer layer growth, and ZnO crystal layer growth were performed.
- a normal Zn flux beam was used without generating a Zn + flux beam during the growth of the ZnO crystal layer, and the other growth conditions were the same as in Example 3.
- the crystal obtained on the substrate according to Comparative Example 3 was confirmed to be ZnO by XRD measurement.
- the crystal growth rate was estimated to be 12 nmZh from the results of film thickness measurement by cross-sectional SEM observation.
- a 10 mm square sapphire substrate 32h having a thickness of 0.35 mm was prepared, and thermal cleaning, ZnO low temperature deposition buffer layer growth, and ZnO crystal layer growth were performed.
- a normal Zn flux beam was used without generating a Zn + flux beam during the growth of the ZnO crystal layer, and the other growth conditions were the same as in Example 4.
- the crystal grown on the substrate according to Comparative Example 4 had such a power that the diffraction pattern caused by the XRD measurement force ZnO could not be confirmed.
- cross-sectional SEM observation revealed that no ZnO crystal had grown on the sapphire substrate 32h.
- a 10 mm square sapphire substrate 32i having a thickness of 0.35 mm was prepared, and thermal cleaning, ZnO low temperature deposition buffer layer growth, and ZnO crystal layer growth were performed.
- the growth temperature during the growth of the ZnO crystal layer was 1200 ° C.
- the other growth conditions were the same as in Example 1.
- the film thickness can be measured by cross-sectional SEM observation.
- Figure 8 shows a graph plotting the growth rate.
- Zn + flux indicates that ZnO flux beam was generated and ZnO crystal was grown
- Zn flux indicated that ZnO crystal was not generated with Zn + flux beam, but with normal Zn flux beam. Shows that it has grown. From this figure, it was found that the crystal growth rate was improved by using a Zn + flux beam under the same crystal growth temperature conditions. In particular, the growth rate of the crystal at 900 ° C was more than twice that without the Zn + flux beam.
- the force ZnO crystal does not grow up to a crystal growth temperature of 900 ° C or lower, whereas when the Zn + flux beam is generated, the temperature is 1200 ° C. Even ZnO crystals grew.
- the process vacuum degree in the growth chamber 1 X 10 _4 Torr or less in any case, preferably 2. to less OX 10 _5 Torr, very few impurities grown in ZnO crystals, High quality ZnO-based semiconductor crystals can be obtained.
- the crystal growth temperature be in the range of 600 to 1200 ° C. Considering that it is possible to more efficiently obtain a practical film thickness for manufacturing a light emitting device. ⁇ : More preferably within the range of LOOO ° C.
- the present invention uses Zn and O gas as raw materials and ionizes part or all of the former.
- Non-Patent Document 3 focuses on growing a ZnO crystal at a crystal growth temperature of 300 ° C or lower by using Zn clusters in an ionized state.
- the crystal growth temperature is increased in order to grow a crystal having excellent surface flatness and crystallinity, and the surface flatness and crystallinity are further improved by using ionized Zn.
- the main focus is on improving the crystal growth rate. Therefore, the concept of the present invention is fundamentally different from the technique disclosed in Non-Patent Document 3.
- Non-Patent Document 3 Zn clusters are ionized (one or a plurality of electrons are emitted from a lump of 500 to 2000 Zn atoms to have a positive potential) to reach the substrate surface.
- Non-Patent Document 3 is characterized in that a ZnO crystal is grown using mass energy as a driving force by utilizing the fact that this Zn + cluster has a huge mass.
- the present invention is characterized in that a single atom of Zn is ionized, acceleration energy is applied by applying a voltage, and a ZnO crystal is grown using this acceleration energy as a driving force. Due to this difference in mechanism, Non-Patent Document 3 differs from the present invention.
- the present invention is effective not only when a ZnO crystal is grown at a high crystal growth temperature but also when it is grown at a relatively low crystal growth temperature.
- a ZnO low temperature deposition buffer layer described in Example 1 when the ZnO low temperature deposition buffer layer described in Example 1 is grown, a ZnO low temperature deposition buffer layer having a relatively flat surface can be grown by generating a Zn + flux beam.
- This low-temperature ZnO deposition buffer layer allows ZnO crystals to grow on substrates having lattice constants that have a lattice mismatch of ⁇ 20% or less with respect to ZnO crystals, such as sapphire substrates and scandium aluminum oxide magnetic substrates. At this time, it is introduced for the purpose of further improving the surface flatness and crystallinity of the ZnO crystal. If the surface flatness of this ZnO low temperature deposition buffer layer is high, Since the surface flatness and crystallinity of the ZnO crystal grown on the buffer layer can be further improved as the value is higher, the present invention is more effective.
- this ZnO low-temperature deposited buffer layer is grown at a crystal growth temperature lower than 400 ° C or higher than 600 ° C, the surface flatness and crystallinity of the ZnO crystal grown on the buffer layer sexuality will be low. Therefore, it is desirable that the ZnO low temperature deposition buffer layer is crystal-grown within the range of 400-600 ° C.
- the power described only for the non-doped ZnO crystal is not limited to this embodiment.
- the present invention is not limited to this embodiment.
- a mixed crystal based on ZnO such as ZnMgO and ZnCdO, Ga, It can also be applied to the growth of ZnO crystals doped with elements such as N or the like, or mixed crystals based on Z ⁇ .
- elements for mixed crystals include S, Se, Te and the like in addition to Mg and Cd, and ZnO is mixed with these elements.
- a mixed crystal containing as a base it is possible to change the emission wavelength of the light-emitting element or to manufacture a double heterostructure for further improving the light-emitting efficiency of the light-emitting element.
- B, Al, In, P, As, H, Li, Na, K and the like can be cited as elements for conductivity control, and these elements can be mixed.
- ZnO with specific conductivity (p-type and n-type)
- pn p-type junction for realizing a light-emitting element
- the base ZnO crystal may contain only one of these elements or two or more. It is also possible to include an element for controlling the band gap and an element for controlling the conductivity at the same time.
- the crystal growth rate is high and the surface flatness and crystallinity are excellent. It is possible to provide a method for producing a ZnO-based semiconductor crystal with very few impurities in the crystal.
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US12/305,802 US8268075B2 (en) | 2006-06-22 | 2007-06-22 | Method of producing zinc oxide semiconductor crystal |
JP2008522555A JP5196655B2 (ja) | 2006-06-22 | 2007-06-22 | 酸化亜鉛系半導体結晶の製造方法 |
CN2007800306994A CN101506959B (zh) | 2006-06-22 | 2007-06-22 | 氧化锌系半导体晶体的制造方法 |
EP07767443.0A EP2045838A4 (en) | 2006-06-22 | 2007-06-22 | METHOD FOR PRODUCING A ZINC OXIDE SEMICONDUCTOR CRYSTAL |
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KR101980195B1 (ko) | 2012-05-16 | 2019-05-21 | 삼성전자주식회사 | 황 도핑 징크옥시 나이트라이드 채널층을 가진 트랜지스터 및 그 제조방법 |
CN104357798B (zh) * | 2014-10-23 | 2016-08-24 | 湖北大学 | 一种CdZnOS四元ZnO合金半导体材料及其制备方法 |
WO2016073796A1 (en) * | 2014-11-05 | 2016-05-12 | Solarcity Corporation | System and method for efficient deposition of transparent conductive oxide |
US20170092747A1 (en) * | 2015-09-30 | 2017-03-30 | Sumitomo Electric Industries, Ltd. | Hemt having heavily doped n-type regions and process of forming the same |
CN105297072B (zh) * | 2015-10-26 | 2017-11-17 | 南开大学 | 一种含硒的ZnO光阳极及其制备方法和应用 |
CN105695947A (zh) * | 2016-04-09 | 2016-06-22 | 浙江大学 | 一种具有高迁移率的非金属共掺杂ZnO透明导电薄膜及其制备方法 |
CN108070903A (zh) * | 2016-11-16 | 2018-05-25 | 北京大学 | 一种对衬底加电调控薄膜材料生长的装置 |
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JP5196655B2 (ja) | 2013-05-15 |
CN101506959A (zh) | 2009-08-12 |
US8268075B2 (en) | 2012-09-18 |
CN101506959B (zh) | 2012-06-13 |
JPWO2007148802A1 (ja) | 2009-11-19 |
KR20090029271A (ko) | 2009-03-20 |
EP2045838A4 (en) | 2014-06-11 |
US20090260563A1 (en) | 2009-10-22 |
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