WO2016024442A1 - 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイス - Google Patents
酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイス Download PDFInfo
- Publication number
- WO2016024442A1 WO2016024442A1 PCT/JP2015/067623 JP2015067623W WO2016024442A1 WO 2016024442 A1 WO2016024442 A1 WO 2016024442A1 JP 2015067623 W JP2015067623 W JP 2015067623W WO 2016024442 A1 WO2016024442 A1 WO 2016024442A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- oxide
- sintered body
- tungsten
- oxide sintered
- zinc
- Prior art date
Links
- 239000004065 semiconductor Substances 0.000 title claims abstract description 246
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 32
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims abstract description 124
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 123
- 239000010937 tungsten Substances 0.000 claims abstract description 123
- 239000011701 zinc Substances 0.000 claims abstract description 99
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 70
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims abstract description 69
- 229910052738 indium Inorganic materials 0.000 claims abstract description 40
- APFVFJFRJDLVQX-UHFFFAOYSA-N indium atom Chemical compound [In] APFVFJFRJDLVQX-UHFFFAOYSA-N 0.000 claims abstract description 40
- 238000004544 sputter deposition Methods 0.000 claims abstract description 34
- 239000000843 powder Substances 0.000 claims description 141
- 239000013078 crystal Substances 0.000 claims description 116
- 239000000203 mixture Substances 0.000 claims description 60
- 238000000034 method Methods 0.000 claims description 37
- 238000005477 sputtering target Methods 0.000 claims description 33
- XLOMVQKBTHCTTD-UHFFFAOYSA-N Zinc monoxide Chemical compound [Zn]=O XLOMVQKBTHCTTD-UHFFFAOYSA-N 0.000 claims description 31
- 239000002994 raw material Substances 0.000 claims description 30
- QGLKJKCYBOYXKC-UHFFFAOYSA-N nonaoxidotritungsten Chemical compound O=[W]1(=O)O[W](=O)(=O)O[W](=O)(=O)O1 QGLKJKCYBOYXKC-UHFFFAOYSA-N 0.000 claims description 29
- 229910001930 tungsten oxide Inorganic materials 0.000 claims description 29
- 239000002245 particle Substances 0.000 claims description 23
- 238000004833 X-ray photoelectron spectroscopy Methods 0.000 claims description 19
- 239000012298 atmosphere Substances 0.000 claims description 17
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 13
- 239000001301 oxygen Substances 0.000 claims description 13
- 229910052760 oxygen Inorganic materials 0.000 claims description 13
- 238000005245 sintering Methods 0.000 claims description 13
- 239000010936 titanium Substances 0.000 claims description 13
- 229910003437 indium oxide Inorganic materials 0.000 claims description 10
- PJXISJQVUVHSOJ-UHFFFAOYSA-N indium(iii) oxide Chemical compound [O-2].[O-2].[O-2].[In+3].[In+3] PJXISJQVUVHSOJ-UHFFFAOYSA-N 0.000 claims description 10
- 238000000465 moulding Methods 0.000 claims description 7
- 229910052710 silicon Inorganic materials 0.000 claims description 7
- 239000011651 chromium Substances 0.000 claims description 6
- 239000010703 silicon Substances 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- GYHNNYVSQQEPJS-UHFFFAOYSA-N Gallium Chemical compound [Ga] GYHNNYVSQQEPJS-UHFFFAOYSA-N 0.000 claims description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 5
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 5
- 229910052797 bismuth Inorganic materials 0.000 claims description 5
- 229910052733 gallium Inorganic materials 0.000 claims description 5
- 239000010955 niobium Substances 0.000 claims description 5
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- JCXGWMGPZLAOME-UHFFFAOYSA-N bismuth atom Chemical compound [Bi] JCXGWMGPZLAOME-UHFFFAOYSA-N 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052750 molybdenum Inorganic materials 0.000 claims description 4
- 229910052758 niobium Inorganic materials 0.000 claims description 4
- 229910052715 tantalum Inorganic materials 0.000 claims description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 3
- 229910052735 hafnium Inorganic materials 0.000 claims description 3
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 claims description 3
- 239000011733 molybdenum Substances 0.000 claims description 3
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 3
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 2
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 2
- 239000010408 film Substances 0.000 description 165
- 230000005669 field effect Effects 0.000 description 27
- 239000000758 substrate Substances 0.000 description 26
- 229910052751 metal Inorganic materials 0.000 description 18
- 238000002156 mixing Methods 0.000 description 15
- 239000002184 metal Substances 0.000 description 14
- 230000015572 biosynthetic process Effects 0.000 description 13
- 238000002441 X-ray diffraction Methods 0.000 description 9
- 239000011787 zinc oxide Substances 0.000 description 9
- 238000001354 calcination Methods 0.000 description 8
- 239000007789 gas Substances 0.000 description 8
- 239000000523 sample Substances 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 7
- 238000005530 etching Methods 0.000 description 6
- 230000000704 physical effect Effects 0.000 description 6
- 238000002360 preparation method Methods 0.000 description 6
- 238000005001 rutherford backscattering spectroscopy Methods 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 238000001755 magnetron sputter deposition Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 239000010409 thin film Substances 0.000 description 5
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 4
- 229910021417 amorphous silicon Inorganic materials 0.000 description 4
- 238000009616 inductively coupled plasma Methods 0.000 description 4
- 238000010298 pulverizing process Methods 0.000 description 4
- 238000007740 vapor deposition Methods 0.000 description 4
- MUBZPKHOEPUJKR-UHFFFAOYSA-N Oxalic acid Chemical compound OC(=O)C(O)=O MUBZPKHOEPUJKR-UHFFFAOYSA-N 0.000 description 3
- 238000004458 analytical method Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N argon Substances [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 230000002950 deficient Effects 0.000 description 3
- 238000004949 mass spectrometry Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910004298 SiO 2 Inorganic materials 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
- 229910010413 TiO 2 Inorganic materials 0.000 description 2
- 239000003513 alkali Substances 0.000 description 2
- 239000007864 aqueous solution Substances 0.000 description 2
- 229910052786 argon Inorganic materials 0.000 description 2
- -1 argon ions Chemical class 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 239000002612 dispersion medium Substances 0.000 description 2
- 238000001035 drying Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000007772 electrode material Substances 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 239000011521 glass Substances 0.000 description 2
- 150000002500 ions Chemical class 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- 238000007088 Archimedes method Methods 0.000 description 1
- 229910015902 Bi 2 O 3 Inorganic materials 0.000 description 1
- 229910005191 Ga 2 O 3 Inorganic materials 0.000 description 1
- OLBVUFHMDRJKTK-UHFFFAOYSA-N [N].[O] Chemical compound [N].[O] OLBVUFHMDRJKTK-UHFFFAOYSA-N 0.000 description 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 1
- 239000011324 bead Substances 0.000 description 1
- 230000005540 biological transmission Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 239000000306 component Substances 0.000 description 1
- 238000012790 confirmation Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- AJNVQOSZGJRYEI-UHFFFAOYSA-N digallium;oxygen(2-) Chemical compound [O-2].[O-2].[O-2].[Ga+3].[Ga+3] AJNVQOSZGJRYEI-UHFFFAOYSA-N 0.000 description 1
- 238000007599 discharging Methods 0.000 description 1
- 238000005401 electroluminescence Methods 0.000 description 1
- 238000010894 electron beam technology Methods 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 229910001195 gallium oxide Inorganic materials 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 239000012212 insulator Substances 0.000 description 1
- 238000007733 ion plating Methods 0.000 description 1
- 239000004973 liquid crystal related substance Substances 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000012299 nitrogen atmosphere Substances 0.000 description 1
- 235000006408 oxalic acid Nutrition 0.000 description 1
- 229920002120 photoresistant polymer Polymers 0.000 description 1
- 238000005268 plasma chemical vapour deposition Methods 0.000 description 1
- 238000000634 powder X-ray diffraction Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 229910001404 rare earth metal oxide Inorganic materials 0.000 description 1
- VSZWPYCFIRKVQL-UHFFFAOYSA-N selanylidenegallium;selenium Chemical compound [Se].[Se]=[Ga].[Se]=[Ga] VSZWPYCFIRKVQL-UHFFFAOYSA-N 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 239000002689 soil Substances 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 238000001694 spray drying Methods 0.000 description 1
- 238000005211 surface analysis Methods 0.000 description 1
- JBQYATWDVHIOAR-UHFFFAOYSA-N tellanylidenegermanium Chemical compound [Te]=[Ge] JBQYATWDVHIOAR-UHFFFAOYSA-N 0.000 description 1
- 238000001771 vacuum deposition Methods 0.000 description 1
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/62605—Treating the starting powders individually or as mixtures
- C04B35/62645—Thermal treatment of powders or mixtures thereof other than sintering
- C04B35/62655—Drying, e.g. freeze-drying, spray-drying, microwave or supercritical drying
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/62605—Treating the starting powders individually or as mixtures
- C04B35/62645—Thermal treatment of powders or mixtures thereof other than sintering
- C04B35/62675—Thermal treatment of powders or mixtures thereof other than sintering characterised by the treatment temperature
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/62605—Treating the starting powders individually or as mixtures
- C04B35/62685—Treating the starting powders individually or as mixtures characterised by the order of addition of constituents or additives
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/64—Burning or sintering processes
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
- C23C14/08—Oxides
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
- C23C14/08—Oxides
- C23C14/086—Oxides of zinc, germanium, cadmium, indium, tin, thallium or bismuth
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
- C23C14/34—Sputtering
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
- C23C14/34—Sputtering
- C23C14/3407—Cathode assembly for sputtering apparatus, e.g. Target
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
- C23C14/22—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the process of coating
- C23C14/34—Sputtering
- C23C14/3407—Cathode assembly for sputtering apparatus, e.g. Target
- C23C14/3414—Metallurgical or chemical aspects of target preparation, e.g. casting, powder metallurgy
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01J—ELECTRIC DISCHARGE TUBES OR DISCHARGE LAMPS
- H01J37/00—Discharge tubes with provision for introducing objects or material to be exposed to the discharge, e.g. for the purpose of examination or processing thereof
- H01J37/32—Gas-filled discharge tubes
- H01J37/34—Gas-filled discharge tubes operating with cathodic sputtering
- H01J37/3411—Constructional aspects of the reactor
- H01J37/3414—Targets
- H01J37/3426—Material
- H01J37/3429—Plural materials
-
- 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
- H01L21/02104—Forming layers
- H01L21/02107—Forming insulating materials on a substrate
- H01L21/02225—Forming insulating materials on a substrate characterised by the process for the formation of the insulating layer
- H01L21/0226—Forming insulating materials on a substrate characterised by the process for the formation of the insulating layer formation by a deposition process
- H01L21/02263—Forming insulating materials on a substrate characterised by the process for the formation of the insulating layer formation by a deposition process deposition from the gas or vapour phase
- H01L21/02266—Forming insulating materials on a substrate characterised by the process for the formation of the insulating layer formation by a deposition process deposition from the gas or vapour phase deposition by physical ablation of a target, e.g. sputtering, reactive sputtering, physical vapour deposition or pulsed laser deposition
-
- 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
- H01L21/02104—Forming layers
- H01L21/02365—Forming inorganic semiconducting materials on a substrate
- H01L21/02518—Deposited layers
- H01L21/02521—Materials
- H01L21/02551—Group 12/16 materials
- H01L21/02554—Oxides
-
- 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
- H01L21/02104—Forming layers
- H01L21/02365—Forming inorganic semiconducting materials on a substrate
- H01L21/02518—Deposited layers
- H01L21/02521—Materials
- H01L21/02565—Oxide semiconducting materials not being Group 12/16 materials, e.g. ternary compounds
-
- 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
- H01L21/02104—Forming layers
- 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
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L29/00—Semiconductor devices specially adapted for rectifying, amplifying, oscillating or switching and having potential barriers; Capacitors or resistors having potential barriers, e.g. a PN-junction depletion layer or carrier concentration layer; Details of semiconductor bodies or of electrodes thereof ; Multistep manufacturing processes therefor
- H01L29/02—Semiconductor bodies ; Multistep manufacturing processes therefor
- H01L29/12—Semiconductor bodies ; Multistep manufacturing processes therefor characterised by the materials of which they are formed
- H01L29/24—Semiconductor bodies ; Multistep manufacturing processes therefor characterised by the materials of which they are formed including, apart from doping materials or other impurities, only semiconductor materials not provided for in groups H01L29/16, H01L29/18, H01L29/20, H01L29/22
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L29/00—Semiconductor devices specially adapted for rectifying, amplifying, oscillating or switching and having potential barriers; Capacitors or resistors having potential barriers, e.g. a PN-junction depletion layer or carrier concentration layer; Details of semiconductor bodies or of electrodes thereof ; Multistep manufacturing processes therefor
- H01L29/66—Types of semiconductor device ; Multistep manufacturing processes therefor
- H01L29/66007—Multistep manufacturing processes
- H01L29/66969—Multistep manufacturing processes of devices having semiconductor bodies not comprising group 14 or group 13/15 materials
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L29/00—Semiconductor devices specially adapted for rectifying, amplifying, oscillating or switching and having potential barriers; Capacitors or resistors having potential barriers, e.g. a PN-junction depletion layer or carrier concentration layer; Details of semiconductor bodies or of electrodes thereof ; Multistep manufacturing processes therefor
- H01L29/66—Types of semiconductor device ; Multistep manufacturing processes therefor
- H01L29/68—Types of semiconductor device ; Multistep manufacturing processes therefor controllable by only the electric current supplied, or only the electric potential applied, to an electrode which does not carry the current to be rectified, amplified or switched
- H01L29/76—Unipolar devices, e.g. field effect transistors
- H01L29/772—Field effect transistors
- H01L29/78—Field effect transistors with field effect produced by an insulated gate
- H01L29/786—Thin film transistors, i.e. transistors with a channel being at least partly a thin film
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L29/00—Semiconductor devices specially adapted for rectifying, amplifying, oscillating or switching and having potential barriers; Capacitors or resistors having potential barriers, e.g. a PN-junction depletion layer or carrier concentration layer; Details of semiconductor bodies or of electrodes thereof ; Multistep manufacturing processes therefor
- H01L29/66—Types of semiconductor device ; Multistep manufacturing processes therefor
- H01L29/68—Types of semiconductor device ; Multistep manufacturing processes therefor controllable by only the electric current supplied, or only the electric potential applied, to an electrode which does not carry the current to be rectified, amplified or switched
- H01L29/76—Unipolar devices, e.g. field effect transistors
- H01L29/772—Field effect transistors
- H01L29/78—Field effect transistors with field effect produced by an insulated gate
- H01L29/786—Thin film transistors, i.e. transistors with a channel being at least partly a thin film
- H01L29/7869—Thin film transistors, i.e. transistors with a channel being at least partly a thin film having a semiconductor body comprising an oxide semiconductor material, e.g. zinc oxide, copper aluminium oxide, cadmium stannate
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3217—Aluminum oxide or oxide forming salts thereof, e.g. bauxite, alpha-alumina
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3232—Titanium oxides or titanates, e.g. rutile or anatase
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3239—Vanadium oxides, vanadates or oxide forming salts thereof, e.g. magnesium vanadate
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3241—Chromium oxides, chromates, or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3244—Zirconium oxides, zirconates, hafnium oxides, hafnates, or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3251—Niobium oxides, niobates, tantalum oxides, tantalates, or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3256—Molybdenum oxides, molybdates or oxide forming salts thereof, e.g. cadmium molybdate
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3258—Tungsten oxides, tungstates, or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3284—Zinc oxides, zincates, cadmium oxides, cadmiates, mercury oxides, mercurates or oxide forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3286—Gallium oxides, gallates, indium oxides, indates, thallium oxides, thallates or oxide forming salts thereof, e.g. zinc gallate
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3298—Bismuth oxides, bismuthates or oxide forming salts thereof, e.g. zinc bismuthate
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/34—Non-metal oxides, non-metal mixed oxides, or salts thereof that form the non-metal oxides upon heating, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3418—Silicon oxide, silicic acids, or oxide forming salts thereof, e.g. silica sol, fused silica, silica fume, cristobalite, quartz or flint
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/60—Aspects relating to the preparation, properties or mechanical treatment of green bodies or pre-forms
- C04B2235/604—Pressing at temperatures other than sintering temperatures
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/72—Products characterised by the absence or the low content of specific components, e.g. alkali metal free alumina ceramics
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/76—Crystal structural characteristics, e.g. symmetry
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/76—Crystal structural characteristics, e.g. symmetry
- C04B2235/762—Cubic symmetry, e.g. beta-SiC
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/77—Density
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/79—Non-stoichiometric products, e.g. perovskites (ABO3) with an A/B-ratio other than 1
Definitions
- the present invention uses an oxide sintered body that can be suitably used as a sputtering target for forming an oxide semiconductor film by a sputtering method, a manufacturing method thereof, a sputtering target including the oxide sintered body, and a sputtering target.
- the present invention relates to a semiconductor device including an oxide semiconductor film formed by sputtering.
- a thin film EL electroluminescence
- organic EL organic EL
- an amorphous silicon film is mainly used as a semiconductor film functioning as a channel layer of a TFT (thin film transistor) which is a semiconductor device. I came.
- a composite oxide containing indium (In), gallium (Ga), and zinc (Zn), that is, an In—Ga—Zn composite oxide also referred to as “IGZO”.
- IGZO In—Ga—Zn composite oxide
- Patent Document 1 discloses that an oxide semiconductor film containing IGZO as a main component is formed by a sputtering method using an oxide sintered body as a target.
- Patent Document 2 discloses an oxide sintered body mainly made of indium and containing tungsten as a material suitably used for forming an oxide semiconductor film by a sputtering method or the like.
- Patent Document 3 Japanese Patent Laid-Open No. 2006-347807 is suitable for forming an oxide transparent conductive film by a vacuum vapor deposition method such as an electron beam vapor deposition method, an ion plating method, or a high density plasma assisted vapor deposition method.
- Indium oxide containing tungsten as a solid solution is contained as a material used for the material, and tungsten is contained in an atomic ratio of 0.001 to 0.034 in terms of indium, and the density (apparent density) is 4.0 g / cm 3 or more.
- an oxide sintered body of 6.5 g / cm 3 or less.
- the TFT including the IGZO-based oxide semiconductor film described in Patent Document 1 as a channel layer has a problem of high manufacturing cost because gallium oxide manufactured from metal gallium having a high market price is used as a raw material.
- a TFT including an oxide semiconductor film manufactured using an oxide sintered body described in Patent Document 2 as a channel layer has a problem that a threshold voltage Vth is larger than 4V.
- Vth is generally 2 to 4 V in a-Si, which is a semiconductor material of a TFT that has been used for display applications so far. Even when the semiconductor material is replaced with an oxide semiconductor, it is desirable from the viewpoint of simplicity of device design that it can operate at V th in the same range.
- the oxide sintered body described in Patent Document 3 has a density (apparent density) as small as 6.5 g / cm 3 or less, a sputtering target that is an optimum method for forming an oxide semiconductor film is used. There is a problem that cannot be used.
- an oxide sintered body that can solve the above-described problems and can be suitably used as a sputtering target for forming an oxide semiconductor film of a semiconductor device with high characteristics by a sputtering method, a manufacturing method thereof, and oxide sintering
- An object of the present invention is to provide a sputtering target including a body, and a semiconductor device including an oxide semiconductor film formed by a sputtering method using the sputtering target.
- the oxide sintered body according to one embodiment of the present invention is an oxide sintered body containing indium, tungsten, and zinc, includes a bixbyite crystal phase as a main component, and has an apparent density of 6.8 g / cm. It is larger than 3 and 7.2 g / cm 3 or less.
- the content of tungsten with respect to the total of indium, tungsten and zinc in the oxide sintered body is greater than 0.5 atomic percent and 1.2 atomic percent or less, and the content of zinc with respect to the total of indium, tungsten and zinc is More than 0.5 atomic% and 1.2 atomic% or less.
- a sputter target according to another aspect of the present invention includes the oxide sintered body according to the above aspect.
- a semiconductor device according to still another aspect of the present invention includes an oxide semiconductor film formed by a sputtering method using the sputtering target according to the above aspect.
- the method for producing an oxide sintered body according to still another aspect of the present invention is a method for producing an oxide sintered body according to the above aspect, wherein a primary mixture of zinc oxide powder and tungsten oxide powder is prepared. Forming a calcined powder by heat-treating the primary mixture, preparing a secondary mixture of raw material powders including the calcined powder, and forming a molded body by molding the secondary mixture. The step of forming an oxide sintered body by sintering the formed body, and the step of forming the calcined powder is performed at a temperature of 550 ° C. or higher and lower than 1200 ° C. in an oxygen-containing atmosphere. The heat treatment of the next mixture includes forming a double oxide powder containing zinc and tungsten as the calcined powder.
- an oxide sintered body that can be suitably used as a sputtering target for forming an oxide semiconductor film of a semiconductor device with high characteristics by a sputtering method, a manufacturing method thereof, and a sputtering including the oxide sintered body
- a semiconductor device including a target and an oxide semiconductor film formed by a sputtering method using a sputtering target can be provided.
- FIG. 1A and 1B are schematic views illustrating an example of a semiconductor device according to one embodiment of the present invention, in which FIG. 1A is a schematic plan view, and FIG. 1B is a schematic cross-sectional view taken along line IB-IB illustrated in FIG. It is a schematic sectional drawing which shows an example of the manufacturing method of the semiconductor device which concerns on 1 aspect of this invention.
- An oxide sintered body is an oxide sintered body containing indium, tungsten, and zinc, includes a bixbite type crystal phase as a main component, and has an apparent density of 6 greater than .8g / cm 3 7.2g / cm 3 or less. Further, the content of tungsten with respect to the total of indium, tungsten and zinc in the oxide sintered body is greater than 0.5 atomic percent and 1.2 atomic percent or less, and the content of zinc with respect to the total of indium, tungsten and zinc The rate is greater than 0.5 atomic percent and 1.2 atomic percent or less.
- the oxide sintered body according to the present embodiment includes as a main component bixbite type crystal phase, since the apparent density is greater 7.2 g / cm 3 or less than 6.8 g / cm 3, a high characteristic semiconductor device
- the oxide semiconductor film is preferably used as a sputtering target for forming the oxide semiconductor film by sputtering.
- the content of tungsten with respect to the total of indium, tungsten and zinc in the oxide sintered body is greater than 0.5 atomic percent and 1.2 atomic percent or less, and the content of zinc with respect to the total of indium, tungsten and zinc In a semiconductor device including an oxide semiconductor film formed using a sputter target including the oxide sintered body as a channel layer, by being more than 0.5 atomic% and not more than 1.2 atomic%.
- V th can be set to 0 or more and 4 V or less, and high field effect mobility can be realized.
- the bixbite type crystal phase contains indium oxide as a main component, and tungsten and zinc that are dissolved in at least a part of the bixbite type crystal phase. Can be contained.
- the threshold voltage V th can be more effectively set to 0 to 4 V.
- high field effect mobility can be realized.
- the oxide sintered body according to this embodiment includes at least one element selected from the group consisting of aluminum, titanium, chromium, gallium, hafnium, zirconium, silicon, molybdenum, vanadium, niobium, tantalum, and bismuth. Can further be contained.
- the content ratio of the element with respect to the total of indium, tungsten, zinc and the element in the oxide sintered body can be 0.1 atomic% or more and 10 atomic% or less.
- the oxide sintered body according to the present embodiment can contain tungsten having at least one valence of hexavalent and tetravalent.
- the threshold voltage V th can be more effectively set to 0 to 4 V.
- high field effect mobility can be realized.
- the oxide sintered body according to the present embodiment can contain tungsten having a bond energy measured by X-ray photoelectron spectroscopy of 32.9 eV or more and 36.5 eV or less.
- the threshold voltage V th can be more effectively set to 0 to 4 V.
- high field effect mobility can be realized.
- a sputter target according to another embodiment of the present invention includes the oxide sintered body of the above embodiment. Since the sputter target of this embodiment includes the oxide sintered body of the above-described embodiment, it is suitably used for forming an oxide semiconductor film of a semiconductor device having high characteristics by a sputtering method.
- a semiconductor device includes an oxide semiconductor film formed by sputtering using the sputtering target of the above embodiment. Since the semiconductor device of this embodiment includes an oxide semiconductor film formed by a sputtering method using the sputtering target of the above embodiment, high characteristics can be exhibited.
- the semiconductor device described here is not particularly limited, but a TFT (thin film transistor) including an oxide semiconductor film formed by a sputtering method using the sputtering target of the above embodiment as a channel layer is a preferable example.
- the content of tungsten with respect to the sum of indium, tungsten, and zinc in the oxide semiconductor film can be greater than 0.5 atomic% and not greater than 1.2 atomic%.
- the zinc content relative to the sum of indium, tungsten, and zinc in the oxide semiconductor film can be greater than 0.5 atomic percent and 1.2 atomic percent or less.
- the atomic ratio of tungsten to zinc contained in the oxide semiconductor film may be in a range greater than 0.5 and less than 3.0.
- the threshold voltage V th can be more effectively set to 0 to 4 V, and high field effect mobility can be realized.
- the semiconductor device includes the following (a) and (b): (A) the atomic ratio of silicon to indium in the oxide semiconductor film is less than 0.007; (B) the atomic ratio of titanium to indium in the oxide semiconductor film is less than 0.004; It is possible to satisfy at least one of the following. Accordingly, the electrical resistivity of the oxide semiconductor film can be increased to 1 ⁇ 10 2 ⁇ cm or more.
- the oxide semiconductor film can contain tungsten having at least one valence of hexavalence and tetravalence.
- the threshold voltage V th can be more effectively set to 0 to 4 V, and high field effect mobility can be realized.
- the oxide semiconductor film can contain tungsten having a binding energy measured by X-ray photoelectron spectroscopy of 32.9 eV or more and 36.5 eV or less.
- the threshold voltage V th can be more effectively set to 0 to 4 V, and high field effect mobility can be realized.
- a method for producing an oxide sintered body according to still another embodiment of the present invention is a method for producing an oxide sintered body of the oxide sintered body according to the above-described embodiment, which includes zinc oxide powder and A step of preparing a primary mixture with the tungsten oxide powder, a step of forming a calcined powder by heat-treating the primary mixture, a step of preparing a secondary mixture of raw material powders including the calcined powder, and 2 A step of forming a compact by forming the next mixture and a step of forming an oxide sintered body by sintering the compact, wherein the step of forming the calcined powder is performed under an oxygen-containing atmosphere.
- It includes forming a double oxide powder containing zinc and tungsten as the calcined powder by heat treating the primary mixture at a temperature of 550 ° C. or higher and lower than 1200 ° C.
- zinc oxide powder and tungsten oxide powder are mixed and 550 ° C. or higher and 1200 ° C. in an oxygen-containing atmosphere.
- the tungsten oxide powder is at least one crystal selected from the group consisting of a WO 3 crystal phase, a WO 2 crystal phase, and a WO 2.72 crystal phase. Phases can be included. Thereby, the apparent density of the oxide sintered body is increased, and an oxide sintered body that can be suitably used as a sputtering target is obtained.
- the tungsten oxide powder may have a median particle size d50 of 0.1 ⁇ m or more and 4 ⁇ m or less. Thereby, the apparent density of the oxide sintered body is increased, and an oxide sintered body that can be suitably used as a sputtering target is obtained.
- the double oxide may contain a ZnWO 4 type crystal phase. Thereby, the apparent density of the oxide sintered body is increased, and an oxide sintered body that can be suitably used as a sputtering target is obtained.
- the oxide sintered body according to the present embodiment is an oxide sintered body containing indium, tungsten, and zinc, includes a bixbite type crystal phase as a main component, and has an apparent density of 6.8 g / cm 3 . It is 7.2 g / cm 3 or less.
- the oxide sintered body according to the present embodiment includes as a main component bixbite type crystal phase, since the apparent density is greater 7.2 g / cm 3 or less than 6.8 g / cm 3, a high characteristic semiconductor device
- the oxide semiconductor film is preferably used as a sputtering target for forming the oxide semiconductor film by sputtering.
- the bixbite type crystal phase means a bixbite crystal phase, and a phase in which at least a part of the bixbite crystal phase includes a metal element other than indium (In) and at least one element of silicon (Si). It is a generic name for those having the same crystal structure as the bixbite crystal phase.
- the bixbite crystal phase is one of the crystal phases of indium oxide (In 2 O 3 ), refers to the crystal structure defined in JCPDS card 6-0416, and is a rare earth oxide C-type phase (or C-rare). Also called soil structure phase.
- bixbite type crystal phase It can be identified by X-ray diffraction that it is a bixbite type crystal phase. That is, the existence of a bixbite type crystal phase is confirmed by X-ray diffraction, and the spacing between each plane can be measured.
- “contains a bixbite type crystal phase as a main component” means that the proportion of the bixbite type crystal phase in the oxide sintered body (the bixbite type crystal phase occupancy described later) is 90% or more Means.
- the oxide sintered body may contain other crystal phases such as a crystal phase that is unavoidably mixed.
- the phase confirmed by X-ray diffraction may be only a bixbite type crystal phase.
- the bixbite type crystal phase is the main component.
- X-ray diffraction confirms the presence of a bixbite type crystal phase and the presence of other crystal phases
- a sample is taken from a portion of the oxide sintered body, and the surface of the sample is polished and smoothed.
- SEM-EDX scanning secondary electron microscope with an energy dispersive fluorescence X-ray analyzer
- the composition ratio of the metal element is analyzed by EDX (energy dispersive fluorescence X-ray analyzer).
- the crystal particles are grouped according to the tendency of the composition ratio of the metal elements of the crystal particles.
- a group of crystal grains having a high Zn content, a high W content, or both, and a group of crystal grains having a very low Zn content and W content and a high In content Can be divided into It can be concluded that the former group is the other crystal phase and the latter group is the bixbite type In 2 O 3 phase.
- the bixbite type phase occupancy in the oxide sintered body is the area of the bixbite type crystal phase in the measured surface of the oxide sintered body. Defined as a percentage.
- the oxide sintered body according to the present embodiment has a bixbite type phase occupancy in accordance with this definition of 90% or more.
- the oxide sintered body according to the present embodiment has an apparent density greater than 6.8 g / cm 3 and 7.2 g / cm 3 or less.
- the oxide sintered body disclosed in Patent Document 3 has an apparent density of 4.0 g / cm 3 or more and 6.5 g / cm 3 or less, and the density disclosed in the comparative example is also The apparent density of the sintered body is 6.8 g / cm 3, which is lower than that of the oxide sintered body according to this embodiment.
- the theoretical density of the bixbite type crystal phase that is the main component of the oxide sintered body according to the present embodiment is such that the theoretical density of the bixbite crystal phase formed of indium oxide is 7.28 g / cm 3 ;
- the minimum It is considered to be 7.19 g / cm 3 and a maximum of 7.22 g / cm 3 .
- the percentage of the apparent density of the sintered body relative to the theoretical density, that is, the relative density of the sintered body is the same as that in the oxide sintered body disclosed in Patent Document 3. Compared with 55.4% or more and 93% or less, it is extremely high at 95.5% or more and 100% or less.
- the apparent density of the sintered body is preferably as high as possible.
- the low apparent density of the sintered body means that there are many voids in the sintered body.
- the sputter target is used while its surface is etched with argon ions during use. Therefore, if there are vacancies in the sintered body, this is exposed during film formation and the internal gas is released, so that the gas released from the target is mixed in the deposited oxide semiconductor thin film, Film characteristics deteriorate.
- an indium insulator called a nodule is formed on the target at the time of film formation, and good sputter discharge is inhibited. It is desirable to increase the apparent density of the body.
- the oxide sintered body apparent density according to a large present embodiment greatly 7.2 g / cm 3 or less than 6.8 g / cm 3, the threshold voltage V th is 0 or less than 4V Therefore, it can be suitably used as a sputtering target for forming an oxide semiconductor film of a semiconductor device having high field effect mobility and high characteristics by a sputtering method.
- the tungsten content relative to the total of indium, tungsten and zinc in the oxide sintered body (hereinafter referred to as the W content of the oxide sintered body) is 0.00. More than 5 atomic% and not more than 1.2 atomic%, and the zinc content relative to the total of indium, tungsten and zinc in the oxide sintered body (hereinafter referred to as Zn content in the oxide sintered body). Is greater than 0.5 atomic% and not greater than 1.2 atomic%.
- the threshold voltage V th is set to 0 or more and 4 V or less in a semiconductor device (for example, TFT) including, as a channel layer, an oxide semiconductor film formed using a sputtering target including the oxide sintered body.
- a semiconductor device for example, TFT
- high field effect mobility can be realized.
- the W content and Zn content of the oxide sintered body are preferably 0.6 atomic percent or more and 1.1 atomic percent or less, respectively.
- the threshold voltage V th is 0 V Will be smaller than.
- the threshold voltage Vth exceeds 4V.
- the threshold voltage V th is 0 V in a semiconductor device including an oxide semiconductor film formed using the oxide sintered body as a channel layer. Will be smaller than.
- a threshold voltage Vth exceeds 4V in a semiconductor device including an oxide semiconductor film formed using a sputter target including the oxide sintered body as a channel layer.
- the bixbite type crystal phase contains indium oxide as a main component, and contains tungsten and zinc that are dissolved in at least part of the bixbite type crystal phase.
- the threshold voltage V th is more effectively 0 or more. 4V or less can be achieved, and high field effect mobility can be realized.
- the bixbite type crystal phase contains indium oxide as a main component, and at least a part thereof includes tungsten and zinc as a solid solution”
- tungsten and zinc are dissolved in substitutional form in at least a part of the crystal lattice of indium oxide having n It means the form that is in solid solution in both forms of the mold.
- the distance between the planes specified in JCPDS card 6-0416 may be increased. It becomes narrower.
- the peak position shifts to the high angle side or shifts to the low angle side. This peak shift is confirmed, and SEM-EDX (scanning secondary electron microscope with an energy dispersive fluorescent X-ray analyzer) and TEM-EDX (transmission with an energy dispersive fluorescent X-ray analyzer) are used. Surface analysis using a scanning secondary electron microscope), and the presence of a mixture of indium, tungsten, and zinc is confirmed, it can be considered that tungsten and zinc are in solid solution in the bixbite crystal phase. .
- the presence of zinc and tungsten along with indium was confirmed using ICP (inductively coupled plasma) mass spectrometry, SEM-EDX, and other element identification methods. It can also be determined that tungsten and zinc are in solid solution in the bixbite type crystal phase when no zinc oxide, tungsten oxide, or double oxide of zinc and tungsten is confirmed.
- ICP inductively coupled plasma
- the oxide sintered body according to the present embodiment includes aluminum (Al), titanium (Ti), chromium (Cr), gallium (Ga), hafnium (Hf), zirconium (Zr), silicon (Si), molybdenum (Mo ), Vanadium (V), niobium (Nb), tantalum (Ta), and bismuth (Bi), it can further contain at least one element M selected from the group consisting of bismuth (Bi).
- the content ratio of the element M with respect to the sum of indium, tungsten, zinc and the element M in the oxide sintered body hereinafter, the content ratio of the at least one element M selected from the above group with respect to the total is referred to as oxide firing).
- the threshold voltage Vth can be more effectively set to 0 or more and 4 V or less for a semiconductor device including an oxide semiconductor film formed using a sputtering target including such an oxide sintered body as a channel layer.
- the M content of the oxide sintered body is more preferably from 0.1 atomic% to 5 atomic%, and further preferably from 0.1 atomic% to 1 atomic%.
- the sputtering target including the oxide sintered body is used.
- an oxide semiconductor film obtained using a sputtering target including the oxide sintered body is included.
- the oxide sintered body according to the present embodiment preferably includes tungsten having at least one valence of hexavalent and tetravalent.
- the threshold voltage Vth is more effectively 0 or more and 4V or less.
- high field-effect mobility can be realized.
- the oxide sintered body according to the present embodiment preferably contains tungsten having a binding energy measured by X-ray photoelectron spectroscopy of 32.9 eV or more and 36.5 eV or less. This also makes it possible to more effectively set the threshold voltage V th to 0 or more and 4 V for a semiconductor device (for example, TFT) including an oxide semiconductor film formed using a sputter target including the oxide sintered body as a channel layer. In addition to the following, high field effect mobility can be realized.
- the binding energy measured by X-ray photoelectron spectroscopy refers to the binding energy of tungsten 4f7 / 2.
- Tungsten is known to have various valences as ions.
- a semiconductor device comprising an oxide semiconductor film formed using a sputter target containing such an oxide sintered body as a channel layer
- the threshold voltage V th can be more effectively set to 0 to 4 V, and high field effect mobility can be realized.
- the valence of tungsten may be tetravalent only or hexavalent only, may include both tetravalent and hexavalent, and may include other valences that are not the main component.
- Tungsten having at least one valence of tetravalent and hexavalent preferably has a total amount of tungsten of 70 atomic% or more.
- the valence can be obtained from the bond energy of tungsten, and the valence valence ratio can also be obtained by peak separation.
- XPS X-ray photoelectron spectroscopy
- the peak position when the binding energy is measured by X-ray photoelectron spectroscopy is 32.9 eV or more and 36.5 eV or less
- a sputter target including such an oxide sintered body is used. It is clear that for a semiconductor device including the formed oxide semiconductor film as a channel layer, the threshold voltage V th can be more effectively set to 0 to 4 V and high field-effect mobility can be realized.
- the binding energy is more preferably 34 eV or more and 36.5 eV or less, and further preferably 35 eV or more and 36.5 eV or less.
- the oxide sintered body according to the present embodiment is mainly a hexavalent semiconductor that includes, as a channel layer, an oxide semiconductor film formed using a sputter target including the oxide sintered body.
- the threshold voltage V th can be more effectively set to 0 or more and 4 V or less, and it is preferable from the viewpoint of realizing high field effect mobility.
- the method for producing an oxide sintered body according to the present embodiment is a method for producing an oxide sintered body according to Embodiment 1, and a step of preparing a primary mixture of zinc oxide powder and tungsten oxide powder.
- a step of forming an oxide sintered body by sintering the molded body In the step of forming the calcined powder, the primary mixture is heat-treated at a temperature of 550 ° C. or higher and lower than 1200 ° C. in an oxygen-containing atmosphere, thereby forming a double oxide powder containing zinc and tungsten as the calcined powder. Including that.
- a primary mixture of zinc oxide powder and tungsten oxide powder is 550 ° C. or higher in an oxygen-containing atmosphere. Since it includes forming a double oxide powder containing zinc and tungsten as the calcined powder by heat treatment at a temperature of less than 1200 ° C., the apparent density of the oxide sintered body is increased, making it suitable as a sputtering target. An oxide sintered body that can be used is obtained.
- the double oxide may be deficient in oxygen or substituted with metal.
- the temperature of the heat treatment is less than 550 ° C., double oxide powder containing zinc and tungsten cannot be obtained, and if it is 1200 ° C. or higher, double oxide powder containing zinc and tungsten is decomposed or scattered. The particle size of the powder tends to be too large for use.
- tungsten in the oxide sintered body may contain at least one valence of tetravalent and hexavalent. it can.
- the threshold voltage V th can be more effectively set to 0 or more and 4 V or less for a semiconductor device including an oxide semiconductor film formed using a sputtering target including the obtained oxide sintered body as a channel layer.
- a high field effect mobility can be realized.
- the double oxide containing zinc and tungsten preferably contains a ZnWO 4 type crystal phase.
- the ZnWO 4 type crystal phase is a zinc tungstate compound crystal phase having a crystal structure represented by the space group P12 / c1 (13) and having a crystal structure defined by JCPDS card 01-088-0251. .
- oxygen may be deficient or metal may be dissolved, and the lattice constant may be changed.
- the tungsten oxide powder preferably contains at least one crystal phase selected from the group consisting of a WO 3 crystal phase, a WO 2 crystal phase, and a WO 2.72 crystal phase.
- the apparent density of the oxide sintered body can be increased, and the proportion of tungsten having at least one valence of hexavalent and tetravalent in the oxide sintered body can be increased.
- the tungsten oxide powder is preferably at least one powder selected from the group consisting of WO 3 powder, WO 2 powder, and WO 2.72 powder.
- the tungsten oxide powder preferably has a median particle size d50 of 0.1 ⁇ m to 4 ⁇ m, more preferably 0.2 ⁇ m to 2 ⁇ m, and still more preferably 0.3 ⁇ m to 1.5 ⁇ m. Thereby, the apparent density of oxide sinter can be raised.
- the median particle size d50 is determined by BET specific surface area measurement. When the median particle size d50 is smaller than 0.1 ⁇ m, it is difficult to handle the powder, and it tends to be difficult to uniformly mix the zinc oxide powder and the tungsten oxide powder.
- the median particle size d50 is larger than 4 ⁇ m, the mixed oxide powder containing zinc and tungsten obtained by heat treatment at a temperature of 550 ° C. or more and less than 1200 ° C. in an oxygen-containing atmosphere after mixing with the zinc oxide powder. The particle size also increases, and it tends to be difficult to increase the apparent density of the oxide sintered body.
- the manufacturing method of the oxide sintered body according to the present embodiment is not particularly limited, but includes, for example, the following steps from the viewpoint of efficiently forming the oxide sintered body of Embodiment 1.
- Indium oxide powder for example, In 2 O 3 powder
- tungsten oxide powder for example, WO 3 powder, WO 2.72 powder, WO 2 powder
- a metal element oxide powder constituting the oxide sintered body such as zinc oxide powder (for example, ZnO powder)
- the purity of the raw material powder is preferably a high purity of 99.9% by mass or more from the viewpoint of preventing unintentional mixing of metal elements and Si into the oxide sintered body and obtaining stable physical properties.
- the median particle diameter d50 of the tungsten oxide powder is preferably 0.1 ⁇ m or more and 4 ⁇ m or less from the viewpoint of increasing the apparent density of the oxide sintered body.
- the tungsten oxide powder and the zinc oxide powder are mixed (or ground and mixed).
- the molar ratio of the tungsten oxide powder and the zinc oxide powder is 1: 1, and the Zn 2 W 3 O 8
- the tungsten oxide powder and the zinc oxide powder are mixed at a molar ratio of 3: 2.
- the ZnWO 4 type phase is preferable from the viewpoint of increasing the apparent density of the oxide sintered body.
- any of dry and wet methods may be used, and specifically, pulverized and mixed using a ball mill, a planetary ball mill, a bead mill or the like. Is done. In this way, a primary mixture of raw material powders is obtained.
- a drying method such as natural drying or a spray dryer can be used to dry the mixture obtained using the wet pulverization and mixing method.
- the obtained primary mixture is heat-treated (calcined) to form a calcined powder (a double oxide powder containing zinc and tungsten).
- the calcining temperature of the primary mixture is preferably less than 1200 ° C. so that the particle size of the calcined product becomes too large and the apparent density of the sintered body does not decrease.
- the calcined product ZnWO 4 type
- the temperature is preferably 550 ° C. or higher. More preferably, it is 550 degreeC or more and less than 1000 degreeC, More preferably, it is 550 degreeC or more and 800 degrees C or less.
- the calcination temperature is a temperature at which a crystal phase is formed
- a lower calcination temperature is preferable from the viewpoint that the particle size of the calcination powder can be made as small as possible.
- the calcining atmosphere may be an atmosphere containing oxygen, but may be an air atmosphere having a pressure higher than atmospheric pressure or air, or an oxygen-nitrogen mixed atmosphere containing 25% by volume or more of oxygen having a pressure higher than atmospheric pressure or air. preferable. From the viewpoint of high productivity, an air atmosphere at atmospheric pressure or in the vicinity thereof is more preferable.
- the sputter target according to the present embodiment includes the oxide sintered body according to the first embodiment. Therefore, the sputter target according to this embodiment can be suitably used for forming an oxide semiconductor film of a semiconductor device having high characteristics by a sputtering method.
- the sputter target according to the present embodiment includes the oxide sintered body according to the first embodiment in order to be suitably used for forming an oxide semiconductor film of a semiconductor device having high characteristics by a sputtering method.
- the oxide sintered body of the first embodiment is more preferable.
- a semiconductor device 10 includes an oxide semiconductor film 14 formed by a sputtering method using the oxide sintered body of Embodiment 1 as a sputtering target. Since the oxide semiconductor film 14 is included, the semiconductor device according to the present embodiment can have high characteristics, that is, a threshold voltage Vth of 0 to 4 V and a high field effect mobility.
- the semiconductor device 10 is not particularly limited.
- the semiconductor device 10 is a semiconductor device including, as a channel layer, an oxide semiconductor film 14 formed by a sputtering method using the oxide sintered body of Embodiment 1 as a sputtering target.
- the semiconductor device can be a TFT (Thin Film Transistor), for example. Since the TFT as an example of the semiconductor device 10 according to the present embodiment includes the oxide semiconductor film 14 formed by sputtering using the oxide sintered body of the first embodiment as a target, the threshold voltage V th Can be 0 or more and 4 V or less, and can have high field-effect mobility.
- the TFT which is the semiconductor device 10 according to the present embodiment includes a substrate 11, a gate electrode 12 disposed on the substrate 11, and an insulating layer on the gate electrode 12, as shown in FIG.
- the gate insulating film 13 disposed, the oxide semiconductor film 14 disposed as a channel layer on the gate insulating film 13, and the source electrode 15 and the drain electrode 16 disposed on the oxide semiconductor film 14 so as not to contact each other And including.
- the content of tungsten with respect to the total of indium, tungsten, and zinc in the oxide semiconductor film 14 is 0. It is preferably greater than 0.5 atomic% and 1.2 atomic% or less, and the zinc content relative to the total of indium, tungsten, and zinc in the oxide semiconductor film 14 (hereinafter referred to as Zn content in the oxide semiconductor film 14)
- the ratio is preferably larger than 0.5 atomic% and not larger than 1.2 atomic%.
- the W content and the Zn content of the oxide semiconductor film 14 are more preferably 0.6 atomic% or more and 1.1 atomic% or less, respectively.
- the chemical composition of the oxide semiconductor film 14, that is, the content of various elements is measured by RBS (Rutherford backscattering analysis).
- the threshold voltage V th becomes lower than 0V. There is a tendency.
- the threshold voltage V th tends to exceed 4 V in the TFT which is the semiconductor device 10 including the oxide semiconductor film 14 as a channel layer. is there.
- the threshold voltage V th becomes lower than 0 V in the TFT which is the semiconductor device 10 including the oxide semiconductor film 14 as a channel layer. There is a tendency.
- the threshold voltage V th tends to exceed 4 V in the TFT that is the semiconductor device 10 including the oxide semiconductor film 14 as a channel layer. is there.
- the atomic ratio of tungsten to zinc contained in the oxide semiconductor film 14 (hereinafter referred to as W / Zn atomic ratio) is larger than 0.5 and smaller than 3.0. More preferably, it is larger than 0.8 and smaller than 2.5, more preferably larger than 0.9 and smaller than 2.2.
- the chemical composition of the oxide semiconductor film 14, that is, the W / Zn atomic ratio is measured by RBS (Rutherford backscattering analysis).
- the threshold voltage V th tends to be lower than 0 V in the TFT which is the semiconductor device 10 including the oxide semiconductor film 14 as a channel layer.
- the threshold voltage V th tends to exceed 4 V in the TFT which is the semiconductor device 10 including the oxide semiconductor film 14 as a channel layer.
- the oxide semiconductor film 14 included in the semiconductor device 10 according to the present embodiment is used as a semiconductor layer of the semiconductor device 10, it is desirable that the electrical resistivity is higher than that desired as a transparent conductive film.
- the oxide semiconductor film 14 preferably has an electric resistivity of 1 ⁇ 10 2 ⁇ cm or more.
- the Si content that can be included in the oxide semiconductor film 14 is preferably less than 0.007 in terms of the Si / In atomic ratio
- the Ti content that can be included in the oxide semiconductor film 14 Is preferably smaller than 0.004 in Ti / In atomic ratio.
- the electrical resistivity of the oxide semiconductor film 14 is measured by a four-terminal method.
- Mo electrode is formed by sputtering method as electrode material, voltage between -40V to + 40V is swept between outer electrodes, current is passed, voltage between inner electrodes is measured, and electric resistivity is calculated To do.
- the oxide semiconductor film 14 has at least hexavalent and tetravalent at least from the viewpoint of easily realizing the threshold voltage V th of 0 to 4 V and high field effect mobility. It is preferable to contain tungsten having one valence.
- the oxide semiconductor film 14 is measured by X-ray photoelectron spectroscopy from the viewpoint of easily realizing the threshold voltage V th of 0 to 4 V and high field effect mobility. It is preferable to contain tungsten having a binding energy of 32.9 eV or more and 36.5 eV or less.
- the manufacturing method of the semiconductor device 10 according to the present embodiment is not particularly limited, but the gate electrode 12 is formed on the substrate 11 from the viewpoint of efficiently manufacturing the high-performance semiconductor device 10.
- a step (FIG. 2A) a step of forming a gate insulating film 13 as an insulating layer over the gate electrode 12 (FIG. 2B), and an oxide semiconductor film 14 as a channel layer over the gate insulating film 13
- gate electrode 12 is formed on substrate 11.
- substrate 11 from a viewpoint of making transparency, price stability, and surface smoothness high, a quartz glass substrate, an alkali free glass substrate, an alkali glass substrate, etc. are preferable.
- a Mo electrode, Ti electrode, W electrode, Al electrode, Cu electrode, etc. From a point with high oxidation resistance and a low electrical resistance, a Mo electrode, Ti electrode, W electrode, Al electrode, Cu electrode, etc. are preferable.
- the method for forming the gate electrode 12 is not particularly limited, but a vacuum deposition method, a sputtering method, or the like is preferable because it can be uniformly formed on the main surface of the substrate 11 with a large area.
- a gate insulating film 13 is formed on the gate electrode 12 as an insulating layer.
- the gate insulating film 13 because of its high insulating property, SiO x film, SiN x film and the like are preferable.
- the method for forming the gate insulating film 13 is not particularly limited. However, it is possible to form the gate insulating film 13 over a main surface of the substrate 11 on which the gate electrode 12 is formed in a large area and to ensure insulation. Vapor deposition) is preferred.
- an oxide semiconductor film 14 is formed as a channel layer over the gate insulating film 13.
- the oxide semiconductor film 14 is formed by sputtering using the oxide sintered body of Embodiment 1 as a sputtering target from the viewpoint of manufacturing the semiconductor device 10 having high characteristics.
- a target and a substrate are placed facing each other in a film formation chamber, a voltage is applied to the target, and the surface of the target is sputtered with a rare gas ion, so that atoms constituting the target are changed from the target.
- a method of forming a film composed of atoms constituting a target by discharging and depositing on a substrate (including the substrate on which the gate electrode and the gate insulating film are formed).
- source electrode 15 and drain electrode 16 are formed on oxide semiconductor film 14 so as not to contact each other.
- the source electrode 15 and the drain electrode 16 are not particularly limited, but have a high oxidation resistance, a low electric resistance, and a low contact electric resistance with the oxide semiconductor film 14, so that the Mo electrode, the Ti electrode, and the W electrode Al electrodes, Cu electrodes and the like are preferable.
- a method for forming the source electrode 15 and the drain electrode 16 is not particularly limited. However, the source electrode 15 and the drain electrode 16 can be uniformly formed in a large area on the main surface of the substrate 11 on which the oxide semiconductor film 14 is formed. The method is preferred.
- a method for forming the source electrode 15 and the drain electrode 16 so as not to contact each other is not particularly limited, but the source electrode 15 and the drain having a large area and a uniform area on the main surface of the substrate 11 on which the oxide semiconductor film 14 is formed. From the viewpoint that the pattern of the electrode 16 can be formed, formation by an etching method using a photoresist is preferable.
- the valence of tungsten contained in the oxide semiconductor film in the oxide sintered body of Embodiment 1, the sputter target of Embodiment 3, and the semiconductor device of Embodiment 4 is measured by X-ray photoelectron spectroscopy (XPS).
- XPS X-ray photoelectron spectroscopy
- the ratio of tungsten having at least one valence of hexavalent and tetravalent can be determined from the intensity areas of the peaks existing in these ranges and the peaks existing in other ranges.
- the total peak intensity area ratio of hexavalent and tetravalent to the total peak intensity area of tungsten is 70% or more, it can be determined that tungsten having at least one valence of hexavalent and tetravalent is the main component. .
- the oxide semiconductor film in which tungsten contained in the oxide semiconductor film 14 in the oxide sintered body of Embodiment 1, the sputter target of Embodiment 3, and the semiconductor device 10 of Embodiment 4 is mainly hexavalent.
- the threshold voltage V th is preferably 0 to 4 V, and high field effect mobility can be easily realized.
- valence of tungsten is hexavalent can be confirmed from the fact that the binding energy of tungsten investigated by X-ray photoelectron spectroscopy is 32.9 eV or more and 36.5 eV or less.
- Example 1 to Example 8> Preparation of powder raw material Tungsten oxide powder (shown as “W” in Table 1) having the composition and median particle size d50 shown in Table 1 and having a purity of 99.99% by mass, and median particle size ZnO powder having a d50 of 1.0 ⁇ m and a purity of 99.99% by mass (indicated as “Z” in Table 1), and In 2 O having a median particle diameter d50 of 1.0 ⁇ m and a purity of 99.99% by mass 3 powders (indicated as “I” in Table 1) were prepared.
- W powder raw material
- Z median particle size ZnO powder having a d50 of 1.0 ⁇ m and a purity of 99.99% by mass
- a primary mixture of raw material powders is prepared by putting tungsten oxide powder and ZnO powder among the prepared raw material powders in a ball mill and pulverizing and mixing for 18 hours. did.
- ethanol was used as a dispersion medium. The obtained primary mixture of raw material powders was dried in the air.
- the crystal phase of the obtained oxide sintered body is identified by taking a sample from a part of the oxide sintered body and analyzing the crystal by a powder X-ray diffraction method. went. Cu X-rays were used as X-rays. Table 1 summarizes the crystal phases present in the oxide sintered body.
- the In 2 O 3 type phase which is a bixbite type phase
- the main component the In 2 O 3 type phase
- the existence of a bixbite type crystal phase and the presence of other crystal phases were confirmed by X-ray diffraction.
- the phase confirmed by X-ray diffraction was only a bixbite type crystal phase.
- the bixbite type crystal phase was the main component.
- a sample was taken from a part of the oxide sintered body, and the surface of the sample was polished and smoothed. Next, the surface of the sample was observed with SEM using SEM-EDX, and the composition ratio of the metal elements of each crystal particle was analyzed with EDX.
- the crystal particles were grouped according to the tendency of the composition ratio of the metal elements of the crystal particles, a group of crystal particles having a high Zn content and a high W content, a Zn content and a W content being very low, It could be divided into a group of crystal grains with high content.
- the group of crystal grains having a high Zn content and W content is a crystal phase other than the bixbite type crystal phase, and the group of crystal grains having a very low Zn content and W content and a high In content is a bixbite type. It was concluded that the crystal phase was an In 2 O 3 type crystal phase.
- the Bixbite type crystal phase which is a phase
- the Bixbite type crystal phase was determined to be the main component.
- Each of the oxide sintered bodies of Examples 1 to 8 was mainly composed of an In 2 O 3 type crystal phase which is a bixbite type crystal phase.
- the apparent density of the obtained oxide sintered body was determined by the Archimedes method.
- X-ray photoelectron spectroscopy (XPS) was used as a method for measuring the valence of tungsten contained in the obtained oxide sintered body (sputter target).
- the peak of the binding energy of WO 3 tungsten 4f7 / 2 in which tungsten is hexavalent appears in the range of 35 eV or more and 36.5 eV or less, and the binding energy of tungsten metal 4f 7/2 in WO 2 in which tungsten metal and tungsten are tetravalent.
- the peak appeared in the range of 32 eV or more and 33.5 eV or less.
- Table 2 summarizes the valence of tungsten (denoted as “W valence” in Table 2) and the peak position of bond energy (denoted as “W bond energy” in Table 2) identified from XPS. .
- a synthetic quartz glass substrate having a size of 50 mm ⁇ 50 mm ⁇ thickness 0.6 mm is prepared as substrate 11, and gate electrode 12 is formed on substrate 11 by sputtering.
- a Mo electrode having a thickness of 100 nm was formed.
- an amorphous SiO x film having a thickness of 200 nm was formed as a gate insulating film 13 on the gate electrode 12 by a plasma CVD method.
- an oxide semiconductor film 14 having a thickness of 10 nm is formed on the gate insulating film 13 by DC (direct current) magnetron sputtering using the target manufactured in (8) above. did.
- a plane having a target diameter of 3 inches (76.2 mm) was a sputter surface.
- the gate insulating film 13 is exposed on the substrate 11 on which the gate electrode 12 and the gate insulating film 13 are formed on a water-cooled substrate holder in a film forming chamber of a sputtering apparatus (not shown). Arranged.
- the target was disposed at a distance of 90 mm so as to face the gate insulating film 13.
- the target was sputtered as follows with the vacuum in the film formation chamber being about 6 ⁇ 10 ⁇ 5 Pa.
- a mixed gas of Ar (argon) gas and O 2 (oxygen) gas was introduced into the film formation chamber up to a pressure of 0.5 Pa in a state where a shutter was put between the gate insulating film 13 and the target.
- the O 2 gas content in the mixed gas was 30% by volume.
- Sputtering discharge was caused by applying a DC power of 110 W to the target, thereby cleaning the target surface (pre-sputtering) for 5 minutes.
- the oxide semiconductor film 14 was formed on the gate insulating film 13 by removing the shutter while maintaining the atmosphere in the film formation chamber. Note that no bias voltage was applied to the substrate holder, and the substrate holder was only water-cooled. At the time of film formation, the film formation time was set so that the thickness of the oxide semiconductor film 14 was 10 nm. Thus, the oxide semiconductor film 14 was formed by the DC (direct current) magnetron sputtering method using the target processed from the oxide sintered body. The oxide semiconductor film 14 functions as a channel layer in the TFT that is the semiconductor device 10.
- a source electrode forming portion 14s, a drain electrode forming portion 14d, and a channel portion 14c were formed.
- the size of the main surface of the source electrode forming portion 14s and the drain electrode forming portion 14d is 50 ⁇ m ⁇ 50 ⁇ m and the channel length C L (refer to FIGS. 1A and 1B and FIG. C L refers to the distance of the channel portion 14c between the source electrode 15 and the drain electrode 16.
- the channel width C W is 30 ⁇ m (refer to FIGS. 1A and 1B and FIG. 2)
- the channel width C W is the width of the channel portion 14c.) was 40 ⁇ m.
- the channel portion 14c has a vertical length of 25 mm at 3 mm intervals in a main surface of 75 mm ⁇ 75 mm so that TFTs, which are semiconductor devices, are arranged in a vertical direction of 25 mm ⁇ 25 mm at intervals of 3 mm in the main surface of the substrate of 75 mm ⁇ 75 mm. 25 ⁇ 25 were arranged.
- the substrate 11 was immersed in the etching aqueous solution at 40 ° C.
- a source electrode 15 and a drain electrode 16 were formed on the oxide semiconductor film 14 separately from each other.
- a resist (not shown) is applied on the oxide semiconductor film 14 so that only the main surfaces of the source electrode forming portion 14s and the drain electrode forming portion 14d of the oxide semiconductor film 14 are exposed. , Exposed and developed. Next, a Mo electrode having a thickness of 100 nm, which is the source electrode 15 and the drain electrode 16, respectively, was formed on the main surfaces of the source electrode forming portion 14s and the drain electrode forming portion 14d of the oxide semiconductor film 14 by sputtering. Thereafter, the resist on the oxide semiconductor film 14 was peeled off.
- Each of the Mo electrode as the source electrode 15 and the Mo electrode as the drain electrode 16 is arranged such that the TFT which is the semiconductor device 10 is arranged in 25 ⁇ 25 ⁇ 25 mm in the main surface of the substrate of 75 mm ⁇ 75 mm at intervals of 3 mm.
- One channel portion 14c is arranged at a time.
- the TFT as the obtained semiconductor device 10 was heat-treated at 150 ° C. for 15 minutes in a nitrogen atmosphere.
- a TFT including the oxide semiconductor film 14 as a channel layer was manufactured as the semiconductor device 10.
- the characteristics of the TFT as the semiconductor device 10 were evaluated as follows. First, a measuring needle was brought into contact with the gate electrode 12, the source electrode 15, and the drain electrode 16. A source-drain voltage V ds of 5 V is applied between the source electrode 15 and the drain electrode 16, and the source-gate voltage V gs applied between the source electrode 15 and the gate electrode 12 is changed from ⁇ 10 V to 15 V. The source-drain current I ds at that time was measured.
- V gs ⁇ (I ds ) 1 the relationship between the source-gate voltage V gs and the square root [(I ds ) 1/2 ] of the source-drain current I ds was graphed (hereinafter this graph is expressed as “V gs ⁇ (I ds ) 1”. / 2 curve ").
- V gs- (I ds ) A tangent line is drawn on the 1/2 curve, and the point (x intercept) where the tangent line with the point where the slope of the tangent is the maximum intersects the x axis (V gs ) is defined as the threshold voltage V th . did.
- the contents of indium, tungsten and zinc in the oxide semiconductor film 14 included in the TFT which is the semiconductor device 10 were measured by RBS (Rutherford backscattering analysis). Based on these contents, the W content and Zn content of the oxide semiconductor film 14 were calculated in atomic%. Moreover, W / Zn atomic ratio was computed based on these content. The results are summarized in Table 2.
- the valence of tungsten contained in the obtained oxide semiconductor film 14 was measured by X-ray photoelectron spectroscopy (XPS).
- XPS X-ray photoelectron spectroscopy
- the peak of the binding energy of WO 3 tungsten 4f7 / 2 in which tungsten is hexavalent appears in the range of 35 eV or more and 36.5 eV or less, and the binding energy of tungsten metal 4f 7/2 in WO 2 in which tungsten metal and tungsten are tetravalent.
- Table 2 summarizes the valence of tungsten (denoted as “W valence” in Table 2) and the peak position of bond energy (denoted as “W bond energy” in Table 2) identified from XPS. .
- oxide powders Al 2 O 3 , TiO 2 , Cr
- element M shown in Table 1 in addition to the calcined powder and In 2 O 3 powder are used as the raw material powder.
- an oxide sintered body containing a bixbite type crystal phase In 2 O 3 type phase in which tungsten and zinc were dissolved and further contained the element M was produced.
- the addition amount of the oxide powder containing the element M is as shown in Table 1 in the molar mixing ratio of the tungsten oxide powder, the ZnO powder, the In 2 O 3 powder, and the molar mixing ratio of the oxide powder containing the element M. It was made to become. In all of the oxide sintered bodies of Examples 9 to 20, the In 2 O 3 type crystal phase, which is a bixbite type crystal phase, was the main component.
- the contents of indium, zinc, tungsten and element M in the obtained oxide sintered body were measured by ICP mass spectrometry. Based on these contents, the W content of the oxide sintered body (atomic%, expressed as “W content” in Table 2), Zn content (expressed as “Zn content” in Table 2) And M content (denoted as “M content” in Table 2). The results are summarized in Table 2.
- a TFT was produced.
- the physical properties of the obtained oxide sintered body and oxide semiconductor film and the characteristics of the TFT as the semiconductor device are summarized in Tables 1 and 2 in the same manner as in Examples 1 to 8.
- tungsten oxide powder having the composition and median particle size d50 shown in Table 1 and a purity of 99.99% by mass, a median particle size d50 of 1.0 ⁇ m and a purity of 99.99%.
- a tungsten oxide powder having the composition and median particle size d50 shown in Table 1 and a purity of 99.99% by mass, a median particle size d50 of 1.0 ⁇ m and a purity of 99.99%.
- 99 mass% ZnO powder and In 2 O 3 powder having a median particle diameter d50 of 1.0 ⁇ m and a purity of 99.99 mass% using a ball mill at a molar mixing ratio shown in Table 1.
- the mixture of raw material powders was molded without calcining and sintered at the sintering temperature shown in Table 1 for 8 hours.
- an oxide sintered body is prepared, and this is processed into a target in the same manner as in Examples 1 to 8, and an oxide semiconductor film formed by DC magnetron sputtering using such a target.
- Semiconductor devices including The TFT is to prepare. It was confirmed that there was no formation of a double oxide crystal phase by molding and sintering a mixture of raw material powders without calcining.
- Tables 1 and 2 summarize the manufacturing conditions of the oxide sintered bodies, the physical properties of the obtained oxide sintered bodies and oxide semiconductor films, and the characteristics of TFTs as semiconductor devices in Comparative Examples 1 to 3. It was.
- Example 21 to Example 24 In preparation of the secondary mixture of raw material powder, oxide powder (TiO 2 , SiO 2 ) containing element M shown in Table 3 was added in addition to the calcined powder and In 2 O 3 powder as raw material powder. Except for this, an oxide sintered body containing a bixbite type crystal phase (In 2 O 3 type phase) in which tungsten and zinc are in solid solution and further contains the element M, in the same manner as in Examples 1 to 8. was made. Table 3 shows the M content in the oxide sintered body and the atomic ratio of element M to In (M / In ratio). In all of the oxide sintered bodies of Examples 21 to 24, an In 2 O 3 type crystal phase which is a bixbite type crystal phase was a main component. The obtained oxide sintered body is processed into a target, and a TFT which is a semiconductor device including an oxide semiconductor film formed by a DC magnetron sputtering method using the target is made in the same manner as in Examples 1 to 8. Made.
- Table 3 summarizes the physical properties of the obtained oxide sintered body and oxide semiconductor film and the characteristics of the TFT as a semiconductor device. The measurement methods of physical properties and characteristics are the same as in Examples 1 to 8.
- the electrical resistivity of the oxide semiconductor film was measured by the following procedure. First, an oxide semiconductor film was formed in a manner similar to the method described in “(9) Fabrication of semiconductor device” in Examples 1 to 8 (etching after forming the oxide semiconductor film was not performed). About the obtained oxide semiconductor film, the electrical resistivity was measured by the four probe method. At this time, a Mo electrode is formed as an electrode material by a sputtering method so that the electrode interval is 10 mm, a voltage of ⁇ 40 V to +40 V is swept between the outer electrodes, and a current is passed between the inner electrodes. The electrical resistivity was calculated by measuring the voltage. The results are shown in Table 3.
- the Si / In atomic ratio is preferably smaller than 0.007.
- the Ti / In atomic ratio is preferably less than 0.004.
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Ceramic Engineering (AREA)
- Manufacturing & Machinery (AREA)
- Microelectronics & Electronic Packaging (AREA)
- Power Engineering (AREA)
- Physics & Mathematics (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Condensed Matter Physics & Semiconductors (AREA)
- Computer Hardware Design (AREA)
- General Physics & Mathematics (AREA)
- Structural Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Inorganic Chemistry (AREA)
- Thermal Sciences (AREA)
- Plasma & Fusion (AREA)
- Analytical Chemistry (AREA)
- Optics & Photonics (AREA)
- Thin Film Transistor (AREA)
- Physical Vapour Deposition (AREA)
- Compositions Of Oxide Ceramics (AREA)
- Physical Deposition Of Substances That Are Components Of Semiconductor Devices (AREA)
Abstract
Description
本発明のさらに別の態様に係る半導体デバイスは、上記態様のスパッタターゲットを用いてスパッタ法により形成した酸化物半導体膜を含む。
まず、本発明の実施態様を列記して説明する。
(a)酸化物半導体膜中における、インジウムに対するシリコンの原子比が0.007より小さい、
(b)酸化物半導体膜中における、インジウムに対するチタンの原子比が0.004より小さい、
の少なくともいずれか一方を満たすものであることができる。これにより、酸化物半導体膜の電気抵抗率を1×102Ωcm以上に高めることができる。
[実施形態1:酸化物焼結体]
本実施形態に係る酸化物焼結体は、インジウム、タングステンおよび亜鉛を含有する酸化物焼結体であって、ビックスバイト型結晶相を主成分として含み、見かけ密度が6.8g/cm3より大きく7.2g/cm3以下である。本実施形態に係る酸化物焼結体は、ビックスバイト型結晶相を主成分として含み、見かけ密度が6.8g/cm3より大きく7.2g/cm3以下であるため、特性の高い半導体デバイスの酸化物半導体膜をスパッタ法で形成するためのスパッタターゲットとして好適に用いられる。
本実施形態に係る酸化物焼結体の製造方法は、実施形態1に係る酸化物焼結体の製造方法であって、亜鉛酸化物粉末とタングステン酸化物粉末との1次混合物を調製する工程と、1次混合物を熱処理することにより仮焼粉末を形成する工程と、仮焼粉末を含む原料粉末の2次混合物を調製する工程と、2次混合物を成形することにより成形体を形成する工程と、成形体を焼結することにより酸化物焼結体を形成する工程とを含む。仮焼粉末を形成する工程は、酸素含有雰囲気下、550℃以上1200℃未満の温度で1次混合物を熱処理することにより、仮焼粉末として亜鉛とタングステンとを含む複酸化物の粉末を形成することを含む。
酸化物焼結体の原料粉末として、インジウム酸化物粉末(たとえばIn2O3粉末)、タングステン酸化物粉末(たとえばWO3粉末、WO2.72粉末、WO2粉末)、亜鉛酸化物粉末(たとえばZnO粉末)等、酸化物焼結体を構成する金属元素の酸化物粉末を準備する。タングステン酸化物粉末としてはWO3粉末だけでなく、WO2.72粉末、WO2粉末のようなWO3粉末に比べて酸素が欠損した化学組成を有する粉末を原料として用いることが、酸化物焼結体中のタングステンの原子価を6価および4価の少なくとも1つにする観点から、好ましい。かかる観点から、WO2.72粉末およびWO2粉末の少なくとも1つをタングステン酸化物粉末の少なくとも一部として用いることがより好ましい。原料粉末の純度は、酸化物焼結体への意図しない金属元素およびSiの混入を防止し、安定した物性を得る観点から、99.9質量%以上の高純度であることが好ましい。
上記原料粉末の内、タングステン酸化物粉末と亜鉛酸化物粉末とを混合(または粉砕混合)する。このとき、酸化物焼結体の結晶相として、ZnWO4型相を得たい場合は、タングステン酸化物粉末と亜鉛酸化物粉末とをモル比で1:1の割合で、Zn2W3O8型相を得たい場合は、タングステン酸化物粉末と亜鉛酸化物粉末とをモル比で3:2の割合で混合する。上述のように、酸化物焼結体の見かけ密度を高める観点からは、ZnWO4型相が好ましい。タングステン酸化物粉末と亜鉛酸化物粉末とを混合する方法に特に制限はなく、乾式および湿式のいずれの方式であってもよく、具体的には、ボールミル、遊星ボールミル、ビーズミル等を用いて粉砕混合される。このようにして、原料粉末の1次混合物が得られる。湿式の粉砕混合方式を用いて得られた混合物の乾燥には、自然乾燥やスプレードライヤのような乾燥方法を用いることができる。
次に、得られた1次混合物を熱処理(仮焼)して、仮焼粉末(亜鉛とタングステンとを含む複酸化物粉末)を形成する。1次混合物の仮焼温度は、仮焼物の粒径が大きくなりすぎて焼結体の見かけ密度が低下することがないように1200℃未満であることが好ましく、仮焼生成物としてZnWO4型結晶相やZn2W3O8型結晶相を得るためには550℃以上であることが好ましい。より好ましくは550℃以上1000℃未満であり、さらに好ましくは550℃以上800℃以下である。仮焼温度は結晶相が形成される温度である限り、仮焼粉の粒径をなるべく小さくできる点から低い方が好ましい。このようにして、ZnWO4型結晶相またはZn2W3O8型結晶相を含む仮焼粉末が得られる。仮焼雰囲気は、酸素を含む雰囲気であればよいが、大気圧もしくは大気よりも圧力の高い空気雰囲気、または大気圧もしくは大気よりも圧力の高い酸素を25体積%以上含む酸素-窒素混合雰囲気が好ましい。生産性が高いことから、大気圧又はその近傍下での空気雰囲気がより好ましい。
次に、得られた仮焼粉末と、上記原料粉末の内のインジウム酸化物粉末(たとえばIn2O3粉末)とを、1次混合物の調製と同様にして、混合(または粉砕混合)する。このようにして、原料粉末の2次混合物が得られる。
次に、得られた2次混合物を成形する。2次混合物を成形する方法に特に制限はないが、焼結体の見かけ密度を高くする点から、一軸プレス法、CIP(冷間静水圧処理)法、キャスティング法等が好ましい。
次に、得られた成形体を焼結して、酸化物焼結体を形成する。この際、ホットプレス焼結法は用いないことが好ましい。成形体の焼結温度に特に制限はないが、形成する酸化物焼結体の見かけ密度を6.8g/cm3より大きくするために、900℃以上1200℃以下が好ましい。焼結雰囲気にも特に制限はないが、酸化物焼結体の構成結晶の粒径が大きくなることを防いでクラックの発生を防止する観点から、大気圧又はその近傍下での空気雰囲気が好ましい。
本実施形態に係るスパッタターゲットは、実施形態1の酸化物焼結体を含む。したがって、本実施形態に係るスパッタターゲットは、特性の高い半導体デバイスの酸化物半導体膜をスパッタ法で形成するために好適に用いることができる。
図1を参照して、本実施形態に係る半導体デバイス10は、実施形態1の酸化物焼結体をスパッタターゲットとして用いるスパッタ法により形成した酸化物半導体膜14を含む。かかる酸化物半導体膜14を含むため、本実施形態に係る半導体デバイスは、高い特性、すなわち、閾値電圧Vthを0以上4V以下であり、電界効果移動度も高いという特性を有することができる。
図2を参照して、本実施形態に係る半導体デバイス10の製造方法は、特に制限はないが、効率よく高特性の半導体デバイス10を製造する観点から、基板11上にゲート電極12を形成する工程(図2(A))と、ゲート電極12上に絶縁層としてゲート絶縁膜13を形成する工程(図2(B))と、ゲート絶縁膜13上にチャネル層として酸化物半導体膜14を形成する工程(図2(C))と、酸化物半導体膜14上にソース電極15およびドレイン電極16を互いに接触しないように形成する工程(図2(D))と、を含むことが好ましい。
図2(A)を参照して、基板11上にゲート電極12を形成する。基板11に特に制限はないが、透明性、価格安定性、および表面平滑性を高くする観点から、石英ガラス基板、無アルカリガラス基板、アルカリガラス基板等が好ましい。ゲート電極12に特に制限はないが、耐酸化性が高くかつ電気抵抗が低い点から、Mo電極、Ti電極、W電極、Al電極、Cu電極等が好ましい。ゲート電極12の形成方法は、特に制限はないが、基板11の主面上に大面積で均一に形成できる点から、真空蒸着法、スパッタ法等が好ましい。
図2(B)を参照して、ゲート電極12上に絶縁層としてゲート絶縁膜13を形成する。ゲート絶縁膜13に特に制限はないが、絶縁性が高いことから、SiOx膜、SiNx膜等が好ましい。ゲート絶縁膜13の形成方法は、特に制限はないが、ゲート電極12が形成された基板11の主面上に大面積で均一に形成できる点および絶縁性を確保する点から、プラズマCVD(化学気相堆積)法等が好ましい。
図2(C)を参照して、ゲート絶縁膜13上にチャネル層として酸化物半導体膜14を形成する。酸化物半導体膜14は、特性の高い半導体デバイス10を製造する観点から、実施形態1の酸化物焼結体をスパッタターゲットとして用いてスパッタ法により形成する。スパッタ法とは、成膜室内に、ターゲットと基板とを対向させて配置し、ターゲットに電圧を印加して、希ガスイオンでターゲットの表面をスパッタリングすることにより、ターゲットからターゲットを構成する原子を放出させて基板(上記のゲート電極およびゲート絶縁膜が形成された基板も含む。)上に堆積させることによりターゲットを構成する原子で構成される膜を形成する方法をいう。
図2(D)を参照して、酸化物半導体膜14上にソース電極15およびドレイン電極16を互いに接触しないように形成する。ソース電極15およびドレイン電極16は、特に制限はないが、耐酸化性が高く、電気抵抗が低く、かつ酸化物半導体膜14との接触電気抵抗が低いことから、Mo電極、Ti電極、W電極、Al電極、Cu電極等が好ましい。ソース電極15およびドレイン電極16を形成する方法は、特に制限はないが、酸化物半導体膜14が形成された基板11の主面上に大面積で均一に形成できる点から、真空蒸着法、スパッタ法等が好ましい。ソース電極15およびドレイン電極16を互いに接触しないように形成する方法は、特に制限はないが、酸化物半導体膜14が形成された基板11の主面上に大面積で均一なソース電極15とドレイン電極16のパターンを形成できる点から、フォトレジストを使ったエッチング法による形成が好ましい。
(1)粉末原料の準備
表1に示す組成とメジアン粒径d50を有し、純度が99.99質量%のタングステン酸化物粉末(表1において「W」と表記した。)と、メジアン粒径d50が1.0μmで純度が99.99質量%のZnO粉末(表1において「Z」と表記した。)と、メジアン粒径d50が1.0μmで純度が99.99質量%のIn2O3粉末(表1において「I」と表記した。)と、を準備した。
まず、ボールミルに、準備した原料粉末の内、タングステン酸化物粉末とZnO粉末とを入れて、18時間粉砕混合することにより原料粉末の1次混合物を調製した。タングステン酸化物粉末とZnO粉末とのモル混合比率は、およそタングステン粉末:ZnO粉末=1:1とした。粉砕混合の際、分散媒としてエタノールを用いた。得られた原料粉末の1次混合物は大気中で乾燥させた。
次に、得られた原料粉末の1次混合物をアルミナ製坩堝に入れて、空気雰囲気中、表1に示す仮焼温度で8時間仮焼し、結晶相としてZnWO4型相またはZn2W3O8型結晶相を含む仮焼粉末が得られた。表1に、得られた仮焼粉末を構成する結晶相の組成を示す。
次に、得られた仮焼粉末を、準備した原料粉末であるIn2O3粉末とともにポットへ投入し、さらに粉砕混合ボールミルに入れて12時間粉砕混合することにより原料粉末の2次混合物を調製した。In2O3粉末の混合量は、タングステン酸化物粉末とZnO粉末とIn2O3粉末とのモル混合比率が表1に示されるとおりとなるようにした。粉砕混合の際、分散媒としてエタノールを用いた。得られた混合粉末はスプレードライで乾燥させた。
次に、得られた2次混合物をプレスにより成形し、さらにCIPにより室温(5℃~30℃)の静水中、190MPaの圧力で加圧成形して、直径100mmで厚み約9mmの円板状の成形体を得た。
次に、得られた成形体を大気圧下、空気雰囲気中にて表1に示す焼結温度で8時間焼結して、タングステンおよび亜鉛が固溶したビックスバイト型結晶相(In2O3型相)を含む酸化物焼結体を得た。
得られた酸化物焼結体の結晶相の同定は、酸化物焼結体の一部からサンプルを採取して、粉末X線回折法よる結晶解析により行った。X線にはCuのKα線を用いた。酸化物焼結体に存在する結晶相を表1にまとめた。
得られた酸化物焼結体(スパッタターゲット)に含まれるタングステンの原子価を測定する方法として、X線光電子分光法(XPS)を用いた。タングステンが6価となるWO3のタングステン4f7/2の結合エネルギーのピークは35eV以上36.5eV以下の範囲に現れ、タングステン金属およびタングステンが4価となるWO2のタングステン4f7/2の結合エネルギーのピークは、32eV以上33.5eV以下の範囲に現れた。XPSから同定された、タングステンの原子価(表2において「W原子価」と表記した。)および結合エネルギーのピーク位置(表2において「W結合エネルギー」と表記した。)を表2にまとめた。
得られた酸化物焼結体を、直径3インチ(76.2mm)で厚み5.0mmのターゲットに加工した。
図2(A)を参照して、まず、基板11として50mm×50mm×厚み0.6mmの合成石英ガラス基板を準備し、その基板11上にスパッタ法によりゲート電極12として厚み100nmのMo電極を形成した。
半導体デバイス10であるTFTの特性を次のようにして評価した。まず、ゲート電極12、ソース電極15およびドレイン電極16に測定針を接触させた。ソース電極15とドレイン電極16との間に5Vのソース-ドレイン間電圧Vdsを印加し、ソース電極15とゲート電極12との間に印加するソース-ゲート間電圧Vgsを-10Vから15Vに変化させて、そのときのソース-ドレイン間電流Idsを測定した。そして、ソース-ゲート間電圧Vgsとソース-ドレイン間電流Idsの平方根〔(Ids)1/2〕との関係をグラフ化した(以下、このグラフを「Vgs-(Ids)1/2曲線」ともいう)。Vgs-(Ids)1/2曲線に接線を引き、その接線の傾きが最大となる点を接点とする接線がx軸(Vgs)と交わる点(x切片)を閾値電圧Vthとした。
gm=dIds/dVgs 〔a〕
に従って、ソース-ドレイン間電流Idsをソース-ゲート間電圧Vgsについて微分することによりgmを導出した。そしてVgs=8.0Vにおけるgmの値を用いて、下記式〔b〕:
μfe=gm・CL/(CW・Ci・Vds) 〔b〕
に基づいて、電界効果移動度μfeを算出した。上記式〔b〕におけるチャネル長さCLは30μmであり、チャネル幅CWは40μmである。また、ゲート絶縁膜13のキャパシタンスCiは3.4×10-8F/cm2とし、ソース-ドレイン間電圧Vdsは1.0Vとした。
原料粉末の2次混合物の調製の際に、原料粉末として、仮焼粉末およびIn2O3粉末の他に、表1に示す元素Mを含む酸化物粉末(Al2O3、TiO2、Cr2O3、Ga2O3、HfO2、SiO2、V2O5、Nb2O3、ZrO2、MoO2、Ta2O3、Bi2O3)を添加したこと以外は、実施例1~実施例8の場合と同様にして、タングステンおよび亜鉛が固溶し、元素Mをさらに含有するビックスバイト型結晶相(In2O3型相)を含む酸化物焼結体を作製した。元素Mを含む酸化物粉末の添加量は、タングステン酸化物粉末とZnO粉末とIn2O3粉末と元素Mを含む酸化物粉末のモル混合比率とのモル混合比率が表1に示されるとおりとなるようにした。実施例9~実施例20の酸化物焼結体はいずれも、ビックスバイト型結晶相であるIn2O3型結晶相が主成分であった。
酸化物焼結体の作製において、表1に示す組成とメジアン粒径d50を有し、純度が99.99質量%のタングステン酸化物粉末と、メジアン粒径d50が1.0μmで純度が99.99質量%のZnO粉末と、メジアン粒径d50が1.0μmで純度が99.99質量%のIn2O3粉末とを、表1に示すモル混合比率でボールミルを用いて粉砕混合することにより原料粉末の混合物を調製した後、仮焼をすることなく、当該原料粉末の混合物を成形し、表1に示す焼結温度で8時間焼結したこと以外は、実施例1~実施例8と同様にして、酸化物焼結体を作製し、これを実施例1~実施例8と同様にして、ターゲットに加工して、かかるターゲットを用いたDCマグネトロンスパッタ法により形成された酸化物半導体膜を含む半導体デバイスであるTFTを作製した。仮焼をすることなく、原料粉末の混合物を成形し焼結したことにより、複酸化物結晶相の生成がないことを確認した。比較例1~比較例3における、酸化物焼結体の製造条件、得られた酸化物焼結体および酸化物半導体膜の物性ならびに半導体デバイスであるTFTの特性を、表1および表2にまとめた。
原料粉末の2次混合物の調製の際に、原料粉末として、仮焼粉末およびIn2O3粉末の他に、表3に示す元素Mを含む酸化物粉末(TiO2、SiO2)を添加したこと以外は、実施例1~実施例8と同様にして、タングステンおよび亜鉛が固溶し、元素Mをさらに含有するビックスバイト型結晶相(In2O3型相)を含む酸化物焼結体を作製した。酸化物焼結体中のM含有率、及びInに対する元素Mの原子比(M/In比)を表3に示した。実施例21~実施例24の酸化物焼結体はいずれも、ビックスバイト型結晶相であるIn2O3型結晶相が主成分であった。得られた酸化物焼結体をターゲットに加工して、かかるターゲットを用いたDCマグネトロンスパッタ法により形成された酸化物半導体膜を含む半導体デバイスであるTFTを実施例1~実施例8と同様にして作製した。
Claims (16)
- インジウム、タングステンおよび亜鉛を含有する酸化物焼結体であって、
ビックスバイト型結晶相を主成分として含み、
見かけ密度が6.8g/cm3より大きく7.2g/cm3以下であり、
前記酸化物焼結体中のインジウム、タングステンおよび亜鉛の合計に対するタングステンの含有率が0.5原子%より大きく1.2原子%以下であり、
前記酸化物焼結体中のインジウム、タングステンおよび亜鉛の合計に対する亜鉛の含有率が0.5原子%より大きく1.2原子%以下である、酸化物焼結体。 - 前記ビックスバイト型結晶相は、インジウム酸化物を主成分として含み、前記ビックスバイト型結晶相の少なくとも一部に固溶しているタングステンおよび亜鉛を含有する、請求項1に記載の酸化物焼結体。
- アルミニウム、チタン、クロム、ガリウム、ハフニウム、ジルコニウム、シリコン、モリブデン、バナジウム、ニオブ、タンタル、およびビスマスからなる群より選ばれる少なくとも1種の元素をさらに含有し、
前記酸化物焼結体中のインジウム、タングステン、亜鉛および前記元素の合計に対する前記元素の含有率が0.1原子%以上10原子%以下である、請求項1または請求項2に記載の酸化物焼結体。 - 6価および4価の少なくとも1つの原子価を有するタングステンを含有する、請求項1~請求項3のいずれか1項に記載の酸化物焼結体。
- X線光電子分光法により測定される結合エネルギーが32.9eV以上36.5eV以下のタングステンを含有する、請求項1~請求項3のいずれか1項に記載の酸化物焼結体。
- 請求項1~請求項5のいずれか1項に記載の酸化物焼結体を含む、スパッタターゲット。
- 請求項6に記載のスパッタターゲットを用いてスパッタ法により形成した酸化物半導体膜を含む、半導体デバイス。
- 前記酸化物半導体膜中のインジウム、タングステンおよび亜鉛の合計に対するタングステンの含有率が0.5原子%より大きく1.2原子%以下であり、
前記酸化物半導体膜中のインジウム、タングステンおよび亜鉛の合計に対する亜鉛の含有率が0.5原子%より大きく1.2原子%以下である、請求項7に記載の半導体デバイス。 - 前記酸化物半導体膜に含まれる亜鉛に対するタングステンの原子比が0.5より大きく3.0より小さい、請求項7または請求項8に記載の半導体デバイス。
- 下記(a)および(b):
(a)前記酸化物半導体膜中における、インジウムに対するシリコンの原子比が0.007より小さい、
(b)前記酸化物半導体膜中における、インジウムに対するチタンの原子比が0.004より小さい、
の少なくともいずれか一方を満たし、かつ
前記酸化物半導体膜の電気抵抗率が1×102Ωcm以上である、請求項7~請求項9のいずれか1項に記載の半導体デバイス。 - 前記酸化物半導体膜は、6価および4価の少なくとも1つの原子価を有するタングステンを含有する、請求項7~請求項10のいずれか1項に記載の半導体デバイス。
- 前記酸化物半導体膜は、X線光電子分光法により測定される結合エネルギーが32.9eV以上36.5eV以下のタングステンを含有する、請求項7~請求項10のいずれか1項に記載の半導体デバイス。
- 請求項1~請求項4のいずれか1項に記載の酸化物焼結体の製造方法であって、
亜鉛酸化物粉末とタングステン酸化物粉末との1次混合物を調製する工程と、
前記1次混合物を熱処理することにより仮焼粉末を形成する工程と、
前記仮焼粉末を含む原料粉末の2次混合物を調製する工程と、
前記2次混合物を成形することにより成形体を形成する工程と、
前記成形体を焼結することにより酸化物焼結体を形成する工程と、
を含み、
前記仮焼粉末を形成する工程は、酸素含有雰囲気下、550℃以上1200℃未満の温度で前記1次混合物を熱処理することにより、前記仮焼成粉末として亜鉛とタングステンとを含む複酸化物の粉末を形成することを含む、酸化物焼結体の製造方法。 - 前記タングステン酸化物粉末は、WO3結晶相、WO2結晶相、およびWO2.72結晶相からなる群より選ばれる少なくとも1種の結晶相を含む、請求項13に記載の酸化物焼結体の製造方法。
- 前記タングステン酸化物粉末は、メジアン粒径d50が0.1μm以上4μm以下である、請求項13または請求項14に記載の酸化物焼結体の製造方法。
- 前記複酸化物がZnWO4型結晶相を含む、請求項13~請求項15のいずれか1項に記載の酸化物焼結体の製造方法。
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US15/027,396 US20160251264A1 (en) | 2014-08-12 | 2015-06-18 | Oxide sintered body and method for manufacturing the same, sputtering target, and semiconductor device |
JP2016542516A JP6428780B2 (ja) | 2014-08-12 | 2015-06-18 | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイス |
CN201580002686.0A CN105745183B (zh) | 2014-08-12 | 2015-06-18 | 氧化物烧结体及其制造方法、溅射靶、以及半导体器件 |
KR1020167011648A KR101863467B1 (ko) | 2014-08-12 | 2015-06-18 | 산화물 소결체 및 그 제조 방법, 스퍼터 타겟, 및 반도체 디바이스 |
EP15832559.7A EP3181537A1 (en) | 2014-08-12 | 2015-06-18 | Oxide sintered body and method of manufacturing same, sputter target, and semiconductor device |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2014-164142 | 2014-08-12 | ||
JP2014164142 | 2014-08-12 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2016024442A1 true WO2016024442A1 (ja) | 2016-02-18 |
Family
ID=55304072
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2015/067623 WO2016024442A1 (ja) | 2014-08-12 | 2015-06-18 | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイス |
Country Status (7)
Country | Link |
---|---|
US (1) | US20160251264A1 (ja) |
EP (1) | EP3181537A1 (ja) |
JP (1) | JP6428780B2 (ja) |
KR (1) | KR101863467B1 (ja) |
CN (1) | CN105745183B (ja) |
TW (1) | TWI648241B (ja) |
WO (1) | WO2016024442A1 (ja) |
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2017224650A (ja) * | 2016-06-13 | 2017-12-21 | 住友電気工業株式会社 | 半導体デバイスおよびその製造方法 |
WO2018020719A1 (ja) * | 2016-07-25 | 2018-02-01 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 |
WO2018083837A1 (ja) * | 2016-11-04 | 2018-05-11 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 |
WO2018211724A1 (ja) * | 2017-05-16 | 2018-11-22 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、酸化物半導体膜、ならびに半導体デバイスの製造方法 |
JPWO2018109970A1 (ja) * | 2016-12-12 | 2019-10-24 | 住友電気工業株式会社 | 半導体デバイスおよびその製造方法 |
Families Citing this family (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP6119773B2 (ja) | 2014-03-25 | 2017-04-26 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイス |
WO2016063557A1 (ja) | 2014-10-22 | 2016-04-28 | 住友電気工業株式会社 | 酸化物焼結体および半導体デバイス |
CN106164016B (zh) * | 2015-02-13 | 2019-08-09 | 住友电气工业株式会社 | 氧化物烧结体及其制造方法、溅射靶和半导体器件 |
KR102401709B1 (ko) * | 2017-02-20 | 2022-05-26 | 스미토모덴키고교가부시키가이샤 | 산화물 소결체 및 그 제조 방법, 스퍼터 타겟, 그리고 반도체 디바이스의 제조 방법 |
WO2018150621A1 (ja) * | 2017-02-20 | 2018-08-23 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 |
US12009433B2 (en) * | 2018-06-06 | 2024-06-11 | Intel Corporation | Multi-dielectric gate stack for crystalline thin film transistors |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2005314131A (ja) * | 2004-04-27 | 2005-11-10 | Sumitomo Metal Mining Co Ltd | 酸化物焼結体、スパッタリングターゲット、透明導電性薄膜およびその製造方法 |
JP2006022373A (ja) * | 2004-07-07 | 2006-01-26 | Sumitomo Metal Mining Co Ltd | 透明導電性薄膜作製用スパッタリングターゲットの製造方法 |
JP2006160535A (ja) * | 2004-12-02 | 2006-06-22 | Sumitomo Metal Mining Co Ltd | 酸化物焼結体、スパッタリングターゲットおよび透明導電性薄膜 |
JP2006193363A (ja) * | 2005-01-12 | 2006-07-27 | Sumitomo Metal Mining Co Ltd | 酸化物焼結体、スパッタリングターゲットおよび透明導電性薄膜 |
JP2010251604A (ja) * | 2009-04-17 | 2010-11-04 | Bridgestone Corp | 薄膜トランジスタの製造方法 |
Family Cites Families (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP3906766B2 (ja) | 2002-08-30 | 2007-04-18 | 住友金属鉱山株式会社 | 酸化物焼結体 |
JP4760154B2 (ja) | 2005-06-15 | 2011-08-31 | 住友金属鉱山株式会社 | 酸化物焼結体、酸化物透明導電膜、およびこれらの製造方法 |
KR101312259B1 (ko) | 2007-02-09 | 2013-09-25 | 삼성전자주식회사 | 박막 트랜지스터 및 그 제조방법 |
US20120037897A1 (en) * | 2009-04-17 | 2012-02-16 | Bridgestone Corporation | Thin film transistor and method for manufacturing thin film transistor |
JP5966840B2 (ja) * | 2012-10-11 | 2016-08-10 | 住友金属鉱山株式会社 | 酸化物半導体薄膜および薄膜トランジスタ |
-
2015
- 2015-06-18 EP EP15832559.7A patent/EP3181537A1/en not_active Withdrawn
- 2015-06-18 WO PCT/JP2015/067623 patent/WO2016024442A1/ja active Application Filing
- 2015-06-18 KR KR1020167011648A patent/KR101863467B1/ko active IP Right Grant
- 2015-06-18 US US15/027,396 patent/US20160251264A1/en not_active Abandoned
- 2015-06-18 JP JP2016542516A patent/JP6428780B2/ja active Active
- 2015-06-18 CN CN201580002686.0A patent/CN105745183B/zh active Active
- 2015-07-22 TW TW104123750A patent/TWI648241B/zh active
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2005314131A (ja) * | 2004-04-27 | 2005-11-10 | Sumitomo Metal Mining Co Ltd | 酸化物焼結体、スパッタリングターゲット、透明導電性薄膜およびその製造方法 |
JP2006022373A (ja) * | 2004-07-07 | 2006-01-26 | Sumitomo Metal Mining Co Ltd | 透明導電性薄膜作製用スパッタリングターゲットの製造方法 |
JP2006160535A (ja) * | 2004-12-02 | 2006-06-22 | Sumitomo Metal Mining Co Ltd | 酸化物焼結体、スパッタリングターゲットおよび透明導電性薄膜 |
JP2006193363A (ja) * | 2005-01-12 | 2006-07-27 | Sumitomo Metal Mining Co Ltd | 酸化物焼結体、スパッタリングターゲットおよび透明導電性薄膜 |
JP2010251604A (ja) * | 2009-04-17 | 2010-11-04 | Bridgestone Corp | 薄膜トランジスタの製造方法 |
Cited By (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2017217007A1 (ja) * | 2016-06-13 | 2017-12-21 | 住友電気工業株式会社 | 半導体デバイスおよびその製造方法 |
JP2017224650A (ja) * | 2016-06-13 | 2017-12-21 | 住友電気工業株式会社 | 半導体デバイスおよびその製造方法 |
US10822276B2 (en) | 2016-07-25 | 2020-11-03 | Sumitomo Electric Industries, Ltd. | Oxide sintered material and method of manufacturing the same, sputtering target, and method of manufacturing semiconductor device |
WO2018020719A1 (ja) * | 2016-07-25 | 2018-02-01 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 |
JP2018016495A (ja) * | 2016-07-25 | 2018-02-01 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 |
KR102645967B1 (ko) | 2016-07-25 | 2024-03-08 | 미쓰이금속광업주식회사 | 산화물 소결체 및 그 제조 방법, 스퍼터 타겟, 그리고 반도체 디바이스의 제조 방법 |
KR20190033522A (ko) * | 2016-07-25 | 2019-03-29 | 스미토모덴키고교가부시키가이샤 | 산화물 소결체 및 그 제조 방법, 스퍼터 타겟, 그리고 반도체 디바이스의 제조 방법 |
WO2018083837A1 (ja) * | 2016-11-04 | 2018-05-11 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 |
JPWO2018109970A1 (ja) * | 2016-12-12 | 2019-10-24 | 住友電気工業株式会社 | 半導体デバイスおよびその製造方法 |
WO2018211977A1 (ja) * | 2017-05-16 | 2018-11-22 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、酸化物半導体膜、ならびに半導体デバイスの製造方法 |
JPWO2018211977A1 (ja) * | 2017-05-16 | 2020-05-14 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、酸化物半導体膜、ならびに半導体デバイスの製造方法 |
KR20200009007A (ko) * | 2017-05-16 | 2020-01-29 | 스미토모덴키고교가부시키가이샤 | 산화물 소결체 및 그 제조 방법, 스퍼터 타겟, 산화물 반도체막, 그리고 반도체 디바이스의 제조 방법 |
KR102573496B1 (ko) | 2017-05-16 | 2023-08-31 | 미쓰이금속광업주식회사 | 산화물 소결체 및 그 제조 방법, 스퍼터 타겟, 산화물 반도체막, 그리고 반도체 디바이스의 제조 방법 |
WO2018211724A1 (ja) * | 2017-05-16 | 2018-11-22 | 住友電気工業株式会社 | 酸化物焼結体およびその製造方法、スパッタターゲット、酸化物半導体膜、ならびに半導体デバイスの製造方法 |
Also Published As
Publication number | Publication date |
---|---|
KR20160065188A (ko) | 2016-06-08 |
JPWO2016024442A1 (ja) | 2017-05-25 |
EP3181537A1 (en) | 2017-06-21 |
TW201607913A (zh) | 2016-03-01 |
CN105745183A (zh) | 2016-07-06 |
TWI648241B (zh) | 2019-01-21 |
KR101863467B1 (ko) | 2018-05-31 |
CN105745183B (zh) | 2018-03-13 |
JP6428780B2 (ja) | 2018-11-28 |
US20160251264A1 (en) | 2016-09-01 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP6428780B2 (ja) | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイス | |
JP6119773B2 (ja) | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイス | |
JP6137111B2 (ja) | 酸化物焼結体および半導体デバイスの製造方法 | |
JP6493502B2 (ja) | 酸化物焼結体の製造方法 | |
TWI704123B (zh) | 氧化物燒結體及其製造方法、濺鍍靶、以及半導體裝置之製造方法 | |
WO2016063557A1 (ja) | 酸化物焼結体および半導体デバイス | |
JP6593268B2 (ja) | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 | |
JP6233447B2 (ja) | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイス | |
JP6350466B2 (ja) | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 | |
JP6493501B2 (ja) | 酸化物焼結体の製造方法 | |
WO2018083837A1 (ja) | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 | |
JP2016060686A (ja) | 酸化物焼結体およびその製造方法、スパッタリング用ターゲット、ならびに半導体デバイス | |
JP6493601B2 (ja) | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 | |
JP6458883B2 (ja) | 酸化物焼結体およびその製造方法、スパッタターゲット、ならびに半導体デバイスの製造方法 | |
JP6255813B2 (ja) | 酸化物焼結体および半導体デバイス |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 15832559 Country of ref document: EP Kind code of ref document: A1 |
|
REEP | Request for entry into the european phase |
Ref document number: 2015832559 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 15027396 Country of ref document: US |
|
ENP | Entry into the national phase |
Ref document number: 2016542516 Country of ref document: JP Kind code of ref document: A |
|
ENP | Entry into the national phase |
Ref document number: 20167011648 Country of ref document: KR Kind code of ref document: A |
|
NENP | Non-entry into the national phase |
Ref country code: DE |