WO2013094058A1 - 窒化アルミニウム単結晶基板、およびこれらの製造方法 - Google Patents
窒化アルミニウム単結晶基板、およびこれらの製造方法 Download PDFInfo
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- WO2013094058A1 WO2013094058A1 PCT/JP2011/079838 JP2011079838W WO2013094058A1 WO 2013094058 A1 WO2013094058 A1 WO 2013094058A1 JP 2011079838 W JP2011079838 W JP 2011079838W WO 2013094058 A1 WO2013094058 A1 WO 2013094058A1
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- single crystal
- aln
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- PMHQVHHXPFUNSP-UHFFFAOYSA-M copper(1+);methylsulfanylmethane;bromide Chemical compound Br[Cu].CSC PMHQVHHXPFUNSP-UHFFFAOYSA-M 0.000 title claims abstract description 194
- 239000013078 crystal Substances 0.000 title claims abstract description 186
- 239000000758 substrate Substances 0.000 title claims description 60
- 238000004519 manufacturing process Methods 0.000 title claims description 15
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 59
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 57
- 229910052801 chlorine Inorganic materials 0.000 claims abstract description 39
- 239000000460 chlorine Substances 0.000 claims abstract description 36
- ZAMOUSCENKQFHK-UHFFFAOYSA-N Chlorine atom Chemical compound [Cl] ZAMOUSCENKQFHK-UHFFFAOYSA-N 0.000 claims abstract description 34
- 238000010521 absorption reaction Methods 0.000 claims abstract description 29
- 238000000034 method Methods 0.000 claims description 45
- 238000002248 hydride vapour-phase epitaxy Methods 0.000 claims description 37
- 125000004429 atom Chemical group 0.000 claims description 31
- 239000007789 gas Substances 0.000 claims description 22
- 125000004432 carbon atom Chemical group C* 0.000 claims description 21
- 239000000463 material Substances 0.000 claims description 21
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 19
- 229910052760 oxygen Inorganic materials 0.000 claims description 19
- 239000001301 oxygen Substances 0.000 claims description 19
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 18
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 18
- 229910052796 boron Inorganic materials 0.000 claims description 18
- 229910052710 silicon Inorganic materials 0.000 claims description 18
- 239000010703 silicon Substances 0.000 claims description 18
- 230000002829 reductive effect Effects 0.000 claims description 14
- 238000005259 measurement Methods 0.000 claims description 12
- 238000000354 decomposition reaction Methods 0.000 claims description 10
- 238000005424 photoluminescence Methods 0.000 claims description 10
- 238000005979 thermal decomposition reaction Methods 0.000 claims description 9
- 229910052721 tungsten Inorganic materials 0.000 claims description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 239000010410 layer Substances 0.000 description 58
- 239000012535 impurity Substances 0.000 description 57
- 238000002834 transmittance Methods 0.000 description 44
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 24
- 125000001309 chloro group Chemical group Cl* 0.000 description 17
- 238000002441 X-ray diffraction Methods 0.000 description 14
- 230000005540 biological transmission Effects 0.000 description 13
- 229910052757 nitrogen Inorganic materials 0.000 description 13
- 239000002131 composite material Substances 0.000 description 11
- 229910002804 graphite Inorganic materials 0.000 description 11
- 239000010439 graphite Substances 0.000 description 11
- 125000004430 oxygen atom Chemical group O* 0.000 description 10
- 150000004767 nitrides Chemical class 0.000 description 9
- 238000005498 polishing Methods 0.000 description 9
- 150000001721 carbon Chemical group 0.000 description 8
- 239000004065 semiconductor Substances 0.000 description 8
- VSCWAEJMTAWNJL-UHFFFAOYSA-K aluminium trichloride Chemical compound Cl[Al](Cl)Cl VSCWAEJMTAWNJL-UHFFFAOYSA-K 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 6
- 238000000103 photoluminescence spectrum Methods 0.000 description 6
- 230000007547 defect Effects 0.000 description 5
- 239000010409 thin film Substances 0.000 description 5
- 239000012159 carrier gas Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 4
- 229910010271 silicon carbide Inorganic materials 0.000 description 4
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 3
- KFZMGEQAYNKOFK-UHFFFAOYSA-N Isopropanol Chemical compound CC(C)O KFZMGEQAYNKOFK-UHFFFAOYSA-N 0.000 description 3
- 239000002585 base Substances 0.000 description 3
- 239000011247 coating layer Substances 0.000 description 3
- 229910052736 halogen Inorganic materials 0.000 description 3
- 150000002367 halogens Chemical class 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 238000002156 mixing Methods 0.000 description 3
- 125000004433 nitrogen atom Chemical group N* 0.000 description 3
- 229910052594 sapphire Inorganic materials 0.000 description 3
- 239000010980 sapphire Substances 0.000 description 3
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000000919 ceramic Substances 0.000 description 2
- 238000011109 contamination Methods 0.000 description 2
- 229910001873 dinitrogen Inorganic materials 0.000 description 2
- 230000005284 excitation Effects 0.000 description 2
- 150000002500 ions Chemical class 0.000 description 2
- 238000004020 luminiscence type Methods 0.000 description 2
- 229910021421 monocrystalline silicon Inorganic materials 0.000 description 2
- 238000001228 spectrum Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910003468 tantalcarbide Inorganic materials 0.000 description 2
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 description 2
- 239000010937 tungsten Substances 0.000 description 2
- 229910021642 ultra pure water Inorganic materials 0.000 description 2
- 239000012498 ultrapure water Substances 0.000 description 2
- PIGFYZPCRLYGLF-UHFFFAOYSA-N Aluminum nitride Chemical compound [Al]#N PIGFYZPCRLYGLF-UHFFFAOYSA-N 0.000 description 1
- 108020000946 Bacterial DNA Proteins 0.000 description 1
- 108020004414 DNA Proteins 0.000 description 1
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 230000001133 acceleration Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- AZDRQVAHHNSJOQ-UHFFFAOYSA-N alumane Chemical group [AlH3] AZDRQVAHHNSJOQ-UHFFFAOYSA-N 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- RNQKDQAVIXDKAG-UHFFFAOYSA-N aluminum gallium Chemical compound [Al].[Ga] RNQKDQAVIXDKAG-UHFFFAOYSA-N 0.000 description 1
- 238000000149 argon plasma sintering Methods 0.000 description 1
- NWAIGJYBQQYSPW-UHFFFAOYSA-N azanylidyneindigane Chemical compound [In]#N NWAIGJYBQQYSPW-UHFFFAOYSA-N 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 230000008033 biological extinction Effects 0.000 description 1
- 229910052792 caesium Inorganic materials 0.000 description 1
- 238000011088 calibration curve Methods 0.000 description 1
- -1 cesium ions Chemical class 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000002109 crystal growth method Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000000407 epitaxy Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000010408 film Substances 0.000 description 1
- 239000007770 graphite material Substances 0.000 description 1
- 229910000041 hydrogen chloride Inorganic materials 0.000 description 1
- IXCSERBJSXMMFS-UHFFFAOYSA-N hydrogen chloride Substances Cl.Cl IXCSERBJSXMMFS-UHFFFAOYSA-N 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 230000010354 integration Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 230000001678 irradiating effect Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000006386 neutralization reaction Methods 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000001004 secondary ion mass spectrometry Methods 0.000 description 1
- 230000001954 sterilising effect Effects 0.000 description 1
- 238000004659 sterilization and disinfection Methods 0.000 description 1
- 238000005092 sublimation method Methods 0.000 description 1
- 229910052715 tantalum Inorganic materials 0.000 description 1
- 238000000870 ultraviolet spectroscopy Methods 0.000 description 1
- 238000001947 vapour-phase growth Methods 0.000 description 1
Classifications
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L33/00—Semiconductor devices having potential barriers specially adapted for light emission; Processes or apparatus specially adapted for the manufacture or treatment thereof or of parts thereof; Details thereof
- H01L33/02—Semiconductor devices having potential barriers specially adapted for light emission; Processes or apparatus specially adapted for the manufacture or treatment thereof or of parts thereof; Details thereof characterised by the semiconductor bodies
- H01L33/26—Materials of the light emitting region
- H01L33/34—Materials of the light emitting region containing only elements of Group IV of the Periodic Table
- H01L33/343—Materials of the light emitting region containing only elements of Group IV of the Periodic Table characterised by the doping materials
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B25/00—Single-crystal growth by chemical reaction of reactive gases, e.g. chemical vapour-deposition growth
- C30B25/02—Epitaxial-layer growth
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B25/00—Single-crystal growth by chemical reaction of reactive gases, e.g. chemical vapour-deposition growth
- C30B25/02—Epitaxial-layer growth
- C30B25/08—Reaction chambers; Selection of materials therefor
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/10—Inorganic compounds or compositions
- C30B29/40—AIIIBV compounds wherein A is B, Al, Ga, In or Tl and B is N, P, As, Sb or Bi
- C30B29/403—AIII-nitrides
-
- 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
- H01L21/02538—Group 13/15 materials
- H01L21/0254—Nitrides
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L33/00—Semiconductor devices having potential barriers specially adapted for light emission; Processes or apparatus specially adapted for the manufacture or treatment thereof or of parts thereof; Details thereof
- H01L33/005—Processes
- H01L33/0054—Processes for devices with an active region comprising only group IV elements
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B23/00—Single-crystal growth by condensing evaporated or sublimed materials
Definitions
- the present invention relates to a novel aluminum nitride (hereinafter sometimes referred to as AlN) single crystal and a method for producing the same. More specifically, the present invention relates to a novel AlN single crystal having a low concentration of carbon atoms contained in the AlN single crystal and good ultraviolet light transmittance, and a method for producing the same.
- AlN aluminum nitride
- a semiconductor element such as an ultraviolet light emitting element, a cladding layer, an active layer, etc. are provided between an n-type semiconductor layer electrically bonded to the n-electrode and a p-type semiconductor layer electrically bonded to the p-electrode. It is necessary to form a laminated structure including it, and from the viewpoint of light emission efficiency, it is important that any layer has high crystallinity, that is, few crystal dislocations and point defects. For these reasons, the above laminated structure is generally formed on a single crystal substrate (hereinafter, also referred to as “self-standing substrate”) having sufficient mechanical strength to exist independently.
- a single crystal substrate hereinafter, also referred to as “self-standing substrate” having sufficient mechanical strength to exist independently.
- the self-standing substrate for forming the laminated structure has a small lattice constant difference and thermal expansion coefficient difference from an Al group III nitride single crystal such as aluminum gallium indium nitride (AlGaInN) forming the laminated structure, A high thermal conductivity is required from the viewpoint of preventing deterioration of the element. Therefore, in order to produce a semiconductor element containing AlN, it is advantageous to form the above layer structure using an Al-based group III nitride single crystal substrate as a self-supporting substrate.
- AlGaInN aluminum gallium indium nitride
- the Al-based group III nitride single crystal substrate which is a self-supporting substrate transmits light. If light cannot be transmitted, even if the light emission efficiency of the semiconductor device structure is high, the light is absorbed by the Al-based group III nitride single crystal substrate, resulting in an ultraviolet light emitting device with low light emission efficiency. .
- aluminum nitride single crystal in particular, has a band gap energy of about 6 eV and can emit light with a short wavelength in the ultraviolet region.
- Use as a base substrate is expected. From the viewpoint of efficiency as an LED, it is important for the AlN single crystal to transmit light having a short wavelength in the ultraviolet region, and the higher the transmittance, the more useful the LED for the light source.
- HVPE method hydride vapor phase epitaxy method
- Patent Document 2 as a method of reducing the absorption coefficient of a nitride semiconductor single crystal substrate, that is, improving the transmittance of the nitride semiconductor single crystal substrate, 1 ⁇ 10 17 cm ⁇ 3 or less as an impurity of AlN
- the total impurity density is described as having an absorption coefficient of 50 cm ⁇ 1 or less in the entire wavelength range of 350 to 780 nm.
- the substrate temperature during the growth of a single crystal is set to a relatively low value of 900 to 1100 ° C., the concentration of all impurities can be suppressed, while the crystallinity may be lowered.
- light having a wavelength of 265 nm which is ultraviolet light, is easily absorbed by bacterial DNA, is useful for sterilization from the viewpoint of destroying DNA, and is expected to be put to practical use.
- the transmittance of 300 nm or less, particularly 265 nm, necessary as a base substrate of the LED for the white light source is sufficient. Instead, it was desired to improve the transmittance around 265 nm.
- AlN single crystals produced by the hydride vapor phase epitaxy method are known to have a relatively high light transmittance to 265 nm, but the light transmittance is about 40% (the absorption coefficient at 265 nm is 120 cm ⁇ 1 ), which is not sufficient (see Non-Patent Document 1).
- an object of the present invention is to provide an AlN single crystal that has good transmittance for light having a short wavelength of 265 nm in the ultraviolet region, in other words, has a low absorption coefficient at 265 nm. Furthermore, it is providing the manufacturing method of the said AlN single crystal with favorable ultraviolet-light transmittance.
- the present inventors have conducted intensive studies. Then, paying attention to the type and concentration of impurity atoms contained in the AlN single crystal, the light transmittance in the ultraviolet region of the AlN single crystal was examined. Then, even if the AlN single crystal obtained by growing at a high temperature by the HVPE method contains a large amount of impurities of 1 ⁇ 10 15 to 1 ⁇ 10 20 atoms / cm 3 , If the concentration is 1 ⁇ 10 14 atoms / cm 3 or more and less than 3 ⁇ 10 17 atoms / cm 3 and the chlorine concentration is 1 ⁇ 10 14 to 1 ⁇ 10 17 atoms / cm 3 , the short wavelength in the ultraviolet region is 265 nm.
- the main atom that hinders the transmission of light at 265 nm is a carbon atom.
- the concentration of chlorine atoms contained in the AlN single crystal to a relatively low concentration instead of zero, and controlling the carbon concentration as low as possible, the ultraviolet light transmittance is good.
- the inventors have found that an AlN single crystal can be obtained, and have completed the present invention.
- the gist of the present invention for solving the above problems is as follows.
- the carbon concentration is 1 ⁇ 10 14 atoms / cm 3 or more and less than 3 ⁇ 10 17 atoms / cm 3
- the chlorine concentration is 1 ⁇ 10 14 to 1 ⁇ 10 17 atoms / cm 3
- An aluminum nitride single crystal having an absorption coefficient at 265 nm of 40 cm ⁇ 1 or less.
- An aluminum nitride single crystal is grown on the substrate, and the exposed surface in the hydride vapor phase epitaxy apparatus at a temperature of 1200 ° C. or higher during crystal growth is not reduced or thermally decomposed at a temperature of 1200 ° C. or higher and 1700 ° C. or lower.
- the exposed surface of the region of 1200 ° C. or higher in the hydride vapor phase epitaxy apparatus is preferably composed of at least one selected from the group consisting of BN, TaC, W and Mo (5 )
- a method for producing an aluminum nitride single crystal is preferably composed of at least one selected from the group consisting of BN, TaC, W and Mo (5 ) A method for producing an aluminum nitride single crystal.
- the light transmittance of the AlN single crystal is determined by a number of complicated factors (for example, factors such as manufacturing conditions and crystallinity reflecting it). Therefore, simply reducing the total impurity concentration does not improve the light transmittance.
- An ideal single crystal that does not contain any impurities (the total amount of impurities is zero) and has no defects is considered to exhibit light transmittance close to the theoretical value, but from the raw material or from the atmosphere in the single crystal manufacturing process. It is impossible with current technology to completely eliminate the contamination and to eliminate all defects.
- the aluminum nitride (AlN) single crystal of the present invention has excellent ultraviolet light transmittance even when the total impurity concentration is relatively high, and an AlN single crystal that can be used for LEDs in the ultraviolet region is obtained. be able to.
- AlN single crystal having such an excellent characteristic was obtained by crystal growth at a temperature exceeding 1200 ° C. in the HVPE method, having good crystallinity and a predetermined amount of C and Cl as impurities.
- the transmittance in a short wavelength region of 300 nm or less greatly depends on the concentration of carbon contained as an impurity.
- Patent Document 2 Even in Patent Document 2, an AlN single crystal is obtained under a condition that the total impurity concentration is lowered by the HVPE method (naturally, the impurity carbon concentration is also lowered).
- crystal growth is performed at a temperature of 1100 ° C. or lower. Therefore, it is considered that the light transmittance for light having a wavelength of 300 nm or less could not be improved even if the carbon concentration was low due to the influence of crystallinity and other impurity elements.
- the carbon concentration is 1 ⁇ 10 14 atoms / cm 3 or more and less than 3 ⁇ 10 17 atoms / cm 3
- the chlorine concentration is 1 ⁇ 10 14 to 1 ⁇ 10 17 atoms / cm 3
- the present invention relates to an AlN single crystal having an absorption coefficient at 265 nm of 40 cm ⁇ 1 or less.
- the AlN single crystal of the present invention has high transparency to light having a wavelength of 265 nm even if the total impurity concentration is relatively high, as long as the concentration of carbon atoms and chlorine atoms contained as impurities is within a predetermined range. Can do.
- the reason why the AlN single crystal of the present invention can exhibit excellent transparency to light having a wavelength of 265 nm is not necessarily clear, but the present inventors have estimated as follows. That is, in the AlN single crystal having particularly good crystallinity, as described in detail later, the cause of deteriorating the ultraviolet light transmission characteristics is N vacancies generated when carbon impurities are mixed into the AlN single crystal. In addition to reducing the carbon impurity concentration, it is estimated that the formation of N vacancies was suppressed by the electrical neutralization effect of chlorine atoms inevitably mixed in the HVPE method, and the ultraviolet light transmission characteristics were improved. is doing.
- the N vacancies have a negative charge because they originally lack nitrogen atoms that were in the nitrogen lattice sites of AlN. In this way, when carbon atoms are mixed as impurities, it is considered that the electrical neutrality in the AlN single crystal is maintained by compensating the charges by generating N vacancies. It is done.
- the ultraviolet light transmission characteristics in the wavelength region are deteriorated particularly when a large amount of carbon impurities is contained among the impurities. Therefore, the present inventors have estimated that N vacancies generated when carbon impurities are mixed into the AlN single crystal deteriorate the ultraviolet light transmission characteristics.
- chlorine impurities are mixed into the AlN single crystal from a halogen gas containing aluminum atoms, which is a raw material gas for growing the AlN single crystal.
- concentration of chlorine impurities taken into the AlN single crystal is affected by the growth conditions and the influence of the airflow in the HVPE apparatus, generally, the concentration of chlorine impurities tends to increase as the temperature for growing the AlN single crystal increases. There is.
- by controlling the carbon impurity it is possible to maintain the ultraviolet light transmission characteristics even if the concentration of the chlorine impurity is increased.
- halogen-based gas is not used for the raw material gas, so that halogen is not mixed in principle.
- Chlorine impurities are mixed by hydride vapor phase epitaxy. This is a characteristic characteristic of the grown AlN single crystal.
- N vacancies generated by the mixing of carbon impurities can be reduced by making the mixing of carbon impurities, chlorine impurities, etc. within a certain range.
- the present inventors presume that the AlN single crystal of the present invention has good ultraviolet light transmission characteristics.
- the carbon and chlorine concentrations must satisfy the above range.
- the concentration of carbon and chlorine is 1 ⁇ 10 14 atoms / cm 3 or more and less than 3 ⁇ 10 17 atoms / cm 3 (carbon Concentration) and 1 ⁇ 10 14 to 1 ⁇ 10 17 atoms / cm 3 (chlorine concentration), and more preferably 5 ⁇ 10 14 to 1 ⁇ 10 17 atoms / cm 3 (carbon concentration) and 5 ⁇ 10 14 to 5 ⁇ 10 16 atoms / cm 3 (chlorine concentration) is preferable. Furthermore, it is more preferable to set to 1 ⁇ 10 15 to 1 ⁇ 10 17 atoms / cm 3 (carbon concentration) and 1 ⁇ 10 15 to 1 ⁇ 10 16 atoms / cm 3 (chlorine concentration).
- the total concentration of carbon, chlorine, boron, silicon and oxygen contained in the AlN single crystal is preferably 1 ⁇ 10 15 to 1 ⁇ 10 20 atoms / cm 3 , more preferably 1 ⁇ 10. 16 to 5 ⁇ 10 19 atoms / cm 3 , more preferably 1 ⁇ 10 17 to 1 ⁇ 10 19 atoms / cm 3 .
- the concentrations of boron, silicon, and oxygen are preferably 1 ⁇ 10 15 to 5 ⁇ 10 19 atoms / cm 3 , more preferably 1 ⁇ 10 16 to 1 ⁇ 10 19 atoms / cm 3 , and still more preferably. 5 ⁇ 10 16 to 1 ⁇ 10 18 atoms / cm 3 .
- impurities are usually mixed from members of a crystal growth apparatus or a raw material for growing an AlN single crystal. Even if the single crystal AlN of the present invention contains such an impurity, it can increase the transparency to light having a wavelength of 300 nm or less, for example, 265 nm.
- the absorption coefficient at a wavelength of 265 nm which is an index of ultraviolet light transmission, is 40 cm ⁇ 1 or less, more preferably 30 cm ⁇ 1 or less.
- a product of 20 cm ⁇ 1 or less can be obtained.
- An absorption coefficient (unit: cm ⁇ 1 ) is used as an index of good or bad light transmission. The smaller the absorption coefficient, the better the light transmittance.
- the absorption coefficient are those values depending on different wavelengths, for use as ultraviolet light-emitting diodes, the absorption coefficient at a wavelength of 265nm is 40 cm -1 or less, more 30 cm -1 or less, more preferably 20 cm -1 It is as follows. Further, the smaller the absorption coefficient is, the better the light transmittance is. Therefore, the lower limit is better, and it is not particularly limited. However, considering industrial production, the lower limit of the absorption coefficient at a wavelength of 265 nm is 1 cm ⁇ 1 . In the present invention, the ultraviolet light transmission index is indicated by an absorption coefficient at a wavelength of 265 nm. However, if the absorption coefficient is a low value satisfying the above range at a wavelength of 265 nm, the absorption coefficient at a wavelength of 240 to 300 nm. Is naturally low, and the light transmission in this region is good.
- the half width of the X-ray rocking curve of the (0002) plane of the AlN single crystal is preferably 3000 seconds or less, more preferably 1 to 1500 seconds, and further preferably 5 to 1000 seconds.
- the effect of the present invention tends to be difficult to obtain.
- the crystal growth temperature in order to improve the crystallinity, it is necessary to increase the crystal growth temperature.
- problems such as increased contamination of impurities occur.
- the present invention as described above, it is only necessary to control the mixing amount of carbon and chlorine, so that such excellent crystallinity can be easily achieved.
- the peak due to the c-plane of AlN such as the (0002) plane or the (0004) plane when X-ray diffraction ⁇ -2 ⁇ mode measurement is performed. Is mainly observed.
- the AlN single crystal of the present invention can confirm a peak at 209 nm, which is the band edge emission of AlN, in photoluminescence measurement. That is, using a 193 nm ArF laser as an excitation light source, the sample is irradiated vertically to excite the sample. Further, the luminescence light generated from the sample is imaged by a focusing lens and then detected by a spectroscope to obtain an intensity spectrum with respect to the wavelength. In the band edge emission, the emission wavelength may slightly vary depending on the impurities contained in AlN. However, in the AlN single crystal of the present invention, band edge emission is observed in the range of 205 to 215 nm when measured at room temperature (23 ° C.). .
- the method for producing an AlN single crystal of the present invention is not particularly limited as long as the carbon concentration and the chlorine concentration can be controlled within a predetermined range, but the single crystal AlN of the present invention can be produced with good reproducibility.
- HVPE method hydride vapor phase epitaxy method
- the HVPE method is a method of growing AlN by supplying an Al source gas and a nitrogen source gas onto a heated single crystal substrate.
- aluminum trichloride gas is used as the Al source gas.
- ammonia gas is used as the nitrogen source gas.
- aluminum trichloride gas is preferably used as the Al source gas because the concentration of chlorine contained in the single crystal AlN is easily controlled.
- the single crystal substrate is not particularly limited as long as it is a single crystal AlN substrate with good crystallinity, but for the reason that the single crystal AlN of the present invention with good crystallinity can be obtained efficiently, the following It is preferable to use a single-crystal AlN free-standing substrate obtained by the method or a composite AlN free-standing substrate in which a layer made of single-crystal AlN is laminated on a main layer made of polycrystalline and / or amorphous AlN.
- the single crystal AlN free-standing substrate can be suitably manufactured by the method disclosed in JP 2010-89971. Specifically, first, a seed crystal substrate having a first AlN single crystal layer on its surface is prepared by a method such as forming a single crystal AlN layer on a heterogeneous single crystal substrate such as sapphire or single crystal Si. Next, on the first AlN single crystal layer of the seed crystal substrate, a layer made of the AlN single crystal (hereinafter sometimes referred to as “second AlN single crystal layer”) is formed by vapor phase growth. A laminated body is manufactured. Next, by separating the second AlN single crystal layer from the laminate (removing the seed crystal substrate), a single crystal AlN free-standing substrate made of an AlN single crystal (second AlN single crystal layer) is obtained. Can do.
- a seed crystal substrate having a first AlN single crystal layer on its surface is prepared by a method such as forming a single crystal AlN layer on a heterogeneous single crystal substrate such as sapphire or single crystal Si.
- the composite AlN free-standing substrate can be manufactured, for example, according to the method described in WO2009 / 090821 and JP2010-10613.
- a single crystal AlN thin film layer is formed on a heterogeneous single crystal substrate such as sapphire or single crystal Si, and an AlN non-single crystal layer made of polycrystalline, amorphous, or a mixture thereof is formed thereon. Then, it can be manufactured by removing the heterogeneous single crystal substrate.
- a heterogeneous single crystal substrate such as sapphire or single crystal Si
- an AlN non-single crystal layer made of polycrystalline, amorphous, or a mixture thereof is formed thereon. Then, it can be manufactured by removing the heterogeneous single crystal substrate.
- the composite AlN free-standing substrate is used as a substrate for the HVPE method
- the single crystal AlN thin film layer exposed by removing the different single crystal substrate is used as the crystal growth surface.
- the thickness of the single crystal AlN thin film layer forming the outermost surface is 10 nm to 1.5 ⁇ m, and the thickness of the AlN non-single crystal layer is However, those having a thickness 100 times or more that of the AlN single crystal thin film layer are preferably used.
- the growth temperature (substrate temperature at the time of crystal growth) is set to 1200 ° C. or more and 1700 ° C. or less.
- a material that does not undergo reductive decomposition or thermal decomposition of the exposed surface of a region in the apparatus (hereinafter also referred to as a “high temperature heating region”) that is 1200 ° C. or higher during crystal growth at a temperature of 1200 ° C. or higher and 1700 ° C. or lower, or reductive decomposition
- it is necessary to use an apparatus composed only of members made of materials that do not generate carbon atom-containing gas even when pyrolyzed hereinafter collectively referred to as “carbon-free materials”).
- the chlorine concentration contained in the grown single crystal AlN may be outside the range of the chlorine concentration in the single crystal AlN of the present invention, but also a single crystal with high crystallinity. It becomes difficult to obtain AlN, and the single crystal AlN of the present invention cannot be produced with good reproducibility.
- an HVPE apparatus an apparatus in which a material that generates a gas containing carbon atoms by reductive decomposition or thermal decomposition at a temperature of 1200 ° C. or higher and 1700 ° C. or lower in a region where the temperature is 1200 ° C. or higher during crystal growth is exposed. Is used, it is very difficult to make the carbon concentration contained in the single crystal AlN within the range of the single crystal AlN of the present invention.
- the HVPE apparatus will be described in more detail.
- the HVPE apparatus currently used is a susceptor equipped with a high-frequency induction heating apparatus or a rotation mechanism in order to grow single crystal AlN having good crystallinity uniformly and at high speed on a substrate.
- graphite or silicon carbide is generally used as a material of a member constituting a region having a temperature of 1200 ° C. or higher.
- a nitride ceramic sintered member, graphite, or the like was surface-coated with TaC or BN having extremely high heat resistance.
- a member etc. may be used, and the carbon generation amount can be significantly reduced by taking such measures.
- the inventors of the present invention thoroughly studied the above-described points regarding the HVPE apparatus, and took measures to configure the exposed surface of the high-temperature heating region in the HVPE apparatus only with members made of carbon-free materials.
- the single crystal AlN of the present invention was successfully produced.
- the underlying material is exposed on the surface (via the pinholes). Therefore, when using a member whose surface is coated with a graphite material such as TaC or BN, it is necessary to strictly check for the presence of pinholes and use those that do not have pinholes. Also, if a gas containing carbon atoms leaks into the reaction atmosphere through a gap after the screws are mounted, at least the surface thereof needs to be a carbon-free material.
- BN, TaC, W, Mo, Ta etc. can be considered as a carbon non-generation material.
- carbon, carbon with SiC coating layer, BN sintered body, AlN sintered body, SiC sintered body, TaC or BN coated Even if it is carbon with a layer, what has a crack and a pinhole in a coating layer, etc. can be considered.
- the single crystal AlN of the present invention can be grown in the presence of a suitable carbon source and chlorine source by employing the above conditions.
- the thickness of the layer made of the AlN of the present invention obtained by the method of the present invention is not particularly limited, and may be appropriately determined according to the application to be used. Usually, it is 50 ⁇ m or more and 2000 ⁇ m or less.
- the AlN single crystal of the present invention can be obtained by separating and removing the substrate from the laminate produced by the above method.
- a known method can be adopted as a method for separating and removing the substrate.
- the seed crystal substrate can be removed from the laminate by mechanically cutting or polishing to obtain a second AlN single crystal layer (AlN single crystal of the present invention).
- Example 1 (Preparation of substrate)
- a composite AlN free-standing substrate was produced as a substrate by the method described in WO2009 / 090821.
- the thickness of the AlN single crystal thin film layer constituting the AlN single crystal plane is 230 nm
- the thickness of the underlying AlN non-single crystal layer is 350 ⁇ m.
- the composite AlN free-standing substrate was cleaned in acetone for 3 minutes with an ultrasonic wave with a frequency of 100 kHz, and further washed in 2-propanol with an ultrasonic wave with a frequency of 100 kHz for 3 minutes, and then with ultrapure water. Rinse and blow the substrate with dry nitrogen to remove ultra pure water.
- the susceptor is made of BN coated graphite with the entire surface of the susceptor, BN is used for the susceptor rotation shaft and the heat shield around the susceptor, and BN is used to fix the susceptor and the rotation shaft.
- a graphite screw coated with is used.
- the BN coat layer of the susceptor was observed over the entire periphery with a stereomicroscope at an observation magnification of 8 to 56 times, and it was confirmed that there were no pinholes or cracks in the coat layer.
- the composite AlN free-standing substrate is placed on a tungsten susceptor in an HVPE apparatus so that the AlN single crystal surface becomes the outermost surface, and then the pressure is set to 150 Torr, and hydrogen gas (7000 sccm) and nitrogen gas (3000 sccm) are mixed. While circulating with a carrier gas, the composite AlN free-standing substrate was heated to 1450 ° C. and held for 10 minutes to perform surface cleaning. At this time, ammonia gas was supplied so that it might become 0.5 volume% with respect to the total carrier gas flow rate (10000 sccm). Next, aluminum chloride gas obtained by reacting metal aluminum heated to 420 ° C. with hydrogen chloride gas was supplied at 0.05% by volume with respect to the total carrier gas flow rate. This state was maintained for 15 hours, and an AlN single crystal layer of the present invention was grown on the substrate by 300 ⁇ m.
- the supply of aluminum chloride gas was stopped, and the type of carrier gas was switched to nitrogen gas and cooled to room temperature. Ammonia gas was continuously supplied until the substrate temperature dropped to 800 ° C.
- the composite AlN free-standing substrate used in this example is supported by an AlN polycrystalline layer having a thickness of 350 ⁇ m.
- the AlN polycrystalline layer has many particle interfaces, light scattering occurs and ultraviolet light transmittance is reduced. I can't get it. Therefore, in order to evaluate the absorption coefficient of the grown AlN single crystal layer, the composite AlN free-standing substrate is removed by polishing, and the surface of the remaining AlN single crystal layer is further polished, thereby growing the grown AlN single crystal layer.
- a sample made of AlN single crystal consisting of only 200 ⁇ m thick was prepared. The surface of the sample was finished in a double-sided mirror polished state having an RMS value of about 5 nm.
- the concentration of oxygen atoms and the concentration of carbon atoms in the sample were determined based on a calibration curve using a separately prepared AlN standard sample by measuring the secondary ion intensity at a depth of 5 ⁇ m from the surface side.
- the carbon atom concentration of the sample was 1 ⁇ 10 17 cm ⁇ 3
- the oxygen atom concentration was 3 ⁇ 10 17 cm ⁇ 3 .
- the concentration of chlorine atoms is 1 ⁇ 10 15 cm ⁇ 3
- the total concentration of carbon, chlorine, boron, silicon and oxygen contained in this sample is 5.1 ⁇ 10 17 cm ⁇ 3.
- the total concentration of boron, silicon, and oxygen contained in the solution was 4.1 ⁇ 10 17 cm ⁇ 3 .
- the half-value width of the X-ray rocking curve on the (0002) plane of the sample was 1200 seconds. Further, when X-ray diffraction measurement of the ⁇ -2 ⁇ mode was performed, only the (0002) plane and (0004) plane of AlN were observed.
- photoluminescence measurement at room temperature was performed.
- HT800UV Laser light source: ExciStarS-200
- Horiba, Ltd. was used as a measuring apparatus.
- the sample was excited by irradiating the sample perpendicularly.
- the luminescence light generated from the sample was imaged with a condenser lens and then detected with a spectroscope to obtain a spectrum with respect to wavelength.
- the irradiation time was 10 seconds, the number of integrations was 3, the hole diameter was 1000 ⁇ m, and the grating was 300 grooves / mm.
- a peak near 209 nm which is emission at the band edge of AlN, was confirmed.
- Example 2 In order to fix the susceptor and the rotating shaft of the HVPE apparatus, a tungsten screw was used, and the temperature during growth of the AlN single crystal layer of the present invention was set to 1350 ° C. A crystal layer was grown.
- a sample having a thickness of 200 ⁇ m composed of only the grown AlN single crystal layer is prepared by mirror polishing both surfaces, and the linear transmittance at 265 nm, the concentration of impurities, the half-value width of the X-ray rocking curve of the (0002) plane, An X-ray diffraction profile and a photoluminescence spectrum in the ⁇ -2 ⁇ mode were measured by the same method as in Example 1.
- the linear transmittance was 58%, and the absorption coefficient was calculated to be 27 cm ⁇ 1 .
- the concentration of carbon atoms was 3 ⁇ 10 16 cm ⁇ 3 and the concentration of oxygen atoms was 5 ⁇ 10 17 cm ⁇ 3 .
- the concentration of chlorine atoms is 5 ⁇ 10 15 cm ⁇ 3
- the total concentration of carbon, chlorine, boron, silicon and oxygen contained in this sample is 8.4 ⁇ 10 17 cm ⁇ 3.
- the total concentration of boron, silicon, and oxygen contained in the solution was 8.0 ⁇ 10 17 cm ⁇ 3 .
- the half width of the X-ray rocking curve on the (0002) plane of the sample was 1800 seconds. Further, when X-ray diffraction measurement of the ⁇ -2 ⁇ mode was performed, only the (0002) plane and (0004) plane of AlN were observed. In addition, as a result of performing photoluminescence measurement at room temperature (23 ° C.), a peak near 209 nm, which is AlN band edge emission, was confirmed.
- Example 3 In order to fix the susceptor and the rotating shaft of the HVPE apparatus, a TaC screw was used, and the temperature during growth of the AlN single crystal layer of the present invention was set to 1250 ° C. A crystal layer was grown.
- a sample having a thickness of 200 ⁇ m composed of only the grown AlN single crystal layer is prepared by mirror polishing both surfaces, and the linear transmittance at 265 nm, the concentration of impurities, the half-value width of the X-ray rocking curve of the (0002) plane, An X-ray diffraction profile and a photoluminescence spectrum in the ⁇ -2 ⁇ mode were measured by the same method as in Example 1.
- the linear transmittance was calculated to be 45%
- the absorption coefficient was calculated to be 40 cm ⁇ 1 .
- the concentration of carbon atoms was 3 ⁇ 10 16 cm ⁇ 3
- the concentration of oxygen atoms was 1 ⁇ 10 17 cm ⁇ 3 .
- the concentration of chlorine atoms is 7 ⁇ 10 14 cm ⁇ 3
- the total concentration of carbon, chlorine, boron, silicon and oxygen contained in this sample is 5.3 ⁇ 10 17 cm ⁇ 3.
- the total concentration of boron, silicon, and oxygen contained in was 5.0 ⁇ 10 17 cm ⁇ 3 .
- the half width of the X-ray rocking curve on the (0002) plane of the sample was 2800 seconds. Further, when X-ray diffraction measurement of the ⁇ -2 ⁇ mode was performed, only the (0002) plane and (0004) plane of AlN were observed. In addition, as a result of performing photoluminescence measurement at room temperature (23 ° C.), a peak near 209 nm, which is AlN band edge emission, was confirmed.
- Comparative Example 1 In order to fix the susceptor and the rotating shaft of the HVPE apparatus, a graphite screw was used, and the temperature during growth of the AlN single crystal layer of the present invention was changed to 1550 ° C. A crystal layer was grown.
- a sample having a thickness of 200 ⁇ m composed of only the grown AlN single crystal layer is prepared by mirror polishing both surfaces, and the linear transmittance at 265 nm, the concentration of impurities, the half-value width of the X-ray rocking curve of the (0002) plane, An X-ray diffraction profile and a photoluminescence spectrum in the ⁇ -2 ⁇ mode were measured by the same method as in Example 1.
- the linear transmittance was 38%, and the absorption coefficient was calculated to be 48 cm ⁇ 1 .
- the concentration of carbon atoms was 7 ⁇ 10 17 cm ⁇ 3
- the concentration of oxygen atoms was 5 ⁇ 10 16 cm ⁇ 3 .
- the concentration of chlorine atoms is 4 ⁇ 10 14 cm ⁇ 3
- the total concentration of carbon, chlorine, boron, silicon, and oxygen contained in this sample is 1.1 ⁇ 10 18 cm ⁇ 3.
- the total concentration of boron, silicon and oxygen contained in was 3.5 ⁇ 10 17 cm ⁇ 3 .
- the half-value width of the X-ray rocking curve on the (0002) plane of the sample was 1000 seconds. Further, when X-ray diffraction measurement of the ⁇ -2 ⁇ mode was performed, only the (0002) plane and (0004) plane of AlN were observed. In addition, as a result of performing photoluminescence measurement at room temperature (23 ° C.), a peak near 209 nm, which is AlN band edge emission, was confirmed.
- Comparative Example 2 The AlN single crystal layer is formed in the same procedure as in Example 1 except that graphite with BN coated on the entire susceptor surface is used as the susceptor material of the HVPE apparatus, and graphite is used for the screws for fixing the susceptor and the rotating shaft. did.
- graphite with BN coated on the entire susceptor surface is used as the susceptor material of the HVPE apparatus, and graphite is used for the screws for fixing the susceptor and the rotating shaft.
- graphite with BN coated on the entire susceptor surface is used as the susceptor material of the HVPE apparatus, and graphite is used for the screws for fixing the susceptor and the rotating shaft. did.
- graphite with BN coated on the entire susceptor surface is used as the susceptor material of the HVPE apparatus, and graphite is used for the screws for fixing the susceptor and the rotating shaft.
- the entire outer periphery of the BN coat layer of the susceptor used in this comparative example
- a sample having a thickness of 200 ⁇ m composed of only the grown AlN single crystal layer is prepared by mirror polishing both surfaces, and the linear transmittance at 265 nm, the concentration of impurities, the half-value width of the X-ray rocking curve of the (0002) plane, An X-ray diffraction profile and a photoluminescence spectrum in the ⁇ -2 ⁇ mode were measured by the same method as in Example 1.
- the linear transmittance was 17%, and the absorption coefficient was calculated to be 90 cm ⁇ 1 .
- the concentration of carbon atoms was 4 ⁇ 10 18 cm ⁇ 3 and the concentration of oxygen atoms was 5 ⁇ 10 16 cm ⁇ 3 .
- the concentration of chlorine atoms is 4 ⁇ 10 15 cm ⁇ 3
- the total concentration of carbon, chlorine, boron, silicon, and oxygen contained in this sample is 4.1 ⁇ 10 18 cm ⁇ 3.
- the total concentration of boron, silicon, and oxygen contained in 9.1 was 9.1 ⁇ 10 16 cm ⁇ 3 .
- the half width of the X-ray rocking curve of the (0002) plane of the sample plate was 1250 seconds. Further, when X-ray diffraction measurement of the ⁇ -2 ⁇ mode was performed, only the (0002) plane and (0004) plane of AlN were observed. In addition, as a result of performing photoluminescence measurement at room temperature (23 ° C.), a peak near 209 nm, which is AlN band edge emission, was confirmed.
- Comparative Example 3 The AlN single crystal is processed in the same manner as in Example 1 except that SiC is used as the susceptor material of the HVPE apparatus, TaC is used as a screw for fixing the susceptor and the rotating shaft, and the thickness of the grown AlN layer is 150 ⁇ m. A layer was formed.
- a sample having a thickness of 150 ⁇ m consisting only of the grown AlN single crystal layer is prepared by mirror polishing both surfaces, and the linear transmittance at 265 nm, the concentration of impurities, the half width of the X-ray rocking curve of the (0002) plane, An X-ray diffraction profile and a photoluminescence spectrum in the ⁇ -2 ⁇ mode were measured by the same method as in Example 1.
- the linear transmittance was 0.1%, and the absorption coefficient was calculated to be 435 cm ⁇ 1 .
- the concentration of carbon atoms was 1 ⁇ 10 19 cm ⁇ 3
- the concentration of oxygen atoms was 5 ⁇ 10 17 cm ⁇ 3 .
- the concentration of chlorine atoms is 8 ⁇ 10 14 cm ⁇ 3
- the total concentration of carbon, chlorine, boron, silicon and oxygen contained in this sample is 1.1 ⁇ 10 19 cm ⁇ 3.
- the total concentration of boron, silicon, and oxygen contained in the solution was 1.0 ⁇ 10 18 cm ⁇ 3 .
- the half width of the X-ray rocking curve on the (0002) plane of the sample was 2500 seconds. Further, when X-ray diffraction measurement of the ⁇ -2 ⁇ mode was performed, only the (0002) plane and (0004) plane of AlN were observed. In addition, as a result of performing photoluminescence measurement at room temperature (23 ° C.), a peak near 209 nm, which is AlN band edge emission, was confirmed.
- Comparative Example 4 Using graphite as the susceptor material of the HVPE apparatus, a sapphire substrate is installed as an oxygen source so as to surround the entire outer periphery of the substrate, and graphite is used as a screw for fixing the susceptor and the rotating shaft.
- An AlN single crystal layer was grown in the same procedure as in Example 1 except that.
- a sample having a thickness of 200 ⁇ m composed of only the grown AlN single crystal layer is prepared by mirror polishing both surfaces, and the linear transmittance at 265 nm, the concentration of impurities, the half-value width of the X-ray rocking curve of the (0002) plane, An X-ray diffraction profile and a photoluminescence spectrum in the ⁇ -2 ⁇ mode were measured by the same method as in Example 1.
- the linear transmittance was 6%, and the absorption coefficient was calculated to be 141 cm ⁇ 1 .
- the concentration of carbon atoms was 6 ⁇ 10 17 cm ⁇ 3
- the concentration of oxygen atoms was 2 ⁇ 10 20 cm ⁇ 3 .
- the concentration of chlorine atoms is 8 ⁇ 10 16 cm ⁇ 3
- the total concentration of carbon, chlorine, boron, silicon and oxygen contained in this sample is 2.1 ⁇ 10 20 cm ⁇ 3.
- the total concentration of boron, silicon, and oxygen contained in the single-crystal free-standing substrate was 2.1 ⁇ 10 20 cm ⁇ 3 .
- the half width of the X-ray rocking curve of the (0002) plane of the AlN single crystal free-standing substrate was 5300 seconds. Further, when X-ray diffraction measurement of the ⁇ -2 ⁇ mode was performed, only the (0002) plane and (0004) plane of AlN were observed. In addition, as a result of performing photoluminescence measurement at room temperature (23 ° C.), a peak near 209 nm, which is AlN band edge emission, was confirmed.
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Abstract
Description
(1) 炭素の濃度が、1×1014 atoms/cm3以上3×1017 atoms/cm3未満であり、塩素の濃度が、1×1014~1×1017 atoms/cm3であり、265nmにおける吸収係数が40cm-1以下である窒化アルミニウム単結晶。
(2) 前記窒化アルミニウム単結晶に含まれる炭素、塩素、ホウ素、ケイ素、酸素の濃度の総和が、1×1015~1×1020 atoms/cm3である(1)記載の窒化アルミニウム単結晶。
(3) 前記窒化アルミニウム単結晶の(0002)面のX線ロッキングカーブの半値幅が2000秒以下である(1)または(2)記載の窒化アルミニウム単結晶。
(4) フォトルミネッセンス測定において、窒化アルミニウムのバンド端発光である209nmのピークを確認することが出来る(1)乃至(3)記載の窒化アルミニウム単結晶。
(5) ハイドライド気相エピタキシー法により単結晶基板上に窒化アルミニウム単結晶を成長させることにより(1)記載の窒化アルミニウム単結晶を製造する方法であって、1200℃以上1700℃以下の温度で前記基板上に窒化アルミニウム単結晶を成長させると共に、ハイドライド気相エピタキシー装置内の、結晶成長時において1200℃以上となる領域の露出表面を、1200℃以上1700℃以下の温度において還元分解若しくは熱分解しない材料、又は還元分解若しくは熱分解しても炭素原子を含むガスを発生させない材料からなる部材のみで構成した装置を用いることを特徴とする方法。
(6) ハイドライド気相エピタキシー装置内の1200℃以上となる領域の露出表面を、好ましくは、BN、TaC、WおよびMoからなる群より選ばれる少なくとも1種で構成することを特徴とする(5)記載の窒化アルミニウム単結晶の製造方法。
(窒化アルミニウム単結晶)
本発明は、炭素の濃度が、1×1014 atoms/cm3以上3×1017 atoms/cm3未満であり、塩素の濃度が、1×1014~1×1017 atoms/cm3であり、265nmにおける吸収係数が40cm-1以下であるAlN単結晶に関する。
以下に現時点で考えられるメカニズムを詳述する。
α=2.303/t×log10(100/T)
本発明のAlN単結晶の製造方法は、炭素濃度及び塩素濃度を所定の範囲に制御できる方法であれば特に限定されないが、再現性よく確実に本発明の単結晶AlNを製造することができるという理由から、ハイドライド気相エピタキシー法(HVPE法)により、次のようにして製造することが好ましい。すなわち、本発明のAlN単結晶は、HVPE法において単結晶基板上にAlN単結晶を成長させるに際し、1200℃以上1700℃以下の温度で前記基板上にAlN単結晶を成長させると共に、ハイドライド気相エピタキシー装置内の、結晶成長時において1200℃以上となる領域の露出表面を、1200℃以上1700℃以下の温度において還元分解若しくは熱分解しない材料、又は還元分解若しくは熱分解しても炭素原子を含むガスを発生させない材料からなる部材のみで構成した装置を用いる方法(本発明の方法)により、好適に製造することができる。
(基板の準備)
本発明においては、基板として、複合AlN自立基板をWO2009/090821に記載の方法により作製した。この複合AlN自立基板は、AlN単結晶面を構成するAlN単結晶薄膜層の厚みが230nmであって、その下のAlN非単結晶層(AlN多結晶層)の厚みが350μmである。
本実施例で使用したHVPE装置においては、1200℃以上となる領域において還元分解又は熱分解して炭素原子を含むガスを発生させる部材を排除した。具体的には、サセプタ材質にはサセプタ表面全体をBNでコートされたグラファイトを使用し、サセプタの回転軸とサセプタ周囲の遮熱板にBNを使用し、サセプタと回転軸を固定するためにBNでコートされたグラファイト製のネジを使用した。なお、サセプタのBNコート層は実体顕微鏡を用いて観察倍率8倍から56倍の範囲で外周全体の観察を行って、コート層のピンホールやクラックがないことを確認した。
本実施例で用いた複合AlN自立基板は厚さ350μmのAlN多結晶層に支持されているが、該AlN多結晶層は多くの粒子界面を有するため、光の散乱が起こり紫外光透過性が得られない。そこで、成長させたAlN単結晶層の吸収係数を評価するために、複合AlN自立基板を研磨により除去し、さらに残ったAlN単結晶層の表面を研磨することにより、成長させたAlN単結晶層のみからなる厚さ200μmのAlN単結晶からなる試料を作製した。試料の表面はRMS値が5nm程度の両面鏡面研磨状態に仕上げた。
HVPE装置のサセプタと回転軸を固定するためにタングステン製のネジを使用して、本発明のAlN単結晶層の成長時の温度を1350℃とした以外は実施例1と同様の手順でAlN単結晶層を成長した。
HVPE装置のサセプタと回転軸を固定するためにTaC製のネジを使用して、本発明のAlN単結晶層の成長時の温度を1250℃とした以外は実施例1と同様の手順でAlN単結晶層を成長した。
HVPE装置のサセプタと回転軸を固定するためにグラファイト製のネジを使用して、本発明のAlN単結晶層の成長時の温度を1550℃とした以外は実施例1と同様の手順でAlN単結晶層を成長した。
HVPE装置のサセプタ材質としてサセプタ表面全体をBNでコートされたグラファイトを使用し、サセプタと回転軸を固定するネジにはグラファイトを使用した以外は実施例1と同様の手順でAlN単結晶層を形成した。なお、本比較例で使用した本サセプタのBNコート層を実体顕微鏡を用いて観察倍率8倍から56倍の範囲で外周全体の観察を行ったところ、コート層に直径1mm程度のピンホールが数カ所あり、ピンホール部分はサセプタの基材であるグラファイトが露出していることを確認した。
HVPE装置のサセプタ材質としてSiCを使用し、サセプタと回転軸を固定するネジにはTaCを使用し、成長させるAlN層の厚さを150μmとした以外は実施例1と同様の手順でAlN単結晶層を形成した。
HVPE装置のサセプタ材質としてグラファイトを使用して、基板の全外周部を取り囲むように酸素源としてサファイア基板を設置し、サセプタと回転軸を固定するネジにグラファイトを使用して、成長温度を1490℃とした以外は実施例1と同様の手順でのAlN単結晶層を成長した。
Claims (6)
- 炭素の濃度が、1×1014 atoms/cm3以上3×1017 atoms/cm3未満であり、塩素の濃度が、1×1014~1×1017 atoms/cm3であり、波長265nmにおける吸収係数が40cm-1以下であることを特徴とする窒化アルミニウム単結晶。
- 前記窒化アルミニウム単結晶に含まれる炭素、塩素、ホウ素、ケイ素、酸素の濃度の総和が、1×1015~1×1020 atoms/cm3である請求項1記載の窒化アルミニウム単結晶。
- 前記窒化アルミニウム単結晶の(0002)面のX線ロッキングカーブの半値幅が3000秒以下である請求項1又は請求項2記載の窒化アルミニウム単結晶。
- フォトルミネッセンス測定において、窒化アルミニウムのバンド端発光である209nmのピークを確認することが出来る請求項1乃至請求項3記載の窒化アルミニウム単結晶。
- ハイドライド気相エピタキシー法により単結晶基板上に窒化アルミニウム単結晶を成長させることにより、請求項1記載の窒化アルミニウム単結晶を製造する方法であって、1200℃以上1700℃以下の温度で前記基板上に窒化アルミニウム単結晶を成長させると共に、ハイドライド気相エピタキシー装置内の、結晶成長時において1200℃以上となる領域の露出表面を、1200℃以上1700℃以下の温度において還元分解若しくは熱分解しない材料、又は還元分解若しくは熱分解しても炭素原子を含むガスを発生させない材料からなる部材のみで構成した装置を用いることを特徴とする方法。
- ハイドライド気相エピタキシー装置内の1200℃以上となる領域の露出表面を、好ましくは、BN、TaC、WおよびMoからなる群より選ばれる少なくとも1種で構成することを特徴とする請求項5に記載方法。
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JP2014181178A (ja) * | 2013-03-15 | 2014-09-29 | Nitride Solutions Inc | 低炭素iii族窒化物結晶 |
WO2015133562A1 (ja) * | 2014-03-07 | 2015-09-11 | 国立大学法人東京農工大学 | ノロウイルスの不活性化方法、ノロウイルス不活性化用発光ダイオード、およびノロウイルスの不活性化装置 |
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Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2008096884A1 (ja) * | 2007-02-07 | 2008-08-14 | National University Corporation Tokyo University Of Agriculture And Technology | n型導電性窒化アルミニウム半導体結晶及びその製造方法 |
JP2009078971A (ja) | 2009-01-07 | 2009-04-16 | Sumitomo Electric Ind Ltd | 窒化物半導体単結晶基板とその合成方法 |
WO2009090821A1 (ja) | 2008-01-16 | 2009-07-23 | National University Corporation Tokyo University Of Agriculture And Technology | Al系III族窒化物単結晶層を有する積層体の製造方法、該製法で製造される積層体、該積層体を用いたAl系III族窒化物単結晶基板の製造方法、および、窒化アルミニウム単結晶基板 |
JP2010010613A (ja) | 2008-06-30 | 2010-01-14 | Tokuyama Corp | 積層体、自立基板製造用基板、自立基板およびこれらの製造方法 |
JP2010042950A (ja) * | 2008-08-11 | 2010-02-25 | Sumitomo Electric Ind Ltd | AlN結晶の製造方法、AlN基板の製造方法および圧電振動子の製造方法 |
JP2010089971A (ja) | 2008-10-03 | 2010-04-22 | Tokyo Univ Of Agriculture & Technology | 窒化アルミニウム単結晶基板、積層体、およびこれらの製造方法 |
WO2010122801A1 (ja) * | 2009-04-24 | 2010-10-28 | 独立行政法人産業技術総合研究所 | 窒化アルミニウム単結晶の製造装置、窒化アルミニウム単結晶の製造方法および窒化アルミニウム単結晶 |
Family Cites Families (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2006044982A (ja) * | 2004-08-04 | 2006-02-16 | Sumitomo Electric Ind Ltd | 窒化物半導体単結晶基板とその合成方法 |
JP5186733B2 (ja) * | 2005-07-29 | 2013-04-24 | 住友電気工業株式会社 | AlN結晶の成長方法 |
JP2009517329A (ja) * | 2005-11-28 | 2009-04-30 | クリスタル・イズ,インコーポレイテッド | 低欠陥の大きな窒化アルミニウム結晶及びそれを製造する方法 |
JP2009536605A (ja) * | 2006-05-08 | 2009-10-15 | ザ リージェンツ オブ ザ ユニバーシティ オブ カリフォルニア | アルミニウムを含むiii族窒化物半導体化合物の成長方法及び材料。 |
JP5099008B2 (ja) * | 2006-07-26 | 2012-12-12 | 富士通株式会社 | SiC基板を用いた化合物半導体装置とその製造方法 |
CN101205627A (zh) * | 2006-12-21 | 2008-06-25 | 中国科学院半导体研究所 | 一种制备氮化物单晶衬底的氢化物气相外延装置 |
JP2011151163A (ja) | 2010-01-21 | 2011-08-04 | Furukawa Electric Co Ltd:The | 半導体ウエハ表面保護テープ、樹脂製基材フィルム |
-
2011
- 2011-12-22 WO PCT/JP2011/079838 patent/WO2013094058A1/ja active Application Filing
- 2011-12-22 CN CN202010518150.7A patent/CN111621852A/zh active Pending
- 2011-12-22 KR KR1020147016397A patent/KR101821301B1/ko active IP Right Grant
- 2011-12-22 US US14/366,020 patent/US9691942B2/en active Active
- 2011-12-22 JP JP2013550032A patent/JP5904470B2/ja active Active
- 2011-12-22 CN CN201180075372.5A patent/CN103975098A/zh active Pending
- 2011-12-22 EP EP11878135.0A patent/EP2796596B1/en active Active
Patent Citations (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2008096884A1 (ja) * | 2007-02-07 | 2008-08-14 | National University Corporation Tokyo University Of Agriculture And Technology | n型導電性窒化アルミニウム半導体結晶及びその製造方法 |
WO2009090821A1 (ja) | 2008-01-16 | 2009-07-23 | National University Corporation Tokyo University Of Agriculture And Technology | Al系III族窒化物単結晶層を有する積層体の製造方法、該製法で製造される積層体、該積層体を用いたAl系III族窒化物単結晶基板の製造方法、および、窒化アルミニウム単結晶基板 |
JP2010010613A (ja) | 2008-06-30 | 2010-01-14 | Tokuyama Corp | 積層体、自立基板製造用基板、自立基板およびこれらの製造方法 |
JP2010042950A (ja) * | 2008-08-11 | 2010-02-25 | Sumitomo Electric Ind Ltd | AlN結晶の製造方法、AlN基板の製造方法および圧電振動子の製造方法 |
JP2010089971A (ja) | 2008-10-03 | 2010-04-22 | Tokyo Univ Of Agriculture & Technology | 窒化アルミニウム単結晶基板、積層体、およびこれらの製造方法 |
JP2009078971A (ja) | 2009-01-07 | 2009-04-16 | Sumitomo Electric Ind Ltd | 窒化物半導体単結晶基板とその合成方法 |
WO2010122801A1 (ja) * | 2009-04-24 | 2010-10-28 | 独立行政法人産業技術総合研究所 | 窒化アルミニウム単結晶の製造装置、窒化アルミニウム単結晶の製造方法および窒化アルミニウム単結晶 |
Non-Patent Citations (3)
Title |
---|
JOURNAL OF CRYSTAL GROWTH, vol. 312, 2010, pages 2530 - 2536 |
PHYSICA STATUS SOLIDI, vol. 246, no. 6, 2009, pages 1181 - 1183 |
See also references of EP2796596A4 |
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EP3219833A4 (en) * | 2014-11-10 | 2018-05-30 | Tokuyama Corporation | Device for manufacturing group-iii nitride single crystal, method for manufacturing group-iii nitride single crystal using same, and aluminum nitride single crystal |
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JPWO2019059381A1 (ja) * | 2017-09-22 | 2020-09-10 | 株式会社トクヤマ | Iii族窒化物単結晶基板 |
WO2019059381A1 (ja) | 2017-09-22 | 2019-03-28 | 株式会社トクヤマ | Iii族窒化物単結晶基板 |
JP7107951B2 (ja) | 2017-09-22 | 2022-07-27 | 株式会社トクヤマ | Iii族窒化物単結晶基板 |
US11767612B2 (en) | 2017-09-22 | 2023-09-26 | Tokuyama Corporation | Group III nitride single crystal substrate |
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