WO2009069564A1 - 炭化珪素単結晶の成長法 - Google Patents
炭化珪素単結晶の成長法 Download PDFInfo
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- WO2009069564A1 WO2009069564A1 PCT/JP2008/071277 JP2008071277W WO2009069564A1 WO 2009069564 A1 WO2009069564 A1 WO 2009069564A1 JP 2008071277 W JP2008071277 W JP 2008071277W WO 2009069564 A1 WO2009069564 A1 WO 2009069564A1
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- WIPO (PCT)
- Prior art keywords
- silicon carbide
- single crystal
- melt
- crystal
- growth
- Prior art date
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Classifications
-
- 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
- C30B9/00—Single-crystal growth from melt solutions using molten solvents
- C30B9/04—Single-crystal growth from melt solutions using molten solvents by cooling of the solution
- C30B9/08—Single-crystal growth from melt solutions using molten solvents by cooling of the solution using other solvents
- C30B9/10—Metal solvents
-
- 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
- C30B19/00—Liquid-phase epitaxial-layer growth
- C30B19/02—Liquid-phase epitaxial-layer growth using molten solvents, e.g. flux
-
- 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
- C30B29/36—Carbides
-
- 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
- C30B9/00—Single-crystal growth from melt solutions using molten solvents
- C30B9/04—Single-crystal growth from melt solutions using molten solvents by cooling of the solution
- C30B9/06—Single-crystal growth from melt solutions using molten solvents by cooling of the solution using as solvent a component of the crystal composition
Definitions
- the present invention relates to a novel method of growing a silicon carbide single crystal by a solution method, and more specifically, by a solution method using a novel melt (sometimes referred to as a solution), and the morphology of a crystal growth surface
- the present invention relates to a method for growing a silicon carbide single crystal that achieves one improvement and has a relatively high growth rate.
- Silicon carbide (SiC) single crystal is very thermally and chemically stable, excellent in mechanical strength, resistant to radiation, and has a higher dielectric breakdown voltage and higher thermal conductivity than Si
- the addition of impurities makes it easy to control p- and n-conducting type electrons, and has a wide forbidden band (approximately 3.0 e V in 6 H-type single crystal S i C. 4 H-type single crystal S i C has a feature of about 3.3 eV). Therefore, it is possible to realize high temperature, high frequency, withstand voltage, and environmental resistance that cannot be realized with existing semiconductor materials such as silicon (Si) and gallium arsenide (GaAs). Expectations are growing as a material. Conventionally, as a growth method of a silicon carbide single crystal, a vapor phase method, an ac h esson method and a solution method are typically known.
- the sublimation method causes various defects in the crystal and is easily polycrystallized.
- the crystals produced from this are thin films, making it difficult to produce bulk single crystals.
- the Atchison method uses quartzite and coke as raw materials and heats them in an electric furnace, it cannot be highly purified due to impurities in the raw materials.
- a silicon-containing alloy is melted in a graphite crucible, carbon is dissolved in the melt from the graphite crucible, and a silicon carbide crystal layer is grown on the seed crystal substrate placed in a low temperature portion by solution precipitation. Is the way.
- the solution method is known to be advantageous as a method for obtaining a bulk single crystal although the growth rate is low.
- a raw material containing at least one element of transition metals, S i, and C is melted to form a melt.
- a single crystal silicon carbide seed crystal is brought into contact with the liquid, and the temperature of the melt is cooled to a melt state having a temperature lower than the liquidus phase of the melt, so that the silicon carbide single crystal is deposited and grown.
- a method for producing crystals is described.
- transition metals are Fe, Co, Ni (above VIII group), Ti, Zr, Hf (above group IVb), V, Nb, Ta (above) Forces that are group Vb), Cr, Mo and W (group VIb above)
- the specifically disclosed composition is only when the transition metal is Mo, Cr, Co.
- the measurement method and confirmation method are not disclosed, and macro defects on the crystal growth surface are not recognized.
- Japanese Laid-Open Patent Publication No. 2 0 0 6 — 1 4 3 5 5 5 includes 3 1 binding and ⁇ 1 (M: one of F e or Co), and the molar concentration of M is [M], S i When the molar concentration is [S i], the value of [M] / ([M] + [S i]) is 0.2 or more and 0.7 or less when M is Fe, and M is Co
- a silicon carbide seed crystal substrate is immersed in a melt of an alloy that is not less than 0.05 and not more than 0.25, so that the combined liquid around the seed crystal substrate is oversaturated with silicon carbide.
- a method for producing a silicon carbide single crystal is described in which a silicon carbide seed crystal is grown on a seed crystal substrate.
- macro defects on the crystal growth surface are not recognized.
- Japanese Laid-Open Patent Publication No. 2 0 7 — 7 9 8 6 includes S i, T i and M (M: Co and / or M n) and C, and the atomic ratio of S i, T i and M Is expressed as S i x T i y M z and satisfies the following conditions: 0. 1 7 ⁇ yZx ⁇ 0. 3 3 and 0.9.9 0 ⁇ (y + z) / X ⁇ 1. 8 0, or Including S i, Ding 1 and 1 ⁇ ( ⁇ : 8 1) and C, the atomic ratio of 3 1 and Ding 1 is expressed as S i x T i y M z , 0.
- a single crystal substrate for silicon carbide growth is brought into contact with a melt satisfying 0. 3 3 and 0. 3 3 ⁇ (y + z) / X ⁇ 0.6 0, and the melt is cooled around the single crystal substrate.
- a method for producing a silicon carbide single crystal is described in which silicon carbide single crystal is grown on a single crystal substrate by bringing silicon carbide dissolved in the melt into a supersaturated state.
- the present inventors have found that a relatively large growth rate can be obtained by adding a certain amount or more of Cr in a Si 1 C r 1 C melt.
- the surface of the silicon carbide single crystal growth layer obtained is unstable, and minute changes in growth conditions adversely affect the surface of the growth layer. It has been found that the surface morphology (morphology) is not sufficient, which in turn may affect the quality of the grown crystal obtained.
- An object of the present invention is to provide a method for growing a silicon carbide single crystal that realizes an improvement in the morphology of the surface of a crystal growth layer by a solution method.
- This invention melts Si heated in a graphite crucible.
- Cr and X In the method of growing a silicon carbide single crystal on a single crystal substrate by bringing a silicon carbide single crystal into contact with the melt, Cr and X (X is at least one of Ni and Co) in the melt.
- the morphology of the surface of the crystal growth layer is improved and the growth rate is equal to or higher than that of the solution method described in the known literature.
- a silicon single crystal can be grown.
- FIG. 1 shows one embodiment of a manufacturing apparatus for carrying out the method of the present invention.
- Figure 2 shows the equipment used for the silicon carbide single crystal growth experiments in each example.
- Fig. 3A shows a photograph of the morphology of the silicon carbide crystal growth layer surface obtained in Comparative Example 1 when the Si: Cr composition ratio (at.%) Is 50:50. Show.
- FIG. 3B shows the composition ratio (at.%) Of S i: C r obtained in Comparative Example 1.
- FIG. 4 shows a photograph of the morphology of the crystal growth layer surface of the silicon carbide crystal obtained in Example 1.
- FIG. 1 shows one embodiment of a manufacturing apparatus for carrying out the method of the present invention.
- silicon carbide single crystal growth is performed using a graphite crucible 5 surrounded by a heat insulating material 6 as a reaction vessel.
- Silicon carbide single crystal growth consists of a silicon carbide single crystal at the tip of a graphite rod 3 (also called a graphite shaft), which is an example of a silicon carbide seed crystal support member, in a melt 2 heated by a high-frequency coil 1 as a heating device. This can be achieved by bonding and fixing the single crystal substrate 4 and immersing this in the melt 2 to grow the single crystal substrate 4.
- a method for growing a silicon carbide single crystal by a solution method is used.
- S i and C, Cr and X (X is at least one of N i and C o)
- C r and X in combination, for example, Mo—S i — C 3 element, C r ⁇ S i-C 3 element, Co o-Si i C 3 element can improve the growth rate, but the quality of the precipitated crystals is insufficient
- the Si_Cr-X-C melt if the Cr is less than 3 O at.%, The growth rate of the silicon carbide single crystal is remarkably small. It is not suitable because it becomes difficult to carry out the growth of only a single crystal with a polycrystal around it.
- the Si — C r _ X _ C melt if the X force is less than 1 at •%, the surface morphology of the silicon carbide single crystal does not improve, and if it exceeds 25 at. Part or all of the silicon crystal is polycrystallized, making it difficult to achieve stable growth as a single crystal. Rejected ⁇ This is not preferable In this invention, the Si—Cr—X—C melt having the above composition is used.
- the reason for this is that the growth rate of the silicon carbide single crystal is increased and the morphology of the crystal surface is improved. This is because the melting ability of C (carbon) from the graphite (crucible in Fig. 1) with which the melt is in contact with Cr As a result, this C is considered to be the raw material of the silicon carbide crystal, and X decreases the energy of the solid-liquid interface or the surface energy of the melt (solution).
- a Si-Cr-XC melt having the above composition was prepared.
- the method for obtaining a silicon carbide single crystal manufactured For example, first, Si, Cr and X are added as raw materials to a graphite crucible as a reaction vessel, the raw materials are melted, and the solid line of the produced alloy is obtained. Heat to a temperature higher than the temperature to form a melt.
- at least a part of C in the above S i — C r _ X— C melt is dissolved in the melt from the graphite crucible, and in particular, all of C is dissolved by dissolution from the graphite crucible. It is preferable to supply.
- a part of C may be charged using carbide or carbon as a raw material.
- a method in which a part of C is supplied by blowing a carbon-containing gas such as methane into the melt.
- the crucible By continuing to heat the melt, the crucible, the raw material consisting of Si, Cr and X, and C are sufficiently dissolved, and the carbon concentration in the resulting melt becomes the saturation concentration of silicon carbide using the melt as a solvent. If it becomes close and constant, the seed crystal substrate for silicon carbide growth is brought into contact with the melt, and the melt is prepared by operating a temperature gradient method or a heating device that provides a temperature gradient of, for example, about 50 to 50 cm to the melt.
- the silicon carbide dissolved in the melt is supersaturated by supercooling the melt around the seed crystal substrate to a temperature of 2 100 or less, in particular from 1600 to 1800, by the cooling method of cooling. By doing so, a silicon carbide single crystal is grown on the single crystal substrate.
- a single crystal substrate having the same crystal form as that of the target silicon carbide It is preferable to use a single crystal substrate having the same crystal form as that of the target silicon carbide.
- a single crystal of silicon carbide manufactured by a sublimation method can be used.
- a production method known per se in the solution method for example, the shape of the graphite crucible, the heating method, the heating time, the atmosphere, the heating rate and the cooling rate can be applied.
- high-frequency induction heating can be used as a heating method, and the heating time (approximately the time from the preparation of raw materials until reaching the S i C saturation concentration) is several hours to 10 hours, depending on the size of the crucible.
- a rare gas as an atmosphere for example H e, N e, include those portions thereof or an inert gas such as A r was replaced with N 2 and methane.
- a conventionally known three-component system for example, S i — C r — C melt system
- four-component system for example, S i — T i — A 1 — C melt system, S i —
- a silicon carbide single crystal that realizes improved morphology on the surface of the crystal growth layer can be produced by the method of the present invention.
- the method of the present invention can be applied not only to a bulk single crystal growth method but also to a liquid phase epitaxial growth layer forming technique on the surface of a silicon carbide substrate.
- a silicon carbide single crystal growth experiment was performed using an apparatus having a black lead crucible shown in FIG. 2 as a reaction vessel.
- the graphite rod 3 has a built-in W—Re thermocouple 7 and the graphite crucible 5 has a radiation thermometer 8 installed.
- the morphology of the surface of the crystal growth layer was observed visually and with a microscope.
- thermometer and a thermocouple are used to measure the temperature of the solution, etc.
- the radiation thermometer is installed in the observation window above the solution surface where the solution surface can be directly observed, and before and after contact with the solution. It was possible to measure temperature.
- a thermocouple was installed inside the black smoke stick to which the single crystal substrate was bonded (2 mm from the single crystal substrate), and the temperature immediately after contact with the solution was measured.
- the growth rate of the silicon carbide single crystal was 2 10 mZ h.
- FIG. 3A shows the S i: Cr composition ratio 50:50 at%.
- FIG. 3B shows the S i: Cr composition ratio 60:40 at%. From Fig. 3A and Fig. 3B, according to the S i — C r — C melt, the morphology (state) of the growth surface of the silicon carbide single crystal shows that many steps appear on the surface and the morphology is poor. I understand.
- Example 1 Raw materials having composition ratios of S i, Cr and Ni at 50 at.%, 45 at.% And 5 at.%, Respectively, were added to the graphite crucible 5 and dissolved by heating. Crystal growth was carried out by maintaining a constant temperature and immersing the single crystal substrate in the solution. The obtained silicon carbide crystal was confirmed to be a single crystal.
- the growth rate of the S 1 C single crystal was 2440 mZ h.
- Figure 4 shows the morphology of the crystal growth layer surface. From Figure 4,
- the ratio of A 1 is 0 ⁇ ! In the range of O at.%, The raw materials of S i, T i and A 1 are put in the graphite crucible 5, heated and dissolved, and kept at a constant temperature (at about 1 8 1 0), Crystal growth was performed in the same manner as in Example 1 except that the seed crystal was immersed in the solution.
- the growth rate was at most 14 O / z mZ h or less even when the proportion of A 1 in the total composition was changed.
- the growth rate of the silicon carbide single crystal was 2 2 5; mZ h.
- the morphology of the crystal growth layer surface was the same as in Fig. 4. From this result, it was confirmed that the morphology of the growth surface of the silicon carbide single crystal was remarkably improved with the Si—Cr—Co—C melt.
- N i is not added, and the ratio of C r is changed within the range of 3 to 95 at.%, And the raw materials of S i and C r are put in the graphite crucible 5 and heated to dissolve at a constant temperature (about 19% The crystal growth was performed in the same manner as in Example 1 except that the seed crystal was immersed in the solution.
- the morphology of the surface of the crystal growth layer of the obtained silicon carbide crystal is poor as in Comparative Example 1, and is obtained when the ratio of Cr in the total amount of S i binding r is more than 7 O at.%. Some or all of the silicon carbide crystals were polycrystallized.
- the silicon carbide single crystal growth method of the present invention is capable of achieving high temperature, high frequency, withstand voltage and environmental resistance, and obtaining a single crystal of silicon carbide that has potential as a next-generation semiconductor material. Can be possible.
- the silicon carbide single crystal growth method of the present invention can improve the morphology of the surface of the silicon carbide growth crystal.
- the silicon carbide single crystal growth method of the present invention can make it possible to grow a silicon carbide single crystal at a crystal growth rate equal to or higher than that of a conventionally known solution method.
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Abstract
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Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE112008003497.4T DE112008003497B4 (de) | 2007-11-27 | 2008-11-18 | Verfahren zum Aufwachsen eines Siliziumcarbideinkristalls |
KR1020097023496A KR101085690B1 (ko) | 2007-11-27 | 2008-11-18 | 탄화규소 단결정의 성장법 |
US12/599,520 US8685163B2 (en) | 2007-11-27 | 2008-11-18 | Method for growing silicon carbide single crystal |
CN2008800253811A CN101796227B (zh) | 2007-11-27 | 2008-11-18 | 碳化硅单晶的生长方法 |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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JP2007-306367 | 2007-11-27 | ||
JP2007306367A JP4277926B1 (ja) | 2007-11-27 | 2007-11-27 | 炭化珪素単結晶の成長法 |
Publications (1)
Publication Number | Publication Date |
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WO2009069564A1 true WO2009069564A1 (ja) | 2009-06-04 |
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Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
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PCT/JP2008/071277 WO2009069564A1 (ja) | 2007-11-27 | 2008-11-18 | 炭化珪素単結晶の成長法 |
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US (1) | US8685163B2 (ja) |
JP (1) | JP4277926B1 (ja) |
KR (1) | KR101085690B1 (ja) |
CN (1) | CN101796227B (ja) |
DE (1) | DE112008003497B4 (ja) |
WO (1) | WO2009069564A1 (ja) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US8328937B2 (en) | 2009-07-21 | 2012-12-11 | Toyota Jidosha Kabushiki Kaisha | Seed crystal axis for solution growth of single crystal |
CN114232097A (zh) * | 2021-12-31 | 2022-03-25 | 广州半导体材料研究所 | 一种制备碳化硅单晶的方法 |
Families Citing this family (13)
Publication number | Priority date | Publication date | Assignee | Title |
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JP5428706B2 (ja) * | 2009-09-25 | 2014-02-26 | トヨタ自動車株式会社 | SiC単結晶の製造方法 |
US10167573B2 (en) * | 2010-11-26 | 2019-01-01 | Shin-Etsu Chemical Co., Ltd. | Method of producing SiC single crystal |
JP5287840B2 (ja) * | 2010-12-16 | 2013-09-11 | 株式会社デンソー | 炭化珪素単結晶の製造装置 |
JP5568054B2 (ja) | 2011-05-16 | 2014-08-06 | トヨタ自動車株式会社 | 半導体素子の製造方法 |
CN104246026B (zh) * | 2012-04-20 | 2017-05-31 | 丰田自动车株式会社 | SiC单晶及其制造方法 |
JP5828810B2 (ja) * | 2012-07-18 | 2015-12-09 | 新日鐵住金株式会社 | 溶液成長法に用いられるSiC単結晶の製造装置、当該製造装置に用いられる坩堝及び当該製造装置を用いたSiC単結晶の製造方法 |
WO2014103394A1 (ja) * | 2012-12-28 | 2014-07-03 | トヨタ自動車株式会社 | n型SiC単結晶の製造方法 |
JP5761264B2 (ja) * | 2013-07-24 | 2015-08-12 | トヨタ自動車株式会社 | SiC基板の製造方法 |
JP5854013B2 (ja) | 2013-09-13 | 2016-02-09 | トヨタ自動車株式会社 | SiC単結晶の製造方法 |
CN106012021B (zh) * | 2016-06-30 | 2019-04-12 | 山东天岳先进材料科技有限公司 | 一种液相生长碳化硅的籽晶轴及方法 |
CN106521629B (zh) * | 2016-09-19 | 2018-12-28 | 山东天岳晶体材料有限公司 | 一种获得液体硅的方法及实现该方法的坩埚 |
JP2019151530A (ja) * | 2018-03-05 | 2019-09-12 | 国立大学法人信州大学 | SiC単結晶の製造方法 |
CN116926670B (zh) * | 2023-07-12 | 2024-04-16 | 通威微电子有限公司 | 一种用液相法制备碳化硅的方法和制得的碳化硅 |
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2008
- 2008-11-18 US US12/599,520 patent/US8685163B2/en active Active
- 2008-11-18 WO PCT/JP2008/071277 patent/WO2009069564A1/ja active Application Filing
- 2008-11-18 CN CN2008800253811A patent/CN101796227B/zh not_active Expired - Fee Related
- 2008-11-18 DE DE112008003497.4T patent/DE112008003497B4/de not_active Expired - Fee Related
- 2008-11-18 KR KR1020097023496A patent/KR101085690B1/ko active IP Right Grant
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US8328937B2 (en) | 2009-07-21 | 2012-12-11 | Toyota Jidosha Kabushiki Kaisha | Seed crystal axis for solution growth of single crystal |
CN114232097A (zh) * | 2021-12-31 | 2022-03-25 | 广州半导体材料研究所 | 一种制备碳化硅单晶的方法 |
Also Published As
Publication number | Publication date |
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US8685163B2 (en) | 2014-04-01 |
CN101796227A (zh) | 2010-08-04 |
KR101085690B1 (ko) | 2011-11-22 |
JP4277926B1 (ja) | 2009-06-10 |
US20100236472A1 (en) | 2010-09-23 |
CN101796227B (zh) | 2012-09-26 |
DE112008003497T5 (de) | 2010-10-28 |
DE112008003497B4 (de) | 2015-06-25 |
KR20090129514A (ko) | 2009-12-16 |
JP2009126770A (ja) | 2009-06-11 |
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