WO1999013139A1 - SiC MONOCRISTALLIN ET SON PROCEDE DE FABRICATION - Google Patents
SiC MONOCRISTALLIN ET SON PROCEDE DE FABRICATION Download PDFInfo
- Publication number
- WO1999013139A1 WO1999013139A1 PCT/JP1998/003480 JP9803480W WO9913139A1 WO 1999013139 A1 WO1999013139 A1 WO 1999013139A1 JP 9803480 W JP9803480 W JP 9803480W WO 9913139 A1 WO9913139 A1 WO 9913139A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- single crystal
- sic
- crystal
- plate
- composite
- Prior art date
Links
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
- C30B1/00—Single-crystal growth directly from the solid state
-
- 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
Definitions
- the present invention relates to a single crystal SiC and a method for manufacturing the same, and more particularly, to an X-ray optical element such as a light emitting diode or a monochromator,
- the present invention relates to a single crystal SiC used as a semiconductor substrate wafer of a semiconductor electronic element or a power device, and a method of manufacturing the same.
- SiC silicon carbide
- Si silicon carbide
- GaAs gallium arsenide
- it also excels in high-temperature characteristics, high-frequency characteristics, withstand voltage characteristics, and environmental resistance characteristics.Furthermore, it is easy to control the valence electrons of electrons and holes by adding impurities. In addition, it has a wide forbidden band width. (By the way, about 3.0 eV for 6H-type SiC single crystal and 3.26 eV for 4H-type SiC single crystal.) For this reason, it has been noted and expected as a semiconductor material for next-generation power devices.
- the present invention has been made in view of the background of the prior art as described above, and it is easy to specify the crystal orientation, and it is large, and the quality of the single crystal S is very high.
- a method for producing a single crystal SiC which can produce a high quality single crystal with high productivity by increasing the growth rate of the single crystal SiC and the single crystal SiC.
- the purpose of this is.
- the single crystal SiC according to the first invention a plurality of plate-like SiC single crystal pieces are arranged in almost the same plane with their crystal orientation planes being oriented in one direction.
- the stacked layers are composed of Si atoms and C atoms on the crystal orientation plane of a plurality of SiC single crystal pieces stacked on top of each other.
- a plurality of plate-like SiC single crystal pieces are arranged with their crystal orientation planes substantially in the same plane. After stacking them so that the crystal orientation is unified in one direction and fixing them with a sintered carbon jig, a plurality of SiC singles fixed in a laminated state By stacking a polycrystalline plate composed of Si atoms and C atoms on the crystal orientation plane of the crystal piece, and then heat treating the composite, the above-mentioned plurality of S It is characterized in that a single crystal is grown from a crystal orientation plane of an iC single crystal piece toward a polycrystalline plate.
- a plurality of SiC single-crystal pieces having a plate-like shape are used in a stacked state, and thus, they are used.
- the Si and C atoms are placed on the specified crystal orientation plane.
- the heat treatment is performed after laminating the polycrystalline plates, so that the polycrystalline body of the polycrystalline plate undergoes a phase transformation, and the crystal axes of a plurality of SiC single crystal pieces are formed.
- a single crystal which is all oriented in the same direction and grows at high speed toward a polycrystalline plate, can be made into a single crystal.
- crystal nuclei or impurities may be present at the interface. It is possible to efficiently grow high-quality, thick single-crystal SiC which does not cause defects such as pipe defects and mouth opening. . As a result, compared to existing semiconductor materials such as Si (silicon) and GaAs (gallium arsenide), high-temperature characteristics, high-frequency characteristics, withstand voltage characteristics, and withstand voltage characteristics are improved. It excels in environmental characteristics, etc., and has the effect of promoting the practical use of single crystal SiC, which is expected as a semiconductor material for power devices. .
- the crystal orientation of a plurality of SiC single crystal pieces forming the above-described complex Grinding or polishing the surface to a surface roughness less than RMS 100 Angstroms, especially RMS 100-500 Angstroms By adjusting the surface roughness within the range described above, the crystal orientation plane of the multiple SiC single crystal pieces on which the polycrystalline plates are stacked can be easily changed to a surface with few physical irregularities. Although it can be processed, it is possible to improve the quality of single crystal SiC by sufficiently suppressing the generation of crystal nuclei at the interface. This has the effect.
- the polycrystalline plate forming the above-mentioned composite is thermochemically treated.
- a film is formed by a vapor deposition method, and the film is polished so as to have a thickness of 300 to 700 jum, particularly, about 500 m. It is possible to eliminate the crystal lattice mismatch caused by the lattice distortion of the crystal orientation plane of the SiC single crystal piece by a short heat treatment, and to obtain a high-quality single crystal SiC. This has the effect of being able to obtain good productivity.
- the composite was housed in a carbon container, and the outside of the carbon container was covered with sic powder to cover 1
- a temperature in the range of 850-240 ° C in particular, a 3-SiC polycrystalline plate in which a polycrystalline plate is formed by a thermochemical vapor deposition method If so, the surface of the yS—SiC polycrystalline plate was polished and polished; 3—A carbon was placed on the surface of the SiC polycrystalline plate.
- the composite is housed in a carbon container, and the outside of the carbon container is covered with SiC powder so as to be in the range of 180 to 2
- SiC powder placed in the high-temperature atmosphere during the heat treatment is decomposed, and the decomposed Si, C is reduced.
- Part and strength Heat treatment in saturated SiC vapor atmosphere is performed by transferring the material through a container made of boron and into the container, thereby decomposing the SiC single crystal pieces and polycrystalline plates.
- the method for producing a single crystal SiC according to the third invention is characterized in that the surface of the single crystal SiC produced by the production method according to the second invention is ground or polished again. After that, a polycrystalline plate is laminated on the surface of the ground or polished single crystal SiC, and then the composite is heat-treated to obtain the single crystal. It is characterized in that a single crystal is grown from a crystal orientation plane of SiC toward a polycrystalline plate.
- a single crystal having not only high quality but also a very large thickness and having a wide applicability as a semiconductor material is provided.
- FIG. 1 is a plate-like ⁇ -SiC single-crystal piece used in the method for producing a single-crystal SiC according to the present invention.
- FIG. 2 is a schematic perspective view showing an iC single crystal mass
- FIG. 2 is a front view of a plate-like ⁇ —SiC single crystal piece cut out from the ⁇ -SiC single crystal mass
- 3 is a side view of the same plate-like ⁇ -SiC single crystal fragment
- Fig. 4 is a cutout of the same plate-like a-SiC single crystal fragment, and the size is the same.
- 5 is a side view of the ⁇ -SiC single crystal piece
- FIG. 1 is a plate-like ⁇ -SiC single-crystal piece used in the method for producing a single-crystal SiC according to the present invention.
- FIG. 2 is a schematic perspective view showing an iC single crystal mass
- FIG. 2 is a front view of a plate-like
- FIG. 6 is a side view of the ⁇ -SiC single crystal piece.
- FIG. 7 is a schematic perspective view showing a state in which the sheets are fixed in the laminated adhesion state.
- / 3 Schematic side showing the state where the SiC polycrystalline plate is deposited
- Fig. 8 is a schematic side view showing the state of heat treatment of the composite
- Fig. 9 is an enlarged side view of the main part showing the state where single crystal SiC grows by heat treatment. .
- a-SiC single-crystal lump formed by the spinning method and the a-SiC single-crystal lump 1 is the arrow in Fig. 1
- a large number of plate-like SiC single crystal pieces 1A of various sizes are used. It has the feature that it is easy to specify the crystal orientation.
- Fig. 2 and Fig. 3 a large number of plate-like SiC single crystal pieces 1A were cut out from the above ⁇ -SiC single crystal lump 1 and taken out.
- the plate-shaped SiC single crystal pieces 1A have a side length L of about lcm and a thickness T of 0.
- a rectangular plate-like a-SiC single crystal piece 2 of about 5 mm is cut out along the (110) crystal orientation plane 2a, and the crystal orientation plane 2a is polished. It is processed to the same size.
- the crystal orientation plane 2a of the plurality of ⁇ -SiC single crystal pieces 2 fixed to the sintered carbon jig 3 has physical irregularities caused by grinding or polishing. Remove .
- the crystal orientation plane 2a is less than RMS 100 Angstroms, preferably RMS 100 to 500 Angstroms. Adjust to a surface roughness in the range of.
- the crystal orientation plane 2a of the plurality of ⁇ -SiC single crystal pieces 2 adhered to each other by the above-mentioned lamination is thermo-chemically vapor-deposited (hereinafter referred to as thermal CVD) to obtain a Fig.
- thermal CVD thermo-chemically vapor-deposited
- the SiC plate 4 is formed.
- 3—SiC plate 4 has a thickness t of 300 to 700 ⁇ m, preferably about 500 ⁇ m, after being formed by the thermal CVD method.
- the surface is polished so that
- a plurality of ⁇ -SiC single crystal pieces cut out into a rectangular plate shape from a-SiC single crystal mass 1 made by the Achinso method By using 2 in the laminated adhesion state, it is possible to easily specify the crystal orientation of the plurality of ⁇ -SiC single crystal pieces 2 in one direction.
- the RMS is less than 100 Angstroms.
- the RMS 100 to 500 should be adjusted to the surface roughness of the Angstrom.
- crystal nuclei is preferable as much as possible, it takes a lot of labor and labor to process the surface to a surface roughness less than RMS 100 angstrom. If time is required and the surface becomes rough beyond the RMS 1000 angstrom, phase transformation occurs simultaneously from the bottom and side surfaces of the recess during heat treatment. For example, the possibility of resolving the crystal lattice mismatch is reduced, resulting in a poor quality product with crystal nuclei generated at the interface.
- the 5 — SiC plate 4 is polished to a film thickness 1 after film formation of 300 to 700; «m, more preferably about 500 / m. I hope you like it.
- the heat treatment for a relatively short period of time eliminates the crystal lattice mismatch caused by the lattice distortion, thereby improving the crystallinity. It is possible to improve the productivity of high quality single crystal SiC. That is, if the SiC plate 4 is a thick film exceeding 700 m, the heat treatment is performed. Sometimes a phase transformation occurs while preserving the lattice distortion of the original crystal, so long-term heat treatment is required to eliminate the lattice distortion, resulting in a high quality single crystal.
- the productivity of the crystal S i C may be reduced, and the crystal of a plurality of ⁇ -S i C single crystal pieces 2 serving as a base of the S—S i C plate 4 Crystal lattice mismatch caused by lattice distortion in the azimuthal plane 2a is rapidly resolved in the thickness range of about 300 to 700; um from the ⁇ -SiC single crystal piece. This is because, when it exceeds 700 / m, the degree of resolving the lattice defect mismatch is reduced.
- the surface of the ⁇ -SiC plate 4 after film formation is polished, and a carbon 5 is put on the polished surface.
- the composite M is put into the bonbon container 6, and the outside of the bonbon container 6 is covered with ⁇ -SiC powder 7 in a predetermined state. Due to the heat treatment, ⁇ -SiC powder 7 is decomposed in a high-temperature atmosphere, and at least a part of the decomposed Si, C is partially polarized. After being transferred into the container 6 through the carbon container 6 and subjected to a predetermined heat treatment in a saturated SiC vapor atmosphere, only ⁇ -SiC can be obtained.
- Crystal pieces 2 and 8 It is possible to produce high-quality single-crystal SiC by suppressing decomposition of the SiC plate 4, and at the same time, it is possible to produce porous crystals. ⁇ made of Bonn
- the Si and C transferred into the container 6 through the vessel 6 can also be prevented from adhering to the SiC before the phase transformation, whereby the quality and the quality are improved. It is possible to produce beautiful single crystal SiC.
- the surface of the single-crystal SiC manufactured through the above-described steps is again ground or polished, and the polished surface is subjected to thermal CVD by a thermal CVD method.
- a plate-like ⁇ -SiC single-crystal piece 2 was used as the SiC single-crystal piece, but in addition to this, for example, ⁇ -SiC A plate-like crystal piece such as a sintered body or a / 9-SiC single crystal may be used.
- a plurality of pieces may be formed by a thermal CVD method.
- the yS-SiC crystal plate 2 formed on the crystal orientation plane 2a of the ⁇ -SiC single crystal pieces 2 was used, but in addition to this, for example, SiC A polycrystalline plate, a high-purity SIC sintered body, or an amorphous plate having a high purity (10 14 at lD / cm 3 ) or less may be used. It is possible to obtain a crystal SiC.
- the ⁇ -SiC single crystal piece 2 in the above embodiment either 6H type or 4H type may be used, and 6H type is used.
- the single crystal converted from ⁇ / SiC from the polycrystalline body of the 9-SiC polycrystalline plate 2 by heat treatment has the same morphology as the 6H-type single crystal.
- a 4H-type single crystal piece is used, a single crystal having the same morphology as that of the 4H-type single crystal is converted and grown by the heat treatment. It will be easy.
- the present invention provides a method in which Si atoms and C atoms are added to the crystal orientation plane of a plurality of plate-like SiC single crystal pieces that are stacked and adhered so that the crystal orientations are unified.
- the composite formed by laminating the polycrystalline plates is heat-treated, and the crystal axis of each single crystal fragment is shifted from the crystal orientation plane of each SiC single crystal fragment toward the polycrystalline plate.
- the single crystal oriented in the same direction is grown together, so that the crystal nuclei, impurities and micro-hole pipe defects do not occur at the interface. This is a technology that enables efficient production of high-quality, thick single-crystal SiC.
Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
CA002269709A CA2269709A1 (en) | 1997-09-10 | 1998-08-05 | Single crystal sic and process for preparing the same |
EP98936661A EP0964084A1 (en) | 1997-09-10 | 1998-08-05 | SINGLE CRYSTAL SiC AND PROCESS FOR PREPARING THE SAME |
US09/284,484 US6143267A (en) | 1997-09-10 | 1998-08-05 | Single crystal SiC and a method of producing the same |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP9/245432 | 1997-09-10 | ||
JP9245432A JP3043675B2 (ja) | 1997-09-10 | 1997-09-10 | 単結晶SiC及びその製造方法 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO1999013139A1 true WO1999013139A1 (fr) | 1999-03-18 |
Family
ID=17133580
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP1998/003480 WO1999013139A1 (fr) | 1997-09-10 | 1998-08-05 | SiC MONOCRISTALLIN ET SON PROCEDE DE FABRICATION |
Country Status (9)
Country | Link |
---|---|
US (1) | US6143267A (ja) |
EP (1) | EP0964084A1 (ja) |
JP (1) | JP3043675B2 (ja) |
KR (1) | KR100288473B1 (ja) |
CN (1) | CN1239519A (ja) |
CA (1) | CA2269709A1 (ja) |
RU (1) | RU2162902C1 (ja) |
TW (1) | TW514685B (ja) |
WO (1) | WO1999013139A1 (ja) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0964081A2 (en) * | 1998-04-13 | 1999-12-15 | Nippon Pillar Packing Co. Ltd. | Single crystal SiC and a method of producing the same |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1130137B1 (en) | 1999-07-30 | 2006-03-08 | Nissin Electric Co., Ltd. | Material for raising single crystal sic and method of preparing single crystal sic |
JP3087070B1 (ja) * | 1999-08-24 | 2000-09-11 | 日本ピラー工業株式会社 | 半導体デバイス製作用単結晶SiC複合素材及びその製造方法 |
US6706114B2 (en) * | 2001-05-21 | 2004-03-16 | Cree, Inc. | Methods of fabricating silicon carbide crystals |
US7314520B2 (en) | 2004-10-04 | 2008-01-01 | Cree, Inc. | Low 1c screw dislocation 3 inch silicon carbide wafer |
CN100400723C (zh) * | 2006-05-29 | 2008-07-09 | 中国科学院物理研究所 | 一种碳化硅单晶生长后的热处理方法 |
KR101597537B1 (ko) * | 2013-09-27 | 2016-02-25 | 정진 | 핸드레일 걸이 장치 |
CN103940837A (zh) * | 2014-04-01 | 2014-07-23 | 中国科学院物理研究所 | 一种SiC晶体单色器 |
JP6544166B2 (ja) * | 2015-09-14 | 2019-07-17 | 信越化学工業株式会社 | SiC複合基板の製造方法 |
JP6515757B2 (ja) * | 2015-09-15 | 2019-05-22 | 信越化学工業株式会社 | SiC複合基板の製造方法 |
Family Cites Families (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5915194A (en) * | 1997-07-03 | 1999-06-22 | The United States Of America As Represented By The Administrator Of National Aeronautics And Space Administration | Method for growth of crystal surfaces and growth of heteroepitaxial single crystal films thereon |
JP3043689B2 (ja) * | 1997-11-17 | 2000-05-22 | 日本ピラー工業株式会社 | 単結晶SiC及びその製造方法 |
-
1997
- 1997-09-10 JP JP9245432A patent/JP3043675B2/ja not_active Expired - Fee Related
-
1998
- 1998-08-05 US US09/284,484 patent/US6143267A/en not_active Expired - Fee Related
- 1998-08-05 KR KR1019997003831A patent/KR100288473B1/ko not_active IP Right Cessation
- 1998-08-05 EP EP98936661A patent/EP0964084A1/en not_active Withdrawn
- 1998-08-05 RU RU99112120/12A patent/RU2162902C1/ru not_active IP Right Cessation
- 1998-08-05 CA CA002269709A patent/CA2269709A1/en not_active Abandoned
- 1998-08-05 CN CN98801298A patent/CN1239519A/zh active Pending
- 1998-08-05 WO PCT/JP1998/003480 patent/WO1999013139A1/ja not_active Application Discontinuation
- 1998-08-07 TW TW087113065A patent/TW514685B/zh active
Non-Patent Citations (2)
Title |
---|
CHEMICAL ABSTRACTS, Vol. 78, No. 18, 7 May 1973, (Columbus, Ohio, USA), page 337, Abstract No. 116269j, BERMAN I. et al., "Influence of Annealing on Thin Films of beta SiC"; & U.S. AIR FORCE CAMBRIDGE RES. LAB., PHYS SCI. RES. PAP., 1972, No. 516, 11 pp. (Eng). * |
CHEMICAL ABSTRACTS, Vol. 81, No. 24, 16 Dec. 1974, (Columbus, Ohio, USA), page 462, Abstract No. 160152b, BERMAN I. et al., "Annealing of Sputterd beta-Silicon Carbide"; & SILICON CARBIDE, PROC. INT. CONF., 3rd, 1973 (Pub. 1974), 42-50 (Eng). * |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0964081A2 (en) * | 1998-04-13 | 1999-12-15 | Nippon Pillar Packing Co. Ltd. | Single crystal SiC and a method of producing the same |
EP0964081A3 (en) * | 1998-04-13 | 2000-01-19 | Nippon Pillar Packing Co. Ltd. | Single crystal SiC and a method of producing the same |
Also Published As
Publication number | Publication date |
---|---|
JP3043675B2 (ja) | 2000-05-22 |
TW514685B (en) | 2002-12-21 |
EP0964084A1 (en) | 1999-12-15 |
US6143267A (en) | 2000-11-07 |
JPH1192293A (ja) | 1999-04-06 |
KR100288473B1 (ko) | 2001-04-16 |
KR20000068876A (ko) | 2000-11-25 |
RU2162902C1 (ru) | 2001-02-10 |
CA2269709A1 (en) | 1999-03-18 |
CN1239519A (zh) | 1999-12-22 |
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