WO2023067736A1 - SiC単結晶基板及びその製造方法 - Google Patents
SiC単結晶基板及びその製造方法 Download PDFInfo
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- 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
- C30B1/02—Single-crystal growth directly from the solid state by thermal treatment, e.g. strain annealing
-
- 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
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01L—SEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
- H01L21/00—Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
- H01L21/02—Manufacture or treatment of semiconductor devices or of parts thereof
- H01L21/04—Manufacture or treatment of semiconductor devices or of parts thereof the devices having potential barriers, e.g. a PN junction, depletion layer or carrier concentration layer
- H01L21/18—Manufacture or treatment of semiconductor devices or of parts thereof the devices having potential barriers, e.g. a PN junction, depletion layer or carrier concentration layer the devices having semiconductor bodies comprising elements of Group IV of the Periodic Table or AIIIBV compounds with or without impurities, e.g. doping materials
- H01L21/20—Deposition of semiconductor materials on a substrate, e.g. epitaxial growth solid phase epitaxy
Definitions
- the present invention relates to a SiC single crystal substrate and its manufacturing method.
- SiC silicon carbide
- SiC power devices power semiconductor devices using SiC materials
- SiC power devices are superior to those using Si semiconductors in terms of miniaturization, low power consumption, and high efficiency, so they are expected to be used in various applications.
- SiC power devices converters, inverters, on-board chargers, etc. for electric vehicles (EV) and plug-in hybrid vehicles (PHEV) can be made smaller and more efficient.
- EV electric vehicles
- PHEV plug-in hybrid vehicles
- Patent Document 1 Japanese Patent No. 3248071 discloses that a composite obtained by providing a SiC polycrystal on a SiC single crystal is heat-treated to cause a solid phase transformation of the SiC polycrystal. It is disclosed that a SiC single crystal with few micropipes can be obtained by this.
- Patent Document 2 Japanese Patent No. 4069508 discloses a method for producing a SiC single crystal with closed micropipes, characterized by embedding the SiC single crystal in SiC powder and heat-treating it. .
- Patent Literature 1 does not address the reduction of defects other than micropipes, and also has the problem that the substrate tends to warp.
- Patent Document 2 deals with reduction of micropipes, there is a problem that dislocations other than micropipes cannot be reduced. Therefore, it is desired to reduce the defects in the SiC wafer, especially the basal plane dislocations called device killer defects.
- the present inventors recently discovered that by heat-treating a SiC single crystal as a seed crystal and a SiC powder layer in contact with each other and with a small temperature gradient, the basal plane dislocation density is low and warp is reduced. It was found that a SiC single crystal substrate with a small amount can be manufactured.
- an object of the present invention is to provide a SiC single crystal substrate with a low basal plane dislocation density and a small amount of warpage, and a method for manufacturing the same.
- a SiC single crystal as a seed crystal and a SiC powder layer in contact with each other in a container; a step of placing the container in an effective heating zone within a firing furnace, the temperature range being controlled within ⁇ 50° C. of a set temperature, and performing heat treatment, thereby growing a SiC single crystal on the seed crystal;
- a method for manufacturing a SiC single crystal substrate comprising:
- a SiC single crystal having a basal plane dislocation density of 0 to 1.0 ⁇ 10 2 cm ⁇ 2 on at least one surface and a substrate warp amount of 0 to 40 ⁇ m a substrate,
- the amount of warp is obtained by drawing two straight lines X and Y perpendicular to each other that pass through a point G, which is the center of gravity of the SiC single crystal substrate, in a plan view figure when the surface of the SiC single crystal substrate is viewed in plan.
- the SiC single crystal substrate Among the line segments extended perpendicular to the line segment AB from any point on the curve AB between the point A and the point B on the surface, the distance of the line segment is the longest A point P on the curve AB is determined, (ii) the distance between the line segment AB and the point P is set as a warpage amount ⁇ , and (iii) the distance between the points C and D on the surface of the SiC single crystal substrate is Among the line segments extended perpendicular to the line segment CD from an arbitrary point on the curve CD between iv) A SiC single crystal substrate defined as an arithmetic mean value of (v) the warpage amounts ⁇ and ⁇ , where ⁇ is the distance between the line segment CD and the point R.
- FIG. 4 is a schematic cross-sectional view showing one mode of arrangement of a SiC powder layer and seed crystals in a container;
- FIG. 4 is a schematic cross-sectional view showing another form of arrangement of SiC powder layers and seed crystals in a container;
- FIG. 4 is a schematic cross-sectional view showing another form of arrangement of SiC powder layers and seed crystals in a container;
- FIG. 4 is a schematic cross-sectional view showing another form of arrangement of SiC powder layers and seed crystals in a container;
- FIG. 4 is a schematic cross-sectional view showing one mode of arrangement of a SiC powder layer, seed crystals, and a dense body in a container;
- FIG. 4 is a schematic cross-sectional view showing one mode of arrangement of a SiC powder layer, seed crystals, and a dense body in a container;
- FIG. 4 is a schematic cross-sectional view showing another form of arrangement of a SiC powder layer, seed crystals, and a dense body in a container;
- FIG. 4 is a schematic cross-sectional view showing another form of arrangement of a SiC powder layer, seed crystals, and a dense body in a container;
- FIG. 4 is a schematic cross-sectional view showing another form of arrangement of a SiC powder layer, seed crystals, and a dense body in a container;
- FIG. 4 is a schematic cross-sectional view showing another form of arrangement of a SiC powder layer, seed crystals, and a dense body in a container;
- 2 is a top view of SiC single crystal substrate 10 for explaining a method for measuring the amount of warpage of SiC single crystal substrate 10.
- FIG. 2 is a schematic cross-sectional view of SiC single crystal substrate 10 for explaining a method for measuring the amount of warpage of SiC single crystal substrate 10;
- FIG. 2 is a schematic cross-sectional view of SiC single crystal substrate 10 for explaining a method for measuring the amount of warpage of SiC single crystal substrate 10;
- the present invention relates to a method for manufacturing a SiC single crystal substrate.
- a SiC single crystal as a seed crystal and a SiC powder layer are arranged in a container while being in contact with each other.
- the container is placed in an effective heating zone within the firing furnace, the temperature being controlled within ⁇ 50° C. of the set temperature, and heat treatment is performed, thereby growing a SiC single crystal on the seed crystal.
- SiC single crystal as the seed crystal and the SiC powder layer in contact with each other and with a small temperature gradient, SiC with a low basal plane dislocation density and a small amount of warpage can be obtained.
- Single crystal substrates can be produced.
- the method for manufacturing a SiC single crystal substrate includes (1) arranging a seed crystal and a SiC powder layer, and (2) performing heat treatment to grow a SiC single crystal.
- a SiC single crystal as a seed crystal and a SiC powder layer are arranged in a container while being in contact with each other.
- the seed crystal is typically composed of a SiC single crystal and has a crystal growth surface.
- the polymorph (polytype), off-angle and polarity of the SiC single crystal are not particularly limited, but the polymorph is preferably 4H, 6H or 3C.
- a SiC single crystal formed on a Si substrate may be used as the seed crystal.
- the crystal growth plane on the SiC single crystal as the seed crystal may be the Si plane, the C plane, or both the Si plane and the C plane.
- a SiC powder layer typically refers to SiC powder spread in layers in a container. Also, this SiC powder layer is typically composed of SiC powder.
- the SiC powder may be either ⁇ -SiC or ⁇ -SiC.
- the particle size and purity of the SiC powder are not particularly limited, and any commercially available powder can be used. However, in order to produce a SiC single crystal substrate of high purity, it is desirable that the SiC powder also be of high purity.
- the SiC powder layer may contain additives in addition to the SiC powder.
- the arrangement positions of the seed crystal 4 and the SiC powder layer 6 are not particularly limited as long as they are in contact with each other. That is, as shown in FIG. 1, the seed crystal 4 may be arranged on the inner bottom surface of the container 2, and the SiC powder layer 6 may be arranged thereon. Alternatively, as shown in FIG. A seed crystal 4 may be embedded in the layer 6 . Alternatively, the seed crystal 4 may be placed on the upper surface of the SiC powder layer 6 arranged on the inner bottom surface of the container 2 as shown in FIG. In any case, it is preferred that the seed crystal 4 is in contact with the SiC powder layer 6 only on one side thereof.
- a plurality of seed crystals 4 may be arranged in one container 2 as long as the seed crystals 4 and the SiC powder layer 6 are in contact with each other. Furthermore, as long as the seed crystal 4 and the SiC powder layer 6 are in contact with each other as shown in FIG. A lateral space may be provided in the .
- the dense body 8 may be arranged on the bottom and/or top surface of the SiC powder layer 6 (excluding the surface that contacts the seed crystal 4). By arranging the dense body 8 in this way, it is possible to prevent impurities from entering from the inner bottom surface of the container 2 and/or the container lid 2b, and it is possible to grow a SiC single crystal of higher purity.
- the dense body 8 may be arranged on the upper surface of the SiC powder layer 6 as shown in FIG. If the seed crystal 4 is not placed on the inner bottom surface of the container 2, a dense body 8 may be placed between the SiC powder layer 6 and the inner bottom surface of the container 2 as shown in FIG. When the seed crystal 4 is embedded in the SiC powder layer 6, as shown in FIG. 8 may be placed.
- a dense body 8 may be arranged around the outer edge of the SiC powder layer 6 .
- a dense body 8 may be arranged between the outer peripheral portion of the SiC powder layer 6 and the inner wall of the container 2 . At this time, it is preferable that the dense body 8 is in contact with at least the outer peripheral portion of the SiC powder layer 6 .
- FIG. 8 shows that the dense body 8 is in contact with at least the outer peripheral portion of the SiC powder layer 6 .
- the dense body 8 is arranged on the bottom surface and/or the top surface of the SiC powder layer 6 (excluding the surface in contact with the seed crystal 4), and the outer peripheral edge of the SiC powder layer 6 It is preferable that the dense body 8 is arranged in the .
- the dense body 8 is preferably a solid with a relative density of 90% or higher, more preferably 95% or higher, and even more preferably 99% or higher.
- the relative density can be determined, for example, by dividing the bulk density of a dense body measured by the Archimedes method by the theoretical density of the dense body and multiplying the value by 100.
- the dense body 8 is not particularly limited as long as it does not sublime or melt and does not react with SiC at the firing temperature for the heat treatment described below. Examples of materials for such a dense body 8 include carbides such as TiC, TaC, NbC and WC, and polycrystalline nitrides such as Si 3 N 4 and TiN.
- the shape of the dense body 8 is not particularly limited, it is preferably layered.
- the material of the container 2 is not particularly limited as long as it does not sublime or melt at the firing temperature during the heat treatment described later, but a graphite or SiC container is desirable.
- the inner wall and the outer wall of the container 2 may be coated. Examples of coating materials include SiC, TiC, TaC, NbC, WC, and the like.
- the shape of the container 2 is not particularly limited. Preferably, a lid 2b is provided.
- heat treatment is performed by placing the container in an effective heating zone controlled within a temperature range of ⁇ 50° C. set temperature in the firing furnace, thereby growing a SiC single crystal on the seed crystal. .
- the heat treatment can be performed in a state where the temperature gradient is small.
- the "effective heating zone” is defined by JIS B 6905:1995 as "the charge zone in the heat treatment apparatus capable of keeping the metal product within the allowable temperature range according to the purpose of the heat treatment”.
- the temperature range of the effective heating zone is within ⁇ 50°C of the set temperature, preferably within ⁇ 20°C of the set temperature, and more preferably within ⁇ 10°C of the set temperature. As the temperature range is narrower, the heat treatment can be performed with a smaller temperature gradient, which makes it possible to grow a SiC single crystal of higher quality (that is, with a lower dislocation density and a smaller amount of warpage). .
- the firing furnace used for heat treatment is not particularly limited as long as SiC crystal growth occurs on the seed crystal, and known firing furnaces such as resistance furnaces, arc furnaces and induction furnaces may be used.
- the atmosphere in the firing furnace during firing is preferably vacuum, nitrogen, inert gas, or a mixed atmosphere of nitrogen and inert gas.
- the heat treatment may be performed under normal pressure or under pressure such as hot pressing.
- the heat treatment temperature is preferably 1700 to 2700°C, more preferably 2000 to 2600°C, still more preferably 2200 to 2500°C.
- the holding time at the temperature within the above range is not particularly limited, and the longer the holding time, the thicker the SiC single crystal can be grown. Therefore, the holding time can be set according to the desired thickness. .
- a SiC single crystal substrate can be obtained by performing chemical mechanical polishing (CMP) finishing after polishing using diamond abrasive grains.
- a SiC single crystal substrate having a low basal plane dislocation density and a small amount of warpage can be manufactured.
- the basal plane dislocation density of at least one surface of the SiC single crystal substrate is preferably 0 to 1.0 ⁇ 10 2 cm ⁇ 2 , more preferably 0 to 5.0 ⁇ 10 1 cm ⁇ 2 , still more preferably 0 to 1.0 ⁇ 10 1 cm ⁇ 2 . 1.0 ⁇ 10 1 cm ⁇ 2 .
- the amount of warpage of the SiC single crystal substrate is preferably 0 to 40 ⁇ m, more preferably 0 to 30 ⁇ m, still more preferably 0 to 20 ⁇ m.
- warp amount refers to a point G Draw two straight lines X and Y that are perpendicular to each other through
- a line segment extending from an arbitrary point on the curve AB between points A and B on the surface of the SiC single crystal substrate so as to be perpendicular to the line segment AB, this A point P is determined on the curve AB such that the distance of the line segment is the longest
- the distance between the line segment AB and the point P is the amount of warpage ⁇
- the point C on the surface of the SiC single crystal substrate and Among the line segments extending perpendicular to the line segment CD from any point on the curve CD between the point D, the point R on the curve CD that has the longest distance from this line segment is When (iv) the distance between the line segment CD and the point R is the amount of warp ⁇ , (v) the arithmetic mean value of the amounts of warp ⁇ and
- the SiC single crystal substrate is preferably oriented in the c-axis direction and the a-axis direction.
- the SiC single crystal substrate may be a SiC single crystal or a mosaic crystal as long as it is oriented in the biaxial directions of the c-axis and the a-axis.
- Mosaic crystals are aggregates of crystals that do not have distinct grain boundaries but have slightly different crystal orientations in one or both of the c-axis and a-axis.
- the orientation evaluation method is not particularly limited, but for example, a known analysis method such as an EBSD (Electron Back Scatter Diffraction Patterns) method or an X-ray pole figure can be used.
- inverse pole figure mapping of the surface (plate surface) of the SiC single crystal substrate or a cross section perpendicular to the plate surface is measured.
- (C) the tilt angle from the first axis is distributed within ⁇ 10°;
- (D) the tilt angle from the second axis is ⁇ 10 It can be defined that it is oriented in two axes, the substantially normal direction and the substantially plate surface direction, when it satisfies the four conditions that the distribution is within 100°.
- the film is oriented along two axes, the c-axis and the a-axis.
- the substantially in-plane direction of the plate may be oriented in a specific direction (for example, the a-axis) orthogonal to the c-axis.
- the SiC single crystal substrate may be oriented in two axes, ie, the substantially normal direction and the substantially in-plane direction, but the substantially normal direction is preferably oriented along the c-axis.
- the smaller the tilt angle distribution in the substantially normal direction and/or the substantially in-plane direction the smaller the mosaic property of the SiC single crystal substrate. Therefore, from the viewpoint of the crystallinity of the SiC single crystal substrate, the tilt angle distribution is preferably small both in the normal direction and in the plate surface direction.
- Example 1 Production of SiC single crystal A commercially available SiC single crystal substrate (4H—SiC, diameter 100 mm (4 inches), off angle 4°, thickness 0.35 mm) to be used as a seed crystal is filled in a carbon container. It was embedded in commercially available ⁇ -SiC powder (volume-based D50 particle size: 2.3 ⁇ m). The container is placed in an effective heating zone of a resistance furnace (firing furnace) controlled within a set temperature range of ⁇ 50°C, and heat-treated at 2450°C for 10 hours in an argon atmosphere to form SiC on the seed crystal. A single crystal was grown.
- a resistance furnace firing furnace
- SiC single crystal substrate 3-1 Measurement of substrate warpage
- LT-9010M manufactured by Keyence Corporation
- amount was measured.
- FIG. 10 in a plan view figure when the surface of SiC single crystal substrate 10 (SiC single crystal 30) is viewed in plan, two straight lines X that pass through point G, which is the center of gravity of the plan view figure, are perpendicular to each other. and Y were drawn, and two points A and B on the straight line X, each 45 mm away from the point G, and two points C and D, each 45 mm away from the point G on the straight line Y, were determined. Subsequently, as shown in FIG.
- the line AB becomes perpendicular to line segment AB.
- a point P on the curve AB that has the longest distance of the line segment is determined (for example, in FIG. 11, points P, O, etc. are arbitrary points on the curve AB
- the longest line segment among the line segments extended from each point so as to be perpendicular to the line segment AB is the line segment extended from the point P).
- the distance between the line segment AB and the point P was defined as the amount of warpage ⁇ . Further, as shown in FIG.
- a point R on the curve CD that maximizes the distance of the line segment is determined (for example, in FIG. 12, the point R, the point O, etc. are arbitrary points on the curve CD
- the longest line segment among the line segments extended from each point so as to be perpendicular to the line segment CD is the line segment extended from the point R).
- the distance between the line segment CD and the point R was defined as the amount of warpage ⁇ .
- the average value of these warp amounts ⁇ and ⁇ was taken as the warp amount of the SiC single crystal substrate. The results were as shown in Table 1.
- the total number of basal plane dislocations was measured by photographing 100 fields of view of 2.8 mm long ⁇ 3.6 mm wide at a magnification of 20 for an arbitrary portion of the sample surface.
- the basal plane dislocation density was calculated by dividing by 10.1 cm 2 , which is the total area of the visual field. The results were as shown in Table 1.
- Example 2 In the above (1), a commercially available SiC single crystal substrate as a seed crystal is placed on a commercially available ⁇ -SiC powder filled in a carbon container so that only the Si surface of the seed crystal is in contact with the powder. A SiC single crystal substrate was produced and evaluated in the same manner as in Example 1, except that the above was performed. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- Example 3 In the above (1), a commercially available SiC single crystal substrate as a seed crystal is placed on the bottom of a carbon container so that the Si surface of the substrate faces upward, and commercially available ⁇ -SiC powder is filled from above. A SiC single crystal substrate was produced and evaluated in the same manner as in Example 1, except that the above was performed. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- Example 4 In the above (1), (i) a commercially available SiC single crystal substrate as a seed crystal is placed on the bottom of a carbon container so that the Si surface of the substrate faces upward, and commercially available ⁇ -SiC is placed on the bottom of the container.
- a SiC single crystal substrate was fabricated in the same manner as in Example 1 except that the powder was filled and (ii) a TaC polycrystalline dense body (relative density of 90% or more) was further placed on the upper surface of the ⁇ -SiC powder layer. Production and evaluation were performed. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- a TaC polycrystalline dense body (relative density of 90% or more) is placed at the bottom of a carbon container, and (ii) commercially available ⁇ -SiC powder is filled from above, Furthermore, a SiC single crystal substrate in the same manner as in Example 1 except that a commercially available SiC single crystal substrate as a seed crystal was placed on the ⁇ -SiC powder layer so that only the Si surface of the substrate was in contact with the powder. was produced and evaluated. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- Example 6 In the above (1), (i) a TaC polycrystalline dense body (relative density of 90% or more) is placed on the bottom of a carbon container, (ii) after filling commercially available ⁇ -SiC powder from above, except that a commercially available SiC single crystal substrate serving as a seed crystal was embedded inside, and (iii) a TaC polycrystalline dense body (relative density of 90% or more) was further placed on the ⁇ -SiC powder. A SiC single crystal substrate was produced and evaluated in the same manner as in Example 1. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- Example 7 In the above (1), the ring-shaped TaC polycrystalline dense body (relative density of 90% or more) is arranged along the inner wall of the carbon container (i.e., the SiC powder layer has a relative density of 90% at the outer edge of the container.
- SiC single crystal substrates were produced and evaluated in the same manner as in Example 1, except that the above dense bodies were arranged. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- Example 8 In the above (1), the SiC single crystal substrate was fabricated in the same manner as in Example 2, except that the ring-shaped TaC polycrystalline dense body (relative density of 90% or more) was arranged along the inner wall of the carbon container. Production and evaluation were performed. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- Example 9 the SiC single crystal substrate was fabricated in the same manner as in Example 3, except that the ring-shaped TaC polycrystalline dense body (relative density of 90% or more) was arranged along the inner wall of the carbon container. Production and evaluation were performed. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- the SiC single crystal substrate was fabricated in the same manner as in Example 4, except that the ring-shaped TaC polycrystalline dense body (relative density of 90% or more) was arranged along the inner wall of the carbon container. Production and evaluation were performed. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- Example 11 the SiC single crystal substrate was fabricated in the same manner as in Example 5, except that the ring-shaped TaC polycrystalline dense body (relative density of 90% or more) was arranged along the inner wall of the carbon container. Production and evaluation were performed. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- Example 12 A SiC single crystal substrate was fabricated in the same manner as in Example 6, except that in (1) above, a ring-shaped TaC polycrystalline dense body (with a relative density of 90% or more) was arranged along the inner wall of the carbon container. Production and evaluation were performed. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- Example 13 (Comparison) In the above (1), a ⁇ -SiC polycrystalline plate produced by a thermal CVD method is used instead of the ⁇ -SiC powder, and the ⁇ -SiC polycrystalline plate and the Si surface of a commercially available SiC single crystal substrate serving as a seed crystal.
- a SiC single crystal substrate was produced and evaluated in the same manner as in Example 1, except that it was placed in a carbon container and heat-treated while in contact with each other. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- Example 14 (comparative) In the above (1), a commercially available SiC single crystal substrate as a seed crystal is placed on a commercially available ⁇ -SiC powder filled in a carbon container, and a carbon-made seed crystal is placed on the ⁇ -SiC powder so that the seed crystal does not come into contact with the ⁇ -SiC powder.
- Example 15 (comparative) A SiC single crystal substrate was polished and evaluated in the same manner as in Example 1, except that the SiC single crystal was produced as follows. Table 1 shows the amount of warpage and basal plane dislocation density of the obtained substrate.
- the SiC single crystal as the seed crystal and the SiC powder layer are brought into contact with each other, and the heat treatment is performed in a state where the temperature gradient is small (that is, the effective heating controlled within the set temperature ⁇ 50 ° C.
- the temperature gradient is small (that is, the effective heating controlled within the set temperature ⁇ 50 ° C.)
- SiC single crystal substrates with a low basal plane dislocation density can be obtained by heat treatment in the tropics).
- the SiC single crystal substrate has a small amount of thermal stress, a SiC single crystal substrate with a small amount of warpage can be obtained.
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Abstract
Description
前記容器を焼成炉内の、設定温度±50℃以内の温度域に制御された有効加熱帯に配置して熱処理を行い、それにより前記種結晶上にSiC単結晶を成長させる工程と、
を含む、SiC単結晶基板の製造方法が提供される。
前記反り量は、前記SiC単結晶基板の表面を平面視したときの平面視図形において、前記平面視図形の重心である点Gを通り互いに直交する2つの直線X及びYを引き、前記直線X上で前記点Gからそれぞれ45mm離れた2点A及びBと、前記直線Y上で前記点Gからそれぞれ45mm離れた2点C及びDとを定めた場合、(i)前記SiC単結晶基板の表面における前記点Aと前記点Bとの間の曲線AB上の任意の点から線分ABに対して垂直になるように延ばした線分のうち、該線分の距離が最長となるような前記曲線AB上の点Pを定め、(ii)前記線分ABと前記点Pとの距離を反り量αとし、(iii)前記SiC単結晶基板の表面における前記点Cと前記点Dとの間の曲線CD上の任意の点から線分CDに対して垂直になるように延ばした線分のうち、該線分の距離が最長となるような前記曲線CD上の点Rを定め、(iv)前記線分CDと前記点Rとの距離を反り量βとしたとき、(v)前記反り量α及びβの算術平均値として定義される、SiC単結晶基板が提供される。
本発明は、SiC単結晶基板の製造方法に関する。この製造方法においては、まず、種結晶としてのSiC単結晶と、SiC粉末層とを互いに接触した状態で容器内に配置する。次に、容器を焼成炉内の、設定温度±50℃以内の温度域に制御された有効加熱帯に配置して熱処理を行い、それにより種結晶上にSiC単結晶を成長させる。このように、種結晶としてのSiC単結晶とSiC粉末層とを、互いに接触した状態、かつ、温度勾配が小さい状態で熱処理することにより、基底面転位密度が低く、かつ、反り量が小さいSiC単結晶基板を製造することができる。
まず、種結晶としてのSiC単結晶と、SiC粉末層とを互いに接触した状態で容器内に配置する。種結晶は、典型的にはSiC単結晶で構成されており、結晶成長面を有する。SiC単結晶の多形(ポリタイプ)、オフ角、及び極性は特に限定されるものではないが、多形は4H、6H又は3Cが好ましい。また、種結晶として、Si基板上に成膜されたSiC単結晶を用いてもよい。種結晶としてのSiC単結晶上の結晶成長面は、Si面でもC面でもよく、Si面及びC面の両面でもよい。
上記(1)の後、容器を焼成炉内の、設定温度±50℃以内の温度域に制御された有効加熱帯に配置して熱処理を行い、それにより種結晶上にSiC単結晶を成長させる。こうすることで、温度勾配が小さい状態で熱処理を行うことができる。ここで、「有効加熱帯」とはJIS B 6905:1995により定義される「熱処理の目的に応じて、金属製品を温度許容範囲内に保持できる熱処理装置における装入領域」のことをいう。上記有効加熱帯の温度域は、設定温度±50℃以内であり、好ましくは設定温度±20℃以内、より好ましくは設定温度±10℃以内である。このように温度域が狭いほど、温度勾配がより小さい状態で熱処理を行うことができ、より品質の良い(すなわち、転位密度が低く反り量が小さい)SiC単結晶を成長させることが可能となる。
こうして種結晶上にSiC単結晶を成長させた後、SiC単結晶の表面を研磨するのが好ましい。例えば、ダイヤモンド砥粒を用いて研磨加工した後、化学機械研磨(CMP)仕上げをすることで、SiC単結晶基板を得ることができる。
上述した製造方法により、基底面転位密度が低く、かつ、反り量が小さいSiC単結晶基板を製造することができる。SiC単結晶基板の少なくとも一方の表面の基底面転位密度は、好ましくは0~1.0×102cm-2、より好ましくは0~5.0×101cm-2、さらに好ましくは0~1.0×101cm-2である。また、SiC単結晶基板の反り量は、好ましくは0~40μm、より好ましくは0~30μm、さらに好ましくは0~20μmである。
(1)SiC単結晶の作製
種結晶となる市販のSiC単結晶基板(4H-SiC、直径100mm(4インチ)、オフ角4°、厚さ0.35mm)を、カーボン製の容器内に充填した市販のβ-SiC粉末(体積基準D50粒径:2.3μm)に埋設した。容器を抵抗炉(焼成炉)の、設定温度±50℃以内の温度域に制御された有効加熱帯に配置し、アルゴン雰囲気中で2450℃にて10時間熱処理することで、種結晶上にSiC単結晶を成長させた。
得られたSiC単結晶の表面(Si面及びC面)を、ダイヤモンド砥粒を用いて研磨加工した後、化学機械研磨(CMP)仕上げをしてSiC単結晶基板を得た。
(3-1)基板の反り測定
得られたSiC単結晶基板の研磨面に対し、高精度レーザ測定器(株式会社キーエンス製 LT-9010M)を用いて、反り量を測定した。図10に示すように、SiC単結晶基板10の表面(SiC単結晶30)を平面視したときの平面視図形において、その平面視図形の重心である点Gを通り互いに直交する2つの直線X及びYを引き、直線X上で点Gからそれぞれ45mm離れた2点A及びBと、直線Y上で点Gからそれぞれ45mm離れた2点C及びDとを定めた。続いて、図11に示すように、SiC単結晶基板10の表面(SiC単結晶30)における点Aと点Bとの間の曲線AB上の任意の点から線分ABに対して垂直になるように延ばした線分のうち、その線分の距離が最長となるような曲線AB上の点Pを定めた(例えば、図11において、曲線AB上の任意の点として点Pや点O等があるが、それぞれの点から線分ABに対して垂直になるように延ばした線分のうち最長の線分となるのは点Pから伸ばした線分となる)。そして、線分ABと点Pとの距離を反り量αとした。また、図12に示すように、SiC単結晶基板10の表面(SiC単結晶30)における点Cと点Dとの間の曲線CD上の任意の点から線分CDに対して垂直になるように延ばした線分のうち、その線分の距離が最長となるような曲線CD上の点Rを定めた(例えば、図12において、曲線CD上の任意の点として点Rや点O等があるが、それぞれの点から線分CDに対して垂直になるように延ばした線分のうち最長の線分となるのは点Rから伸ばした線分となる)。そして、線分CDと点Rとの距離を反り量βとした。これらの反り量α及びβの平均値をSiC単結晶基板の反り量とした。結果は表1に示されるとおりであった。
ニッケル製の坩堝に、上記(2)で得られたSiC単結晶基板をKOH結晶と共に入れた。この坩堝を電気炉で、500℃で10分間、エッチング処理した。エッチング処理後のサンプル(SiC単結晶基板)を洗浄し、その表面を光学顕微鏡にて観察し、ピットの形状から各種欠陥の種類を判断した。このうち、基底面転位の数を測定し、基底面転位数(個)を観察領域の面積(cm2)で除することで、基底面転位密度(cm-2)を計算した。具体的には、サンプル表面の任意の箇所の部位について、縦2.8mm×横3.6mmの視野を倍率20倍で100視野分撮影して基底面転位の総数を測定し、この総数を100視野分の総面積である10.1cm2で除することにより基底面転位密度を算出した。結果は表1に示されるとおりであった。
上記(1)において、種結晶となる市販のSiC単結晶基板を、カーボン製の容器内に充填した市販のβ-SiC粉末上に、種結晶のSi面のみが粉末と接触するように載置したこと以外は、例1と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、種結晶となる市販のSiC単結晶基板を、基板のSi面が上向きとなるように、カーボン製の容器の底に配置し、その上から市販のβ-SiC粉末を充填したこと以外は、例1と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、(i)種結晶となる市販のSiC単結晶基板を、基板のSi面が上向きとなるように、カーボン製の容器の底に配置し、その上から市販のβ-SiC粉末を充填したこと、及び(ii)さらにβ-SiC粉末層の上面にTaC多結晶緻密体(相対密度90%以上)を載置したこと以外は、例1と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、(i)TaC多結晶緻密体(相対密度90%以上)をカーボン製の容器の底に配置したこと、及び(ii)その上から市販のβ-SiC粉末を充填し、さらにβ-SiC粉末層の上に種結晶となる市販のSiC単結晶基板を、基板のSi面のみが粉末と接触するように載置したこと以外は、例1と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、(i)TaC多結晶緻密体(相対密度90%以上)をカーボン製の容器の底に配置したこと、(ii)その上から市販のβ-SiC粉末を充填後、その中に種結晶となる市販のSiC単結晶基板を埋設したこと、及び(iii)さらにβ-SiC粉末の上にTaC多結晶緻密体(相対密度90%以上)を載置したこと以外は、例1と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、リング状のTaC多結晶緻密体(相対密度90%以上)を、カーボン製の容器の内壁に沿うように配置したこと(すなわちSiC粉末層の外周縁に相対密度が90%以上の緻密体を配置したこと)以外は、例1と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、リング状のTaC多結晶緻密体(相対密度90%以上)を、カーボン製の容器の内壁に沿うように配置したこと以外は、例2と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、リング状のTaC多結晶緻密体(相対密度90%以上)を、カーボン製の容器の内壁に沿うように配置したこと以外は、例3と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、リング状のTaC多結晶緻密体(相対密度90%以上)を、カーボン製の容器の内壁に沿うように配置したこと以外は、例4と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、リング状のTaC多結晶緻密体(相対密度90%以上)を、カーボン製の容器の内壁に沿うように配置したこと以外は、例5と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、リング状のTaC多結晶緻密体(相対密度90%以上)を、カーボン製の容器の内壁に沿うように配置したこと以外は、例6と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、β-SiC粉末の代わりに熱CVD法で作製したβ-SiC多結晶板を用い、β-SiC多結晶板と、種結晶となる市販のSiC単結晶基板のSi面とを接触させた状態でカーボン製の容器に配置して熱処理したこと以外は、例1と同様にしてSiC単結晶基板の作製及び評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、種結晶となる市販のSiC単結晶基板を、カーボン製の容器内に充填した市販のβ-SiC粉末上に、種結晶がβ-SiC粉末と接触しないようにカーボン製のスペーサー(厚さ2mm)を介して配置したこと以外は、例1と同様に熱処理を行い、SiC単結晶基板の作製を試みた。しかし、種結晶上にSiC単結晶が成長しなかったため、反り測定及び基底面転位密度の評価は実施しなかった。
SiC単結晶の作製を以下のように行ったこと以外は、例1と同様に、SiC単結晶基板を研磨し、評価を行った。得られた基板の反り量及び基底面転位密度は表1に示されるとおりであった。
上記(1)において、種結晶となる市販のSiC単結晶基板を、カーボン製の容器内に充填した市販のβ-SiC粉末に埋設した。この容器を抵抗炉の有効加熱帯の外に配置し、設定温度±50℃を超えるような温度勾配が大きい状態で、アルゴン雰囲気中で2450℃にて10時間熱処理することで、種結晶上にSiC単結晶を成長させた。
Claims (10)
- 種結晶としてのSiC単結晶と、SiC粉末層とを互いに接触した状態で容器内に配置する工程と、
前記容器を焼成炉内の、設定温度±50℃以内の温度域に制御された有効加熱帯に配置して熱処理を行い、それにより前記種結晶上にSiC単結晶を成長させる工程と、
を含む、SiC単結晶基板の製造方法。 - 前記種結晶が、その一方の面でのみ、前記SiC粉末層と接触している、請求項1に記載のSiC単結晶基板の製造方法。
- 前記温度域が設定温度±20℃以内である、請求項1又は2に記載のSiC単結晶基板の製造方法。
- 前記温度域が設定温度±10℃以内である、請求項1~3のいずれか一項に記載のSiC単結晶基板の製造方法。
- 前記SiC粉末層の底面及び/又は上面(但し、前記種結晶と接触する面を除く)に、相対密度が90%以上の緻密体が配置される、請求項1~4のいずれか一項に記載のSiC単結晶基板の製造方法。
- 前記SiC粉末層の外周縁に、相対密度が90%以上の緻密体が配置される、請求項1~5のいずれか一項に記載のSiC単結晶基板の製造方法。
- 前記SiC粉末層の底面及び/又は上面(但し、前記種結晶と接触する面を除く)に、相対密度が90%以上の緻密体が配置され、かつ、前記SiC粉末層の外周縁に、相対密度が90%以上の緻密体が配置される、請求項1~4のいずれか一項に記載のSiC単結晶基板の製造方法。
- 前記緻密体の相対密度が95%以上である、請求項5~7のいずれか一項に記載のSiC単結晶基板の製造方法。
- 前記緻密体の相対密度が99%以上である、請求項5~8のいずれか一項に記載のSiC単結晶基板の製造方法。
- 少なくとも一方の表面の基底面転位密度が0~1.0×102cm-2であり、かつ、基板の反り量が0~40μmであるSiC単結晶基板であって、
前記反り量は、前記SiC単結晶基板の表面を平面視したときの平面視図形において、前記平面視図形の重心である点Gを通り互いに直交する2つの直線X及びYを引き、前記直線X上で前記点Gからそれぞれ45mm離れた2点A及びBと、前記直線Y上で前記点Gからそれぞれ45mm離れた2点C及びDとを定めた場合、(i)前記SiC単結晶基板の表面における前記点Aと前記点Bとの間の曲線AB上の任意の点から線分ABに対して垂直になるように延ばした線分のうち、該線分の距離が最長となるような前記曲線AB上の点Pを定め、(ii)前記線分ABと前記点Pとの距離を反り量αとし、(iii)前記SiC単結晶基板の表面における前記点Cと前記点Dとの間の曲線CD上の任意の点から線分CDに対して垂直になるように延ばした線分のうち、該線分の距離が最長となるような前記曲線CD上の点Rを定め、(iv)前記線分CDと前記点Rとの距離を反り量βとしたとき、(v)前記反り量α及びβの算術平均値として定義される、SiC単結晶基板。
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Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
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JP3248071B2 (ja) | 1998-10-08 | 2002-01-21 | 日本ピラー工業株式会社 | 単結晶SiC |
JP4069508B2 (ja) | 1998-07-21 | 2008-04-02 | 株式会社デンソー | 炭化珪素単結晶の製造方法 |
JP2010280546A (ja) * | 2009-06-05 | 2010-12-16 | Bridgestone Corp | 炭化珪素単結晶の製造方法 |
WO2020184059A1 (ja) * | 2019-03-11 | 2020-09-17 | 日本碍子株式会社 | SiC複合基板及び半導体デバイス |
WO2021060368A1 (ja) * | 2019-09-27 | 2021-04-01 | 学校法人関西学院 | SiC単結晶の製造方法、SiC単結晶の製造装置及びSiC単結晶ウェハ |
WO2021100564A1 (ja) * | 2019-11-20 | 2021-05-27 | 日本碍子株式会社 | SiC基板及びその製法 |
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Patent Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP4069508B2 (ja) | 1998-07-21 | 2008-04-02 | 株式会社デンソー | 炭化珪素単結晶の製造方法 |
JP3248071B2 (ja) | 1998-10-08 | 2002-01-21 | 日本ピラー工業株式会社 | 単結晶SiC |
JP2010280546A (ja) * | 2009-06-05 | 2010-12-16 | Bridgestone Corp | 炭化珪素単結晶の製造方法 |
WO2020184059A1 (ja) * | 2019-03-11 | 2020-09-17 | 日本碍子株式会社 | SiC複合基板及び半導体デバイス |
WO2021060368A1 (ja) * | 2019-09-27 | 2021-04-01 | 学校法人関西学院 | SiC単結晶の製造方法、SiC単結晶の製造装置及びSiC単結晶ウェハ |
WO2021100564A1 (ja) * | 2019-11-20 | 2021-05-27 | 日本碍子株式会社 | SiC基板及びその製法 |
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JPWO2023067736A1 (ja) | 2023-04-27 |
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