Method for forming crystal layer on a substrate

Abstract: A method for forming a crystal comprises implanting ions on the surface of a substrate to change the ion concentration in the depth direction of said substrate surface by said ion implantation, subjecting a desired position of said substrate surface with a sufficient area for crystal growth from a single crystal to exposure treatment to the depth where an exposed surface having larger nucleation density than the nucleation density of the surface of said substrate is exposed, thereby forming a nucleation surface comprising said exposed surface exposed by said exposure treatment and a nonnucleation surface comprising the surface of the substrate remaining without subjected to said exposure treatment, applying a crystal growth treatment for crystal growth from a single nucleus on said substrate to grow a single crystal from said single nucleus or form a polycrystal of a mass of single crystals grown from said single nucleus.

Description: BACKGROUND OF THE INVENTION Field of the Invention This invention relates to a method for forming a crystal, particularly to a method for forming a crystal by utilizing the difference in nucleation density (ΔND). The present invention may be suitably used for, for example, formation of crystals such as single crystals, polycrystals, etc. which can be preferably used for functional devices such as electronic devices, optical devices, magnetic devices, piezoelectric devices and surface acoustic devices of semiconductor integrated circuits, optical integrated circuits, magnetic circuits, etc. Related Background Art In the prior art, single crystal thin films to be used for functional devices such as electronic devices optical devices, etc. using semiconductor materials have been formed by epitaxial growth on a single crystal substrate. For example, on a Si single crystal substrate (silicon wafer), Si, Ge, GaAs, etc. have been known to be epitaxially grown from liquid phase, gas phase or solid phase. Also on a GaAs single crystal substrate, a single crystal such as of GaAs, GaAlAs, etc. has been known to be epitaxially grown. By use of a crystalline semiconductor thin film thus formed, a semiconductor device, an integration circuit, or an emission device such as semiconductor laser, LED, etc. is prepared. Also, recently, researches and developments of an ultra-high speed transitor by two-dimensional electronic gas, ultra-lattice device utilizing quantum well, etc. have been actively done, and these techniques have been made possible by the high precision epitaxial technique such as MBE (molecular beam epitaxy) or MOCVD (metal organic chemical vapor deposition) by use of ultra-high vacuum. In such epitaxial growth on a single crystal substrate, it is necessary to match the lattice constants and the thermal expansion coefficients between the single crystal material and the epitaxial growth layer. If this matching is insufficient, lattice defects will be developed in the epitaxial layer. Also, the elements constituting the substrate may be sometimes diffused into the epitaxial layer. Thus, it can be understood that the method of forming a single crystal semiconductor thin film of the prior art by epitaxial growth depends greatly on its substrate material. Mathews et al examined combinations of the substrate materials and epitaxial growth layers (EPITAXIAL GROWTH, Academic Press, New York, 1975, ed. by J.W. Mathews). Also, the size of the substrate is presently about 15 cm (6 inches) in the case of Si wafer in view of productivity and low cost, and enlargement of GaAs and sapphire substrate is further retarded. Besides, a single crystal substrate is high in production cost and therefore the cost per one chip becomes high. Thus, for forming a single crystal layer of good quality capable of forming a functional device having excellent characteristics according to the method of prior art, there has been the problem that the kinds of the substrate materials are limited to a very narrow scope. On the other hand, there has been active research and development of three-dimensional integrated circuits accomplishing higher integration and higher functions by forming semiconductor devices in the normal direction of the substrate by lamination. Also researches and developments of large area semiconductor devices such as solar batteries having devices arranged in an array on an inexpensive glass, liquid display devices provided with switching transistors, etc. are becoming abundant year by year. What is common to both of these is to require a technique to form a semiconductor thin film on an amorphous insulating material and form an electronic device such as transistor, etc. there. Among them, particularly it has been desired to have a technique for forming a single crystal semiconductor of high quality on an amorphous insulating material. Generally speaking, when a thin film is deposited on an amorphous insulating material substrate such as SiO₂, etc., due to deficiency of long distance order of the substrate material, the crystal structure of the deposited film becomes amorphous or polycrystalline under no control. Here, amorphous film is one under the state where, although the short distance order to the extent of the minimum approximate atoms is preserved, there is no longer distance order than that, while polycrystalline film is a collection of single crystal grains having no specific crystal direction separated by grain boundaries. For example, when Si film is formed on SiO₂ by the CVD method, if the deposition temperature is about 600 °C or lower, it becomes amorphous silicon film, or if it is higher than that temperature, it becomes a polycrystal silicon with a distribution of grain sizes from some 10 nm (100 Å) to some 100 nm (1000 Å). However, the grain sizes and the distribution thereof will vary greatly depending on the formation method. Further, a polycrystalline thin film of large grain sizes of a micrometre to a millimetre has been obtained by melting and solidifying an amorphous film or polycrystalline film with an energy beam such as laser, rod-shaped heater, etc. (Single-Crystal silicon on non-single-crystal insulators, Journal of crystal Growth vol. 63, No. 3, October, 1983, edited by G.W. Cullen). When a transistor is formed on the thin film of each crystal structure thus formed and the electron mobility is measured from the actuation characteristics of said transistor, a mobility of ca. 0.1 cm²/V·sec is obtained in the case of amorphous silicon, 1 to 10 cm²/V·sec in the case of a polycrystalline silicon film having an average grain size of some 10 nm (100 Å), and a value to the same extent as in the case of single crystal silicon film in the polycrystalline silicon film with enlarged grain sizes by melting and solidification. From these results, it can be understood that the device formed in the single crystal region within the crystal grain and the device formed as bridging over the grain boundary differ greatly in their electrical characteristics. More specifically, the deposited film on an amorphous material obtained by the prior art method becomes amorphous or polycrystalline structure having a grain size distribution, and the semiconductor device formed in such deposited film becomes greatly inferior in its performance as compared with the semiconductor device formed in a single crystal film. For this reason, the uses are limited to simple switching devices for which no high characteristic is demanded, solar batteries or photoelectric converting devices, etc. for which no high conversion efficiency is demanded. Also, the method of forming a polycrystalline thin film with large grain sizes by melting and solidification has the problem that it takes enormous time for enlargement of grain size. Productivity is poor because amporhous film or polycrystalline thin film is scanned with an energetic beam for each wafer, and also it is not suitable for large scale area production. Also, within the polycrystalline film thus formed, there exist randomly a large number of grain boundaries, which become the factor for obtaining no device of good characteristics when a semiconductor device is prepared by use of said polycrystalline film. Therefore, it has been strongly desired to have a method which can form a single crystal with high single crystallinity or a polycrystal controlled in the position of grain boundary easily and at low cost even on an amorphous film. Accordingly, the present Applicant has proposed European Published Patent Application No. 244081 which discloses a method of providing a single crystal film containing no grain boundary, a polycrystal controlled in grain size or the position of grain boundary, etc., without restriction of the base material for forming the crystal, for example, without restriction of the material, the chemical composition, size, etc. of the substraate. The above European Published Patent Application No. 244081 effects selective nucleus formation by utilizing the difference in nucleation density (ΔND) in the two kinds of materials with different nucleation densities (ND) depending on the place on the deposition surface relative to a certain deposition material (e.g. Si). Therefore, as the difference in nucleation density (ΔND) between two kinds of materials is greater, better selectivity can be obtained conveniently for selective nucleus formation. The technical meanings of the words "nucleus", "nucleation surface", "nonnucleation surface" as mentioned in the published specification and the present application are as follows. "Nucleus" refers to a stable nucleus having a size greater than the critical nucleus (the nucleus of which free energy becomes the maximum). Unless indicated otherwise, "nucleus" refers to a stable nucleus in this specification. "Nucleation surface" refers to an artificial surface of fine area possessed by the substrate on which crystal growth treatment is applied for forming a stable nucleus and permitting a single crystal to grow from a single nucleus. It is formed of a material with large nucleation density. "Nonnucleation surface" refers to a surface of the region for permitting no crystal to grow even if a nucleus is generated possessed by the substrate on which crystal growth treatment is applied, which covers substantially the whole surface of at least one surface of said substrate. It is formed of a material with small nucleation density. For example, to describe by referring to Fig. 1, when SiO₂ is used for forming the nonnucleation surface material and Si₃N₄ for forming the nucleation surface material, it can be seen from the graph that the difference in nucleation density (ΔND) between the both is about 10²-fold relative to Si. Substantially good selective nucleation is possible by use of the materials having such extent of difference in nucleation density (ΔND), but there may sometimes occur generation of a nucleus not only on the nucleation surface arranged at the desired position on the substrate but also on the nonnucleation surface (Error Nucleation). If the whole nucleation density (ND) is lowered too much by, for example, increasing the amount of HCl added for inhibiting such Error nucleus, there may occur such phenomenon as no formation of nucleus on Si₃N₄ surface which is the nucleation surface, whereby yield is lowered. Accordingly, to describe now about the case of utilizing SiO₂ for the non-nucleation surface and SiO₂ doped with Si ions for the nucleation surface, respectively, as shown in Fig. 1, one having Si ions implanted at a dosing amount of 2 x 10¹⁶ cm⁻² implanted on SiO₂ has a difference in nucleation density (ΔND) of about 10³-fold from SiO₂ itself, and an extremely large difference in nucleation density (ΔND) can be created at a greater dosing amount. Therefore, even if the whole nucleation density (ND) may be lowered by controlling the amount of HCl gas added, nuclei are generated with good yield at the nucleation surface to form a single crystal grown from a single nucleus, and also generation of Error nucleus can be sufficiently inhibited at the non-nucleation surface, whereby formation of a crystal on the nonnucleation surface can be prevented. Thus, it can be understood that the above "ion implantation method" (hereinafter written as I/I method) is a very effective means for the selective nucleation method. However, when the I/I method is practically practiced, the following inconveniences were found to occur in some cases. This is described by referring to Figs. 2A - 2C. First, for implanting ions in a fine nucleation region, the whole non-nucleation surface is required to be covered with a resist having a window opened at the fine nucleation region as mentioned above, and Si ions are implanted in the whole region including the nucleation surface and the non-nucleation surface (resist surface) (Fig. 2A). Next, the resist is removed with the use of an organic solvent, etc. (Fig. 2B). Whereas, at this time, only by implanting Si ions, something which appears to be denatured resist product remains in some cases. The above denatured product, according to the experiment by the present inventor, was sometimes generated when Si ions were implanted at a dosing amount of 3 x 10¹⁶cm⁻² or higher. Also, the denatured product contained carbon as the result of surface analysis, and it may also be estimated to remain in the form such as SiC. The above denatured product is a substance having very high nucleation density, and when selective nucleation is carried out, it has been also found that an Error nucleus may be sometimes formed with the denatured product as the centre and grown to a crystal (Fig. 2C). SUMMARY OF THE INVENTION The present method, of deposition for producing on the surface of a substrate one or more single crystals of a crystal forming material, is a development of that method described in EP-A-0 244 081 and in common with that method it comprises: establishing at a free surface of said substrate one or more deposition surface areas having under chosen conditions of deposition a property of nucleating said crystal forming material at a higher nucleation density than that of the adjacent deposition surface area, each of said one or more deposition surface areas being limited in size so that during an initial stage of the deposition each shall support the formation of a single nucleus only of the crystal forming material; depositing crystal forming material on the exposed free surface of said substrate under said chosen conditions of deposition, these conditions being such that said crystal forming material nucleates selectively on said one or more deposition surface areas and forms on each a single nucleus; and upon further deposition of said crystal forming material, growing a single crystal from each single nucleus. In accordance with the present invention this present method is characterised in that: said one or more deposition surface areas and said adjacent deposition surface area of said free surface of the substrate are established by: implanting ions in said substrate to differentiate the respective properties of substrate material at an exposed surface of the substrate and at a prescribed depth below said exposed surface such that the property of a surface of material at said prescribed depth shall be that of nucleating said crystal forming material at said higher nucleation density; and etching said substrate to produce one or more recesses reaching said prescribed depth so as to reveal a corresponding one or more deposition surface areas of said substrate. In this present method the free surface of the substrate is produced and differentiated by successive steps of ion implantation and etching. As such it does not rely upon the use of a patterned resist mask, and since no mask is exposed to energetic ions, the problem, discussed above, of nucleation on sites of denatured resist, is obviated. Incidentally, mention is made of French Patent Application FR-A-2 588 416. In this document there is disclosed a method of film formation in which film forming material is selectively deposited on respective spaced nucleation sites. Such sites are produced by an ion implantation during which selected areas only of the plane surface of the substrate are exposed to ion irradiation. An example is given of shallow silicon ion implantation in substrate material of silicon oxide. Surface differentiation does not depend on a combination of implant and etch processing as in the present invention. Nor is it disclosed that the nucleation site area is limited so that a single nucleus only shall form on each site. The implanted ions used in the present method may be such that they change the nucleating property of the substrate material to increase the density of nucleation. In such case ions are implanted to a depth which is not less than 10nm (100Å) and not greater than 110nm (1100Å) and etching is to a depth corresponding substantially to the projection range of the implanted ions. Advantageously the ions may be implanted by repeated doses, each dose at a different acceleration voltage. With appropriate choice of respective voltages the ion density profile can be made maximum or near maximum over an extended range of depths below the surface of the substrate. In this case, the depth of etching is then less critical. Where deposition of the crystal forming material is from a gaseous phase, an etchant gas such as hydrogen chloride can be included in the gaseous phase to further enhance the inhibition of nucleation on the adjacent deposition surface area. BRIEF DESCRIPTION OF THE DRAWINGS In the drawings: Fig. 1 is a graph showing difference in Si nucleation density on each material; Figs. 2A - 2C are diagrams illustrating the problem of residual resist denatured product when ion implantation is applied to the resist; Figs. 3A - 3C are schematic illustrations of the embodiments of the present invention; Fig. 4 is Depth profile of the implanted ion concentration when ions are implanted into the substrate; Fig. 5 shows the relationship between the Si atom density on the silicon oxide (SiOx) surface and the Si nucleation density; and Fig. 6 is Depth profile of the implanted ion density when ions are implanted into the substrate in multiple stages. DESCRIPTION OF THE PREFERRED EMBODIMENTS Embodiments of the invention will be described now and reference will be made to the drawings. The description that follows is given by way of example only. First, Fig. 3A shows an example in which Si ions are doped into the whole SiO₂ surface of a substrate having an amorphous SiO₂ surface by an ion implanter. The Si ions implanted into the above substrate exhibit a peculiar density profile (of implanted atoms) by the acceleration voltage of ions during implanting. At this time, the depth where the atomic density of implanted atoms is the highest within the distribution range is indicated as Projected Range: hereinafter called P.R. Next, Fig. 3B shows an example in which the sufficiently fine region is subjected to exposure treatment such as dry etching, wet etching, etc. to near the depth of P.R., thereby having the surface with larger nucleation density than the substrate surface exposed. The depth of this exposure treatment can be determined based on the calculation formula shown below. The exposed surface by the above exposure treatment at this time becomes the nucleation surface, and the SiO₂ surface where no exposure treatment as mentioned above applied becomes the nonnucleation surface. Next, Fig. 3C shows an example in which deposition is performed by use of selective nucleation conditions to form only one nucleus formed within the nucleation surface. The examples of implanting Si ions into the substrate having amorphous SiO₂ surface shown in Figs. 3A - 3C are examples of ions which increase the nucleation density by ion implantation. As other examples, an example of ion which reduces the nucleation density by ion implantation is to be described below. For example, oxygen ions are shallowly implanted on the whole surface of a substrate having amorphous silicon nitride surface by a low acceleration voltage. By doing so, a nonnucleation surface is formed on the above substrate surface by reducing the nucleation density of said substrate surface. Subsequently, a sufficiently fine region which is the desired position on the above nonnucleation surface is subjected to exposure treatment such as wet etching or dry etching beyound the depth of P.R., thereby having a surface with larger nucleation density than the substrate surface exposed, to form a substrate having the above nonnucleation surface and nucleation surface. Subsequently, a crystal growth treatment is applied on the above substrate to permit a single crystal to grow on the above nucleation surface. Further, ion implantation conditions, etc. are to be described in detail below. As also previously described, the method of changing the nucleation density by implantation of ions into the substrate surface which becomes the nonnucleation surface has such merits that the difference in nucleation density (ΔND) can be taken very large, that the difference in nucleation (ΔND) can be controlled by controlling the dosing amount of implanted ions. Here, for carrying out selective nucleation, it is desirable to make the difference in nucleation density (ΔND) between the nucleation surface and the nonnucleation surface 10²-fold or more. When carrying out selective nucleation with good selectivity, the difference in nucleation density (ΔND) may be more preferably about 10³ to 10⁶-fold. In the case of ND(Si₃N₄)/ND(SiO₂), the difference in nucleation density (ΔND) is about 10²-fold or more, and sufficient selective nucleation may be also possible even under such conditions, but generation of Error nucleus cannot be completely inhibited in some cases. In carrying out selective nucleation, for reducing generation of Error nucleus and preventing formation of crystal on the nonnucleation surface even under broad condition range, the difference in nucleation density (ΔND) may be preferably 10³-fold or more, but on the contrary, if the difference in nucleation (ΔND) is too large, it becomes necessary to use an operation such as lowering the whole nucleation density (ND) by flowing a large amount of HCl gas added for suppressing the nucleation density in order to grow a single crystal from only one nucleus on the nucleation surface. Then, the growth speed of the nucleus will become very slow to require a long time before a crystal with a desired size can be obtained, or the amount of the gas consumed becomes large, and therefore the practical upper limit of the difference in nucleation density (ΔND) may be appropriately about 10⁶-fold. In the embodiments of the present invention, as the material for the substrate surface in which ions are implanted, for example, insulating amorphous materials such as amorphous silicon oxide, amorphous silicon nitride, amorphous silicon oxynitride, etc. may be employed. Also, as the kind of the ion to be implanted in the surface of the substrate in the present invention, which may also differ depending on the kind of the crystal to be formed, for example, ions which change the nucleation density of the substrate surface relative to the crystal to be formed, such as Si, Ga, As or O, etc. may be included. Next, the implantation depth of ions is to be described. A depth which can be stably implanted by the ion implantation device used may be determined. In this connection, the P.R. of the implanted ions is not determined by the dosing amount, but only by the acceleration voltage of ions. Here, the depth of ion implantation may be desirably a P.R. of 10 nm (100 Å) to 110 nm (1100 Å). If the depth of P.R. is less than 10 nm (100 Å), because the value of σ becomes small, there is a trend that when ions increasing the nucleation density are implanted, the difference in nucleation density (ΔND) between the nonnucleation surface of the substrate surface and the nucleation surface exposed by the exposure treatment cannot be taken sufficiently. Also, when ions are implanted to a depth lower than 10 nm (100 Å), ion acceleration voltage is lower than 10 KeV and ions can not be implanted stably in general. On the other hand, if P.R. exceeds 110 nm (1100 Å), a long time is required for the exposure treatment, and also the ions implanted have a great energy, whereby the substrate surface tends to be damaged. Subsequently, for effecting selective nucleation with good selectivity, the dosing amount of the ions to be implanted into the substrate surface may be preferably 1 x 10¹⁶ cm⁻² to 1 x 10¹⁷ cm⁻² by taking the difference in nucleation density (ΔND) between the nucleation surafce and the nonnucleation surface within the range as specified above. It may be more preferable to dose ions at 1.5 x 10¹⁶ cm⁻² to 8 x 10¹⁶ cm⁻², optimally 2 x 10¹⁶ cm⁻² to 4 x 10¹⁶ cm⁻². Next, description is made about control of the difference in nucleation density (ΔND) which is also the most important point in applying the present invention. First, Fig. 5 shows the relationship between the Si atom density and the nucleation density(ND) on the surface when Si⁺ is implanted on SiO₂ measured by the present inventor. The surface density of Si atom is a value calculated from the dosing amount of implanted ions, etc, and the value of the nucleation density (ND) is measured under the crystal growth treatment conditions shown below: Gas flow rate ratio: SiH₂Cl₂/HCl/H₂=0.53/1.8/100; Substrate temperature: 950 °C; Pressure: 200 x 10² Pa (150 Torr); Treatment time: 8 minutes. The gas flow rate ratio is shown as SiH₂Cl₂/HCl/H₂=0.53/1.8/100, but when HCl flow rate ratio is varied, only the nucleation density (ND) as a whole moves in parallel, and therefore the difference in nucleation density (ΔND) may be considered to be constant not depending on the flow rate ratio of HCl. Here, when ion implantation and exposure treatment such as wet etching or dry etching are effected to surface densities of Si implanted into SiO₂ of, for example, 7.95 x 10¹⁴ (cm⁻²) and 8.15 x 10¹⁴ (cm⁻²), it can be understood that the difference in nucleation density (ΔND) becomes ca. 10³-fold. Now, the relationship between the surface density D(x) and the depth direction (X) is to be described in ions may be approximated to a Gaussian distribution having a peak at a certain depth as shown in Fig. 4. When the substrate depth direction is made X, and the position of P.R. X₀, its concentration function F(X) can be represented by: Therefore, the concentration F (O) of the implanted ions at the substrate surface becomes from X=0 as follows: Here, N₀ is the dosing amount of ions, and σ is standard deviation. From this, the ratio of the concentration at a certain depth to that at the surface becomes as follows: On the other hand, the ratio of surface density of the implanted ions is given as follows: From the depth of P.R. and the dosing amount determined by the acceleration voltage of implantation by use of these formulas, the surface density D (0) is calculated, and it can be determined what depth from the surface should be subjected to the exposure treatment from the above formulas, for the difference in nucleation density (ΔND) to be obtained from the graph shown in Fig. 5. In the following, Examples are shown. To rearrange the above formula (4) with respect to X, it becomes as follows: Since the above formula (5) is a quadratic function of X, generally two solutions are obtained. Here, for forming a crystal from a single nucleus from the bottom of a concavity formed by the exposure treatment, when an ion which increases the nucleation density relative to the crystal to be grown is implanted, it is preferable to select the smaller solution, while when an ion which reduces the nucleation density relative to the crystal to be grown is implanted, it is preferable to select the larger solution. The above exposure treament may include, for example, wet etching by use of an etchant containing HF, etc., dry etching by use of CHF₃/C₂F₆ gas, CF₄/H₂ gas, etc. Crystal growth treatment is applied on the substrate having the nonnucleation surface and the nucleation surface with sufficiently fine area for forming a single crystal from a single nucleus thus obtained. As the above crystal growth treatment, the gas phase methods including the chemical vapor deposition (CVD) method such as the plasma CVD method, the optical CVD method, the MOCVD method, etc., or the liquid phase method such as the gradual cooling method, the temperature gradient method, etc. may be preferred. As the gases to be introduced, there may be employed starting materials containing the constituent elements of the crystal to be formed which can be supplied in gaseous state and gases of HCl, etc. for inhibiting undesirable nucleus generation on the above substrate surface, and gases such as H₂, etc. When a doped crystal is to be formed, a gas containing the element to be doped may be also added into the above gases introduced. Specific examples of the gases to be introduced may include, for example, (CH₃)₃Ga/AsH3/HCl/H₂), (SiH₂Cl/HCl/H₂), (SiHCl₃/HCl/H₂), (SiCl₄/H₂), (SiCl₄/HCl/H₂), (SiH₄/HCl/H₂), etc. Also, for selective nucleation with good selectivity at a desired position, the pressure during the crystal growth treatment may be preferably 333 x 10²Pa (250 Torr)or lower. Here, in order to obtain high selectivity without lowering the crystal growth speed the pressure may be more preferably 11 x 10³ to 227 x 10² Pa (80 to 170 Torr), optimally 133 x 10² to 200 x 10² Pa (100 to 150 Torr). For formation of a crystal having desired characteristics with good selectivity, the substrate temperature during the crystal growth treatment may be preferably 800 °C to 1200 °C, more preferably 900 °C to 1100 °C, in the case of the hot CVD method. In the case of other gas phase methods, the substrate temperature may be preferably 500 °C to 800 °C, more preferably 600 °C to 700 °C. The example as described above is an example in which ion implantation to a substrate surface is effected at a constant acceleration voltage. As an example of other conditions for effecting ion implantation, an example of performing ion implantation by multi-stage implantation as shown in Fig. 6 is to be described below. When ions are implanted with various acceleration voltages in the same dosing amount, the respective positions of P.R. are varied as X₁, X₂ and X₃, but the atomic concentrations implanted at the respective depths become generally F(X₁)=F(X₂)=F(X₃). Accordingly, since the same nucleation density (ND) can be obtained even if either depth of X₁ to X₃ may be exposed in carrying out the exposure treatment, it is possible to form a substrate having a nonnucleation surface and a nucleation surface more easily with stability between the substrates and with good reproducibility without controlling the depth of the exposure treatment very accurately. Example 1 Example 1 of the present invention is described by referring to Fig. 3A - 3C. First, the surface of a 10 cm (4 inch) Si wafer was thermally oxidized to form an amorphous SiO₂ layer with a thickness of 200 nm (2000 Å)as the material for the nonnucleation surface thereon. There, Si ions were implanted by an ion implanter at an acceleration voltage ot 20 KeV and a dosing amount of 1 x 10¹⁶ cm⁻². P.R. (X₀) when Si was implanted at 20 KeV on the above SiO₂ was 21.1 nm (211 Å), and the standard deviation 9.1 nm (91 Å). From the formula (4), the surface Si atom density (hereinafter written as S.D.) under the above conditions can be understood to be 7.934 x 10¹⁴ cm⁻². from the graph in Fig. 5, since the nucleation density ND is ca. 3 x 10³ when S.D.=7.934 x 10¹⁴, it can be understood that etching may be effected to the depth (X) where S.D.=8.10 x 10¹⁴ cm⁻² for obtaining a difference in nucleation density of about 10³-fold. Since the Si atom density on the SiO₂ surface before implantation of Si ions is 7.863 x 10¹⁴ cm⁻², the Si atom density D(0) implanted into the SiO₂ surface is: and the Si atom density D(X) implanted at the depth (X) is: Accordingly, from the formula (5): X=X₀±√ X₀²-3σ²ℓ n {D (x) /D (o) } (6) from which two solutions of: X=32.6 nm (326 Å), 9.6 nm (96 Å) were obtained. The reason why two solutions are obtained is because the formula (5) becomes the quadratic function of X. In this Example, as the exposure treatment, a fine region of 2 µm square on the SiO₂ surface was etched by wet etching with a solution of HF diluted with water to a depth of 9.6 nm (96 Å) to form nucleation surfaces with 50 µm intervals in both longitudinal and lateral directions. As described above, a substrate as shown in Fig. 3B was obtained. Next, formation and growth of Si nucleus were perfomed under the following conditions: Amounts of gases introduced: SiH₂Cl₂/HCl/H₂=0.53/2.0/100 (litre/min.); Substrate temperature: 950 °C; Pressure: 200 x 10² Pa (150 Torr); Growth time: 30 min. On the substrate, a polycrystalline film was formed which was controlled in grain size to about 50 µm by formation of grain boundaries with single crystals grown from the above nucleation surface being contacted mutually with one another at approximately the center between the nonnucleation surface and the nucleation surface. SEM photographs of the substrate surface having the polycrystalline film formed thereon were taken at any desired 10 points of regions each of about 1 mm x 1 mm, and formation of the crystal on the nucleation surface and the crystal grown from Error nucleus on the nonnucleation surface were observed, to calculate the growth ratio on the nucleation surface and the growth density of Error nucleus. The growth ratio on the nucleation surface was found to be 99.9%, and the growth density of Error nucleus on the nonnucleation surface 0/cm², thus giving an extremely high selectivity. Example 2 Crystal growth treatment was applied in the same manner as in Example 1 except for making the intervals mutually between the nucleation surfaces on the substrate surface 200 µm. On the substrate, single crystals with grain sizes of about 60 µm were formed with good selectivity. Example 3 A plurality of substrates having an amorphous silicon oxide film formed to a layer thickness of 1 µm on a base material made of tungsten according to the conventional plasma CVD method were formed. Into the above amorphous silicon oxide surface were implanted Si ions by an ion implanter at the dosing amount of 1.3 x 10¹⁶ cm⁻² in the three stages of acceleration voltages of 20 KeV, 30 KeV and 40 KeV. At this time. P.R. (X₁) was 21.1 nm (211 Å), P.R. (X₂) 31.2 nm (312 Å) and P.R. (X₃) 41.7 pm (417 Å). The amorphous silicon oxide film surface of the above substrate implanted with Si ions was etched to a depth of 30 nm (300 Å) at fine area regions of 4 µm square at intervals of 100 µm. The reactive ion etching was effected under the etching conditions shown below to form a plurality of substrates having nonnucleation surface and nucleation surface: Flow rate ratio of gases introduced: CHF₃/C₂F₆=18/42 Discharging power: 2.1 KW Pressure: 70 Pa. On each of the above substrates thus obtained, Si crystal was formed under the following crystal growth treatment conditions: Flow rate ratio of gases introduced: SiH₂Cl₂/HCl/H₂=0.53/2.0/100 Substrate temperature: 1030 °C Pressure: 200 x 10² Pa (150 Torr) Growth time: 25 minutes. As the result, on both the same substrate and each substrate, single crystals with grain sizes of about 50 µm could be formed easily without variance between the respective substrates without grown crystal of Error nucleus on the nonnucleation surface with good selectivity at desired positions of the nucleation surfaces arranged. Example 4 Crystal growth treatment was applied in the same manner as in Example 1 except for depositing an amorphous silicon nitride to a layer thickness of 500 nm (5000 Å) according to the plasma CVD method on the 10 cm (4 inch) Si wafer in Example 1. On the substrate, a polycrystalline film controlled in grain size to about 50 µm was formed. Example 5 On an aluminum oxide base material, silicon nitride with a layer thickness of 1.2 µm was formed. Into the above silicon nitride surface, oxygen ions were implanted to a P.R. of 12 nm (120 Å) at a dosing amount of 2 x 10¹⁶ cm⁻². On the above silicon nitride surface implanted with oxygen ions, openings with intervals of 80 µm, 1.8 µm and a depth of 40 nm (400 Å) were formed by use of the reactive ion etching (RIE) method to form a substrate having the nonnucleation surface and the nucleation surface. On the substrate, crystal growth treatment was applied under the following conditions. Flow rate ratio of gases introduced: SiH₂Cl₂/HCl/H₂=0.53/1.6/100 Substrate temperature: 990 °C Pressure: 160 x 10² Pa (120 Torr) Growth time: one hour. As the result, a polycrystalline Si film controlled in grain size to about 80 µm was formed with good selectivity on the above substrate. Example 6 Into the surface of a quartz glass with a thickness of 3 mm, As ions were implanted to a P.R. of 45 nm (450 Å) in a dosing amount of 3 x 10¹⁶ cm⁻². The above quartz glass surface implanted with the As ions was subjected to wet etching with a buffered hydrofluoric acid at fine regions of 2 µm square with intervals of 10 µm to the depth of P.R. (450 µm) to form a substrate having the nonnucleation surface and the nucleation surface. On this substrate, crystal growth treatment was applied under the following conditions. Flow rate ratio of gases introduced: (CH₃)₃Ga/t-C₄H₉AsH₂/H₂=1/35/8000. Substrate temperature: 670 °C Pressure: 11 x 10² Pa (80 Torr) Growth time: 100 minutes. As the result, a GaAs polycrystal with a grain size of 10 µm could be formed with good selectivity on the above substrate.

Claims: A method of deposition for producing on a surface of a substrate one or more single crystals of a crystal forming material, which method comprises: establishing at a free surface of said substrate one or more deposition surface areas having under chosen conditions of deposition a property of nucleating said crystal forming material at a higher nucleation density than that of the adjacent deposition surface area, each of said one or more deposition surface areas being limited in size so that during an initial stage of the deposition each shall support the formation of a single nucleus only of the crystal forming material; depositing crystal forming material on the exposed free surface of said substrate under said chosen conditions of deposition, these conditions being such that said crystal forming material nucleates selectively on said one or more deposition surface areas and forms on each a single nucleus; and upon further deposition of said crystal forming material, growing a single crystal from each single nucleus; which method is characterised in that: said one or more deposition surface areas and said adjacent deposition surface area of said free surface of the substrate are established by: implanting ions in said substrate to differentiate the respective properties of substrate material at an exposed surface of the substrate and at a prescribed depth below said exposed surface such that the property of a surface of material at said prescribed depth shall be that of nucleating said crystal forming material at said higher nucleation density; and etching said substrate to produce one or more recesses reaching said prescribed depth so as to reveal a corresponding one or more deposition surface areas of said substrate. A method as claimed in claim 1 wherein: the ions implanted have the effect of changing the property of said substrate material to one of nucleating the crystal forming material at an increased density; said ions are implanted to a depth which is not less than 10nm (100Å) and not greater than 110nm (1100Å); and said etching is to a depth corresponding substantially to the projection range of said implanted ions. A method as claimed in claim 2 wherein said ions are implanted by repeated doses, each dose at a different acceleration voltage, so as to produce in said substrate an implanted ion density profile which is substantially of maximum or near maximum ion density over an extended range of depths below said exposed surface of the substrate. A method as claimed in either of the preceding claims 2 or 3 wherein: said crystal forming material is of silicon; said substrate material is of amorphous silicon oxide; and said implanted ions are of silicon. A method as claimed in claim 2 wherein: said crystal forming material is of gallium arsenide; said substrate material is of quartz glass; and said implanted ions are of arsenic. A method as claimed in any one of the preceding claims 1 to 4, wherein said substrate comprises a body of bulk material and upon the surface of said body a surface layer of substrate material which layer is of a thickness in excess of said prescribed depth. A method as claimed in any preceding claim wherein said ions are implanted at a dose of between 1x10¹⁶ and 1x10¹⁷ cm⁻². A method as claimed in claim 7 wherein said dose is between 2x10¹⁶ and 4x10¹⁶ cm⁻². A method as claimed in claim 1 wherein said substrate material is amorphous. A method as claimed in claim 1 wherein said substrate material is electrically insulative. A method as claimed in any preceding claim wherein said crystal forming material is deposited from a gaseous phase. A method as claimed in claim 11 wherein an etchant gas is present in said gaseous phase and is effective to inhibit any nucleation of said crystal forming material upon said adjacent surface area. A method as claimed in claim 12 wherein said etchant gas comprises hydrogen chloride. A method as claimed in any preceding claim wherein the respective nucleating properties of said one or more deposition surface areas and said adjacent deposition surface area differ such that respective said nucleation densities differ by a factor of 10³ to 10⁶. A method as claimed in any preceding claim wherein a multiplicity of deposition surface areas are established and said further deposition is continued until a polycrystalline film is formed of a multiplicity of single crystals each grown from a respective single nucleus on each one of said multiplicity of deposition surface areas. A method as claimed in any preceding claim wherein the whole of a main surface of said substrate is exposed to the ion implantation.

Inventors: YAMAGATA KENJI NO SAGINUMA TAB, YAMAGATA, KENJI NO. 401 SAGINUMA TABATA MANSHON
Applicants: CANON KK, CANON KABUSHIKI KAISHA
Application year: 1989
Main classification: C30B25
IPC codes: C30B31, C30B25, H01L21