Method for preparing semiconductor member

Abstract: A method for preparing a semiconductor member comprises process of making a porous Si substrate and then forming a non-porous Si monocrystalline layer on the porous Si substrate; primary bonding process of bonding the porous Si substrate and an insulating substrate via the non-porous Si monocrystalline layer; etching process of etching the porous Si to remove the porous Si by chemical etching after the primary bonding process; and secondary bonding process of strengthening the primary bonding after the etching process.

Description: The present invention relates to a method of producing a semiconductor member comprising a semiconductor layer on an insulating substrate. The widely known silicon on insulator (SOI) technology involves formation of a monocrystalline silicon semiconductor layer on an insulating material. Devices using an SOI structure have many advantages in the preparation of conventional Si integrated circuits which are not provided by bulk Si substrates, and hence have been intensively researched. More particularly the following advantages can be obtained using the SOI structure: 1. A high degree of integration is permitted because dielectric isolation is readily obtainable; 2. Radiation hardness is excellent; 3. Stray capacity is reduced so that resulting devices are of high speed; 4. A well formation step can be permitted. 5. Latch up can be prevented. 6. A fully depleted field effect transistor can be made by thin film formation. For some ten years now, studies have been carried out to realise the many advantageous device characteristics set out above. The following publication summarises these studies: Special Issue: "Single-crystal silicon on non-single-crystal insulators"; edited by G.W. Cullen, Journal of Crystal Growth, Volume 63, No 3, pp. 429-590 (1983). A CVD (Chemical Vapour Deposition) method in which silicon is deposited by heteroepitaxy on a monocrystalline sapphire substrate to form a SOS (silicon on sapphire) has also been known for some time. Although this is the most mature SOI technique and has met with some success, it has not been widely applied because there is lattice mismatching at the interface between the Si layer and the sapphire substrate which gives rise to large amounts of crystal defects, because aluminium is introduced from the sapphire substrate into the Si layer, and above all because of the high cost of the substrate and delay in the availability of substrate wafers of large size. In recent years attempts have been made to produce a SOI structure without the use of a sapphire substrate. These attempts fall into the following two broad classifications: (1) A monocrystalline Si substrate is surface oxidised, after which a window is formed so as to partially expose the Si substrate and the exposed portion is used as a seed to form an Si monocrystalline layer on SiO 2 by a lateral epitaxial growth process. (In this case, the deposition is of a Si layer on SiO 2 ). (2) SiO 2 is formed underneath an Si monocrystalline substrate which is irself used as an active layer. This method does not involve the deposition of a Si layer. The process (1) above may be carried out by CVD which produces a monocrystalline Si layer directly by lateral epitaxial growth, by a method in which amorphous Si is deposited and subjected to heat treatment to bring about solid phase lateral epitaxial growth, a method in which an amorphous or polycrystalline Si layer is irradiated with a convergent energy beam such as a electron beam, laser beam etc to form Si0 2 and a monocrystalline layer is grown on the SiO 2 by melting and recrystallisation, and by a method in which a melting region is scanned zonewise by a rod shaped heater (zone melting recrystallisation). These methods have both advantages and disadvantages. They still have a number of problems concerning controllability, production rate, uniformity and quality and upto now none of them has been industrially applied. For example, in flat thin film formation, the CVD method requires sacrificial-oxidation whilst in the solid phase growth method the crystallinity is poor. In the beam annealing method which involves converged beam scanning, controllability problems arise e.g. as regards treatment time, the manner of overlapping of the beams, focus adjustment etc. Zone melting recrystallisation is the most mature of these methods and a relatively large scale integrated circuit has been made on a trial basis, but a large number of crystal defects such as sub-boundary remain and no device driven by minority carriers has been prepared. Methods in which a non-Si substrate is used as the seed for epitaxial growth include the following: (1) A monocrystalline substrate is anisotropically etched to form V-grooves and an oxide film is formed on the substrate, a polycrystalline Si layer of comparable thickness to the substrate is deposited on the oxide film and thereafter polished from the rear surface of the Si substrate so as to form on the thick polycrystalline Si layer Si monocrystalline regions that are dielectrically separated as a result of their surrounding V-grooves. In this method, although good crystallinity is obtained, problems arise concerning controllability and production rate during the step of depositing the polycrystalline Si which has to be some 100 microns in thickness and also the step in which the monocrystalline Si substrate is polished from its back surface to leave only the separated Si active layer. (2) A method called SIMOX (separation by ion-implanted oxygen) involves ion implantatation of oxygen into an Si monocrystalline substrate so as to form an SiO 2 layer, and is one of the most mature methods because of good matching with the Si-IC (integrated circuit) process. However, formation of the SiO 2 layer requires implantation of 10 18 ions/cm 2 or more requiring prolonged implantation times and hence low production rates. Furthermore the wafer cost is high, many crystal defects remain and from an industrial standpoint it has been impossible to provide a sufficient level of quality for manufacture of devices driven by minority carriers. (3) A method is known in which a dielectrically isolated SOI structure is formed by oxidation of porous Si. In this method islands of an N-type Si layer are formed by proton-ion implantation on the surface of a D-type Si monocrystalline substrate (IMAI et al., J. Crystal Growth, Vol 63, 547 (1983)). Epitaxial growth and patterning may be used instead of proton ion implantation; the P-type Si substrate only is made porous by anodization in HF solution so as to surround the Si islands from the surface, and then the N-type Si islands are dielectrically isolated by accelerated oxidation. In this method the separated Si region is determined before the device steps so that there is the disadvantage in some cases that the degree of freedom in device circuit design is limited. In the formation of a contact sensor which serves as a light-receiving device and a projection-type liquid crystal image display, a light-transparent substrate is important. A high quality driving device is required in order to further increase the density, resolution and definition of the pixels (picture elements) of such a sensor or display. It is consequently necessary to provide for a device to be produced on a light-transparent substrate using a monocrystalline layer having excellent crystallinity. However, an amorphous layer or at best a polycrystalline layer is produced as a result of depositing Si on an amorphous substrate such as a glass substrate. The reason is that the Si layer reflects the disordered crystal structure of the substrate, and using this Si layer, high quality devices are not formed. Simply by depositing a Si layer, it is difficult to obtain a monocrystalline layer of high quality. JP-A-55016464 discloses a method for producing a good SOI layer. An SOI monocrystalline substrate is bonded onto another Si monocrystalline substrate. Said another silicon monocrystalline substrate is subjected to a treatment for forming a porous structure and the porous substrate is then removed after conversion to an oxide. Takao Yonehara, one of the inventors of the present application disclosed in Japanese patent application JP-A-5-021338 a method for forming a semiconductor substrate which is capable of solving the above problems. In the method disclosed in this application, a substrate is formed which has a non-porous monocrystalline semiconductor layer, a porous semiconductor layer. Another substrate having a surface of insulating material is bonded to the surface of the monocrystalline layer, after which the porous semiconductor layer is removed by etching. The method disclosed in this patent application enables a semiconductor layer having crystallinity similar to that of a monocrystalline wafer to be produced on an insulating substrate at excellent production rates, uniformity and controllability. However, in this method, where bonding is carried out at high temperatures and the substrates being bonded together have different coefficients of thermal expansion, exfoliation can occur at the contacting surfaces because of the different coefficient of expansion of the contacting surfaces. Even if a satisfactory bond is initially formed, both substrates are subject to cracking due to reduced flexibility. It is in particular difficult to form a bond between substrates of different kind. A paper by G. Bomchil et al, Materials Letters, September 1988, Vol 7, No. 3, pp 94-98, discloses the deposition by low-pressure vapour-phase epitaxy on porous silicon at lower temperatures than in conventional chemical vapour deposition epitaxy. Epitaxial layers of good crystalline quality were obtained and the original microstructure of porous silicon was only slightly modified during the epitaxial process. Full oxidation of the buried porous silicon layer was subsequently possible. With either of the above methods it is difficult to provide on a light transparent glass substrate a reproducible SOI layer which has a crystallinity equal to that of a Si wafer. A paper by Tsuneo Hamaguchi et al, "Device Layer Transfer Technique using Chemi-Mechanical Polishing", Japanese Journal of Applied Physics, Vol 23, No 10, pp L815-L817 (1984) discloses a new technique for transferring a thin device layer fabricated on a silicon wafer onto an insulating substrate. The fundamental processes used in this technique are wafer thinning by means of chemimechanical polishing and wafer fastening using an insulating polymer adhesive. A 2µm thick device layer of 5cm (2 inch) diameter is formed on a quartz glass substrate without significant degradation in transistor characteristics. An article by J. Haisma et al, "Silicon on Insulator Wafer Bonding-Wafer Thinning Technological Evaluations", Japanese Journal of Applied Physics, 28 , 1989, No 8, pages 1426-1443 discloses a method for producing a semiconductor member having the features set out in the preamble to claim 1. The present invention provides a method as aforesaid, said method having the characterising features set out in claim 1. An embodiment of the above method enables semiconductor members to be produced in which there is SOI structure which does not tend to exfoliate or crack. Embodiments of the invention can enable the semiconductor member to be produced at relatively high production rate in a uniform and controllable manner and in good yield and cost, and gives Si crystalline layer whose crystallinity is similar to that of a monocrystalline wafer. The insulating substrate may be glass. Embodiments of the semiconductor member made by the above process have the advantages of conventional SOI devices and can be used in a variety of field in place of semiconductor members prepared by the expensive SOS or SIMOX processes for the production of large scale integrated circuits. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a schematic view for explaining an example of the method of producing a semiconductor member of the present invention; Fig. 2 is a schematic view for explaining an example of the method of producing a semiconductor member of the present invention. Fig. 3 is a schematic view for explaining an example of the method of producing a semiconductor member of the present invention; Fig. 4 is a schematic view for explaining an example of the method of producing a semiconductor member of the present invention; Fig. 5 is a graphic representation showing the etching characteristics of an etching solution applicable to the present invention; Fig. 6 is a graphic representation showing the etching characteristics of an etching solution applicable to the present invention; Fig. 7 is a graphic representation showing the etching characteristics of an etching solution applicable to the present invention; Fig. 8 is a graphic representation showing the etching characteristics of an etching solution applicable to the present invention; Fig. 9 is a graphic representation showing the etching characteristics of an etching solution applicable to the present invention; Fig. 10 is a graphic representation showing the etching characteristics of an etching solution applicable to the present invention; Fig. 11 is a graphic representation showing the etching characteristics of an etching solution applicable to the present invention; and Fig. 12 is a graphic representation showing the etching characteristics of an etching solution applicable to the present invention. DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS A first embodiment of the method of preparing a semiconductor member of this invention will be now described. That is, it is characterized by comprising, process of making a porous Si substrate and then forming a non-porous Si monocrystalline layer on the porous Si substrate, primary bonding process of bonding the porous Si substrate and an insulating substrate via the non-porous Si monocrystalline layer, etching process of etching porous Si to remove porous Si by chemical etching after the primary bonding process, and secondary bonding process of strengthening the primary bonding after the etching process. A second embodiment of the present invention is a method of preparing a semiconductor member characterized by comprising, process of making a porous Si substrate and then forming a non-porous Si monocrystalline layer on the porous Si substrate, primary bonding process of bonding the porous Si substrate and an insulating substrate via the non-porous Si monocrystalline layer, etching process of etching porous Si to remove porous Si by chemical etching immersing the substrate in hydrofluoric acid after the primary bonding process, and secondary bonding process of strengthening the primary bonding after the etching process. A third embodiment of the present invention is a method of preparing a semiconductor member characterized by comprising, process of making a porous Si substrate and then forming a non-porous Si monocrystalline layer on the porous Si substrate, primary bonding process of bonding the porous Si substrate and an insulating substrate via the non-porous Si monocrystalline layer, etching process of etching porous Si to remove porous Si by chemical etching immersing the substrate in a mixture containing hydrofluoric acid and alcohol after the primary bonding process, and secondary bonding process of strengthening the primary bonding after the etching process. A fourth embodiment of the present invention is a method of preparing a semiconductor member characterized by comprising, process of making a porous Si substrate and then forming a non-porous Si monocrystalline layer on the porous Si substrate, primary bonding process of bonding the porous Si substrate and an insulating substrate via the non-porous Si monocrystalline layer, etching process of etching porous Si to remove porous Si by chemical etching immersing the substrate in a mixture containing hydrofluoric acid and hydrogen peroxide after the primary bonding process, and secondary bonding process of strengthening the primary bonding after the etching process. A fifth embodiment of the present invention is a method of preparing a semiconductor member characterized by comprising, process of making a porous Si substrate and then forming a non-porous Si monocrystalline layer on the porous Si substrate, primary bonding process of bonding the porous Si substrate and an insulating substrate via the non-porous Si monocrystalline layer, etching process of etching porous Si to remove porous Si by chemical etching immersing the substrate in a mixture containing hydrofluoric acid, alcohol and hydrogen peroxide after the primary bonding process, and secondary bonding process of strengthening the primary bonding after the etching process. A sixth embodiment of the present invention is a method of preparing a semiconductor member characterized by comprising, process of making a porous Si substrate and then forming a non-porous Si monocrystalline layer on the porous Si substrate, primary bonding process of bonding the porous Si substrate and an insulating substrate via the non-porous Si monocrystalline layer, etching process of etching porous Si to remove porous Si by chemical etching immersing the substrate in a mixture containing buffered hydrofluoric acid (a mixed aqueous solution of hydrofluoric acid and ammonium fluoride) after the primary bonding process, and secondary bonding process of strengthening the primary bonding after the etching process. A seventh embodiment of the present invention is a method of preparing a semiconductor member characterized by comprising, process of making a porous Si substrate and then forming a non-porous Si monocrystalline layer on the porous Si substrate, primary bonding process of bonding the porous Si substrate and an insulating substrate via the non-porous Si monocrystalline layer, etching process of etching porous Si to remove the porous Si by chemical etching immersing the substrate in a mixture containing buffered hydrofluoric acid (a mixed aqueous solution of hydrofluoric acid and ammonium fluoride) and alcohol after the primary bonding process, and secondary bonding process of strengthening the primary bonding after the etching process. An eighth embodiment of the present invention is a method of preparing a semiconductor member characterized by comprising, process of making a porous Si substrate and then forming a non-porous Si monocrystalline layer on the porous Si substrate, primary bonding process of bonding the porous Si substrate and an insulating substrate via the non-porous Si monocrystalline layer, etching process of etching the porous Si to remove porous Si by chemical etching immersing the substrate in a mixture containing buffered hydrofluoric acid (a mixed aqueous solution of hydrofluoric acid and ammonium fluoride) and hydrogen peroxide after the primary bonding process, and secondary bonding process of strengthening the primary bonding after the etching process. A ninth embodiment of the present invention is a method of preparing a semiconductor member characterized by comprising, process of making a porous Si substrate and then forming a non-porous Si monocrystalline layer on the porous Si substrate, primary bonding process of bonding the porous Si substrate and an insulating substrate via the non-porous Si monocrystalline layer, etching process of etching porous Si to remove porous Si by chemical etching immersing the substrate in a mixture containing buffered hydrofluoric acid (a mixed aqueous solution of hydrofluoric acid and ammonium fluoride), alcohol and hydrogen peroxide after the primary bonding process, and secondary bonding process of strengthening the primary bonding after the etching process. According to the present invention, the secondary bonding process of bonding the Si/SiO 2 layer and an insulating substrate such as a light-transparent substrate more strongly is performed after the porous Si substrate is etched to make a thin film, so that the substrate and the thin film are bonded. Therefore, it is possible to prevent exfoliations or cracks caused by the difference between thermal expansion coefficients of the substrate and the thin film in the bonding process even if they are subjected to the heat treatment at high temperature to provide a stronger bondage thereof, because the thin film is bonded in alignment with the substrate owing to the good flexible property of the thin film. And it is thus possible to form the thin film Si layer having an excellent monocrystalline structure uniformly on the insulating substrate, represented by the light-transparent substrate. For the method of fabricating a semiconductor substrate according to the present invention, when it is made porous with only one surface layer of the Si substrate left behind, it is possible to obtain Si monocrystal with significantly less defects on the insulating substrate at low cost in such a manner as to leave Si active layer on the surface, using the epitaxial Si monocrystal having a uniformly flat and quite excellent crystallinity over a large area and remove the active layer from its one surface. According to the present invention, to obtain Si crystalline layer having the crystallinity excellent equal to that of monocrystalline wafer on the insulating substrate, it is possible to bond Si monocrystalline layer onto the light-transparent substrate having a thermal expansion coefficient different from that of Si more strongly, without yielding exfoliations or cracks, thus providing a method superior in productivity, uniformity, controllability, and economy. Further, according to the present invention, it is possible to provide a method of fabricating a semiconductor substrate by realizing the advantages of conventional SOI devices and can be applied. Also, according to the present invention, it is possible to provide a method of fabricating a semiconductor substrate which can be used in place of the expensive SOS or SIMOX for producing a large-scale integrated circuit having the SOI structure. The present invention is to use an originally excellent monocrystalline Si substrate as a starting material, chemically removing a lower portion of the Si substrate, with a monocrystalline layer left only on the surface thereof, for the transfer onto the light-transparent substrate, thereby establishing a method of bonding materials having different thermal coefficients and enabling many treatments to be performed in a short time. In particular, the invention as described in the second to ninth embodiments is to provide a method of fabricating a semiconductor member by using a wet chemical etching solution which has no bad effect on the semiconductor process in etching of porous Si, thereby exhibiting an etching selection ratio of a five digits value or more of porous Si to non-porous Si in this etching solution and excellent controllability and productivity. The present invention will be described below in detail. (Embodiment 1-1) Figs. 1(a) to (e) are process views for explaining one example of the method of preparing a semiconductor substrate of the present invention, each shown as a schematic cross-sectional view in each process. According to the result of an observation by a transmission electron microscope, micro-pores of an average diameter of about 60nm (600Å) are formed in the porous Si layer, so that the density of the layer has been reduced half or below that of the monocrystalline Si. Nevertheless, the monocrystallinity is still maintained, so that it is possible to form a monocrystalline Si layer on the porous layer by epitaxial growth. When the temperature exceeds 1000°C, rearrangement of internal pores occurs, which impedes the acceleration of the etching. For this reason, the epitaxial growth of the Si layer is preferably effected by a low-temperature growth method such as, for example, a molecular beam epitaxial growth method, a CVD method such as plasma CVD method, low-pressure CVD or photo CVD method, a bias sputter method, or a liquid-phase growth method. A description will now be given of the method in which after making a P-type or high-carrier density N-type (highly dense enough to realize the porous structure) Si substrate entirely porous, the epitaxial growth of a monocrystalline layer is made. First, a P-type Si monocrystalline substrate 11 is prepared and made entirely porous, as shown in Fig. 1(a). Next, the epitaxial growth is made on the surface of a porous substrate 12, with one of various growth methods, as shown in Fig. 1(b), to form a thin film monocrystalline layer 13. The P-type Si substrate is made porous by anodization using an HF solution. The density of the porous Si layer can be changed to the range of 1.1 to 0.6 g/cm 3 by changing the concentration of the HF solution from 50 to 20%, as compared with the density of 2.33 g/cm 3 of monocrystalline Si. This porous layer is not formed on the N-type Si layer, owing to the following reasons, but only on the P-type Si substrate. The porous Si layer has pores having an average size of about 60nm (600Å) which was measured by observation with a transmission electron microscope. Porous Si was discovered in the course of research on electrolytic polishing of a semiconductor which was conducted by Uhlir et al., in 1956 (A. Uhlir, Bell Syst. Tech. J., vol. 35, 333 (1956)). Unagami et al. investigated dissolving reaction of Si during anodization and reported that the anodic reaction of Si in an HF solution requires positive holes, and that the reaction is expressed as follows (T. Unagami, J. Electrochem. soc., vol. 127, 476 (1980)). Si + 2HF + (2-n)e + → SiF 2 + 2H + + ne - SiF 2 + 2HF → SiF 4 + H 2 SiF 4 + 2HF → H 2 SiF 6 or Si + 4HF + (4-λ)e + → SiF 4 + 4H + + λe - SiF 4 + 2HF → H 2 SiF 6 where e + and e - respectively denote a positive hole and an electron, and n and λ each denote the number of positive holes required for dissolving one silicon atom. Porous Si can be formed when the condition, n > 2 or λ > 4, is satisfied. As above described, the P-type Si having positive holes can be made porous, while the N-type Si cannot be made porous. The selectivity in producing a porous structure has been demonstrated by Nagano et al. and Imai (Nagano, Nakajima, Yasumo, Oonaka, Kajiwara, Electronic Communications Institute Technical Studies Report, vol. 79, SSD79-9549 (1979)), (K. Imai, Solid-State Electronics, vol. 24, 159 (1981)). However, it is also reported that high-density N-type Si can be made porous (R. P. Holmstrom and J. K. Chi, Appl. Phys. Lett., vol. 42, 386 (1983)), so that it is important to select a substrate which can be made porous irrespectively of whether it is P-type or N-type. Porous layer is internally formed with a large amount of gaps, resulting in the density decreasing to half or less. Consequently, the surface area will drastically increase as compared with that of deposition, so that its chemical etching rate is remarkably higher than that of the normal monocrystalline layer. Referring now to Fig. 1(c), a light-transparent substrate 14, which is typically a glass sheet, is prepared as an insulating substrate, and bonded on the surface of monocrystalline Si layer 13, to a degree of pulling against each other with a Van der Waals force (primary bonding). It will be appreciated that after an oxide layer is formed on the surface of Si monocrystalline layer 13, the oxide layer and the light-transparent substrate 14 may be bonded. Also, it will be appreciated that in place of the light-transparent substrate 14, a substrate having an oxide layer formed on the surface of monocrystalline Si may be used. The bonding strength of the primary bonding must be strong enough to retain the primary bonding state, without yielding exfoliations in the course to the secondary bonding to be performed later. The primary bonding can be performed at room temperature, or by heating, but when heating, the heating temperature must be lower than the temperatue used for the secondary bonding. The temperature for the secondary bonding is suitably in a range of 200 to 800°C, depending on the material of insulating substrate. Thereafter, the porous Si substrate 12 is entirely etched, whereby a thinned monocrystalline Si layer 13 is left on the light transparent substrate 14, as shown in Fig. 1(d). If the etching solution may also etch the light-transparent glass substrate 14 in etching, an anti-etching film must be provided on the back surface of the light-transparent glass substrate 14, except for an instance where the light-transparent glass substrate 14 is etched more or less, but the etched surface is not different from an optically polished surface, and an instance where the light-transparent glass substrate 14 is not etched at all. An Si 3 N 4 layer is formed by deposition as the anti-etching film to cover wholly the two adjacently placed substrates, and the Si 3 N 4 layer on the porous Si substrate is removed. It is possible to use other materials such as Apiezon wax, in place of Si 3 N 4 , as the material of the anti-etching layer. Finally, with the heat treatment, Si/SiO 2 layer and light-transparent substrate 14 are bonded more strongly for the secondary bonding. Since the thin film and the light-transparent substrate are bonded as above described, the thin film is bonded in alignment with the substrate, so that it is possible to prevent exfoliations and cracks of the substrate caused by the difference between their thermal expansion coefficients. Fig. 1(e) shows the semiconductor substrate obtained by this embodiment, in which a monocrystalline Si layer 13 having a crystallinity equivalent to that of a silicon wafer is formed on the light-transparent substrate 14, with high degrees of smoothness and uniformity, and with a small thickness, over a wide area covering the whole surface of the wafer. The semiconductor substrate thus obtained is advantageous from the view point of production of an insulation-isolated electronic device. (Embodiment 1-2) Another embodiment for the method of fabricating a semiconductor substrate according to the prevent invention will be described in detail with reference to the drawings. Figs. 2(a) to (e) are process views for explaining another example of the method of preparing a semiconductor substrate of the present invention, each shown as a schematic cross-sectional view in each process. First, a low-carrier density layer 22 is formed by epitaxial growth with one of various thin film growth methods or by counter doping the surface of a high-carrier density Si substrate 21, as shown in Fig. 2(a). Alternatively, an N-type monocrystalline layer 22 may be formed in the surface of a P-type Si moncrystalline substrate 21 by ion implantation of protons. They, as shown in Fig. 2(b), the P-type or high-carrier density N-type Si monocrystalline substrate 21 is changed into a porous Si substrate 23 by effecting, on the reverse side thereof, anodization using an HF solution. The initial monocrystalline Si having the density of 2.33 g/cm 3 can be changed into a porous member the density of which can be varied within the range between 1.1 and 0.6 g/cm 3 by varying the HF concentration of the etching solution between 50% and 20%. This porous member is formed into a P-type or high-density N-type Si substrate, as above described. Referring now to Fig. 2(c), a light-transparent substrate 24, which is typically a glass sheet, is prepared as an insulating substrate, and bonded on the surface of Si monocrystalline layer 22, to a degree of pulling against each other with a Van der Waals force (primary bonding). It will be appreciated that after an oxide layer is formed on the surface of Si monocrystalline layer 22, the oxide layer and the light-transparent substrate 24 may be bonded. Also, it will be appreciated that in place of the light-transparent substrate 24, a substrate having an oxide layer formed on the surface of monocrystalline Si may be used. The bonding strength of the primary bonding must be strong enough to retain the primary bonding state, without yielding exfoliations in the course to the secondary bonding to be performed later. Thereafter, the porous Si substrate 23 is entirely etched, whereby a thinned monocrystalline Si layer 22 is left on the light-transparent substrate 24, as shown in Fig. 2(d). If the etching solution may also etch the light-transparent glass substrate 24 in etching, an anti-etching film must be provided on the back surface of the light-transparent glass substrate 24, except for an instance where the light-transparent glass substrate 24 is etched more or less, but the etched surface is not different from an original optically polished surface, and an instance where the light-transparent glass substrate 24 is not etched at all. An Si 3 N 4 layer is formed by deposition as the anti-etching film to cover the entire member composed of the two substrates bonded together, and the Si 3 N 4 layer on the surface of porous Si substrate is removed. It is possible to use other materials such as Apiezon wax, in place of Si 3 N 4 , as the material of the anti-etching layer. Finally, with the heat treatment, Si/SiO 2 layer and light-transparent substrate 14 are bonded more strongly for the secondary bonding, as shown in Fig. 2(e). Since the thin film and the light-transparent substrate are bonded as above described, the thin film is bonded in alignment with the substrate, so that it is possible to prevent exfoliations and cracks of the substrate caused by the difference between their thermal expansion coefficients. Fig. 2(e) shows the semiconductor substrate obtained by this embodiment, in which a monocrystalline Si layer 22 having a crystallinity equivalent to that of a silicon wafer is formed on the light-transparent substrate 24, with high degrees of smoothness and uniformity, and with a small thickness, over a wide area covering the whole surface of the wafer. The semiconductor substrate thus obtained is advantageous from the view point of production of an insulation-isolated electronic device. The above method is one in which an apitaxial layer is formed before making a porous structure, and then the regions other than the epitaxial layer are made porous selectively by anodization. (Embodiment 2-1) Figs. 3(a) to (d) are process views for explaining this embodiment, each shown as a schematic cross-sectional view in each process. The following will be given of a method in which the whole P- or high-carrier density N-type Si substrate is changed into porous structure, and then a non-porous monocrystal Si layer is formed on the porous structure by epitaxial growth. Referring to Fig. 3(a), as the first step, an Si monocrystalline semiconductor member 31 of P-type is prepared, and is wholly changed into porous structure 32. Then, as shown in Fig. 3(b), an epitaxial growth is effected by a suitable method on the surface of the porous member 32, thereby forming a monocrystalline Si layer 33. Then, as shown in Fig. 3(c), the surface of the monocrystalline Si layer 33 on the porous Si substrate 32 is oxidized to form an oxide film 35. This oxide film 35 is formed to reduce the interface level of the monocrystalline layer 33 which is a final active layer. Then, an insulating substrate 34 such as a light-transparent glass substrate is bonded on the surface of the oxide film 35, to a degree of pulling against each other with a Van der Waals force, or to a degree that bonded interfaces may not exfoliate due to a difference between thermal expansion coefficients of both members (primary bonding). It will be appreciated that this insulating substrate 34 may be, in place of the glass substrate, a substrate having an oxide layer formed on the surface of monocrystalline Si. The bonding strength of the primary bonding must be strong enough to retain the primary bonding state, without yielding exfoliations in the course to the secondary bonding for the complete bonding to be performed later. Thereafter, an anti-etching film 36 is provided on the back surface of the light-transparent glass substrate 34. An Si 3 N 4 layer is formed by deposition as the anti-etching film 36 to cover the entire member composed of the two substrates bonded together, and the Si 3 N 4 layer on the surface of porous Si substrate is removed. It is possible to use other materials such as Apiezon wax, in place of Si 3 N 4 , as the material of the anti-etching layer. Then, as shown in Fig. 3(d), the porous Si substrate 32 is entirely immersed in hydrofluoric acid with agitating so that only the porous Si is removed by electroless wet chemical etching, whereby a thinned monocrystalline silicon layer 13 is left on the light-transparent substrate 34. Finally, with the heat treatment, Si/SiO 2 layer and light-transparent substrate 14 are bonded more strongly for the secondary bonding which is a complete bonding, as shown in Fig. 1(e), so that a semiconductor member of this embodiment can be obtained by removing the anti-etching film 36. A description will now be given of the selective etching method of porous Si with hydrofluoric acid used in this embodiment. Fig. 5 shows the etching time dependency of etched thickness of porous Si and monocrystalline Si when the porous Si and the monocrystalline Si are etched by being immersed in 49% hydrofluoric acid and agitated. The porous Si was formed by anodizing a monocrystalline Si. The conditions of anodization are shown below. It is to be noted, however, that the starting material for producing porous Si by anodization is not limited to monocrystalline Si and Si of other crystalline structure may be used as the starting material. Voltage applied : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution: HF:H 2 O:C 2 H 5 OH=1:1:1 Time : 2.4 hours Thickness of porous Si: 300 (µm) Porosity : 56 (%) Test pieces of the porous Si thus prepared were immersed in 49% hydrofluoric acid solution (white circles) at the room temperature and agitated. The reduction in the thickness of the porous Si was then measured. The porous Si was rapidly etched: namely, by a layer thickness of 90 µm in 40 minutes, and further 205 µm in 80 minutes, with high degrees of surface quality and uniformity. The etching rate has dependencies on the concentration of the etching solution and the temperature. Test pieces of non-porous Si having a thickness of 500 µm were immersed in 49% hydrofluoric acid solution (black circles) at the room temperature and agitated. The reduction in the thickness of the non-porous Si was then measured. The non-porous Si was only etched to 5nm (50Å) or less after elapse of 120 minutes. The etched test pieces of porous Si and non-porous Si were then rinsed with water and the surfaces after the rinsing were examined by microanalysis using secondary ions but no impurity was detected. The conditions for the solution concentration and the temperature were set in the range where the etching rate of porous Si and the selection ratio of etching the porous Si and the non-porous Si have no effect in the practical use such as a fabrication process. A description will be made of the etching solution in which the porous Si is etched. Known methods of etching porous Si are the following two methods. 1. The method of etching porous Si with an aqueous NaOH solution (G. Bonchil, R. Herino, K. Barla, and J. C. Pfister, J. Electrochem. Soc., Vol. 130, No. 7, 1611 (1983)). 2. The method of etching porous Si with an etching solution which is capable of etching monocrystalline Si. In the above method 2, a fluoronitric acid-type etching solution is generally used, and etching of Si proceeds as follows: Si + 2O → Si O 2 SiO 2 + 4HF → SiF 4 + H 2 O That is, Si is oxidized by nitric acid to SiO 2 , and the SiO 2 produced is etched with hydrofluoric acid. Examples of etching solutions for non-porous Si include the above fluoronitric acid-type etching solution as well as ethylenediamine-type, KOH-type and hydrazine-type etching solutions and the like. It will be thus understood that it is desirable in selective etching of porous Si to select an etching solution which is capable of etching porous Si, other than the above etching solutions used for the etching of crystalline Si. The porous Si is conventionally selectively etched by the method which uses an aqueous NaOH solution as an etching solution. As above described, the porous Si is etched with the fluoronitric acid-type etching solution, but monocrystalline Si may be possibly etched. In the conventional method of selectively etching porous Si with an aqueous NaOH solution, Na ions are inevitably adsorbed on the etched surface. Since the Na ions cause impurity contamination, are movable and have adverse effects such as the formation of interfacial state, it is desirable that the ions are not introduced into the semiconductor process. In this embodiment, the etching solution is hydrofluoric acid, which has no etching action on the non-porous Si, but is used in an ordinary semiconductor process, with quite less etching contamination. Thus, in this embodiment, it is possible to selectively etch the porous Si, but not the non-porous Si, by the chemical etching with high degrees of efficiency and uniformity, without having no adverse effects on the process. (Embodiment 2-2) Figs. 4(a) to (e) are process views for explaining this embodiment, each shown as a schematic cross-sectional view in each process. First, a low-carrier density layer 42 is formed by epitaxial growth with one of various thin film growth methods or by counter doping the surface of a high-carrier density Si substrate 41, as shown in Fig. 4(a). Alternatively, an N-type monocrystalline layer 42 may be formed on the surface of a P-type Si monocrystalline substrate 41 by ion implantation of protons. Then, as shown in Fig. 4(b), the P-type or high-carrier density N-type Si monocrystalline substrate 41 is changed into a porous Si substrate 43 by effecting, on the reverse side thereof, anodization using an HF solution. The initial monocrystalline Si having the density of 2.33 g/cm 3 can be changed into a porous member the density of which can be varied within the range between 1.1 and 0.6 g/cm 3 by varying the HF concentration of the etching solution between 50% and 20%. This porous member is formed into a P-type or high-carrier density N-type Si substrate, as above described. Referring now to Fig. 4(c), a light-transparent substrate 44, which is typically a glass sheet, is prepared as an insulating substrate, and after oxidizing the surface of monocrystalline Si layer on a porous Si substrate, bonded on the oxidized surface at the room temperature or by heating, to a degree of pulling against each other with a Van der Waals force or to a degree that the bonded interfaces may not exfoliate due to a difference between thermal expansion coefficients of both members (primary bonding). It will be appreciated that in place of the light-transparent substrate 34, a substrate having an oxide layer formed on the surface of monocrystalline Si may be used. The bonding strength of the primary bonding must be strong enough to retain the primary bonding state, without yielding exfoliations in the course to the secondary bonding for the complete bonding to be performed later. The oxide layer 45 on the surface of monocrystalline layer is formed to reduce the interface level of the monocrystalline layer 42 which is a final active layer. Thereafter, an anti-etching film 46 is provided on the back surface of the light-transparent glass substrate 44. An Si 3 N 4 layer is formed by deposition as the anti-etching film to cover the entire member composed of the two substrates bonded together, and the Si 3 N 4 layer on the surface of porous Si substrate is removed. It is possible to use other materials such as Apiezon wax, in place of Si 3 N 4 , as the material of the anti-etching layer. Then, as shown in Fig. 4(d), the porous Si substrate 43 is entirely immersed in hydrofluoric acid, with agitating so that only the porous Si is etched by electroless wet chemical etching, whereby a thinned monocrystalline Si layer 42 is left on the light-transparent substrate 44. Finally, with the heat treatment, Si/SiO 2 layer and light-transparent substrate 44 are bonded completely in the secondary bonding. Since the thin film and the light-transparent substrate are bonded as above described, the thin film is bonded in alignment with the substrate, so that it is possible to prevent exfoliations and cracks of the substrate caused by the difference between their thermal expansion coefficients. Fig. 4(e) shows the semiconductor substrate obtained by this embodiment, in which a monocrystalline Si layer 42 having a crystallinity equivalent to that of a silicon wafer is formed on the light-transparent substrate 44, with high degrees of smoothness and uniformity, and with a small thickness, over a wide area covering the whole surface of the wafer. The semiconductor substrate thus obtained is advantageous from the view point of production of an insulation-isolated electronic device. The conditions for the solution concentration and the temperature were set in the range where the etching rate of porous Si and the selection ratio of etching the porous Si and the non-porous Si have no effect in the practical use such as a fabrication process. The above method is one in which an epitaxial layer is formed before making a porous structure, and then the regions other than the epitaxial layer are made porous selectively by anodization. The above embodiments 2-1 and 2-2 are provided with the oxide layers 35, 45 and the anti-etching films 36, 46, but can be realized without them, with the same effects of the present invention. The etching rate has dependencies on the concentration of the etching solution and the temperature. The etching solution concentration and temperature are suitably determined in practical ranges. In the embodiments 2-1 and 2-2, 49% hydrofluoric acid and the room temperature are used, but the present invention is not limited to such conditions. Preferably, the concentration of the hydrofluoric acid is 5% to 95%, and the temperature is set to a level which is ordinarily adopted. (Embodiment 3-1) The etching can be made using a mixture liquid of hydrofluoric acid and alcohol, in place of hydrofluoric acid used for an etching solution in embodiments 2-1 and 2-2. In this case, porous Si can be selectively etched with high degrees of efficiency and uniformity, without etching non-porous Si, as in the embodiments 2-1 and 2-2. Fig. 6 shows the time dependency of etching thickness of porous Si and monocrystalline Si as observed when the porous Si and the monocrystalline Si are etched by being immersed in the mixture liquid (10:1) of 49% hydrofluoric acid and alcohol without agitation of the liquid. The porous Si was formed by anodizing the monocrystalline Si. The conditions of anodization are shown below. It is to be noted, however, that the starting material for producing porous Si by anodization is not limited to monocrystalline Si and Si of other crystalline structure may be used as the starting material. Voltage applied : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution : HF:H 2 O:C 2 H 5 OH=1:1:1 Time : 2.4 hours Thickness of porous Si: 300 (µm) Porosity : 56 (%) Test pieces of the porous Si prepared as described above were immersed, without agitation, in a mixture solution (10:1) of 49% hydrofluoric acid and alcohol (white circles). The reduction in the thickness of the porous Si was then measured. The porous Si was rapidly etched: namely, by a layer thickness of 85 µm in 40 minutes, and further 195 µm in 80 minutes, with high degrees of surface quality and uniformity. The etching rate has dependencies on the concentration of the etching solution and the temperature. Test pieces of non-porous Si having a thickness of 500 µm were immersed in a mixture liquid (10:1) of 49% hydrofluoric acid and alcohol (black circles) at the room temperature without agitation. The reduction in the thickness of the non-porous Si was then measured. The non-porous Si was only etched to 5nm (50Å) or less after elapse of 120 minutes. In particular, the addition of alcohol serves to remove bubbles of reaction product gases generated as a result of the etching without delay from the surface being etched, without necessitating agitation, thus ensuring a high efficiency and uniformity of the etching. The etched test pieces of porous Si and non-porous Si were then rinsed with water and the surfaces after the rinsing were examined by microanalysis using secondary ions but no impurity was detected. The conditions for the concentration of etching solution and the temperature were set in the range where the etching rate has no effect in the practical use such as a fabrication process, and alcohol can exhibit its effects. Although the mixture solution (10:1) of 49% hydrofluoric acid and ethyl alcohol, as well as the room temperature as the solution temperature, are mentioned, the present invention is not limited to such conditions. The HF concentration with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 5 and 90%, and most preferably between 5 and 80%. The alcohol concentration with respect to the etching solution is preferably 80% or less, more preferably 60% or less, and most preferably 40% or less, and is determined so as to provide an appreciable effect of alcohol. The temperature is set in a range of preferably 0 to 100°C, more preferably 5 to 80°C, and most preferably 5 to 60°C. Although ethyl alcohol has been used in this invention, other alcohols such as isopropyl alcohol, which does not cause any inconvenience in the commercial production and which can provide an appreciable effect of addition of such alcohol, may be used as the alcohol. (Embodiment 3-2) The etching can be made using a mixture liquid of hydrofluoric acid and hydrogen peroxide, in place of hydrofluoric acid used for an etching solution in embodiments 2-1 and 2-2. In this case, porous Si can be selectively etched with high degrees of efficiency and uniformity, without etching non-porous Si, as in the embodiments 2-1 and 2-2. The selective etching of porous Si will be described below with a mixture solution of hydrofluoric acid and hydrogen peroxide for use in this embodiment. Fig. 7 shows the time dependency of etching thickness of porous Si and monocrystalline Si as observed when the porous Si and the monocrystalline Si are etched by being immersed in a mixture liquid (1:5) of 49% hydrofluoric acid and 30% hydrogen peroxide and agitated. The porous Si was formed by anodizing the monocrystalline Si. The conditions of anodization are shown below. It is to be noted, however, that the starting material for producing porous Si by anodization is not limited to monocrystalline Si and Si of other crystalline structure may be used as the starting material. Voltage applied : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution : HF:H 2 O:C 2 H 5 OH=1:1:1 Time : 2.4 hours Thickness of porous Si: 300 (µm) Porosity : 56 (%) Test pieces of the porous Si prepared as described above were immersed, without agitation, in the mixture solution (1:5) of 49% hydrofluoric acid and 30% hydrogen peroxide (white circles) at the room temperature. The reduction in the thickness of the porous Si was then measured. The porous Si was rapidly etched: namely, by a layer thickness of 112 µm in 40 minutes, and further 256 µm in 80 minutes, with high degrees of surface quality and uniformity. The etching rate has dependencies on the concentration of the etching solution and the temperature. Test pieces of non-porous Si having a thickness of 500 µm were immersed in the mixture liquid (1:5) of 49% hydrofluoric acid and 30% hydrogen peroxide (black circles) at the room temperature and agitated. The reduction in the thickness of the non-porous Si was then measured. The non-porous Si was only etched to 5nm (50Å) or less after elapse of 120 minutes. In particular, the addition of hydrogen peroxide serves to accelerate oxidation of silicon, thus enhancing the reaction speed as compared to the case where hydrogen peroxide is not added. Furthermore, the reaction speed can be controlled by suitably selecting the content of the hydrogen peroxide. The etched test pieces of porous Si and non-porous Si were then rinsed with water and the surfaces after the rinsing were examined by microanalysis using secondary ions but no impurity was detected. Although the concentration of hydrogen peroxide solution was 30% herein, it can be set to fall within the ranges which would not impair the addition effect of hydrogen peroxide and cause any practical inconvenience in commercial production. The etching rate has dependencies on the solution concentrations of hydrofluoric acid and hydrogen peroxide, as well as the temperature. The addition of hydrogen peroxide solution makes it possible to accelerate the oxidation of silicon, and the reaction speed as compared to the case when it is not added. Further, the reaction speed can be controlled by suitably selecting the content of the hydrogen peroxide. The conditions for the concentration of etching solution and the temperature can be set to fall within the ranges in which the effects of hydrofluoric acid and hydrogen peroxide solution can be exhibited and the etching rate would not cause any practical inconvenience in commercial production. Although the mixture solution (1:5) of 49% hydrofluoric acid and hydrogen peroxide, as well as the room temperature as the solution temperature, are mentioned as an instance, the present invention is not limited to such conditions. The HF concentration with respect to the etching solution preferably ranges between 1 and 95%, mote preferably between 5 and 90%, and most preferably between 5 and 80%. The H 2 O 2 concentration with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 5 and 90%, and most preferably between 10 and 80%, and is determined so as to provide an appreciable effect of hydrogen peroxide. The temperature is set in a range of preferably 0 to 100°C, more preferably 5 to 80°C, and most preferably 5 to 60°C. (Embodiment 3-3) The etching can be made using a mixture liquid of hydrofluoric acid, alcohol and hydrogen peroxide, in place of hydrofluoric acid used for an etching solution in embodiments 2-1 and 2-2. In this case, porous Si can be selectively etched with high degrees of efficiency and uniformity, without etching non-porous Si, as in the embodiments 2-1 and 2-2. The selective etching of porous Si will be described below with a mixture solution of hydrofluoric acid, alcohol and hydrogen peroxide for use in this embodiment. Fig. 8 shows the time dependency of etching thickness of porous Si and monocrystalline Si as observed when the porous Si and the monocrystalline Si are etched by being immersed in a mixture liquid (10:6:50) of 49% hydrofluoric acid, alcohol and 30% hydrogen peroxide without agitation. The porous Si was formed by anodizing the monocrystalline Si. The conditions of anodization are shown below. It is to be noted, however, that the starting material for producing porous Si by anodization is not limited to monocrystalline Si and Si of other crystalline structure may be used as the starting material. Voltage applied : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution : HF:H 2 O:C 2 H 5 OH=1:1:1 Time : 2.4 hours Thickness of porous Si: 300 (µm) Porosity : 56 (%) Test pieces of the porous Si prepared as described above were immersed, without agitation, in the mixture solution (10:6:5) of 49% hydrofluoric acid, alcohol and 30% hydrogen peroxide (white circles) at the room temperature. The reduction in the thickness of the porous Si was then measured. The porous Si was rapidly etched: namely, by a layer thickness of 107 µm in 40 minutes, and further 244 µm in 80 minutes, with high degrees of surface quality and uniformity. The etching rate has dependencies on the concentration of the etching solution and the temperature. Test pieces of non-porous Si having a thickness of 500 µm were immersed in the mixture liquid (10:6:5) of 49% hydrofluoric acid, alcohol and 30% hydrogen peroxide (black circles) at the room temperature without agitation. The reduction in the thickness of the non-porous Si was then measured. The non-porous Si was only etched to 5nm (50Å) or less after elapse of 120 minutes. The etched test pieces of porous Si and non-porous Si were then rinsed with water and the surfaces after the rinsing were examined by microanalysis using secondary ions but no impurity was detected. Although the concentration of hydrogen peroxide solution was 30% herein, it can be set to fall within the ranges which would not impair the addition effect of hydrogen peroxide and cause any practical inconvenience in commercial production. The etching rate has dependencies on the solution concentrations of hydrofluoric acid and hydrogen peroxide, as well as the temperature. The addition of hydrogen peroxide solution makes it possible to accelerate the oxidation of silicon, and the reaction speed as compared to the case when it is not added. Further, the reaction speed can be controlled by suitably selecting the content of the hydrogen peroxide. In particular, the addition of alcohol serves to remove bubbles of reaction product gases generated as a result of the etching without delay from the surface being etched, without necessitating agitation, thus ensuring a high efficiency and uniformity of the etching for the porous Si. The conditions for the concentration of etching solution and the temperature can be set to fall within the ranges in which the effects of hydrofluoric acid, hydrogen peroxide solution and alcohol can be exhibited and the etching rate would not cause any practical inconvenience in commercial production. Although the mixture solution (10:6:5) of 49% hydrofluoric acid, ethyl alcohol and hydrogen peroxide, as well as the room temperature as the solution temperature, are mentioned as an instance, the present invention is not limited to such conditions. The HF concentration with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 5 and 90%, and most preferably between 5 and 80%. The H 2 O 2 concentration with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 5 and 90%, and most preferably between 10 and 80%, and is determined so as to provide an appreciable effect of hydrogen peroxide. The alcohol concentration with respect to the etching solution is preferably 80% or less, more preferably 60% or less, and most preferably 40% or less, and is determined so as to provide an appreciable effect of alcohol. The temperature is set in a range of preferably 0 to 100°C, more preferably 5 to 80°C, and most preferably 5 to 60°C. Although ethyl alcohol has been specifically used in this invention, other alcohols such as isopropyl alcohol, which does not cause any inconvenience in the commercial production and which can provide an appreciable effect of addition of such alcohol, may be used as the alcohol. (Embodiment 3-4) The etching can be made using a buffered hydrofluoric acid, in place of hydrofluoric acid used for an etching solution in embodiments 2-1 and 2-2. In this case, porous Si can be selectively etched with high degrees of efficiency and uniformity, without etching non-porous Si, as in the embodiments 2-1 and 2-2. The selective etching of porous Si will be described below with the buffered hydrofluoric acid for use in this embodiment. Fig. 9 shows the time dependency of etching thickness of porous Si and monocrystalline Si as observed when the porous Si and the monocrystalline Si are etched by being immersed in buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) and agitated. The porous Si was formed by anodizing the monocrystalline Si. The conditions of anodization are shown below. It is to be noted, however, that the starting material for producing porous Si by anodization is not limited to monocrystalline Si and Si of other crystalline structure may be used as the starting material. Voltage applied : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution : HF:H 2 O:C 2 H 5 OH=1:1:1 Time : 2.4 hours Thickness of porous Si: 300 (µm) Porosity : 56 (%) Test pieces of the porous Si prepared as described above were immersed, without agitation, in the buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) (white circles) at the room temperature. The reduction in the thickness of the porous Si was then measured. The porous Si was rapidly etched: namely, by a layer thickness of 70 µm in 40 minutes, and further 118 µm in 120 minutes, with high degrees of surface quality and uniformity. The etching rate has dependencies on the concentration of the etching solution and the temperature. Test pieces of non-porous Si having a thickness of 500 µm were immersed in the buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) (black circles) at the room temperature and agitated. The reduction in the thickness of the non-porous Si was then measured. The non-porous Si was only etched to 5nm (50Å) or less after elapse of 120 minutes. The etched test pieces of porous Si and non-porous Si were then rinsed with water and the surfaces after the rinsing were examined by microanalysis using secondary ions but no impurity was detected. The buffered hydrofluoric acid is a mixture solution of 36% ammonium fluoride (NH 4 F) and 4.5% hydrogen fluoride. The etching rate has dependencies on the solution concentrations, as well as the temperature. The conditions for the concentration of etching solution and the temperaure can be set to fall within the ranges in which no practical inconvenience would not be caused in commercial production. Although the buffered hydrofluoric acid containing a solution of 36% ammonium fluoride (NH 4 F) and 4.5% hydrogen fluoride (HF), as well as the room temperature as the solution temperature, are mentioned as an instance, the present invention is not limited to such conditions. The HF concentration in the buffered hydrofluoric acid with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 1 and 85%, and most preferably between 1 and 70%. The NH 4 F concentration in the buffered hydrofluoric acid with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 5 and 90%, and most preferably between 5 and 80%. The temperature is set in a range of preferably 0 to 100°C, more preferably 5 to 80°C, and most preferably 5 to 60°C. (Embodiment 3-5) The etching can be made using a mixture solution of buffered hydrofluoric acid and alcohol, in place of hydrofluoric acid used for an etching solution in embodiments 2-1 and 2-2. In this case, porous Si can be selectively etched with high degrees of efficiency and uniformity, without etching non-porous Si, as in the embodiments 2-1 and 2-2. The selective etching of porous Si will be described below with the mixture solution of buffered hydrofluoric acid and alcohol for use in this embodiment. Fig. 10 shows the time dependency of etching thickness of porous Si and monocrystalline Si as observed when the porous Si and the monocrystalline Si are etched by being immersed in the mixture solution (10:1) of buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) and alcohol without agitation. The porous Si was formed by anodizing the monocrystalline Si. The conditions of anodization are shown below. It is to be noted, however, that the starting material for producing porous Si by anodization is not limited to monocrystalline Si and Si of other crystalline structure may be used as the starting material. Voltage applied : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution : HF:H 2 O:C 2 H 5 OH=1:1:1 Time : 2.4 hours Thickness of porous Si: 300 (µm) Porosity : 56 (%) Test pieces of the porous Si prepared as described above were immersed, without agitation, in the mixture solution (10:1) of buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) and alcohol (white circles) at the room temperature. The reduction in the thickness of the porous Si was then measured. The porous Si was rapidly etched: namely, by a layer thickness of 83 µm in 40 minutes, and further 140 µm in 120 minutes, with high degrees of surface quality and uniformity. The etching rate has dependencies on the concentration of the etching solution and the temperature. Test pieces of non-porous Si having a thickness of 500 µm were immersed in the mixture solution of buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) and alcohol (black circles) at the room temperature without agitation. The reduction in the thickness of the non-porous Si was then measured. The non-porous Si was only etched to 5nm (50Å) or less after elapse of 120 minutes. The etched test pieces of porous Si and non-porous Si were then rinsed with water and the surfaces after the rinsing were examined by microanalysis using secondary ions but no impurity was detected. The etching rate has dependencies on the solution concentrations of buffered hydrofluoric acid, as well as the temperature. The addition of alcohol serves to remove bubbles of reaction product gases generated as a result of the etching without delay from the surface being etched, without necessitating agitation, thus ensuring a high efficiency and uniformity of the etching for the porous Si. The conditions for the concentration of etching solution and the temperature can be set to fall within the ranges in which the etching rate would cause no practical inconvenience in commercial production, with an appreciable effect of alcohol. Although the mixture solution (10:1) of buffered hydrofluoric acid (a mixture solution of 4.5% hydrogen fluoride and 36% ammonium fluoride) and ethyl alcohol, as well as the room temperature as the solution temperature, are mentioned as an instance, the present invention is not limited to such conditions. The HF concentration in the buffered hydrofluoric acid with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 1 and 85%, and most preferably between 1 and 70%. The ammonium fluoride (NH 4 F) concentration in the buffered hydrofluoric acid with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 5 and 90%, and most preferably between 5 and 80%. The alcohol concentration with respect to the etching solution is preferably 80% or less, more preferably 60% or less, and most preferably 40% or less, and is determined so as to provide an appreciable effect of alcohol. The temperature is set in a range of preferably 0 to 100°C, more preferably 5 to 80°C, and most preferably 5 to 60°C. Although ethyl alcohol has been specifically used in this invention, other alcohols such as isopropyl alcohol, which does not cause any inconvenience in the commercial production and which can provide an appreciable effect of addition of such alcohol, may be used as the alcohol. (Embodiment 3-6) The etching can be made using a mixture solution of buffered hydrofluoric acid and hydrogen peroxide, in place of hydrofluoric acid used for an etching solution in embodiments 2-1 and 2-2. In this case, porous Si can be selectively etched with high degrees of efficiency and uniformity, without etching non-porous Si, as in the embodiments 2-1 and 2-2. The selective etching of porous Si will be described below with the mixture solution of buffered hydrofluoric acid and hydrogen peroxide for use in this embodiment. Fig. 11 shows the time dependency of etching thickness of porous Si and monocrystalline Si as observed when the porous Si and the monocrystalline Si are etched by being immersed in the mixture solution (1:5) of buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) and 30% hydrogen peroxide and agitated. The porous Si was formed by anodizing the monocrystalline Si. The conditions of anodization are shown below. It is to be noted, however, that the starting material for producing porous Si by anodization is not limited to monocrystalline Si and Si of other crystalline structure may be used as the starting material. Voltage applied : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution : HF:H 2 O:C 2 H 5 OH=1:1:1 Time : 2.4 hours Thickness of porous Si: 300 (µm) Porosity : 56 (%) Test pieces of the porous Si prepared as described above were immersed, with agitation, in the mixture solution (1:5) of buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) and 30% hydrogen peroxide (white circles) at the room temperature. The reduction in the thickness of the porous Si was then measured. The porous Si was rapidly etched: namely, by a layer thickness of 88 µm in 40 minutes, and further 147 µm in 120 minutes, with high degrees of surface quality and uniformity. The etching rate has dependencies on the concentration of the etching solution and the temperature. Test pieces of non-porous Si having a thickness of 500 µm were immersed in the mixture solution (1:5) of buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) and 30% hydrogen peroxide (black circles) at the room temperature and agitated. The reduction in the thickness of the non-porous Si was then measured. The non-porous Si was only etched to 5nm (50Å) or less after elapse of 120 minutes. The etched test pieces of porous Si and non-porous Si were then rinsed with water and the surfaces after the rinsing were examined by microanalysis using secondary ions but no impurity was detected. Although the solution concentration of hydrogen peroxide was 30% herein, it can be set to fall within the ranges in which it would provide an appreciable effect of the addition of hydrogen peroxide and have no practical inconvenience in commercial production. The etching rate has dependencies on the solution concentrations of buffered hydrofluoric acid and hydrogen peroxide, as well as the temperature. The addition of hydrogen peroxide solution makes it possible to accelerate the oxidation of silicon, and the reaction speed as compared to the case when it is not added. Further, the reaction speed can be controlled by suitably selecting the content of the hydrogen peroxide. The conditions for the concentration of etching solution and the temperature can be set to fall within the ranges in which they provide an appreciable effect of buffered hydrofluoric acid and hydrogen peroxide and the etching rate would cause no practical inconvenience in commercial production. Although the mixture solution (1:5) of buffered hydrofluoric acid and hydrogen peroxide, as well as the room temperature as the solution temperature, are mentioned as an instance, the present invention is not limited to such conditions. The HF concentration in the buffered hydrofluoric acid with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 1 and 85%, and most preferably between 1 and 70%. The H 2 O 2 concentration with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 5 and 90%, and most preferably between 5 and 80%, and is determined so as to provide an appreciable effect of hydrogen peroxide. The temperature is set in a range of preferably 0 to 100°C, more preferably 5 to 80°C, and most preferably 5 to 60°C. (Embodiment 3-7) The etching can be made using a mixture solution of buffered hydrofluoric acid, alcohol and hydrogen peroxide, in place of hydrofluoric acid used for an etching solution in embodiments 2-1 and 2-2. In this case, porous Si can be selectively etched with high degrees of efficiency and uniformity, without etching non-porous Si, as in the embodiments 2-1 and 2-2. The selective etching of porous Si will be described below with the mixture solution of buffered hydrofluoric acid, alcohol and hydrogen peroxide for use in this embodiment. Fig. 12 shows the time dependency of etching thickness of porous Si and monocrystalline Si as observed when the porous Si and the monocrystalline Si are etched by being immersed in the mixture solution (10:6:50) of buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride), alcohol and 30% hydrogen peroxide without agitation. The porous Si was formed by anodizing the monocrystalline Si. The conditions of anodization are shown below. It is to be noted, however, that the starting material for producing porous Si by anodization is not limited to monocrystalline Si and Si of other crystalline structure may be used as the starting material. Voltage applied : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution : HF:H 2 O:C 2 H 5 OH=1:1:1 Time : 2.4 hours Thickness of porous Si: 300 (µm) Porosity : 56 (%) Test pieces of the porous Si prepared as described above were immersed, without agitation, in the mixture solution (10:6:50) of buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride), alcohol and 30% hydrogen peroxide (white circles) at the room temperature. The reduction in the thickness of the porous Si was then measured. The porous Si was rapidly etched: namely, by a layer thickness of 83 µm in 40 minutes, and further 140 µm in 120 minutes, with high degrees of surface quality and uniformity. The etching rate has dependencies on the concentration of the etching solution and the temperature. Test pieces of non-porous Si having a thickness of 500 µm were immersed in the mixture solution (10:6:50) of buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride), alcohol and 30% hydrogen peroxide (black circles) at the room temperature without agitation. The reduction in the thickness of the non-porous Si was then measured. The non-porous Si was only etched to 5nm (50Å) or less after elapse of 120 minutes. The etched test pieces of porous Si and non-porous Si were then rinsed with water and the surfaces after the rinsing were examined by microanalysis using secondary ions but no impurity was detected. Although the solution concentration of hydrogen peroxide was 30% herein, it can be set to fall within the ranges in which it would provide an appreciable effect of the addition of hydrogen peroxide and have no practical inconvenience in commercial production. The etching rate has dependencies on the solution concentrations of hydrofluoric acid and hydrogen peroxide, as well as the temperature. The addition of hydrogen peroxide solution makes it possible to accelerate the oxidation of silicon, and the reaction speed as compared to the case when it is not added. Further, the reaction speed can be controlled by suitably selecting the content of the hydrogen peroxide. The addition of alcohol serves to remove bubbles of reaciton product gases generated as a result of the etching without delay from the surface being etched, without necessitating agitation, thus ensuring a high efficiency and uniformity of the etching for the porous Si. The conditions for the concentration of etching solution and the temperature can be set to fall within the ranges in which they provide an appreciable effect of buffered hydrofluoric acid, hydrogen peroxide and alcohol, and the etching rate would cause no practical inconvenience in commercial production. Although the mixture solution (10:6:50) of buffered hydrofluoric acid, ethyl alcohol and hydrogen peroxide, as well as the room temperature as the solution temperature, are mentioned as an instance, the present invention is not limited to such conditions. The HF concentration in the buffered hydrofluoric acid with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 5 and 90%, and most preferably between 5 and 80%. The H 2 O 2 concentration with respect to the etching solution preferably ranges between 1 and 95%, more preferably between 5 and 90%, and most preferably between 10 and 80%, and is determined so as to provide an appreciable effect of hydrogen peroxide. The alcohol concentration with respect to the etching solution is preferably 80% or less, more preferably 60% or less, and most preferably 40% or less, and is determined so as to provide an appreciable effect of alcohol. The temperature is set in a range of preferably 0 to 100°C, more preferably 5 to 80°C, and most preferably 5 to 60°C. Although ethyl alcohol has been specifically used in this invention, other alcohols such as isopropyl alcohol, which does not cause any inconvenience in the commercial production and which can provide an appreciable effect of addition of such alcohol, may be used as the alcohol. The specific examples of the present invention will be described below in detail, but the present invention is not limited to those examples. (Example 1) (example not forming an oxide layer) This example will be explained in accordance with a process of Fig. 1. First, anodization was conducted on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . Also, the porous structure formation rate was 8.4 µm/min, and hence it took twenty four minutes for the (100) Si substrate having a thickness of 200 µm to be made entirely porous (Fig. 1(a)). A 0.5 µm thick Si epitaxial layer 13 of 0.063 Ω·cm was grown at a low temperature on the (100) porous Si substrate with MBE (Molecular Beam Epitaxy) method. Deposition was conducted under the following conditions (Fig. 1(b)). Temperature: 700°C Pressure : 1,33 10 -7 Pa (1x10 -9 Torr) Growth rate: 0.1 nm/sec Next, an optically polished fused silica glass substrate 14 was placed on the surface of this epitaxial layer, and contacted thereto (Fig. 1(c)). The etching speed of the Si monocrystal having a specific resistance of 0.01 Ω·cm with a hydrofluoro-nitro-acetic acid solution (49% hydrofluoric acid: 70% nitric acid: 99.5% acetic acid = 1:3:8) is about 1 µm or less per minute, but the Si monocrystal 13 of 0.063 Ω·cm can be hardly etched in this etching solution. The etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the porous Si substrate having a thickness of 200 µm was removed in 2 minutes with a result that the monocrystalline Si layer 13 having a thickness of 0.5 µm remained on the fused silica glass substrate 14. There was no change on the epitaxial layer 13. The back surface of the fused silica glass substrate 14 was etched 0.1 µm, but its front surface did not have any difference from its original optical polished face (Fig. 1(d)). Then, the SOI thin film layer 13 and the fused silica glass substrate 14 were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (Fig. 1(e)). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer and excellent crystallinity was maintained. (Example 2) First, anodization was conducted on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . Also, the porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the (100) Si substrate having a thickness of 200 µm to be made entirely porous (Fig. 1(a)). A 0.5 µm thick Si epitaxial layer 13 of 0.063 Ω·cm was grown at a low temperature on the (100) porous Si substrate with MBE (Molecular Beam Epitaxy) method. Deposition was conducted under the following conditions (Fig. 1(b)). Temperature: 700°C Pressure : 1,33.10 -7 Pa (1x10 -9 Torr) Growth rate: 0.1 nm/sec Next, the surface of this epitaxial layer was oxidized, and then an optically polished fused silica glass substrate 14 was placed on the surface of the oxidized film, and contacted thereto (Fig. 1(c)). The etching speed of the Si monocrystal having a specific resistance of 0.01 Ω·cm with a hydrofluoro-nitro-acetic acid solution (49% hydrofluoric acid: 70% nitric acid: 99.5% acetic acid = 1:3:8) is about 1 µm or less per minute, but the Si monocrystal 13 of 0.063 Ω·cm can be hardly etched in this etching solution. The etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the porous Si substrate having a thickness of 200 µm was removed in 2 minutes with a result that the monocrystalline Si layer 13 having a thickness of 0.5 µm remained on the fused silica glass substrate 14. There was no change on the epitaxial layer 13. The back surface of the fused silica glass substrate 14 was etched 0.1 µm, but its front surface did not have any difference from its original optical polished face (Fig. 1(d)). Then, the SOI thin film layer 13 and the fused silica glass substrate 14 were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (Fig. 1(e)). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 3) This example was carried out in accordance with a process of Fig. 1. First, anodization was conducted on a P-type or high-carrier density N-type (100) monocrystalline Si substrate having a thickness of 200 µm in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . Also, the porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the (100) Si substrate having a thickness of 200 µm to be made entirely porous (Fig. 1(a)). A 0.5 µm thick Si epitaxial layer was grown at a low temperature on the (100) porous Si substrate with plasma CVD method. Deposition was conducted under the following conditions (Fig. 1 (b)). Gas : SiH 4 High-frequency power: 100 W Temperature : 800°C Pressure : 1,33.10 -7 Pa (1x10 -9 Torr) Growth rate : 2.5 nm/sec Next, the surface of this epitaxial layer was oxidized, and then an optically polished glass substrate having a softening point of about 500°C was placed on the surface of the oxidized film, and contacted thereto (Fig. 1 (c)). The etching speed of the normal Si monocrystal with a KOH 6M solution is about 1 µm or less per minute, but the etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the 200 µm thick porous Si substrate was removed in 2 minutes with a result that the 0.5 µm thick monocrystalline Si layer remained on the glass substrate having a low softening point. There was no change on the epitaxial layer. (Fig. 1(d)) Then, the SOI thin film layer and the glass substrate having a low softening point were firmly joined by heating them at 450°C for 0.5 hour in an oxygen atmosphere (Fig. 1(e)). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal detects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 4) First, anodization was conducted on a P-type or high-carrier density N-type (100) monocrystalline Si substrate having a thickness of 200 µm in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . Also, the porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the (100) Si substrate having a thickness of 200 µm to be made entirely porous (Fig. 1(a)). A 1 µm thick Si epitaxial layer was grown at a low temperature on the (100) porous Si substrate with bias sputtering method. Deposition was conducted under the following conditions (Fig. 1(b)). RF frequency : 100 MHz High-frequency power: 600 W Temperature : 300°C Ar gas pressure : 1.06 Pa (8x10 -3 Torr) Growth time : 60 min. Target d.c. bias : -200 V Substrate d.c. bias : +5 V Next, the surface of this epitaxial layer was oxidized, and then an optically polished glass substrate having a softening point of about 500°C was placed on the surface of the oxidized film, and contacted thereto (Fig. 1(c)). The etching speed of the normal Si monocrystal with an NaOH 7M solution is about 1 µm or less per minute, but the etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the 200 µm thick porous Si substrate was removed in 2 minutes with a result that the 1 µm thick monocrystalline Si layer remained on the glass substrate having a low softening point. There was no change on the epitaxial layer (Fig. 1(d)). Then, the SOI thin film layer and the glass substrate having a low softening point were firmly joined by heating them at 450°C for 0.5 hour in an oxygen atmosphere (Fig. 1(e)). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 5) This example was also carried out in accordance with a process of Fig. 1. Anodization was conducted on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . Also, the porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the (100) Si substrate having a thickness of 200 µm to be made entirely porous. A 0.5 µm thick Si epitaxial layer 13 of 0.063 Ω·cm was grown at a low temperature on the (100) porous Si substrate with liquid phase growth method. Deposition was conducted under the following conditions. Solvent : Sn Growth temperature: 900°C Growth atmosphere : H 2 Growth time : 10 min. Next, the surface of this epitaxial layer was oxidized, and then an optically polished glass substrate having a softening point of about 800°C was placed on the surface of the oxidized film, and contacted thereto. The etching speed of the Si monocrystal having a specific resistance of 0.01 Ω·cm with a hydrofluoro-nitro-acetic acid solution (49% hydrofluoric acid: 70% nitric acid: 99.5% acetic acid = 1:3:8) is about 1 µm or less per minute, but the Si monocrystal 13 of 0.063 Ω·cm can be hardly etched in this etching solution. The etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the porous Si substrate having a thickness of 200 µm was removed in 2 minutes with a result that the monocrystalline Si layer 13 having a thickness of 0.5 µm remained on the glass substrate. There was no change on the epitaxial layer. The back surface of the fused silica glass substrate was etched 0.1 µm, but its front surface did not have any difference from its original optical polished face. Then, the SOI thin film layer and the glass substrate were firmly joined by heating them at 750°C for 0.5 hour in an oxygen atmosphere. Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 6) This example was also carried out in accordance with a process of Fig. 1. Anodization was conducted on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . Also, the porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the (100) Si substrate having a thickness of 200 µm to be made entirely porous. A 0.5 µm thick Si epitaxial layer was grown at a low temperature on the (100) porous Si substrate with low-pressure CVD method. Deposition was conducted under the following conditions. Source gas : SiH 4 Carrier gas: H 2 Temperature: 850°C Pressure : 1,33 Pa (1x10 -2 Torr) Growth rate: 3.3 nm/sec Next, the surface of this epitaxial layer was oxidized, and then an optically polished fused silica glass substrate was placed on the surface of the oxidized film, and contacted thereto. The etching speed of the normal Si monocrystal with a hydrofluoro-nitric acid solution (40% hydrofluoric acid: 65% nitric acid: water = 6:100:40) is about 0.5 µm or less per minute. The etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the porous Si substrate having a thickness of 200 µm was removed in 4 minutes with a result that the monocrystalline Si layer having a thickness of 0.5 µm remained on the fused silica glass substrate. There was no change on the epitaxial layer. The back surface of the fused silica glass substrate was hardly etched but its front surface did not have any difference from its original optical polished face. When SiH 2 Cl 2 was as a source gas, high-speed etching characteristics specific to the porous substrate were maintained, although the growth temperature must be elevated several tens degrees. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in a nitrogen atmosphere. Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 7) (example of not forming an oxide layer) This example was also carried out in accordance with a process of Fig. 2. First, a 1.0 µm thick Si epitaxial layer was grown on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm by CVD method. Deposition was conducted under the following conditions: Reactive gas flow rate: SiH 2 Cl 2 1000 SCCM H 2 230 liter/min Temperature : 1080°C Pressure : 1,01.10 5 Pa (760 Torr) Time : 2 min Anodization was conducted on this substrate in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . The porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the (100) Si substrate having a thickness of 200 µm to be made entirely porous. This anodization made the (100) Si substrate porous, and there was no change in the Si epitaxial layer (Fig. 2(b)). Then, an optically polished fused silica glass substrate was placed on the surface of the epitaxial layer, and contacted thereto (Fig. 2(c)). The etching speed of the Si monocrystal having a specific resistance of 0.01 Ω·cm with a hydrofluoro-nitro-acetic acid solution (40% hydrofluoric acid: 65% nitric acid: 99.5% acetic acid = 1:3:8) is about 1 µm or less per minute, but the Si monocrystal of 0.063 Ω·cm is hardly etched in this etching solution. The etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the porous Si substrate having a thickness of 200 µm was removed in 2 minutes with a result that the monocrystalline Si layer having a thickness of 1 µm remained on the fused silica glass substrate. There was no change on the epitaxial layer. The back surface of the fused silica glass substrate was etched 0.1 µm, but its front surface did not have any difference from its original optical polished face (Fig. 2(d)). Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (Fig. 2(e)). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 8) First, a 1.0 µm thick Si epitaxial layer was grown on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm by CVD method. Deposition was conducted under the following conditions: Reactive gas flow rate: SiH 2 Cl 2 1000 SCCM H 2 230 liter/min PH 3 (500 ppm) 72 SCCM Temperature : 1080°C Pressure : 1,06.10 4 Pa (80 Torr) Time : 2 min Anodization was conducted on this substrate in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . The porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the (100) Si substrate having a thickness of 200 µm to be made entirely porous. As mentioned above, this anodization made only the (100) Si substrate porous, and there was no change in the Si epitaxial layer (Fig. 2(b)). Next, the surface of this epitaxial layer was oxidized, and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and contacted thereto (Fig. 2(c)). The etching speed of the Si monocrystal having a specific resistance of 0.01 Ω·cm with a hydrofluoro-nitro-acetic acid solution (49% hydrofluoric acid: 70% nitric acid: 99.5% acetic acid = 1:3:8) is about 1 µm or less per minute, but the Si monocrystal of 0.063 Ω·cm is hardly etched in this etching solution. The etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the porous Si substrate having a thickness of 200 µm was removed in 2 minutes with a result that the monocrystalline Si layer having a thickness of 1 µm remained on the fused silica glass substrate. There was no change on the epitaxial layer. The back surface of the fused silica glass substrate was etched 0.1 µm, but its front surface did not have any difference from its original optical polished face (Fig. 2(d)). Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (Fig. 2(e)). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 9) This example was also carried out in accordance with a process of Fig. 2. First, a 0.5 µm thick Si epitaxial layer was grown on a P-type or high-density N-type (100) monocrystalline Si substrate having a thickness of 200 µm by CVD method. Deposition was conducted under the following conditions: Reactive gas flow rate: SiH 2 Cl 2 1000 SCCM H 2 230 liter/min PH 3 (500 ppm) 72 SCCM Temperature : 1080°C Pressure : 1,06.10 4 Pa (80 Torr) Time : 2 min Anodization was conducted on this substrate in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . The porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the (100) Si substrate having a thickness of 200 µm to be made entirely porous. As mentioned above, this anodization made only the (100) Si substrate porous, and there was no change in the Si epitaxial layer. Next, the surface of this epitaxial layer was oxidized, and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and contacted thereto. The etching speed of the normal Si monocrystal with a hydrofluoro-nitric acid solution (40% hydrofluoric acid: 65% nitric acid: water = 6:100:40) is about 0.5 µm or less per minute. The etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the porous Si substrate having a thickness of 200 µm was removed in 4 minutes with a result that the monocrystalline Si layer having a thickness of 0.5 µm remained on the fused silica glass substrate. There was no change on the epitaxial layer. The back surface of the fused silica glass substrate was hardly etched but its front surface did not have any difference from its original optical polished face. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in a nitrogen atmosphere. Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 10) This example was also carried out in accordance with a process of Fig. 2. A 0.5 µm thick Si epitaxial layer was grown on a P-type or high-carrier density N-type (100) monocrystalline Si substrate having a thickness of 200 µm by MBE method. Deposition was conducted under the following conditions: Temperature: 700°C Pressure : 1.33x10 -7 Pa (1x10 -9 Torr) Growth rate: 0.1 nm/sec Anodization was conducted on this substrate in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . The porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the (100) Si substrate having a thickness of 200 µm to be made entirely porous. As mentioned above, this anodization made only the (100) Si substrate porous, and there was no change in the Si epitaxial layer. Next, the surface of this epitaxial layer was oxidized, and then an optically polished glass substrate having a softening point of about 800°C was placed on the surface of the oxide film, and contacted thereto. The etching speed of the normal Si monocrystal with a hydrofluoro-nitric acid solution (40% hydrofluoric acid: 65% nitric acid: water = 6:100:40) is about 0.5 µm or less per minute. The etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the porous Si substrate having a thickness of 200 µm was removed in 4 minutes with a result that the monocrystalline Si layer having a thickness of 0.5 µm remained on the fused silica glass substrate. There was no change on the epitaxial layer. The back surface of the glass substrate was hardly etched but its front surface did not have any difference from its original optical polished face. Then, the SOI thin film layer and the glass substrate were firmly joined by heating them at 750°C for 0.5 hour in an oxygen atmosphere. Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 11) This example was carried out in accordance with a process of Fig. 1. A 1 µm thick N-type Si layer was formed in the surface of a P-type (100) monocrystal Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm by proton implantation. Implantation rate of H + was 5x10 15 (ions/cm 2 ). Anodization was conducted on this substrate in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . The porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the P-type (100) Si substrate having a thickness of 200 µm to be made entirely porous. As mentioned above, this anodization made only the P-type (100) Si substrate porous, and there was no change in the N-type Si layer. Next, the surface of this epitaxial N-type Si layer was oxidized, and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and contacted thereto. The etching speed of the Si monocrystal having a specific resistance of 0.01 Ω·cm with a hydrofluoro-nitric acid solution (49% hydrofluoric acid: 70% nitric acid: 99.5% acetic acid = 1:3:8) is about 1 µm or less per minute, but the Si monocrystal of 0.063 Ω·cm is hardly etched in this etching solution. The etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the porous Si substrate having a thickness of 200 µm was removed in 2 minutes with a result that the monocrystalline Si layer having a thickness of 1 µm remained on the fused silica glass substrate. There was no change on the (epitaxial) layer. The back surface of the fused silica glass substrate was etched 0.1 µm but its front surface did not have any difference from its original optical polished face. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere. Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 12) This example was carried out in accordance with a process of Fig. 2. A 1 µm thick high resistive Si layer having a specific resistance of 0.063 Ω·cm was formed on the surface of a P-type (100) monocrystal Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm by ion implantation of P + (phosphorous ion). Implantation rate of P + was 5x10 15 (ions/cm 2 ). Anodization was conducted on this substrate in a 50% HF solution. At this time, the current density was 100 mA/cm 2 . The porous structure formation rate was 8.4 µm/min and hence it took twenty four minutes for the low resistive P-type (100) Si substrate having a thickness of 200 µm to be made entirely porous. As mentioned above, this anodization made only the low resistive P-type (100) Si substrate porous, and there was no change in the high resistive Si layer. Next, the surface of this epitaxial layer was oxidized, and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and contacted thereto. The etching speed of the Si monocrystal having a specific resistance of 0.01 Ω·cm with a hydrofluoro-nitro-acetic acid solution (49% hydrofluoric acid: 70% nitric acid: 99.5% acetic acid = 1:3:8) is about 1 µm or less per minute, but the Si monocrystal of 0.063 Ω·cm is hardly etched in this etching solution. The etching speed of the porous layer is increased to about 100 times thereof, as previously described. That is, the porous Si substrate having a thickness of 200 µm was removed in 2 minutes with a result that the monocrystalline Si layer having a thickness of 1 µm remained on the fused silica glass substrate. There was no change on the epitaxial layer. The back surface of the fused silica glass substrate was etched 0.1 µm but its front surface did not have any difference from its original optical polished face. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere. Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 13) First, anodization was conducted on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm in an HF solution to make the substrate porous. The conditions of anodization are as follows. Applied voltage : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution : HF:H 2 O:C 2 H 5 OH = 1:1:1 Time : 1.6 hours Thickness of porous Si: 200 (µm) Porosity : 56 (%) A 0.5 µm thick Si epitaxial layer (non-porous Si monocrystalline layer) of 0.063 Ω·cm was grown at a low temperature on the (100) porous Si substrate by MBE (Molecular Beam Epitaxy) method. Deposition was conducted under the following conditions. Temperature: 700°C Pressure : 1,33.10 -7 Pa (1x10 -9 Torr) Growth rate: 0.1 nm/sec Next, the surface of this epitaxial layer was oxidized 1000Å, and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and contacted thereto, (primary bonding). The fused silica glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the non-porous monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 0.5 µm-thick monocrystalline Si layer remained on the fused silica glass substrate after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. Coating of Apiezon Wax can be used in place of the Si 3 N 4 coated film. (Example 14) First, anodization was conducted on a P-type or high-carrier density N-type (100) monocrystalline Si substrate having a thickness of 200 µm in an HF solution to make the substrate porous. The conditions of anodization were the sane as those shown in example 13. A 0.5 µm thick Si epitaxial layer (non-porous Si monocrystalline layer) was grown at a low temperature on the (100) porous Si substrate by a plasma CVD method. Deposition was conducted under the following conditions. Gas : SiH 4 High-frequency power: 100 W Temperature : 800°C Pressure : 1.33 Pa (1x10 -2 Torr) Growth rate : 2.5 nm/sec Next, the surface of this epitaxial layer was oxidized 100nm (1000Å), and then an optically polished glass substrate having a softening point of about 500°C was placed on the surface of the oxide film, and contacted thereto (primary bonding). Then, the glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 0.5 µm-thick monocrystalline Si layer remained on the glass substrate having a low softening point after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the glass substrate having a low softening point were firmly joined by heating them at 450°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 15) First, anodization was conducted on a P-type or high-density N-type (100) monocrystalline Si substrate having a thickness of 200 µm in an HF solution to make the substrate porous. The conditions of anodization were the same as those shown in example 13. A 1 µm thick Si epitaxial layer (non-porous Si monocrystalline layer) was grown at a low temperature on the (100) porous Si substrate by bias sputtering. Deposition was conducted under the following conditions. RF frequency : 100 MHz High-frequency power: 600 W Temperature : 300°C Ar gas pressure : 1.06 Pa (8x10 -3 Torr) Growth rate : 60 min. Target d.c. bias : -200 V Substrate d.c. bias: +5 V Next, the surface of this epitaxial layer was oxidized 100nm (1000Å), and then an optically polished glass substrate having a softening point of about 500°C was placed on the surface of the oxide film, and contacted thereto (primary bonding). The glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 1 µm-thick monocrystalline Si layer remained on the glass substrate having a low softening point after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the glass substrate having a low softening point were firmly joined by heating them at 450°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 16) First, anodization was conducted on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm in an HF solution to make the substrate porous. The conditions of anodization were the same as those shown in example 13. A 0.5 µm thick Si epitaxial layer (non-porous Si monocrystalline layer) of 0.063 Ω·cm was grown at a low temperature on the (100) porous Si substrate by liquid phase growth. Deposition was conducted under the following conditions. Solvent : Sn Growth temperature: 900°C Growth atmosphere : H 2 Growth rate : 10 min. Next, the surface of this epitaxial layer was oxidized 100nm (1000Å), and then an optically polished glass substrate having a softening point of about 800°C was placed on the surface of the oxide film, and contacted thereto (primary bonding). The glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 0.5 µm-thick monocrystalline Si layer remained on the glass substrate after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the glass substrate were firmly joined by heating them at 750°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 17) First, anodization was conducted on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm in an HF solution to make the substrate porous. The conditions of anodization were the same as those shown in example 13. A 0.5 µm thick Si epitaxial layer (non-porous Si monocrystalline layer) was grown at a low temperature on the (100) porous Si substrate by liquid phase growth. Deposition was conducted under the following conditions. Source gas : SiH 4 Carrier gas: H 2 Temperature: 850°C Pressure : 1,33 Pa (1x10 -2 Torr) Growth rate: 3.3 nm/sec Next, the surface of this epitaxial layer was oxidized 100nm (1000Å), and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and contacted thereto (primary bonding). The fused silica glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 0.5 µm-thick monocrystalline Si layer on the fused silica glass substrate remained after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. When SiH 2 Cl 2 was used as the source gas, the growth temperature had to be higher by several tens of degrees. However, high-speed etching characteristics to the porous substrate did not deteriorate. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in a nitrogen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 18) A 1 µm thick Si epitaxial layer (non-porous Si monocrystalline layer) was grown on the P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm by CVD method. Deposition was conducted under the following conditions. Reactive gas flow rate: SiH 2 Cl 2 1000 SCCM H 2 230 1/min. PH 3 (50 ppm) 72 SCCM Temperature : 1080°C Pressure : 1,06.10 4 Pa (80 Torr) Time : 2 min. Anodization was conducted on the substrate in an HF solution to make the substrate porous. The conditions of anodization were the same as those shown in example 13. As mentioned above, anodization made only the (100) Si substrate porous, and did not affect the Si epitaxial layer (non-porous Si monocrystalline layer). Next, the surface of this epitaxial layer was oxidized 100nm (1000Å), and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and contacted thereto (primary bonding). The fused silica glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 1 µm-thick monocrystalline Si layer on the fused silica glass substrate remained after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 19) A 0.5 µm thick Si epitaxial layer (non-porous Si monocrystalline layer) was grown on the P-type or high-carrier density N-type (100) monocrystalline Si substrate having a thickness of 200 µm by CVD method. Deposition was conducted under the following conditions. Reactive gas flow rate: SiH 2 Cl 2 1000 SCCM H 2 230 1/min. PH 3 (50 ppm) 72 SCCM Temperature : 1080°C Pressure : 1.06 . 10 4 Pa (80 Torr) Time : 1 min. Anodization was conducted on the substrate in an HF solution to make the substrate porous. The conditions of anodization were the same as those shown in example 13. As mentioned above, anodization made only the (100) Si substrate porous, and did not affect the Si epitaxial layer (non-porous Si monocrystalline layer). Next, the surface of tins epitaxial layer was oxidized 100nm (1000Å), and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and contacted thereto (primary bonding). The fused silica glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 0.5 µm-thick monocrystalline Si layer on the fused silica glass substrate remained after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in a nitrogen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 20) A 0.5 µm thick Si epitaxial layer (non-porous Si monocrystalline layer) was grown on the P-type or high-carrier density N-type (100) monocrystalline Si substrate having a thickness of 200 µm by MBE method. Deposition was conducted under the following conditions. Temperature: 700°C Pressure : 1.33 10 -7 Pa (1x10 -9 Torr) Growth rate: 0.1 nm/sec Anodization was conducted on the substrate in an HF solution to make the substrate porous. The conditions of anodization were the same as those shown in example 13. As mentioned above, anodization made only the (100) Si substrate porous, and did not affect the Si epitaxial layer (non-porous Si monocrystalline layer). Next, the surface of this epitaxial layer was oxidized, and then an optically polished glass substrate having a softening point of about 800°C was placed on the surface of the oxide film, and contacted thereto (primary bonding). The glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 0.5 µm-thick monocrystalline Si layer on the fused silica glass substrate remained after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the glass substrate were firmly joined by heating them at 750°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 21) A 1 µm thick N-type Si layer was grown on the surface of a P-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm by proton implantation. Implantation rate of H + was 5x10 15 (ions/cm 2 ). Anodization was conducted on the substrate in an HF solution to make the substrate porous. The conditions of anodization were the same as those shown in example 13. As mentioned above, anodization made only the P-type (100) Si substrate porous, and did not affect the N-type Si layer. Next, the surface of this N-type Si layer was oxidized 100nm (1000Å), and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and contacted thereto (primary bonding). The fused silica glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 1 µm-thick monocrystalline Si layer on the fused silica glass substrate remained after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 22) A 1 µm thick high-resistance Si layer having a specific resistance of 0.063 Ω·cm was formed on the surface of a P-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm by ion implantation of P + (phosphorus ion). Implantation rate of P + was 5x10 15 (ions/cm 2 ). Anodization was conducted on the substrate in an HF solution to make the substrate porous. The conditions of anodization were the same as those shown in example 13. As mentioned above, anodization made only the low-resistance P-type (100) Si substrate porous, and did not affect the high-resistance Si layer. Next, the surface of this high-resistance Si layer was oxidized 100nm (1000Å), and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and contacted thereto (primary bonding). The fused silica glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 1 µm-thick monocrystalline Si layer on the fused silica glass substrate remained after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 23) First, anodization was conducted on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm in an HF solution to make the substrate porous. The conditions of anodization were the same as those shown in example 13. Then, a 0.5 µm Si epitaxial layer (non-porous Si monocrystalline layer) was grown at a low temperature on the (100) porous Si substrate by MBE (Molecular Beam Epitaxy) method. Deposition was conducted under the following conditions. Temperature: 700°C Pressure : 1,33.10 -7 Pa (1x10 -9 Torr) Growth rate: 0.1 nm/sec Next, an optically polished fused silica glass substrate was placed on the surface of the epitaxial layer, and contacted thereto (primary bonding). The fused silica glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the non-porous monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 0.5 µm-thick monocrystalline Si layer on the fused silica glass substrate remained after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confined that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. Apiezon wax can be used instead of the Si 3 N 4 coating film. (Example 24) A 1 µm si epitaxial layer (non-porous Si monocrystalline layer) was grown on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm by CVD method. Deposition was conducted under the following conditions. Reactive gas flow rate: SiH 2 Cl 2 1000 SCCM H 2 230 1/min. PH 3 (50 ppm) 72 SCCM Temperature : 1080°C Pressure : 1,06.10 4 Pa (80 Torr) Time : 2 min. Anodization was conducted on this substrate in an HF solution to make the substrate porous. As mentioned above, anodization made only the (100) Si substrate porous, and did not affect the Si epitaxial layer (non-porous Si monocrystalline layer). Next, an optically polished fused silica glass substrate was placed on the surface of the epitaxial layer, and contacted thereto (primary bonding). The fused silica glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the non-porous monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 1 µm-thick monocrystalline Si layer on the fused silica glass substrate remained after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (secondary bonding). observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. In the above-described examples, a light-transparent substrate was used as an insulating substrate to realize the SOI structure, but it will be appreciated that a light-opaque substrate can be also used with the same effects of the present invention. Herein, it will be understood that the anti-etching film is not necessary if the light-opaque substrate has a strong resistance to the etching solution of the present invention. (Examples 25 to 36) Etching was performed in the same manner as that of examples 13 to 24 to form a monocrystalline Si layer with the exception that a mixture solution (10:1) of 49% hydrofluoric acid and alcohol was used as an etchant, instead of an etching solution used in examples 13 to 24. In eighty two minutes after initialization of etching, the porous Si was selectively removed by etching using the mixture solution (10:1) of 49% hydrofluoric acid and alcohol, only the non-porous Si monocrystalline layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in eighty two minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. Observing the cross-section of a finally obtained Si layer with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Examples 37 to 48) Etching was performed in the same manner as that of examples 13 to 24 to form a monocrystalline Si layer with the exception that a mixture solution (1:5) of 49% hydrofluoric acid and 30% hydrogen peroxide was used as an etchant, instead of an etching solution used in examples 13 to 24. In sixty two minutes after initialization of etching, the porous Si was selectively removed by etching using the mixture solution (1:5) of 49% hydrofluoric acid and 30% hydrogen peroxide, only the non-porous Si monocrystalline layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in sixty two minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. Observing the cross-section of a finally obtained Si layer with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Examples 49 to 60) Etching was performed in the same manner as that of examples 13 to 24 to form a monocrystalline Si layer with the exception that a mixture solution (10:6:50) of 49% hydrofluoric acid, alcohol and 30% hydrogen peroxide was used as an etchant, instead of an etching solution used in examples 13 to 24. In sixty five minutes after initialization of etching, the porous Si was selectively removed by etching using the mixture solution (10:6:50) of 49% hydrofluoric acid, alcohol and 30% hydrogen peroxide, only the non-porous Si monocrystalline layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in sixty five minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. Observing the cross-section of a finally obtained Si layer with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Examples 61 to 72) Etching was performed in the same manner as that of examples 13 to 24 to form a monocrystalline Si layer with the exception that a buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) was used as an etchant, instead of an etching solution used in examples 13 to 24. In two hundreds fifty eight minutes after initialization of etching, the porous Si was selectively removed by etching using the buffered hydrofluoric acid, only the non-porous Si monocrystalline layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in two hundreds fifty eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. Observing the cross-section of a finally obtained Si layer with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Examples 72 to 84) Etching was performed in the same manner as that of examples 13 to 24 to form a monocrystalline Si layer with the exception that a mixture solution (10:1) of a buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) and alcohol was used as an etchant, instead of an etching solution used in examples 13 to 24. In two hundreds seventy five minutes after initialization of etching, the porous Si was selectively removed by etching using the mixture solution, only the non-porous Si monocrystalline layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in two hundreds seventy five minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. Observing the cross-section of a finally obtained Si layer with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Examples 85 to 96) Etching was performed in the same manner as that of examples 13 to 24 to form a monocrystalline Si layer with the exception that a mixture solution (1:5) of a buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride) and 30% hydrogen peroxide was used as an etchant, instead of an etching solution used in examples 13 to 24. In one hundred ninety one minutes after initialization of etching, the porous Si was selectively removed by etching using the mixture solution, only the non-porous Si monocrystalline layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in one hundred ninety one minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. Observing the cross-section of a finally obtained Si layer with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Examples 97 to 108) Etching was performed in the same manner as that of examples 13 to 24 to form a monocrystalline Si layer with the exception that a mixture solution (10:6:50) of a buffered hydrofluoric acid (a mixture solution of 4.5% hydrofluoric acid and 36% ammonium fluoride), alcohol and 30% hydrogen peroxide was used as an etchant, instead of an etching solution used in examples 13 to 24. In two hundreds five minutes after initialization of etching, the porous Si was selectively removed by etching using the mixture solution, only the non-porous Si monocrystalline layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in two hundreds five minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. Observing the cross-section of a finally obtained Si layer with a transmission electron microscope, it was confirmed taht no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 109) First, anodization was conducted on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm in an HF solution to make the substrate porous. The conditions of anodization are as follows. Applied voltage : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution : HF:H 2 O:C 2 H 5 OH = 1:1:1 Time : 1.6 (hour) Thickness of porous Si: 200 (µm) Porosity : 56 (%) A 0.5 µm thick Si epitaxial layer (non-porous Si monocrystalline layer) was grown at a low temperature on the (100) porous Si substrate by MBE (Molecular Beam Epitaxy) method. Deposition was conducted under the following conditions. Temperature: 700°C Pressure : 1,33.10 -7 Pa (1x10 -9 Torr) Growth rate: 0.1 nm/sec Next, the surface of this epitaxial layer was oxidized 100nm (1000Å), and then an optically polished fused silica glass substrate was placed on the surface of the oxide film, and the bonding strength between the oxide film and the glass substrate was made higher by heating them at 400°C for one hour in N 2 atmosphere (primary bonding). The bonded substrates were not exfoliated. Next, the fused silica glass substrate was only covered with Si 3 N 4 excellent in the chemical etching resistance. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the non-porous monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 0.5 µm-thick monocrystalline Si layer remained on the fused silica glass substrate after the removal of Si 3 N 4 coating film. There was no change on the epitaxial layer. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained. (Example 110) First, anodization was conducted on a P-type or N-type (100) monocrystalline Si substrate having a thickness of 200 µm and a specific resistance of 0.01 Ω·cm in an HF solution to make the substrate porous. The conditions of anodization are as follows. Applied voltage : 2.6 (V) Current density : 30 (mA·cm -2 ) Anodizing solution : HF:H 2 O:C 2 H 5 OH = 1:1:1 Time : 1.6 (hour) Thickness of porous Si: 200 (µm) Porosity : 56 (%) A 0.5 µm thick Si epitaxial layer (non-porous Si monocrystalline layer) was grown at a low temperature on the (100) porous Si substrate by MBE (Molecular Beam Epitaxy) method. Deposition was conducted under the following conditions. Temperature: 700°C Pressure : 1,33.10 -7 Pa (1x10 -9 Torr) Growth rate: 0.1 nm/sec Next, the surface of this epitaxial layer was oxidized 1000Å, and then an Si substrate having a 5000Å thick thermally oxidized membrane formed thereon was placed on the surface of the oxide film, and the bonding strength between the oxidized membranes was made higher by heating them at 400°C for two hours in N 2 atmosphere (primary bonding). The bonded substrates were not exfoliated. Thereafter, selective etching was conducted on the bonded substrates in a 49% hydrofluoric acid solution while the solution was being stirred. In seventy eight minutes, the porous Si substrate was completely removed by the selective etching, with the non-porous monocrystal Si acting as an etch stopper, only the non-porous monocrystalline Si layer being left behind. The etching rate of the non-porous Si monocrystal with the etching solution was so low that only a maximum of 5nm (50Å) of non-porous monocrystalline Si was removed in seventy eight minutes. Since the ratio of the etching rate of the non-porous monocrystalline Si to that of the porous layer is 1:10 5 , the amount of non-porous layer which is etched (several tens angstroms) can be ignored in a practical operation. That is, the 200 µm-thick porous Si substrate was removed with a result that the 0.5 µm-thick monocrystalline Si layer remained via a 500nm (5000Å) thick oxide film on the Si substrate. There was no change on the epitaxial layer. Then, the SOI thin film layer and the fused silica glass substrate were firmly joined by heating them at 800°C for 0.5 hour in an oxygen atmosphere (secondary bonding). Observing the cross-section with a transmission electron microscope, it was confirmed that no crystal defects were newly introduced into the Si layer, and excellent crystallinity was maintained.

Claims: A method of producing a semiconductor member comprising a non-porous silicon monocrystalline layer arranged on an insulating substrate, the method comprising: a process of providing a first substrate having a non-porous Si monocrystalline layer (13, 22, 33, 42) on a semiconductor layer (12, 21, 32, 43); a primary bonding process of bonding said first substrate and an insulating substrate (14, 24, 35, 45) with the non-porous Si monocrystalline layer therebetween (13, 22, 33, 42) ; a process of removing said semiconductor layer (12, 21, 32, 43) by means of chemical etching; and a secondary bonding process of strengthening said primary bonding after said removing process, characterised in that said semiconductor layer (12, 21, 32, 43) is a porous silicon layer. The method of claim 1, wherein said chemical etching is carried out using hydrofluoric acid as an etchant. The method of claim 2, wherein said chemical etching is carried out by using a mixture containing hydrofluoric acid and alcohol. The method of claim 2, wherein said chemical etching is carried out by using, a mixture containing hydrofluoric acid and hydrogen peroxide. The method of claim 2, wherein said chemical etching is carried out by using, as an etchant, a mixture containing hydrofluoric acid, alcohol and hydrogen peroxide. The method of claim 2, wherein said chemical etching is performed by using, as an etchant, a mixture containing buffered hydrofluoric acid (a mixed aqueous solution of hydrofluoric acid and ammonium fluoride). The method of claim 2, wherein said chemical etching is performed by using, as an etchant, a mixture containing buffered hydrofluoric acid (a mixed aqueous solution of hydrofluoric acid and ammonium fluoride) and alcohol. The method of claim 2, wherein said chemical etching is performed by using, as an etchant, a mixture containing buffered hydrofluoric acid (a mixed aqueous solution of hydrofluoric acid and ammonium fluoride) and hydrogen peroxide. The method of claim 2, wherein said chemical etching is performed by using, as an etchant, a mixture containing buffered hydrofluoric acid (a mixed aqueous solution of hydrofluoric acid and ammonium fluoride), alcohol and hydrogen peroxide. The method of any preceding claim wherein said process of providing said first substrate comprises the steps of: forming a low-carrier density layer (22) in a part of said single crystalline Si substrate (21), resp. on said single crystalline Si substrate and converting the remainder part of said single crystalline Si substrate (21), resp. said entire single crystalline Si substrate to make it porous to provide said porous silicon layer, said low-carrier density layer (22) formed in or on said single crystalline Si substrate (21) being left unconverted to provide said non-porous Si monocrystalline layer. The method of claim 10 wherein said remainder part of said single crystalline Si substrate is a high-resistance Si layer. The method of claim 10 wherein said remainder part of said single crystalline Si substrate is an N-type Si layer. The method of claim 10 wherein said low-carrier density layer (22) in, resp. on said single crystalline Si substrate is formed by proton implantation or counter doping in said Si substrate, resp. by epitaxial growth of said low-carrier-density layer (22) on said Si substrate. The method of any of claims 10 to 13 wherein said part of said single crystalline Si substrate is converted by anodisation. The method of claim 14, wherein said anodisation is performed in an HF solution. The method of any preceding claim 1 to 9, wherein said process of providing said first substrate comprises forming said non-porous Si monocrystalline layer (13) on a porous Si substrate (12) by an epitaxial method selected from a molecular beam method, a plasma CVD method, a photo CVD method, a low pressure CVD method, a liquid phase growth method, and a bias sputter method. The method of any preceding claim, wherein the surface of said non-porous Si monocrystalline layer is oxidized, after which the primary bonding process is carried out and an oxidized membrane is interposed between the insulating substrate and said non-porous Si monocrystalline layer. The method of any preceding claim, wherein the etching process for removal of said porous Si is performed after all the surface except for said porous Si face has been covered with an anti-etching film. The method of any preceding claim, wherein the thickness of said non-porous Si monocrystalline layer is 100 µm or less. The method of any preceding claim, wherein said primary bonding process further includes placing said substrate having said porous Si layer and said insulating substrate into contact with each other at room temperature to bond them by Van der Walls force so that they become difficult to pull apart without giving rise to substantial stress due to difference between the thermal expansion coefficients of materials forming the contact face. The method of claims 1 to 10, wherein said primary bonding process includes the step of heating the surfaces in material contact so that the interfaces become bonded and do not exfoliate. The method of any preceding claim, wherein said secondary bonding process is carried out by heat treatment. The method of any preceding claim, wherein said secondary bonding process comprises heating in an oxygen atmosphere. The method of any of claims 1-22, wherein said secondary bonding process further comprises heating in a nitrogen atmosphere. The method of any preceding claim, wherein said secondary bonding process is performed at a temperature 200°C - 800°C. The method of any preceding claim, wherein said porous silicon layer is formed by converting P-type Si, or of N-type Si doped so as to have a sufficiently high-carrier density to give rise to the porosity. The method of any preceding claim, wherein said insulating substrate is a light-transparent substrate. The method of claim 27, wherein said light-transparent substrate is of glass. A method according to any preceding claim 1 to 27, wherein said insulating substrate is produced by forming an oxide layer on a surface of monocrystalline Si.

Inventors: SAKAGUCHI KIYOFUMI, YONEHARA TAKAO, SAKAGUCHI, KIYOFUMI, YONEHARA, TAKAO, SAKAGUCHI, KIYOFUMI, C/O CANON KABUSHIKI KAISHA, YONEHARA, TAKAO, C/O CANON KABUSHIKI KAISHA
Applicants: CANON KK, CANON KABUSHIKI KAISHA
Application year: 1992
Main classification: H01L21
IPC codes: H01L21, H01L27