Patent Publication Number: US-2021189549-A1

Title: Manufacturing Method For Semiconductor Laminated Film, And Semiconductor Laminated Film

Description:
CROSS REFERENCE TO RELATED APPLICATIONS 
     This application is divisional application of U.S. patent application Ser. No. 16/317,751 filed on Jan. 14, 2019, which is a U.S. National Phase Application of International Application No. PCT/JP2017/025436 filed on Jul. 12, 2017 and published in Japanese as WO 2018/012546 A1 on Jan. 18, 2018 and claims the benefit of priority from Japanese Patent Application No. 2016-140117 filed on Jul. 15, 2016. The entire disclosures of all of the above applications are incorporated herein by reference. 
    
    
     BACKGROUND 
     Technical Field 
     The present invention relates to a method of producing a semiconductor laminate film, and a semiconductor laminate film. 
     Related Art 
     As next-generation Si-based ultra-high speed devices, for example, the following devices for communication have been known: high electron mobility transistors (HEMTs); doped-channel field-effect transistors (DCFETs); resonant tunneling diodes (RTDs); hetero-bipolar transistors (HBTs); and strained-channel metal-oxide-semiconductor field-effect transistors (MOSFETs). Of those devices, particularly a HEMT using holes as carriers (p-HEMT or HHMT), a DCFET using holes as carriers (p-DCFET), a hole tunneling RTD (p-RTD), a hetero-bipolar transistor (HBT), a MOSFET with a strained SiGe channel using holes as carriers (strained-SiGe-channel p-MOSFET), and a buried-channel MOSFET using holes as carriers (buried-channel p-MOSFET) each use a hetero structure of a silicon (Si) substrate and a silicon germanium (SiGe) layer having such compressive strain as to be substantially lattice-matched with Si. 
     When SiGe with compressive strain is sandwiched between Si without strain (Si/SiGe with compressive strain/Si), the SiGe layer having compressive strain can form a potential well for a hole in a valence band through a change in a band width, to thereby realize a structure for achieving an increase in speed. In addition, when used as a channel, the SiGe layer having compressive strain can increase a mobility (speed) of a hole passing therethrough. Thus, an increase in speed of the device can be achieved. Particularly when the compressive strain of the SiGe layer is increased by increasing a composition ratio of Ge (ratio of the number of Ge atoms) in the SiGe layer, the potential well becomes deeper, and the mobility becomes higher, and thus a device having a higher speed can be achieved. 
     For example, in  Journal of Applied Physics , vol. 95, no. 12, Jun. 15, 2004, pp. 7681-7689, there is described that a SiGe layer is formed on a Si substrate by a chemical vapor deposition (CVD) method. In addition, for example, in JP-A-2008-21674, there is described that a SiGe layer is formed on a Si substrate by a sputtering method using a mixed gas containing hydrogen as a sputtering gas. 
     However, each of the technology described in Journal of Applied Physics, vol. 95, no. 12 and the technology described in JP-A-2008-21674 has faced a difficult problem in terms of a technology for controlling formation of a semiconductor laminate film in the course of forming a SiGe layer having a high composition ratio of Ge (ratio of the number of Ge atoms) and large compressive strain, with which significant improvement in characteristics of a semiconductor device (e.g., an increase in carrier mobility, and an increase in speed of the semiconductor device) can be expected. 
     The inventors of the invention have focused attention on a sputtering method in order to form a SiGe layer having large compressive strain capable of sufficiently improving the characteristics of a semiconductor device, and have made extensive investigations on various film formation conditions. As a result, the inventors have found that a substrate temperature at the time of formation of the SiGe layer (film formation temperature), the concentration of hydrogen in a sputtering gas at the time of formation of the SiGe layer, and the pressure of the sputtering gas at the time of formation of the SiGe layer (film formation pressure) are particularly important. 
     An objective of the invention is to provide a method of producing a semiconductor laminate film capable of growing a semiconductor layer containing silicon and germanium so as to be better lattice-matched with a silicon substrate even when the semiconductor layer has a high composition ratio of germanium, to thereby produce a semiconductor device having satisfactory characteristics. Another objective of the invention is to provide a semiconductor laminate film which includes a semiconductor layer containing silicon and germanium which is better lattice-matched with a silicon substrate even when the semiconductor layer has a high composition ratio of germanium, and is thus capable of producing a semiconductor device having satisfactory characteristics. 
     SUMMARY 
     According to one embodiment of the invention, there is provided a method of producing a semiconductor laminate film, including 
     forming a semiconductor layer containing silicon and germanium on a silicon substrate by a sputtering method, 
     in the sputtering method, 
     a film formation temperature of the semiconductor layer being less than 500° C., and a film formation pressure of the semiconductor layer ranging from 1 mTorr to 11 mTorr, or, 
     a film formation temperature of the semiconductor layer being less than 600° C., and a film formation pressure of the semiconductor layer being equal to or more than 2 mTorr and less than 5 mTorr, 
     the sputtering method using a sputtering gas having a volume ratio of a hydrogen gas of less than 0.1%, and
         the semiconductor layer satisfying a following relationship       

         t≤ 0.881× x   −4.79  
         where t represents a thickness (nm) of the semiconductor layer, and x represents a ratio of the number of germanium atoms to a sum of the number of silicon atoms and the number of germanium atoms in the semiconductor layer.       

     In such method of producing a semiconductor laminate film, the semiconductor layer having larger compressive strain (i.e., a lower lattice mismatch rate f) than a semiconductor layer formed under the film formation conditions of, for example, a volume ratio of a hydrogen gas in the sputtering gas of 0.1% or more can be formed (the details are described later). Accordingly, in the method of producing a semiconductor laminate film, the semiconductor layer can be grown so as to be better lattice-matched with the silicon substrate even when the semiconductor layer has a high composition ratio of germanium. Thus, a semiconductor laminate film which leads to production of a semiconductor device having such high performance that the related art has not been able to achieve, or significant improvement in characteristics of the device can be produced. 
     In the above method of producing a semiconductor laminate film, the sputtering gas may have a volume ratio of a hydrogen gas of 0.0001% or less. 
     In the above method of producing a semiconductor laminate film, the semiconductor layer may satisfy a relationship of t≤0.881×x −4.79 , where t represents a thickness (nm) of the semiconductor layer, and x represents a ratio of the number of germanium atoms to a sum of the number of silicon atoms and the number of germanium atoms in the semiconductor layer. 
     In the above method of producing a semiconductor laminate film, a film formation temperature of the semiconductor layer ranges from 350° C. to 550° C. 
     In the above method of producing a semiconductor laminate film, the semiconductor layer may contain impurities configured to impart conductivity. 
     In the above method of producing a semiconductor laminate film, a film formation pressure of the semiconductor layer ranges from 2 mTorr to 4 mTorr. 
     In the above method of producing a semiconductor laminate film, the semiconductor layer may be lattice-matched with the silicon substrate. 
     In the above method of producing a semiconductor laminate film, the semiconductor layer may have a surface roughness Rms of 1 nm or less. 
     In the above method of producing a semiconductor laminate film, the semiconductor layer may include silicon and germanium. 
     According to one embodiment of the invention, there is provided a semiconductor laminate film including: 
     a silicon substrate; and 
     a semiconductor layer formed on the silicon substrate and containing silicon and germanium, 
     the semiconductor layer having a surface roughness Rms of 1 nm or less, 
     the semiconductor layer satisfying a following relationship 
         t≤ 0.881× x   −4.79  
         where t represents a thickness (nm) of the semiconductor layer, and x represents a ratio of the number of germanium atoms to a sum of the number of silicon atoms and the number of germanium atoms in the semiconductor layer.       

     In such semiconductor laminate film, a semiconductor layer  20  can have larger compressive strain (i.e., a lower lattice mismatch rate f) even when the semiconductor layer  20  has a high composition ratio x of germanium (see the details described later). Accordingly, in such semiconductor laminate film, the semiconductor layer is better lattice-matched with the silicon substrate even when the semiconductor layer has a high composition ratio of germanium, and a semiconductor device having excellent characteristics can be produced. 
     In the above semiconductor laminate film, the semiconductor layer may be lattice-matched with the silicon substrate, and the semiconductor layer may satisfy a following relationship 
         t&lt; 0.881× x   −4.79  
 
     where t represents a thickness (nm) of the semiconductor layer, and x represents a ratio of the number of germanium atoms to a sum of the number of silicon atoms and the number of germanium atoms in the semiconductor layer. 
     In the above semiconductor laminate film, the semiconductor layer may have a surface roughness Rms of 0.5 nm or less. 
     In the above semiconductor laminate film, the semiconductor layer may include silicon and germanium. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         FIG. 1  is a sectional view for schematically illustrating a semiconductor laminate film according to an embodiment of the invention. 
         FIG. 2  is a diagram for illustrating a state in which a SiGe layer is lattice-matched with a silicon substrate. 
         FIG. 3  is a diagram for illustrating the state in which the SiGe layer is lattice-matched with the silicon substrate. 
         FIG. 4  is a diagram for illustrating a state in which the SiGe layer is not lattice-matched with the silicon substrate. 
         FIG. 5  is a flowchart for illustrating a method of producing a semiconductor laminate film according to an embodiment of the invention. 
         FIG. 6  is a table for illustrating a relationship among a ratio of hydrogen in a sputtering gas, a film formation temperature, and a lattice mismatch rate. 
         FIG. 7  is a chart for illustrating the relationship among the ratio of hydrogen in the sputtering gas, the film formation temperature, and the lattice mismatch rate. 
         FIG. 8  is a table for illustrating a relationship among a film formation pressure, a film formation temperature, and a lattice mismatch rate. 
         FIG. 9  is a chart for illustrating the relationship among the film formation pressure, the film formation temperature, and the lattice mismatch rate. 
         FIG. 10  is a table for illustrating a relationship among a composition ratio of Ge, a thickness, and a lattice mismatch rate. 
         FIG. 11  is a chart for illustrating the relationship among the composition ratio of Ge, the thickness, and the lattice mismatch rate in the case of film formation by a sputtering method. 
         FIG. 12  is a chart for illustrating the relationship among the composition ratio of Ge, the thickness, and the lattice mismatch rate in the case of film formation by a CVD method. 
         FIG. 13  is a chart for illustrating a relationship between a composition ratio of Ge and a maximum thickness at which lattice matching is achieved. 
         FIG. 14  is a table for illustrating a relationship among a composition ratio of Ge, a thickness, and a surface roughness. 
         FIG. 15  is a chart for illustrating the relationship among the composition ratio of Ge, the thickness, and the surface roughness in the case of film formation by a sputtering method. 
         FIG. 16  is a chart for illustrating the relationship among the composition ratio of Ge, the thickness, and the surface roughness in the case of film formation by a CVD method. 
         FIG. 17  is a sectional view for schematically illustrating a first semiconductor device according to an embodiment of the invention. 
         FIG. 18  is a sectional view for schematically illustrating a second semiconductor device according to an embodiment of the invention. 
         FIG. 19  is a sectional view for schematically illustrating a third semiconductor device according to an embodiment of the invention. 
         FIG. 20  is a sectional view for schematically illustrating a fourth semiconductor device according to an embodiment of the invention. 
     
    
    
     DETAILED DESCRIPTION 
     Preferred embodiments of the invention are described in detail below with reference to the drawings. The following embodiments do not unduly limit the scope of the invention as stated in the claims. In addition, all of the elements described below should not necessarily be taken as essential elements of the invention. 
     1. SEMICONDUCTOR LAMINATE FILM 
     First, a semiconductor laminate film according to an embodiment of the invention is described with reference to the drawings.  FIG. 1  is a sectional view for schematically illustrating a semiconductor laminate film  100  according to this embodiment. 
     As illustrated in  FIG. 1 , the semiconductor laminate film  100  includes a silicon (Si) substrate  10  and a semiconductor layer  20 . 
     The material for the silicon substrate  10  is silicon. The silicon substrate  10  may be a monocrystalline substrate. The silicon substrate  10  may be a silicon on insulator (SOI) substrate, in which a monocrystalline silicon thin film is formed on an insulator, or a silicon on quartz (SOQ) substrate. The silicon substrate  10  may be, for example, a (100) substrate. The silicon substrate  10  may be formed of a monocrystalline silicon substrate and a silicon layer formed on the monocrystalline silicon substrate. 
     The semiconductor layer  20  is formed on the silicon substrate  10 . The semiconductor layer  20  contains silicon (Si) and germanium (Ge). The semiconductor layer  20  may be a semiconductor layer containing impurities configured to impart conductivity. The semiconductor layer  20  is substantially lattice-matched with the silicon substrate  10  and has large compressive strain. It is preferred that the semiconductor layer  20  be lattice-matched (completely lattice-matched) with the silicon substrate  10 . The semiconductor layer  20  may be a Si 1-x Ge x  layer (where 0&lt;x&lt;1) including silicon and germanium. Here,  FIG. 2  and  FIG. 3  are views for illustrating a state in which a SiGe layer is lattice-matched with a Si substrate. In each of  FIG. 2  and  FIG. 3 , a white circle represents a Si atom, and a black circle represents a Ge atom. 
     In general, the Si 1-x Ge x  layer has a larger lattice constant than the Si substrate. Si has a lattice constant of 0.543 nm and Ge has a lattice constant of 0.565 nm, and hence the Si 1-x Ge x  layer has a lattice constant of more than 0.543 nm and less than 0.565 nm. In the semiconductor laminate film  100 , as illustrated in  FIG. 3 , the semiconductor layer  20  (SiGe layer in the illustrated example) is compressed in a plane direction (in a direction perpendicular to a lamination direction) and pulled in the lamination direction, and is thus lattice-matched with the silicon substrate  10  (Si substrate in the illustrated example). Therefore, the semiconductor layer  20  has compressive strain in the plane direction. The above-mentioned state in which the semiconductor layer  20  has compressive strain, and the lattice constant of the semiconductor layer  20  is matched with the lattice constant of the silicon substrate  10  is referred to as “the semiconductor layer  20  is lattice-matched with the silicon substrate  10 .” 
     For example, when the SiGe layer is not lattice-matched with the Si substrate as illustrated in  FIG. 4 , the SiGe layer includes a relaxed interfacial region  2 . With this, threading dislocation caused by a mismatch defect may occur on a surface of the semiconductor laminate film. In contrast, in the semiconductor laminate film  100 , the occurrence of the threading dislocation can be sufficiently reduced because the semiconductor layer  20  is substantially lattice-matched with the silicon substrate  10 . Accordingly, when the semiconductor laminate film  100  is used for a semiconductor device, the occurrence of malfunction resulting from the defect is sufficiently reduced, and the reliability of the semiconductor device can be improved. 
     When the semiconductor layer  20  is not completely lattice-matched with the silicon substrate  10 , the semiconductor layer  20  has a lattice mismatch rate f of, for example, 0.3% or less, preferably 0.1% or less. As described above, it is preferred that the semiconductor layer  20  be lattice-matched (completely lattice-matched) with the silicon substrate  10 , and in this case, the semiconductor layer  20  has a lattice mismatch rate f of 0%. When the semiconductor layer  20  has a lattice mismatch rate f of 0%, the lattice spacing of the semiconductor layer  20  in the plane direction is exactly the same as the lattice spacing of the silicon substrate  10  in the plane direction, and the semiconductor layer  20  is lattice-matched with the silicon substrate  10 . When the lattice constant of Si is defined as a Si , and the lattice constant of SiGe is defined as a SiGe , the lattice mismatch rate f (%) can be determined by the following equation (1). The a Si  and the a SiGe  may be determined by, for example, reciprocal lattice map measurement based on X-ray diffraction in a (404) crystal orientation. Even in the case where the ratio of the number of Ge atoms in the SiGe layer is increased, when the SiGe layer is substantially lattice-matched with the silicon substrate and the lattice mismatch rate f is close to 0%, a SiGe layer having large compressive strain is obtained. With this, a potential well for a hole becomes deeper, and the mobility of the hole becomes higher, and thus the characteristics of the device are significantly improved. 
         f =( a   SiGe   −a   Si )/ a   Si ×100  (1)
 
     When the thickness of the semiconductor layer  20  is defined as t (nm), and the ratio of the number of Ge atoms to the sum of the number of Si atoms and the number of Ge atoms in the semiconductor layer  20  is defined as x (hereinafter also referred to as “composition ratio x of Ge”), the semiconductor laminate film  100  satisfies the relationship represented by the following expression (2). It is preferred that the semiconductor laminate film  100  satisfy the relationship represented by the following expression (3). 
         t≤ 0.881× x   −4.79   (2)
 
         t&lt; 0.881× x   −4.79   (3)
 
     The thickness t of the semiconductor layer  20  may be measured by, for example, observing a sectional transmission electron microscope (TEM) image. The composition ratio x of Ge may be measured by, for example, secondary ion mass spectrometry (SIMS) or X-ray diffraction (XRD) spectroscopy. When the semiconductor layer  20  satisfies the expression (2), the lattice mismatch rate f can be reduced to almost 0%. When the semiconductor layer  20  satisfies the expression (3), the lattice mismatch rate f can be reduced to 0% (the details are described later). When the lattice mismatch rate f is 0%, the semiconductor layer  20  is lattice-matched with the silicon substrate  10 , and such state is also referred as “the semiconductor layer  20  is completely compressively strained.” 
     Specifically, when the thickness t of the semiconductor layer  20  is 280 nm or less, the composition ratio x of Ge is 0.30 or less. When the thickness t is 125 nm or less, the composition ratio x of Ge is 0.355 or less. When the thickness t is 50 nm or less, the composition ratio x of Ge is 0.43 or less. The semiconductor layer  20  has a thickness t ranging, for example, from 1 nm to 1 μm, preferably from 5 nm to 500 nm. The thickness t of the semiconductor layer  20  refers to a maximum value of magnitude of the semiconductor layer  20  in the lamination direction. 
     The semiconductor layer  20  has a surface roughness Rms (root mean square surface roughness) of 1 nm or less, preferably 0.5 nm or less. SiGe has a lattice constant of 0.543 nm or more, and hence when the Rms is 0.5 nm, the semiconductor layer  20  can have a surface roughness smaller than the lattice constant of SiGe. The surface roughness Rms is a root mean square roughness, and may be measured with an atomic force microscope (AFM). 
     The semiconductor layer  20  may contain at least one of carbon (C) or tin (Sn) as an additive. The concentration of C and Sn to be added as an additive is 20% or less with respect to a total number of atoms in the semiconductor layer  20 . When C or Sn is added to the semiconductor layer  20 , the lattice constant of the semiconductor layer  20  can be controlled. C has a lattice constant of 0.356 nm, which is smaller than the lattice constant of SiGe. Therefore, when C is added, the lattice constant of the semiconductor layer  20  can be reduced. In this case, the semiconductor layer  20  may be a Si 1-x-y Ge x C y  (0&lt;y&lt;x) layer including Si, Ge, and C. Meanwhile, Sn has a lattice constant of 0.646 nm, which is larger than the lattice constant of SiGe. Therefore, when Sn is added, the lattice constant of the semiconductor layer  20  can be increased. In this case, the semiconductor layer  20  may be a Si 1-x-y Ge x Sn y  (0&lt;y&lt;x) layer including Si, Ge, and Sn. 
     For example, the semiconductor laminate film  100  has the following features. 
     The semiconductor laminate film  100  satisfies the above-mentioned expression (2). In such semiconductor laminate film  100 , even when the semiconductor layer  20  has a high composition ratio x of Ge with respect to its thickness, the semiconductor layer  20  can have larger compressive strain (i.e., a lower lattice mismatch rate f) than a semiconductor layer formed by, for example, a CVD method (see the details described later). Accordingly, in the semiconductor laminate film  100 , even when the semiconductor layer  20  has a high composition ratio of Ge, the semiconductor layer  20  is better lattice-matched with the silicon substrate  10 , and a semiconductor device having satisfactory characteristics can be produced. Specifically, when the semiconductor laminate film  100  is used for a semiconductor device, a deep potential well for a hole can be formed in a valence band. In addition, when the SiGe layer is used as a channel, the mobility (speed) of a hole passing therethrough can be increased. Thus, an increase in speed of the device can be achieved. 
     Further, in the semiconductor laminate film  100 , the semiconductor layer  20  has a surface roughness Rms of 1 nm or less. As described above, the surface roughness Rms of the semiconductor layer  20  can be reduced in the semiconductor laminate film  100 , and hence when the semiconductor laminate film  100  is used for the semiconductor device, a high-density device can be produced. 
     As described above, the semiconductor laminate film  100  can include the semiconductor layer  20  capable of producing the semiconductor device having satisfactory characteristics. 
     In the semiconductor laminate film  100 , the semiconductor layer  20  may have a surface roughness Rms of 0.5 nm or less. Therefore, in the semiconductor laminate film  100 , the surface roughness Rms of the semiconductor layer  20  can be reduced to be smaller than the lattice constant of SiGe, and a higher-density device can be produced. 
     The semiconductor laminate film  100  may satisfy the above-mentioned expression (3). In this case, the lattice mismatch rate f can be reduced to 0%, and the semiconductor layer  20  is lattice-matched with the silicon substrate  10 . 
     2. METHOD OF PRODUCING A SEMICONDUCTOR LAMINATE FILM 
     Next, a method of producing the semiconductor laminate film  100  according to an embodiment of the invention is described with reference to the drawings.  FIG. 5  is a flowchart for illustrating the method of producing the semiconductor laminate film  100  according to this embodiment. 
     First, as illustrated in  FIG. 1 , the silicon substrate  10  is prepared (Step S 1 ). 
     Next, the semiconductor layer  20  is formed on the silicon substrate  10  by a sputtering method (Step S 2 ). In the sputtering method, a sputtering gas is introduced into a chamber of a sputtering device, and a voltage is applied to a target to generate glow discharge and ionize atoms of the sputtering gas. The resultant gas ions are caused to collide with a surface of the target at high speed, and thus particles of a film formation material constituting the target are sputtered to deposit on a surface of the substrate, to thereby form a thin film. As the sputtering device, there is used, for example, a device in which a vacuum reaction vessel (chamber) and a sample introduction vessel (chamber) are connected to each other through a vacuum valve. 
     In the sputtering method for forming the semiconductor layer  20 , the formation temperature of the semiconductor layer  20  is less than 600° C., preferably 350° C. or more and 550° C. or less, more preferably 350° C. or more and 450° C. or less. When the film formation temperature is less than 350° C., an activation rate of a dopant may be remarkably reduced in the case where a dopant (impurities), such as phosphorus, arsenic, antimony, boron, or gallium, is injected into the semiconductor layer  20 . In addition, when the film formation temperature is set to 350° C. or more, the impurities can be activated without heating after the film formation, and the semiconductor layer  20  containing impurities configured to impart conductivity can be formed. When the film formation temperature is 600° C. or more, the lattice mismatch rate f may be increased. The film formation temperature of the semiconductor layer  20  refers to, for example, a substrate temperature of the silicon substrate  10  at the time of formation of the semiconductor layer  20  on the silicon substrate  10 . 
     In the sputtering method for forming the semiconductor layer  20 , the semiconductor layer  20  containing impurities may be formed by, for example, using a sputtering target in which impurities are mixed. Alternatively, the semiconductor layer  20  containing impurities may be formed by performing ion implantation after the film formation by the sputtering method. Alternatively, the semiconductor layer  20  containing impurities may be formed by performing heat diffusion using a gas containing impurities after the film formation by the sputtering method. 
     The semiconductor layer  20  may be formed by performing the sputtering method a plurality of times. That is, the semiconductor layer  20  may have a laminate structure of a plurality of layers. In this case, impurities may be incorporated in any one of the layers constituting the laminate structure, or may be incorporated in all the layers constituting the laminate structure. In addition, the expression (2) and the expression (3) are established when the thickness t (nm) is the total thickness of the laminated layers, and the ratio x is an average value (a value obtained by integrating x in a thickness direction in the range of the total thickness of the layers, and dividing the integrated value by t: x=(∫xdt)/t). 
     Before the formation of the semiconductor layer  20  on the silicon substrate  10 , the silicon substrate  10  may be cleaned by, for example, being heated to 1,000° C. or more and 1,100° C. or less. With this, impurities contained in the silicon substrate  10  can be removed. 
     In the sputtering method for forming the semiconductor layer  20 , the formation pressure of the semiconductor layer  20  ranges from 1 mTorr to 11 mTorr, preferably from 2 mTorr to 10 mTorr, more preferably from 2 mTorr to 5 mTorr still more preferably from 2 mTorr to 4 mTorr. When the formation pressure of the semiconductor layer  20  is less than 1 mTorr, such instability that discharge does not start may occur. When the formation pressure of the semiconductor layer  20  is more than 11 mTorr, the lattice mismatch rate f may be increased. The formation pressure of the semiconductor layer  20  refers to, for example, the pressure of a chamber (chamber of the sputtering device) in which the silicon substrate  10  is placed at the time of formation of the semiconductor layer  20  on the silicon substrate  10 . 
     The sputtering method for forming the semiconductor layer  20  is performed under any of first conditions and second conditions described below. 
     First conditions: The film formation temperature is less than 500° C., and the film formation pressure ranges from 1 mTorr to 11 mTorr. 
     Second conditions: The film formation temperature is less than 600° C., and the film formation pressure is equal to or more than 2 mTorr and less than 5 mTorr. 
     In the sputtering method for forming the semiconductor layer  20 , the sputtering gas has a volume ratio of a hydrogen gas of 0.1% or less, preferably 0.0001% or less, more preferably 0%. When the sputtering gas has a volume ratio of a hydrogen gas of more than 0.1%, the lattice mismatch rate f may be increased, or crystallization may not occur in the first place. Specifically, a mixed gas of an inert gas, such as argon (Ar), and a hydrogen gas, or an argon gas may be used as the sputtering gas. In general, a commercially available argon gas has a purity of about 99.9999%, and hydrogen is mixed therein at a ratio of 0.0001% or less. The same applies to the purities of other inert gases. 
     In the sputtering method for forming the semiconductor layer  20 , a flow rate of the sputtering gas ranges, for example, from 0.1 cc/min to 10,000 cc/min when the sputtering gas to be supplied has a temperature of 0° C. under the atmospheric pressure. When the flow rate of the sputtering gas is set to fall within the above-mentioned range, the semiconductor layer  20  having compressive strain can be formed more reliably. 
     In the sputtering method for forming the semiconductor layer  20 , a high-frequency power of the sputtering device ranges, for example, from 0.1 W/cm 2  to 20 W/cm 2  per unit area of the target. When a direct-current power is applied, the direct-current power is, for example, 0.1 W/cm 2  or more and 10 W/cm 2  or less. When the high-frequency power and the direct-current power are set to fall within the above-mentioned ranges, a formation speed of the semiconductor layer  20  and the composition ratio x can be controlled, and the semiconductor layer  20  having compressive strain can be formed more reliably. 
     Through the above-mentioned steps, the semiconductor laminate film  100  can be produced. 
     In the method of producing the semiconductor laminate film  100 , the sputtering gas has a volume ratio of a hydrogen gas of less than 0.1%, and the sputtering method for forming the semiconductor layer  20  is performed under any of the first conditions and the second conditions described above. Further, in the method of producing the semiconductor laminate film  100 , the above-mentioned expression (2) is satisfied. Therefore, in the method of producing the semiconductor laminate film  100 , the semiconductor layer  20  having larger compressive strain (i.e., a lower lattice mismatch rate f) than a semiconductor layer formed under the film formation conditions of, for example, a volume ratio of a hydrogen gas of the sputtering gas of 0.1% or more can be formed (the details are described later). Accordingly, in the method of producing the semiconductor laminate film  100 , even when the composition ratio of Ge is high, the semiconductor layer  20  can be grown so as to be lattice-matched with the silicon substrate  10 . Thus, the semiconductor laminate film  100  capable of producing a semiconductor device having satisfactory characteristics can be produced. 
     In the method of producing the semiconductor laminate film  100 , the sputtering gas may have a volume ratio of a hydrogen gas of 0.0001% or less. With this, in the method of producing the semiconductor laminate film  100 , the semiconductor layer  20  having a lattice mismatch rate f of 0% can be formed (the details are described later). 
     3. EXPERIMENTAL EXAMPLES 
     The invention is described in more detail by way of Experimental Examples below. The invention is by no means limited by the following Experimental Examples. 
     3.1. Production of Sample 
     A SiGe layer was formed on a Si substrate by a sputtering method with a device in which a vacuum reaction vessel (chamber) and a sample introduction vessel (chamber) were connected to each other through a vacuum valve. The vacuum reaction vessel is equipped with a magnetron sputtering gun for Si and a magnetron sputtering gun for Ge. 
     Specifically, first, the vacuum reaction vessel was evacuated to vacuum. More specifically, the vacuum valve was closed, and the vacuum reaction vessel was evacuated to 1×10 −9  Torr or less. Moreover, while the vacuum valve was closed, the Si substrate was placed in the sample introduction vessel. Next, the sample introduction vessel was evacuated to a vacuum of 1×10 −7  Torr or less with a turbomolecular pump and a rotary pump each connected to the sample introduction vessel. 
     Next, while the degree of vacuum in the sample introduction vessel was kept, the vacuum valve was opened, and the Si substrate was placed at a predetermined position of the vacuum reaction vessel. Next, the vacuum valve was closed, and the vacuum reaction vessel was evacuated to a pressure of 1×10 −9  Torr or less in an ultra-high vacuum region. In the vacuum reaction vessel at a pressure of 1×10 −9  Torr or less, the Si substrate placed at the predetermined position was cleaned by being heated to 800° C. or more with a heater. 
     Next, a sputtering gas was introduced into the vacuum reaction vessel, and the flow rate of the sputtering gas was adjusted so that the sputtering gas in the vacuum reaction vessel achieved a predetermined pressure. 
     Next, the temperature of the Si substrate was adjusted to a predetermined value with the heater. Next, a sputtering target was covered with a shutter, and sputtering was started by applying a high-frequency power to the sputtering gun for Si from a high-frequency power source and applying a direct-current power to a Ge target. In this stage, Si and Ge having flown from the sputtering target adhere to a back surface of the shutter, and do not reach a surface of the Si substrate. 
     Next, under the state in which the sputtering was performed, the shutter was opened so that the sputtering target was viewed from the surface of the Si substrate. Film formation is started when Si atoms and Ge atoms having been sputtered reach the Si substrate. The sputtering rates of Si and Ge, and the ratio (composition ratio) x of the number of Ge atoms to the sum of the number of Si atoms and the number of Ge atoms were controlled with the high-frequency power and the direct-current power in advance. Thus, the SiGe layer was formed on the Si substrate. 
     After the formation of the SiGe layer, the supply of the power to the sputtering guns was stopped, introduction of the sputtering gas was stopped, and the heating with the heater was stopped. The Si substrate having formed thereon the SiGe layer was taken out to a sample introduction vessel side by a reverse procedure to the procedure of its introduction into the vacuum reaction vessel. Specifically, while the pressure of the vacuum reaction vessel was kept at 1×10 −7  Torr or less, the Si substrate was transferred to the sample introduction vessel, and the vacuum valve was closed. After the vacuum valve was closed, the vacuum reaction vessel was evacuated to 1×10 −9  Torr or less with a vacuum pump connected to the vacuum reaction vessel, and the degree of vacuum was maintained. 
     By the above-mentioned procedures, a semiconductor laminate film of the SiGe layer formed on the Si substrate was produced. 
     3.2. Relationship Among Ratio of Hydrogen in Sputtering Gas, Film Formation Temperature, and Lattice Mismatch Rate 
     A SiGe (Si 0.7 Ge 0.3 ) layer was formed on a Si substrate by the method described in the section “3.1.” The thickness of the SiGe layer was set to 30 nm. The formation pressure of the SiGe layer was set to 3 mTorr. The SiGe layer was formed by using, as a sputtering gas, the following three kinds of gases: an Ar gas having a purity of 99.9999% (containing 0.0001% or less of a hydrogen gas etc.); a mixed gas of 99.9% of an Ar gas and 0.1% of a hydrogen gas; and a mixed gas of 95% of an Ar gas and 5% of a hydrogen gas (“%” represents a volume ratio), and setting the film formation temperature to 370° C., 400° C., 450° C., 500° C., and 560° C. 
     The lattice mismatch rate f of the SiGe layer formed as described above (the lattice mismatch rate f of the SiGe layer with respect to the Si substrate) was determined. The lattice constants of Si and SiGe were determined by a reciprocal lattice map based on X-ray diffraction in a (404) crystal orientation or a (224) crystal orientation, and the lattice mismatch rate f was determined by the above-mentioned equation (1).  FIG. 6  is a table for illustrating a relationship among the ratio (volume ratio) of hydrogen in the sputtering gas, the film formation temperature, and the lattice mismatch rate.  FIG. 7  is a chart obtained by plotting the values in the table of  FIG. 6 . 
     In  FIG. 6 , also the state of the SiGe layer is illustrated. The “crystalline” refers to a case in which a peak was observed in the X-ray diffraction, and the “amorphous” refers to a case in which a peak was not observed in the X-ray diffraction. In  FIG. 7 , the boundary between the “crystalline” and the “amorphous” is represented by the broken line. The state at a temperature higher than the broken line corresponds to the “crystalline”, and the state at a temperature lower than the broken line corresponds to the “amorphous”. 
     As illustrated in  FIG. 6  and  FIG. 7 , as the mixing ratio of the hydrogen gas became smaller, the lattice mismatch rate f became lower. When the ratio of the hydrogen gas was 5%, the lattice mismatch rate f exceeded 0.3%, however, when the ratio of the hydrogen gas was 0.1%, the lattice mismatch rate f was less than 0.3%. In the case where the ratio of the hydrogen gas was 0.1%, the result was obtained that, when the temperature exceeded 500° C. and approached 600° C., the lattice mismatch rate f was drastically reduced and nearly lattice matching conditions were achieved. This is presumably because hydrogen is desorbed from the SiGe layer at high temperature, and lattice matching is easily achieved. Further, when the ratio of the hydrogen gas was 0.0001% or less, the lattice mismatch rate f was 0%. 
     3.3. Relationship Among Film Formation Pressure, Film Formation Temperature, and Lattice Mismatch Rate 
     A SiGe (Si 0.77 Ge 0.23 ) layer was formed on a Si substrate by the method described in the section “3.1.” The thickness of the SiGe layer was set to 273 nm. As a sputtering gas, an Ar gas having a purity of 99.9999% (containing 99.9999% of an Ar gas and 0.0001% or less of a hydrogen gas etc.) was used. The film formation pressure was set to 1.2 mTorr, 2 mTorr, 3.5 mTorr, 5 mTorr, 7 mTorr, and 10 mTorr. The film formation temperature was set to 400° C., 450° C., 500° C., and 600° C. In this experiment, the conditions were set to the above-mentioned film formation temperature range in view of general applications of the film formation temperature because the activation rate of impurities decreased in a film formation temperature range of less than 350° C., and the surface flatness decreased in a film formation temperature range of more than 600° C. 
     The lattice mismatch rate f of the SiGe layer formed as described above was determined.  FIG. 8  is a table for illustrating a relationship among the film formation pressure, the film formation temperature, and the lattice mismatch rate f.  FIG. 9  is a chart obtained by plotting the values in the table of  FIG. 8 . 
     As illustrated in  FIG. 8  and  FIG. 9 , when the film formation temperature was less than 500° C. and the film formation pressure ranged from 1 mTorr to 11 mTorr, the lattice mismatch rate f was almost 0% (under the first conditions described above). In addition, when the film formation temperature was less than 600° C. and the film formation pressure ranged from 2 mTorr to 5 mTorr, the lattice mismatch rate f was almost 0% (under the second conditions described above). Further, when the film formation temperature ranged from 400° C. to 500° C. and the film formation pressure ranged from 2 mTorr to 4 mTorr, the lattice mismatch rate f was 0%. 
     As described above, from  FIG. 6  to  FIG. 9 , it was revealed that, when the film formation temperature was set to less than 500° C., the film formation pressure was set to range from 1 mTorr to 11 mTorr, and the volume ratio of a hydrogen gas in the sputtering gas was set to less than 0.1%, the SiGe layer having large compressive strain as compared to a case in which the volume ratio of a hydrogen gas in the sputtering gas was set to, for example, 0.1% or more was able to be formed. In addition, it was revealed that, when the film formation temperature was set to less than 600° C., the film formation pressure was set to equal to or more than 2 mTorr and less than 5 mTorr, and the volume ratio of a hydrogen gas in the sputtering gas was set to less than 0.1%, the SiGe layer having large compressive strain as compared to a case in which the volume ratio of a hydrogen gas in the sputtering gas was set to, for example, more than 0.1% was able to be formed. 
     3.4. Relationship Among Composition Ratio of Ge, Thickness, and Lattice Mismatch Rate 
     A Si 1-x Ge x  layer was formed on a Si substrate by the method described in the section “3.1.” As a sputtering gas, an Ar gas having a purity of 99.9999% (containing 99.9999% of an Ar gas and 0.0001% or less of a hydrogen gas etc.) was used. The film formation temperature was set to 400° C., and the film formation pressure was set to 3.5 mTorr. In each of the cases in which the thickness t of the Si 1-x Ge x  layer was set to 50 nm, 125 nm, and 280 nm, the composition ratio x of Ge in the Si 1-x Ge x  layer which grew so as to be lattice-matched with the Si substrate was determined. 
     The lattice mismatch rate f of the Si 1-x Ge x  layer formed as described above was determined.  FIG. 10  is a table for illustrating a relationship among the composition ratio of Ge, the thickness, and the lattice mismatch rate f.  FIG. 11  is a chart obtained by plotting the values in the table of  FIG. 10 . 
     In  FIG. 10 , the results of a Si 1-x Ge x  layer (74 nm) formed on a Si substrate by a CVD method were also illustrated as Comparative Example. In addition,  FIG. 12  is a chart obtained by plotting the values in the case of a CVD method in the table of  FIG. 10 . 
     As illustrated in  FIG. 10  and  FIG. 11 , as the composition ratio x of Ge became smaller, the lattice mismatch rate f became lower. Further, as the thickness t (nm) became smaller, the lattice mismatch rate f was able to be reduced more even when the composition ratio x of Ge was increased. From  FIG. 10  and  FIG. 11 , it is considered that border composition ratios x of Ge below which the lattice mismatch rate f can be sufficiently reduced to almost 0% are 0.43, 0.355, and 0.3 at the thicknesses t of 50 nm, 125 nm, and 280 nm, respectively. When the three points (50, 0.43), (125, 0.355), and (280, 0.3) were plotted as in  FIG. 13 , the following equation (4) of a line passing through the three points was able to be obtained. The maximum thickness t (nm) at which lattice matching is achieved is plotted on the ordinate of  FIG. 13 . 
         t= 0.881× x   −4.79   (4)
 
     Accordingly, it was revealed that the lattice mismatch rate f was able to be reduced to 0% when the expression t&lt;0.881×x −4.79  was satisfied. The correlation coefficient R of the equation (4) was almost 1. 
     In addition, as illustrated in  FIG. 11  and  FIG. 12 , it was revealed that, even when the composition ratio x of Ge was increased, the lattice mismatch rate f was able to be reduced more in the case of formation of the Si 1-x Ge x  layer by the method described in the section “3.1.” than in the case of formation of the Si 1-x Ge x  layer by a CVD method. 
     3.5. Relationship Among Composition Ratio of Ge, Thickness, and Surface Roughness 
     A Si 1-x Ge x  layer formed by the method described in the section “3.4.” was measured for a surface roughness Rms (root mean square surface roughness) with an AFM.  FIG. 14  is a table for illustrating a relationship among the composition ratio of Ge, the thickness, and the surface roughness.  FIG. 15  is a chart obtained by plotting the values in the case of a sputtering method illustrated in the table of  FIG. 14 .  FIG. 16  is a chart obtained by plotting the values in the case of a CVD method illustrated in the table of  FIG. 14 . 
     As illustrated in  FIG. 14  and  FIG. 15 , as the composition ratio x of Ge became larger, the surface roughness Rms became larger. Further, as the thickness t became larger, the surface roughness Rms became larger. 
     In addition, as illustrated in  FIG. 15  and  FIG. 16 , it was revealed that, even when the composition ratio x of Ge was increased, the surface roughness Rms was able to be reduced more in the case of formation of the Si 1-x Ge x  layer by the method described in the section “3.1.” than in the case of formation of the Si 1-x Ge x  layer by a CVD method. 
     4. SEMICONDUCTOR DEVICE INCLUDING SEMICONDUCTOR LAMINATE FILM 
     Next, a semiconductor device including the semiconductor laminate film according to the invention is described. A semiconductor device including the above-mentioned semiconductor laminate film  100  as the semiconductor laminate film according to the invention is described below. 
     4.1. First Semiconductor Device 
       FIG. 17  is a sectional view for schematically illustrating a first semiconductor device  210  according to an embodiment of the invention. The first semiconductor device  210  is a HEMT using holes as carriers (p-HEMT or a high hole mobility transistor (HHMT)). As illustrated in  FIG. 17 , the first semiconductor device  210  includes: a silicon substrate  10 ; a semiconductor layer  20 ; a Si spacer layer  211 ; a Si supply layer  212 ; a Si spacer layer  213 ; a Si cap layer  214 ; a gate electrode  215 ; a source electrode  216 ; and a drain electrode  217 . 
     The silicon substrate  10  includes: a n-type (100) Si substrate  10   a ; and an i-type Si layer  10   b  arranged on the Si substrate  10   a . The Si substrate  10   a  may be a monocrystalline substrate. The silicon substrate  10  may be a silicon on insulator (SOI) substrate, in which a monocrystalline silicon thin film is formed on an insulator, or a silicon on quartz (SOQ) substrate. The Si layer  10   b  has a thickness of, for example, about 40 nm. 
     The semiconductor layer  20  is arranged on the silicon substrate  10 . The semiconductor layer  20  is of an i type. The semiconductor layer  20  has a thickness of, for example, about 10 nm. The semiconductor layer  20  is a channel layer using holes as carriers. 
     The Si spacer layer  211  is arranged on the semiconductor layer  20 . The Si spacer layer  211  is of an i type. The Si spacer layer  211  has a thickness of, for example, 1 nm or more and 10 nm or less. 
     The Si supply layer  212  is arranged on the Si spacer layer  211 . The Si supply layer  212  is of a p type. The Si supply layer  212  has a thickness of, for example, 1 nm or more and 10 nm or less. The Si supply layer  212  is configured to supply a carrier (hole) to the semiconductor layer  20 . 
     The Si spacer layer  213  is arranged on the Si supply layer  212 . The Si spacer layer  213  is of an i type. The Si spacer layer  213  has a thickness of, for example, 1 nm or more and 10 nm or less. The gate electrode  215  is arranged on the Si spacer layer  213 . 
     The Si cap layer  214  is arranged on the Si spacer layer  213 . The Si cap layer  214  is of a p type. The Si cap layer  214  has a thickness of, for example, 5 nm or more and 50 nm or less. The source electrode  216  and the drain electrode  217  are arranged on the Si cap layer  214 . Further, a SiO 2  layer, a SiN layer, an insulating resist layer, or the like is arranged as a protective layer  218  on the Si cap layer  214 . The protective layer  218  may not be arranged. 
     The first semiconductor device  210  includes the semiconductor layer  20 . As described above, even when the semiconductor layer  20  has a sufficiently large composition ratio x of Ge with respect to its thickness, the semiconductor layer  20  can be reduced in lattice mismatch rate f and thus can have large compressive strain. Here, in the HEMT using holes as carriers, as the composition ratio x of Ge is increased more, the compressive strain can be increased more, and a carrier mobility can be increased more. Accordingly, in the first semiconductor device  210 , an increase in carrier mobility can be achieved, and thus an increase in speed can be achieved by increasing the composition ratio x of Ge and increasing the compressive strain. In addition, the semiconductor layer  20  does not include a dopant atom, and a hole carrier does not suffer from impurities scattering, with the result that a reduction in carrier mobility does not occur. The hole carrier configured to impart electrical conductivity to the semiconductor layer  20  is supplied from the Si supply layer  212 . 
     4.2. Second Semiconductor Device 
       FIG. 18  is a sectional view for schematically illustrating a second semiconductor device  220  according to an embodiment of the invention. The second semiconductor device  220  is a doped channel field effect transistor (DCFET) using holes as carriers (p-DCFET). As illustrated in  FIG. 18 , the second semiconductor device  220  includes: a silicon substrate  10 ; a semiconductor layer  20 ; a Si cap layer  221 ; a gate electrode  222 ; a source electrode  223 ; and a drain electrode  224 . 
     The silicon substrate  10  includes: a n-type (100) Si substrate  10   a ; and an i-type Si layer  10   b  arranged on the Si substrate  10   a . The Si substrate  10   a  may be a monocrystalline substrate. The silicon substrate  10  may be a silicon on insulator (SOI) substrate, in which a monocrystalline silicon thin film is formed on an insulator, or a silicon on quartz (SOQ) substrate. The Si layer  10   b  has a thickness of, for example, 10 nm or more and 100 nm or less. 
     The semiconductor layer  20  is arranged on the silicon substrate  10 . The semiconductor layer  20  is of a p type. The semiconductor layer  20  has a thickness of, for example, 10 nm or more and 100 nm or less. The semiconductor layer  20  is a channel layer using holes as carriers. The source electrode  223  and the drain electrode  224  are arranged on the semiconductor layer  20 . 
     The Si cap layer  221  is arranged on the semiconductor layer  20 . The Si cap layer  221  is of an i type. The Si cap layer  221  has a thickness of, for example, 10 nm or more and 100 nm or less. The gate electrode  222  is arranged on the Si cap layer  214 . 
     The second semiconductor device  220  includes the semiconductor layer  20 . As described above, even when the semiconductor layer  20  has a sufficiently large composition ratio x of Ge with respect to its thickness, the semiconductor layer  20  can be reduced in lattice mismatch rate f and thus can have large compressive strain. Here, in the DCFET using holes as carriers, as the composition ratio x of Ge is increased more, the compressive strain is increased more, and a hole mobility is increased more. Accordingly, in the second semiconductor device  220 , a further increase in speed can be achieved by increasing the composition ratio x of Ge and increasing the compressive strain. 
     4.3. Third Semiconductor Device 
       FIG. 19  is a sectional view for schematically illustrating a third semiconductor device  230  according to an embodiment of the invention. The third semiconductor device  230  is a hole tunneling resonant tunneling diode (RTD) (p-RTD). The third semiconductor device  230  includes: a silicon substrate  10 ; a semiconductor layer  20 ; a Si layer  231 ; a Si layer  232 ; an electrode layer  233  formed of, for example, Al; and an electrode layer  234  formed of, for example, Al. The third semiconductor device  230  includes four SiGe semiconductor layers  20   a ,  20   b ,  20   c , and  20   d.    
     The silicon substrate  10  includes: a p-type (100) Si substrate  10   a ; and a p-type Si layer  10   b  arranged on the Si substrate  10   a . The Si substrate  10   a  may be a monocrystalline substrate. The silicon substrate  10  may be a silicon on insulator (SOI) substrate, in which a monocrystalline silicon thin film is formed on an insulator, or a silicon on quartz (SOQ) substrate. The Si layer  10   b  has a thickness of, for example, 10 nm or more and 100 nm or less. The electrode layer  233  is arranged on the Si substrate  10   a . The electrode layer  233  is one of electrodes of the third semiconductor device  230 . 
     The semiconductor layer  20   a  is arranged on the silicon substrate  10 . The SiGe semiconductor layers  20   a ,  20   b ,  20   c , and  20   d  are laminated in the stated order, and the Si layers  231  are arranged between the semiconductor layers  20   a ,  20   b ,  20   c , and  20   d . The semiconductor layers  20   a ,  20   b ,  20   c , and  20   d  are each formed of i-type SiGe. The semiconductor layers  20   a  and  20   d  each have a thickness of, for example, 10 nm or more and 100 nm or less. The semiconductor layers  20   b  and  20   c  each have a thickness of, for example, 1 nm or more and 6 nm or less. The Si layers  231  are each of an i type. The Si layers  231  each have a thickness of, for example, 1 nm or more and 3 nm or less. The semiconductor layers  20   b  and  20   c  are each a quantum well layer, and the Si layers  231  are each a barrier layer. 
     The Si layer  232  is arranged on the semiconductor layer  20   d . The Si layer  232  is of a p type. The Si layer  232  has a thickness of, for example, 10 nm or more and 100 nm or less. The electrode layer  234  formed of, for example, Al is arranged on the Si layer  232 . The electrode layer  234  is the other one of the electrodes of the third semiconductor device  230 . 
     The third semiconductor device  230  includes the semiconductor layer  20 . As described above, even when the semiconductor layer  20  has a sufficiently large composition ratio x of Ge with respect to its thickness, the semiconductor layer  20  can have large compressive strain. Here, in the hole tunneling RTD, as the composition ratio x of Ge is increased more and the compressive strain is increased more, a deep potential well is formed more easily, and a larger resonant current is obtained, with the result that an operation speed is increased more. Accordingly, in the third semiconductor device  230 , a further increase in speed can be achieved by increasing the composition ratio x of Ge and increasing the compressive strain. 
     4.4. Fourth Semiconductor Device 
       FIG. 20  is a sectional view for schematically illustrating a fourth semiconductor device  240  according to an embodiment of the invention. The fourth semiconductor device  240  is a npn-type hetero-bipolar transistor (HBT). As illustrated in  FIG. 20 , the fourth semiconductor device  240  includes: a silicon substrate  10 ; a semiconductor layer  20 ; a Si layer  241 ; a collector electrode  242 ; a base electrode  243 ; and an emitter electrode  244 . 
     The silicon substrate  10  is a n-type (100) Si substrate. The silicon substrate  10  corresponds to a collector region. A n-type Si layer may be arranged on the silicon substrate  10 . The collector electrode  242  is arranged on the silicon substrate  10 . The silicon substrate  10  may be a monocrystalline substrate. The silicon substrate  10  may be a silicon on insulator (SOI) substrate, in which a n-type monocrystalline silicon thin film is formed on an insulator, or a silicon on quartz (SOQ) substrate. Alternatively, the silicon substrate  10  may be a SOI substrate or a SOQ substrate having formed thereon a n-type Si layer. 
     The semiconductor layer  20  is arranged on the silicon substrate  10 . The semiconductor layer  20  corresponds to a base region. The composition ratio x of Ge in the semiconductor layer  20  may vary in a direction perpendicular to a surface of the substrate. The semiconductor layer  20  is of a p type. The semiconductor layer  20  has a thickness of, for example, 30 nm or more and 200 nm or less. The base electrode  243  is arranged on the semiconductor layer  20 . 
     The Si layer  241  is arranged on the semiconductor layer  20 . The Si layer  241  is of a n type. The Si layer  241  corresponds to an emitter region. The Si layer  241  has a thickness of, for example, 20 nm or more and 100 nm or less. The emitter electrode  244  is arranged on the Si layer  241 . 
     The fourth semiconductor device  240  includes the semiconductor layer  20 . As described above, even when the semiconductor layer  20  has a large composition ratio x of Ge, the semiconductor layer  20  can be lattice-matched or substantially lattice-matched with the silicon substrate  10  or the n-type silicon layer arranged on the silicon substrate. In the npn-type HBT, as the composition ratio x of Ge is increased more, a larger potential barrier is formed for a hole in a valence band at a boundary between the emitter region and the base region, and a current amplification factor can be increased more. Accordingly, in the fourth semiconductor device  240 , an increase in current amplification factor can be achieved, and a further increase in speed can be achieved by increasing the composition ratio x of Ge and increasing the compressive strain. 
     The use of the semiconductor laminate film  100  is not limited to the semiconductor devices described above. For example, the semiconductor laminate film  100  may be used for a MOSFET with a strained SiGe channel using holes as carriers (strained-SiGe-channel p-MOSFET), or a MOSFET with a buried-SiGe-channel using holes as carriers (buried-channel p-MOSFET). For example, the buried-channel p-MOSFET can be realized by replacing the Si cap layer  221  of the second semiconductor device  220  with the following two layers laminated on each other: an i-type Si spacer layer; and an insulating layer, such as a SiO 2  layer. In this case, the i-type Si spacer layer is arranged on the lower side of the two layers. 
     According to the above-mentioned technology for forming the semiconductor layer according to the invention, the semiconductor laminate film including the SiGe layer which has a low lattice mismatch rate, and is substantially lattice-matched or lattice-matched with the Si substrate, and which has a large composition ratio of Ge can be produced. Utilization of a semiconductor device using the technology for the semiconductor laminate film according to the invention is expected to contribute to an increase in performance and a reduction in cost of an electronic device component for millimeter waveband applications. The semiconductor device is expected to significantly contribute to advancement of, for example, wireless communication or a radar in a millimeter waveband, object image detection, and a non-invasive and non-destructive test as an electronic device technology serving as a foundation for high-frequency electronics and measurement sensing technologies in the future in industrial technical fields related to sensor networks, artificial intelligence (AI), internet of things (IoT), and the like. The semiconductor laminate film according to the invention is particularly effective for an increase in performance of a p-type channel transistor, which is inferior in performance of an operation speed to a n-type channel transistor, and also enables a remarkable reduction in power consumption by achieving a high-frequency amplifier with a complementary configuration. 
     The invention includes configurations that are substantially the same (for example, in function, method, and results, or in objective and effects) as the configurations described in the embodiments. The invention also includes configurations in which non-essential elements described in the embodiments are replaced by other elements. The invention also includes configurations having the same effects as those of the configurations described in the embodiments, or configurations capable of achieving the same objectives as those of the configurations described in the embodiments. The invention further includes configurations obtained by adding known art to the configurations described in the embodiments.