Patent Publication Number: US-2023136090-A1

Title: Optical waveguide, method for manufacturing optical waveguide, and optical semiconductor device

Description:
CROSS-REFERENCE TO RELATED APPLICATIONS 
     This patent application is a national phase filing under section 371 of PCT application no. PCT/JP2020/014859, filed on Mar. 31, 2020, which is incorporated herein by reference in its entirety. 
    
    
     TECHNICAL FIELD 
     The present invention relates to an optical waveguide, a method for manufacturing an optical waveguide and an optical semiconductor device that enable curbing light loss. 
     BACKGROUND 
     Semiconductor optical devices in which a light emission region including a quantum well structure (active region) and a region in which light released from the light emission region is guided (including modulation, reflection, etc.) (passive region) are integrated on the same semiconductor substrate have been used as light sources for, e.g., high-speed optical fiber communications or gas sensors each using an absorption line of a molecule. 
     In a case where the active region and the passive region are formed on the same semiconductor substrate in this way, it is necessary that light generated in the active region propagates through the passive region without being absorbed, and thus, in general, the passive region is formed using a material having a bandgap that is larger than that of the active region. 
     In order to form such materials having different bandgaps on the same substrate, an epitaxial growth technique called “butt-joint regrowth” is used. In butt-joint regrowth, materials having different bandgaps can be formed in a surface of the same substrate by forming an active region on the entire surface of the substrate, then removing a part of the active region, the part to be a passive region, and selectively epitaxially growing a material having a different bandgap to be the passive region in the part where the active region is removed. 
     Butt-joint regrowth enables forming arbitrary different materials in an active region and a passive region and thus has the advantage of a high degree of freedom in selection of materials. However, in addition to the necessity to perform semiconductor etching and epitaxial regrowth requiring a high level of expertise, the difference in material (e.g., a composition and a lattice constant of a crystal) between the active region and the passive region easily causes crystal defects or abnormal growth (e.g., failure in forming a layer). Furthermore, from the perspective of light propagation, in order for light to propagate from the active region to the passive region without loss (reflection and coupling loss), it is necessary to control respective film thicknesses and compositions of the materials in the regions with high accuracy. 
     Also, in order to form materials having different bandgaps on the same substrate, it is possible to use a method in which a part of an active region including a quantum well structure, the active region being formed in an entire surface, and the part to be a passive region, is subjected to quantum well disordering (for example, Non-Patent Literature 1). This method utilizes introduction of an impurity or the like to a quantum well structure via, e.g., diffusion or ion implantation, causing a change in composition between a quantum well layer and a barrier layer forming the quantum well structure (quantum well disordering) and thereby causing the quantum well layer and the barrier layer to turn into a bulk semiconductor layer having an average composition. In comparison with the quantum well structure, the bulk semiconductor layer resulting from the disordering of the quantum well structure has a large bandgap and thus can be used as a passive layer. 
     With this method, in comparison with butt-joint regrowth, a passive region is formed from an active region in the same layer structure, enabling curbing occurrence of, e.g., crystal defects at a boundary between the active region and the passive region and eliminating the need for controlling respective film thicknesses and compositions of materials of the regions. As a result, the active region and the passive region can be formed with high quality. 
     CITATION LIST 
     Non-Patent Literature 
     
         
         Non-Patent Literature 1: J. H. Marsh, “Quantum well intermixing”, Semiconductor Science and Technology, vol. 8, p. 1136, 1993. 
       
    
     SUMMARY 
     Technical Problem 
     However, in butt-joint growth and quantum well disordering, a passive region having a large bandgap (small refractive index) in comparison with an active region is formed and thus discontinuity in refractive index (refractive index difference) occurs at a boundary between the active region and the passive region. This refractive index difference causes propagating light guided between the active region and the passive region to be reflected or to leak from the waveguide at the boundary. As a result, as illustrated in  FIG.  16   , loss corresponding to the refractive index difference occurs. 
     In the case of, for example, a semiconductor laser, light returning to the active region via reflection (return light) affects a phase condition for laser oscillation and causes, e.g., an increase in line width or mode skipping. Also, light leaked from the waveguide causes a decrease in laser light output. In this way, there is the problem of discontinuity in refractive index (bandgap) at the boundary between the active region and the passive region causing deterioration in a characteristic of the optical device. 
     In order to solve the above problem, an object of embodiments of the present invention is to provide an optical waveguide and an optical semiconductor device that enables curbing reflected light or leaked light from a boundary between an active region and a passive region without a decrease in efficiency of coupling of propagating light between the active region and the passive region and with excellent characteristics. 
     Means for Solving the Problem 
     In order to solve the aforementioned problem, an optical waveguide according to embodiments of the present invention is an optical waveguide including a semiconductor quantum well structure, the optical waveguide including: a first region in which the semiconductor quantum well structure is not disordered; and a second region in which the semiconductor quantum well structure is disordered, wherein the first region has a first bandgap wavelength, the second region has a second bandgap wavelength, and a third region in which the semiconductor quantum well structure is disordered in such a manner that a bandgap wavelength continuously decreases from the first bandgap wavelength to the second bandgap wavelength is provided between the first region and the second region. 
     Also, a method for manufacturing an optical waveguide according to embodiments of the present invention is a method for manufacturing an optical waveguide including a semiconductor quantum well structure, the optical waveguide including a first region in which the semiconductor quantum well structure is not disordered and a second region in which the semiconductor quantum well structure is disordered, the method including: a step of forming a selective growth mask and an opening portion in the first region and a region between the first region and the second region in a surface of a crystal including the semiconductor quantum well structure; a step of selectively growing a semiconductor crystal in the opening portion; a step of removing the selective growth mask; a step of forming an annealing mask in the second region and the region between the first region and the second region; a step of annealing the crystal with the annealing mask formed thereon; and a step of removing the annealing mask, wherein a ratio between a width of the selective growth mask and a width of the opening portion varies in the region between the first region and the second region. 
     Effects of Embodiments of the Invention 
     Embodiments of the present invention enable provision of an optical waveguide and an optical semiconductor device that enable curbing loss of propagating light and that have excellent characteristics. 
    
    
     
       BRIEF DESCRIPTION OF THE DRAWINGS 
         FIG.  1    is a sectional view of an optical waveguide according to a first embodiment of the present invention. 
         FIG.  2    is a diagram indicating bandgap wavelength variation in a wave-guiding direction of the optical waveguide according to the first embodiment of the present invention. 
         FIG.  3    is a sectional view of a crystal used for manufacturing the optical waveguide according to the first embodiment of the present invention. 
         FIG.  4    is a top view of the crystal with SiO 2  selective growth masks formed thereon in the first embodiment of the present invention. 
         FIG.  5    is a sectional view taken along line V-V′ of  FIG.  4    illustrating the crystal with the SiO 2  selective growth masks formed thereon in the first embodiment of the present invention. 
         FIG.  6    is a diagram indicating dependency of a growth speed of an InP selectively grown layer on a width (Ws) of each SiO 2  selective growth mask in the first embodiment of the present invention. 
         FIG.  7    is a top view of the crystal subjected to selective growth in the first embodiment of the present invention. 
         FIG.  8    is a sectional view taken along line VIII-VIII′ of  FIG.  7    illustrating the crystal subjected to selective growth in the first embodiment of the present invention. 
         FIG.  9    is a sectional view of the crystal with a SiO 2  annealing mask formed in the first embodiment of the present invention. 
         FIG.  10    is a diagram indicating a relationship between a thickness of an InP layer above a quantum well structure and an amount of wavelength variation in quantum well disordering in the first embodiment of the present invention. 
         FIG.  11    is a sectional view of the crystal in which the quantum well structure is disordered in the first embodiment of the present invention. 
         FIG.  12    is a diagram indicating variation in bandgap wavelength of the crystal in which the quantum well structure is disordered in the first embodiment of the present invention. 
         FIG.  13    is a sectional view of a crystal with a SiO 2  annealing mask formed thereon in a second embodiment of the present invention. 
         FIG.  14    is a diagram indicating variation in bandgap wavelength of the crystal in which a quantum well structure is disordered in the second embodiment of the present invention. 
         FIG.  15    is a diagram of an outer appearance of a distributed Bragg reflector laser according to a third embodiment of the present invention. 
         FIG.  16    is a diagram indicating a relationship between a refractive index difference between an active region and a passive region and coupling efficiency. 
     
    
    
     DETAILED DESCRIPTION OF ILLUSTRATIVE EMBODIMENTS 
     First Embodiment 
     A first embodiment of the present invention will be described with reference to the drawings.  FIG.  1    is a sectional view of an optical waveguide  10  according to the present embodiment.  FIG.  2    indicates bandgap wavelength variation in a wave guiding direction of the optical waveguide  10  according to the present embodiment. The wave guiding direction is indicated by arrow X in the figures. 
     In the optical waveguide  10  according to the present embodiment, a light propagation layer formed of a quantum well structure in interposed between cladding layers  102  formed of a material that is the same as that of a substrate  101  is formed on the substrate  101 . An active region no has the quantum well structure iii that is not disordered and a passive region  130  has a quantum well structure  131 , all of which is disordered. An intermediate region  120  has a quantum well structure  121  disordered in such a manner that a bandgap wavelength continuously varies from a bandgap wavelength of the active region no to a bandgap wavelength of the passive region  130 . 
     Here, a bandgap wavelength λg refers to a wavelength corresponding to a bandgap Eg and has the below relationship. 
       λ g (μ m )=1.24/ Eg ( eV )
 
     A bandgap wavelength can be approximated by a peak wavelength of PL light emission, the peak wavelength being obtained by photoluminescence (hereinafter referred to as “PL”) measurement, and can easily be evaluated, and thus, the below description is provided with a peak wavelength of PL light emission as a bandgap wavelength. 
     In the present embodiment, MOVPE using a reacting furnace with a pressure reduced to 50 Torr is used for crystal growth. For a group-III raw material, trimethylindium (TMIn) or triethylgallium (TEGa) is used, and for a group-V raw material, phosphine (PH 3 ) or arsine (AsH 3 ) is used. For a raw material of Zn, which functions as a p-type impurity, diethylzinc (DEZn) is used and for a raw material of Si, which functions as an n-type impurity, monosilane (SiH 4 ) is used. 
     For evaluation of structural characteristics of a grown crystal, an X-ray diffraction device manufactured by Philips is used. For evaluation of optical characteristics, PL measurement using a laser having a wavelength of 532 nm as a light source is performed at room temperature (25° C.). 
       FIG.  3    is a sectional view of a crystal  100  used for manufacturing the waveguide according to the present embodiment. An n-type InP cladding layer  102  (film thickness: 500 nm) with Si doped at a concentration of 1×10 18  cm 3 , a non-doped InGaAsP optical confinement layer (film thickness: 100 nm)  103  having a bandgap wavelength of 1.3 μm, an InAs/InGaAs multi-quantum well structure (MQW)  111  consisting of six InAs well layers (film thickness: 5 nm) and seven InGaAs barrier layers (film thickness: 20 nm), a non-doped InGaAsP optical confinement layer (film thickness: 100 nm)  104  having a bandgap wavelength of 1.3 μm, a non-doped InGaAsP optical confinement layer (film thickness: 100 nm)  105  having a bandgap wavelength of 1.1 μm, and a p-type InP capping layer  106  (film thickness: 50 nm) with Zn doped at a concentration of 5×10 17  cm 3  are sequentially stacked on an n-type InP substrate  101 . 
     An intermediate region  120  and a passive region  130  are formed by the crystal  100  being subjected to quantum well disordering. In usual quantum well disordering, when impurity diffusion or ion implantation, which induces quantum well disordering, is performed, a SiO 2  film is formed only on a surface of the active region no. As a result, in the active region no, the quantum well is not disordered, and in a region in which the SiO 2  film is not formed, the quantum well structure  111  is disordered and becomes a passive region  130 . Therefore, no region (intermediate region  120 ) having a bandgap wavelength between those of the active region  110  and the passive region  130  can be formed. 
     In the present embodiment, the intermediate region  120  whose bandgap wavelength varies between those of the active region no and the passive region  130  is formed by controlling crystal defect diffusion, which induces quantum well disordering, using an InP layer formed by selective growth. The details will be described below. 
     First, SiO 2  selective growth masks  141  are formed on a surface of the crystal.  FIGS.  4  and  5    are a top view of the crystal with the SiO 2  masks  141  formed thereon, the SiO 2  masks  141  being used for quantum well disordering, in the present embodiment and is a sectional view along line V-V′ in  FIG.  4   , respectively. The SiO 2  masks  141  are formed by stacking a SiO 2  film on the surface of the crystal using a usual method and processing the SiO 2  film using photolithography. 
     A width Ws of each SiO 2  mask  141  is 250 μm in the active region no and is continuously varied from 250 μm to 10 μm in the intermediate region  120 . On the other hand, no mask is formed in the passive region  130 . Also, a length of the intermediate region  120  (distance between the active region no and the passive region  130 ) is 20 μm. 
     A width (Wg) of a region (hereinafter referred to as “opening portion”)  142  interposed between the SiO 2  masks  141  is 40 μm. 
     Next, a p-type InP layer with Zn doped at a concentration of 5×10 17  cm 3  is selectively grown in the opening portion  142  on the crystal surface with the SiO 2  masks  141  formed thereon. In this selective growth, InP is grown only in the opening portion  142 . 
     Here, the doping concentration of Zn is not limited to 5×10 17  cm 3  and may be another concentration. Also, an n-type InP layer may be selectively grown by doping e.g., Si or Se other than Zn or a non-doped InP layer may be selectively grown. 
       FIG.  6    indicates dependency of a growth speed of the InP selectively grown layer on the width (Ws) of the SiO 2  masks  141 . In selective growth of InP, raw material species obtained by, e.g., decomposition of a raw material gas, the raw material species coming onto the SiO 2  masks  141 , migrates on the SiO 2  masks  141  and contributes to the growth of InP in the opening portion  142 . 
     As a result, an epitaxial growth speed of InP selectively grown in the opening portion  142  increases in comparison with a case of crystal growth on a surface with no SiO 2  mask  141 . Therefore, the growth speed of the selective growth of InP increases along with an increase in width (Wm) of the SiO 2  masks  141 . 
       FIGS.  7  and  8    are a top view of the crystal subjected to the selective growth and a sectional view along line VIII-VIII′ in  FIG.  7   , respectively. Thicknesses of an InP layer  151  selectively grown in the active region  110 , the intermediate region  120 , and the passive region  130  are 250 nm, 250 to 50 nm, and 50 nm, respectively. Here, the thickness of the InP layer  151  in the intermediate region  120  continuously decreases from one end on the active region  110  side to the other end on the passive region  130  side. 
     Next, after removal of the SiO 2  selective growth masks  141  used for the selective growth, a SiO 2  film (thickness: 300 nm) for annealing is formed on the entire crystal surface via sputtering. 
     Next, a SiO 2  annealing mask  161  is formed by removing a part of the SiO 2  film, the part being in a region not to be subjected to quantum well disordering (active region  110 ).  FIG.  9    is a sectional view of the crystal with the SiO 2  annealing mask  161  formed thereon. 
     Next, this crystal is subjected to ten-minute thermal treatment (rapid thermal annealing, which is hereinafter referred to as “RTA”) at 550° C. under a nitrogen atmosphere. 
     Through the above process, quantum well structure disordering is performed in the regions provided with the SiO 2  annealing mask  161 . Quantum well disordering is considered to occur due to crystal defects, such as vacant lattice points or interstitial atoms, occurring at an interface between the SiO 2  annealing mask  161  and the p-type InP capping layer  106  due to the RTA diffusing from the interface to the multi-quantum well structure (MQW)  111 . 
       FIG.  10    illustrates a relationship between a layer thickness of the InP (corresponding to the InP capping layer  106  and the InP selectively grown layer  151 ) above the quantum well structure in and an amount of variation in bandgap wavelength due to quantum well disordering. In this way, the amount of wavelength variation due to quantum well disordering depends on the thickness of the InP layer above the quantum well structure in, and when the InP layer is thin, the wavelength variation amount is large, and when the InP layer is thick, the wavelength variation amount is small. 
     A reason for the above is as follows. When the InP layer is thin, there are many lattice defects occurring at the aforementioned interface and diffusing, and reaching the MQW  111 . As a result, the effect of quantum well disordering due to the lattice defects is large, and thus, the wavelength variation amount is large. 
     On the other hand, when the InP layer is thick, there are few lattice defects reaching the MQW  111 . As a result, the effect of quantum well disordering due to the lattice defects is small, and thus, the wavelength variation amount is small. 
       FIGS.  11  and  12    illustrate a section of the crystal with the quantum well structure  111  disordered and variation in bandgap wavelength, respectively. The bandgap wavelength of the active region  110  is constantly 2350 nm and the bandgap wavelength of the passive region  130  is constantly 2100 nm. 
     On the other hand, the bandgap wavelength of the intermediate region  120  decreases from 2300 nm at the one end on the active region  110  side (B in the graph) to 2100 nm at the other end on the passive region  130  side (C in the graph). In this way, the bandgap wavelength of the intermediate region  120  can continuously be varied in the direction from the active region no toward the passive region  130 . 
     Here, a bandgap wavelength discontinuity part occurs at a boundary between the active region no and the intermediate region  120 ; however, such bandgap wavelength discontinuity is around one fifth of the wavelength variation amount in the passive region  130  and thus light loss caused by this discontinuity part can be ignored. 
     In the optical waveguide according to the present embodiment, the InAs/InGaAs multi-quantum well structure (MQW)  111  including InAs well layers and seven InGaAs barrier layers is used. 
     In a case where an optical waveguide is formed in the MQW  111  via conventional butt-joint growth, a growth surface (side surface) of the MQW is exposed to a PH 3  atmosphere, which is a growth gas, at a high temperature immediately before a start of crystal growth. At this time, the MQW  111  contains only As as a group-V material, and thus, crystal quality may deteriorate because of, e.g., replacement of As in the InAs/InGaAs growth surface and P in PH 3  with each other. 
     If an optical waveguide is formed (grown) in this deteriorated InAs/InGaAs-MQW growth surface, quality of an interface between the MQW and the optical waveguide deteriorates, resulting in an increase in light loss when light propagates. 
     As described above, in a case where an optical waveguide is formed in an active layer of, e.g., an MQW containing only As as a group-V material via conventional butt-joint growth, light loss may increase. 
     The optical waveguide according to the present embodiment and the method for manufacturing the same enable avoidance of light loss occurring when the aforementioned butt-joint growth is used. 
     Although in the present embodiment, the layer thickness of the selectively grown InP is varied by varying the width Ws of the selective growth masks  141  with the width Wg of the opening portion  142  kept constant, the layer thickness of the selectively grown InP can be varied by varying the width Wg of the opening portion  142  with the width Ws of each selective growth mask  141  kept constant. Also, the layer thickness of the selectively grown InP can be varied by varying both the width Ws of each selective growth mask  141  and the width Wg of the opening portion  142 . 
     In this way, the layer thickness of the selectively grown InP can be varied by varying a ratio between the width Ws of each selective growth mask  141  and the width Wg of the opening portion  142 . However, in consideration of uniformity (flatness) of the layer thickness of the selectively grown InP, varying the width Ws of each selective growth mask  141  with the width Wg of the opening portion  142  kept constant is more desirable for ease of control. 
     Although in the present embodiment, each selective growth mask  141  is formed in such a manner that a distal end of the selective growth mask  141  in the intermediate region  120  reaches a boundary with the passive region  130 , each selective growth mask  141  may be formed in such a manner that a distal end of the selective growth mask  141  falls inside the intermediate region  120 . Each selective growth mask  141  just needs to be formed in a part of the intermediate region  120 . 
     Also, in the present embodiment, the selective growth masks  141  are formed to grow InP thick in the active region no. Here, since no quantum well disordering occurs unless the annealing mask  161  is formed, there is no need to form the selective growth masks  141  to grow InP thick. 
     However, since the bandgap wavelength of the active region no may be affected by annealing, in consideration of bandgap wavelength continuity with the intermediate region  120 , it is desirable to form the selective growth masks  141  to grow InP thick in the active region  110 . 
     Also, although in the present embodiment, the annealing mask  161  is formed in the entire intermediate region  120 , even in a case where the annealing mask  161  is formed not in the entirety but a part of the intermediate region  120 , effects that are substantially the same as those of the present embodiment can be exerted as long as the bandgap wavelength in the intermediate region  120  can be varied. However, in consideration of bandgap wavelength continuity with the passive region  130 , it is desirable that the annealing mask  161  in the intermediate region  120  be formed in contact with the annealing mask  161  in the passive region  130 . 
     As above, the method for manufacturing the optical waveguide according to the present embodiment enables forming an optical waveguide in which a bandgap wavelength continuously varies in a direction from an active region toward a passive region in an intermediate region, by forming selective growth masks in parts of the intermediate region on a semiconductor crystal including a semiconductor quantum well structure and performing selective growth and then forming an annealing mask in a part of the intermediate region and the passive region and performing annealing. 
     Here, in a case where a region in which a semiconductor quantum well structure is not disordered (for example, an active region) is a first region and a region in which the semiconductor quantum well structure is disordered is a second region (for example, a passive region), an optical waveguide in which a bandgap wavelength continuously decreases from a first bandgap wavelength to a second bandgap wavelength between the first region and the second region can be formed by forming a selective growth mask and an opening portion in a region (for example, a part of an intermediate region) between the first region and the second region in a surface of a semiconductor crystal including the semiconductor quantum well structure and performing selective growth and then forming an annealing mask in the second region (for example, the passive region) and a region between the first region and the second region (for example, a part of the intermediate region) and performing annealing. 
     Therefore, in a case where light propagates in the optical waveguide according to the present embodiment, it is possible to curb light loss caused by the refractive index difference between the active region and the passive region. 
     Second Embodiment 
     A second embodiment of the present invention will be described with reference to the drawings. In the optical waveguide according to the first embodiment, a bandgap wavelength discontinuity part occurs at the boundary between the active region no and the intermediate region  120 . An optical waveguide according to the present embodiment and a method for manufacturing the same are intended to avoid the bandgap wavelength discontinuity. 
     In the optical waveguide according to the present embodiment and the method for manufacturing the same, manufacturing conditions such as configurations of a crystal, selective growth masks and an annealing mask used for manufacturing are substantially similar to those of the first embodiment. The present embodiment is different from the first embodiment in a configuration of a part, around a boundary between an active region and an intermediate region, of an annealing mask. 
       FIG.  13    is a sectional view of a crystal with a SiO 2  annealing mask  261  formed thereon, which is used in the present embodiment, (corresponding to the V-V sectional view in  FIG.  5   ). 
     The SiO 2  annealing mask  261  is formed in such a manner as to cover a boundary between an active region  210  and an intermediate region  220 . The SiO 2  annealing mask  261  is formed in such a manner as to cover the boundary in a range of 5 μm to the active region  210  side (E in the figure) from the boundary between the active region  210  and the intermediate region  220  (B in the figure). 
     As in the first embodiment, disordering of a quantum well structure is performed using the SiO 2  annealing mask  261 . 
       FIG.  14    illustrates variation in bandgap wavelength of the crystal in which the quantum well structure is disordered in the present embodiment. A bandgap wavelength of the active region  210  is 2350 nm in a range up to 5 μm away from the boundary between the active region  210  and the intermediate region  220  (from A to E in the figure). 
     The bandgap wavelength decreases from the position (E in the figure) that is 5 μm away from the boundary with the intermediate region  220  to the boundary between the active region  210  and the intermediate region  220  (B in the figure). 
     Furthermore, as in the first embodiment, the bandgap wavelength decreases from the boundary between the active region  210  and the intermediate region  220  (B in the figure) to a boundary between the intermediate region  220  and a passive region  230  (C in the figure) and becomes 2100 nm in the intermediate region  220 . 
     A bandgap wavelength of the passive region  230  is 2100 nm. 
     In this way, the method for manufacturing the optical waveguide according to the present embodiment enables continuously varying the bandgap wavelength with no point of bandgap wavelength discontinuity at the boundary between the active region and the intermediate region, by forming an annealing mask in a part of the active region, the intermediate region and the passive region. 
     Here, in a case where a region in which a semiconductor quantum well structure is not disordered (for example, an active region) is a first region and a region in which the semiconductor quantum well structure is disordered is a second region (for example, a passive region), an optical waveguide in which a bandgap wavelength continuously decreases from a first bandgap wavelength to a second bandgap wavelength between the first region and the second region can be formed by forming a selective growth mask and an opening portion in a region (for example, a part of an intermediate region) between the first region and the second region in a surface of a semiconductor crystal including the semiconductor quantum well structure and performing selective growth and then forming an annealing mask in the second region (for example, the passive region) and a region between the first region and the second region (for example, a part of the active region and a part of the intermediate region) and performing annealing. 
     Therefore, in a case where light propagates in the optical waveguide according to the present embodiment, it is possible to curb light loss caused by bandgap wavelength discontinuity at the interface between the active region and the intermediate region in addition to light loss caused by a refractive index difference between the active region and the passive region. 
     In the present embodiment, the active region  210  is subjected to quantum structure disordering, and thus, light emission performance of the active region  210  may deteriorate. This deterioration can be curbed by increasing a thickness of a selectively grown layer because the thickness increase results in an increase in distance from the SiO 2  annealing mask  261  to the quantum well structure and thus results in a decrease of crystal defects contributing to quantum well disordering. 
     On the other hand, the decrease of crystal defects contributing to quantum well disordering results in a decrease in amount of wavelength variation due to the quantum well disordering. Therefore, in a case where the thickness of the selectively grown layer is increased in the present embodiment, the thickness of the selectively grown layer is adjusted in consideration of the light emission performance and the wavelength variation amount of the active region  210 . 
     Third Embodiment 
     Next, a semiconductor device according to a third embodiment of the present invention will be described. 
     As the semiconductor device according to the present embodiment, a distributed Bragg reflector (DBR) laser  30  using the waveguide  10  according to the first embodiment will be described.  FIG.  15    illustrates the DBR laser  30  using a crystal subjected to quantum well structure disordering. 
     The DBR laser  3   o  includes an optical amplification region  301 , a DBR reflection region (preceding stage)  302 , an active layer region  303 , a phase adjustment region  304  and a DBR reflection region (subsequent stage)  305 . The active layer region  303  is a region in which light is emitted via current injection and the optical amplification region  301  is a region in which light oscillated via current injection is amplified. 
     In the quantum well disordered structure, as active regions  310 , the active layer region  303  and the optical amplification region  301  are provided, and as passive regions  330 , the phase adjustment region  304  and the distributed Bragg reflection regions  302 ,  305  are provided. Also, an intermediate region  320  is provided at each of a boundary between the optical amplification region  301  and the DBR reflection region (preceding stage)  302 , a boundary between the DBR reflection region (preceding stage)  302  and the active layer region  303 , and a boundary between the active layer region  303  and the phase adjustment region  304 . 
     A method for manufacturing a DBR reflection structure in the DBR laser  30  will be described. First, in the crystal with the SiO 2  annealing mask  161  removed after quantum well disordering being performed in the first embodiment, only the InP selectively grown layer  151  and the InP capping layer  106  are selectively removed via wet etching. 
     Next, a diffraction grating is formed in a surface of the InGaAsP optical confinement layer with a bandgap wavelength of 1.1 μm via electron beam exposure and wet etching. 
     Next, a p-type InP cladding layer and a p-type InGaAsP contact layer are sequentially formed via crystal growth using MOVPE growth. 
     Next, a stripe structure is formed using both dry etching and wet etching using SiO 2  used for a mask. 
     Next, SiO 2  is formed on sides of the stripe, and a p-type electrode is formed on the active layer, the optical amplification region, the phase adjustment region, and the distributed Bragg regions. 
     Next, an n-type electrode is formed on a back surface of the substrate. 
     Last, the crystal is cleaved and opposite end surfaces are coated with a non-reflective film. In this way, a ridge-type DBR laser structure is manufactured. 
     For the DBR laser  30 , which is an optical semiconductor device according to the present embodiment, favorable laser characteristics such that in a room-temperature continuous operation, a single-mode oscillation wavelength is 2.340 μm, an amount of wavelength variation via current injection to the DBR regions is 5 nm or more, a side-mode suppression ratio in each of all oscillation wavelengths is 40 dB or more and a light output is 1 mW or more are obtained. 
     As above, the present embodiment enables curbing light loss when light propagates from the active region  310  to the passive region  330 , by introducing the intermediate region  320  and thus enables provision of favorable laser characteristics. 
     Although in the present embodiment, the waveguide  10  according to the first embodiment is used, effects that are similar to or exceed the above are exerted using the waveguide  20  according to the second embodiment. 
     Although the present embodiment has been described in terms of a DBR laser, the optical waveguide according to embodiments of the present invention is applicable to a structure including an active region and a passive region in the same waveguide, and thus, is clearly applicable even to an SSG-DBR laser using a superstructure grating (SSG) for a diffraction grating or a sampled grating (SG)-DBR laser in which diffraction gratings are periodically disposed. Also, the optical waveguide according to embodiments of the present invention is applicable to optical semiconductor devices in which an optical modulator, an optical switch, etc., are integrated other than lasers. 
     Also, the present embodiment indicates a laser with a ridge structure and it is clear that the present invention does not depend on the waveguide structure but is applicable to lasers with a pn buried structure formed by processing each of an active region, an intermediate region, and a passive region into a stripe shape and burying opposite sides of such regions in p-type InP and n-type InP alternately or a buried structure formed by burying such regions in semi-insulation InP. 
     Also, although in the embodiments of the present invention, an InAs/InGaAs quantum well structure that emits light with a wavelength of 2.3 μm is disordered, it is clear that quantum well disordering is applicable not only to this material but also to quantum well structures formed of, e.g., InGaAsP or InGaAlAs, each quantum well structure emitting light with a 1.3 μm band, a 1.55 μm band or a 2 μm band. 
     Also, in the embodiments of the present invention, SiO 2  is used for the selective growth masks and the annealing mask, but another material such as SiN x  or TiO 2  may be used. 
     Although the dimensions of constituent units, components and the like in the optical waveguide, the method for manufacturing the optical waveguide, and the optical semiconductor device according to the first to third embodiments of the present invention have been described, the dimensions in the present invention are not limited to these dimensions but may be any dimensions that allow the respective constituent units, components and the like to function. 
     INDUSTRIAL APPLICABILITY 
     Embodiments of the present invention are applicable to semiconductor devices and semiconductor integrated devices such as semiconductor lasers for, e.g., optical communication, environment measurement or medical purposes. 
     REFERENCE SIGNS LIST 
     
         
         
           
               10  optical waveguide 
               101  substrate 
               102  cladding layer 
               110  active region 
               120  intermediate region 
               130  passive region 
               111  (non-disordered) semiconductor quantum well structure (first region) 
               121  semiconductor quantum well structure disordered in such manner that bandgap wavelength varies 
               131  disordered semiconductor quantum well structure (first region)