WO2001069735A1 - Dispositif laser a semi-conducteur a retroaction repartie et a couplage de gain et son procede de production - Google Patents
Dispositif laser a semi-conducteur a retroaction repartie et a couplage de gain et son procede de production Download PDFInfo
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- WO2001069735A1 WO2001069735A1 PCT/JP2001/000838 JP0100838W WO0169735A1 WO 2001069735 A1 WO2001069735 A1 WO 2001069735A1 JP 0100838 W JP0100838 W JP 0100838W WO 0169735 A1 WO0169735 A1 WO 0169735A1
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- H01S5/00—Semiconductor lasers
- H01S5/30—Structure or shape of the active region; Materials used for the active region
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- B82—NANOTECHNOLOGY
- B82Y—SPECIFIC USES OR APPLICATIONS OF NANOSTRUCTURES; MEASUREMENT OR ANALYSIS OF NANOSTRUCTURES; MANUFACTURE OR TREATMENT OF NANOSTRUCTURES
- B82Y20/00—Nanooptics, e.g. quantum optics or photonic crystals
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- H01S5/00—Semiconductor lasers
- H01S5/10—Construction or shape of the optical resonator, e.g. extended or external cavity, coupled cavities, bent-guide, varying width, thickness or composition of the active region
- H01S5/12—Construction or shape of the optical resonator, e.g. extended or external cavity, coupled cavities, bent-guide, varying width, thickness or composition of the active region the resonator having a periodic structure, e.g. in distributed feedback [DFB] lasers
- H01S5/1228—DFB lasers with a complex coupled grating, e.g. gain or loss coupling
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- H01S5/00—Semiconductor lasers
- H01S5/10—Construction or shape of the optical resonator, e.g. extended or external cavity, coupled cavities, bent-guide, varying width, thickness or composition of the active region
- H01S5/12—Construction or shape of the optical resonator, e.g. extended or external cavity, coupled cavities, bent-guide, varying width, thickness or composition of the active region the resonator having a periodic structure, e.g. in distributed feedback [DFB] lasers
- H01S5/1231—Grating growth or overgrowth details
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- H01S5/00—Semiconductor lasers
- H01S5/30—Structure or shape of the active region; Materials used for the active region
- H01S5/32—Structure or shape of the active region; Materials used for the active region comprising PN junctions, e.g. hetero- or double- heterostructures
- H01S5/3202—Structure or shape of the active region; Materials used for the active region comprising PN junctions, e.g. hetero- or double- heterostructures grown on specifically orientated substrates, or using orientation dependent growth
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- H01S5/00—Semiconductor lasers
- H01S5/30—Structure or shape of the active region; Materials used for the active region
- H01S5/32—Structure or shape of the active region; Materials used for the active region comprising PN junctions, e.g. hetero- or double- heterostructures
- H01S5/323—Structure or shape of the active region; Materials used for the active region comprising PN junctions, e.g. hetero- or double- heterostructures in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser
- H01S5/3235—Structure or shape of the active region; Materials used for the active region comprising PN junctions, e.g. hetero- or double- heterostructures in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser emitting light at a wavelength longer than 1000 nm, e.g. InP-based 1300 nm and 1500 nm lasers
- H01S5/32358—Structure or shape of the active region; Materials used for the active region comprising PN junctions, e.g. hetero- or double- heterostructures in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser emitting light at a wavelength longer than 1000 nm, e.g. InP-based 1300 nm and 1500 nm lasers containing very small amounts, usually less than 1%, of an additional III or V compound to decrease the bandgap strongly in a non-linear way by the bowing effect
- H01S5/32366—(In)GaAs with small amount of N
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- H01S5/00—Semiconductor lasers
- H01S5/30—Structure or shape of the active region; Materials used for the active region
- H01S5/34—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers
- H01S5/343—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser
- H01S5/34306—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser emitting light at a wavelength longer than 1000nm, e.g. InP based 1300 and 1500nm lasers
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- H01S5/00—Semiconductor lasers
- H01S5/30—Structure or shape of the active region; Materials used for the active region
- H01S5/34—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers
- H01S5/343—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser
- H01S5/34313—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser with a well layer having only As as V-compound, e.g. AlGaAs, InGaAs
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- H01S5/00—Semiconductor lasers
- H01S5/30—Structure or shape of the active region; Materials used for the active region
- H01S5/34—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers
- H01S5/343—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser
- H01S5/34313—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser with a well layer having only As as V-compound, e.g. AlGaAs, InGaAs
- H01S5/3432—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser with a well layer having only As as V-compound, e.g. AlGaAs, InGaAs the whole junction comprising only (AI)GaAs
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- H01S5/00—Semiconductor lasers
- H01S5/30—Structure or shape of the active region; Materials used for the active region
- H01S5/34—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers
- H01S5/343—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser
- H01S5/3434—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser with a well layer comprising at least both As and P as V-compounds
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- H01S5/00—Semiconductor lasers
- H01S5/30—Structure or shape of the active region; Materials used for the active region
- H01S5/34—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers
- H01S5/343—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser
- H01S5/34346—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser characterised by the materials of the barrier layers
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- H01S5/00—Semiconductor lasers
- H01S5/30—Structure or shape of the active region; Materials used for the active region
- H01S5/34—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers
- H01S5/343—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser
- H01S5/34346—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser characterised by the materials of the barrier layers
- H01S5/3438—Structure or shape of the active region; Materials used for the active region comprising quantum well or superlattice structures, e.g. single quantum well [SQW] lasers, multiple quantum well [MQW] lasers or graded index separate confinement heterostructure [GRINSCH] lasers in AIIIBV compounds, e.g. AlGaAs-laser, InP-based laser characterised by the materials of the barrier layers based on In(Al)P
Definitions
- the present invention relates to a gain-coupled distributed feedback semiconductor laser device using distributed feedback by gain coupling (hereinafter simply referred to as GC-DFB-LD (Gain-Coupled Di-stributed-FeedBack Laser Diode)) and a method of manufacturing the same.
- GC-DFB-LD Gain-Coupled Di-stributed-FeedBack Laser Diode
- G C -D F B -L D has various excellent features such as good single longitudinal mode characteristics and strong resistance to return light-induced noise.
- the first method as disclosed in a plurality of reports including Japanese Patent Application Laid-Open No. 60-128788 (conventional example 1), periodically modifies the active layer itself of a semiconductor laser. By arranging or applying a periodic structure to the active layer itself (gain diffraction grating), the optical gain in the active layer is periodically changed. Further, as disclosed in a plurality of reports such as Japanese Patent Publication No. 6-7624 (conventional example 2), a second method is to periodically emit light near an active layer in a semiconductor laser. By arranging an absorption layer (absorptive diffraction grating), the mode gain is changed periodically.
- the semiconductor laser structures disclosed in the above-mentioned Conventional Examples 1 and 2 have a basic configuration for periodically changing the gain, but have a configuration in which the refractive index is periodically changed together with the gain. That is, in the above conventional example, gain coupling and refractive index coupling are mixed. For this reason, it can be said that the structure cannot take full advantage of the original excellent performance of gain coupling.
- a plurality of reports such as Japanese Patent Application Laid-Open No. H5-136527 (conventional example 3) include a configuration in which a periodic change in refractive index is canceled out in a gain diffraction grating represented by conventional example 1. It has been disclosed.
- the materials and the thicknesses of the respective layers are as follows.
- Lower cladding layer 1 n-type InP, 0.45 im
- Semiconductor layer 2 n-type InGaAsP, 0.2
- Buffer layer 3 ⁇ type ⁇ ⁇ , 1 Onm
- Active layer 4 i (intrinsic)-InGaAsP, 0.1 urn
- Upper clad layer 6 p-type I nP, 1. 2 M m
- the surface of the semiconductor layer 2 is formed using the two-beam interference exposure method and the etching technique. It is obtained by forming irregularities 7 in the form of a diffraction grating, and laminating each layer from the buffer layer 3 to the upper cladding layer 6 on the semiconductor layer 2 by the second crystal growth.
- the active layer 4 has a periodic structure under the influence of the concavo-convex shape 7 of the semiconductor layer 2 which is the underlying layer, whereby the gain is modulated and gain coupling occurs.
- the distribution of the refractive index increases in the order of the guide layer 5, the semiconductor layer 2, and the active layer 4 depending on the selection of the material.
- the volume of the active layer 4 having a large refractive index is increased, but the volume of the guide layer 5 having a small refractive index is also increased. Therefore, the large refractive index of the active layer 4 is canceled.
- the volume of the active layer 4 having a large refractive index is small, and the volume of the guide layer 5 having a small refractive index is correspondingly small.
- the regions A-A ′, B-B It is possible to balance so that the equivalent refractive index is constant in any region, not limited to '. In this way, a GC-DFB-LD having substantially no refractive index coupling can be obtained.
- an object of the present invention is to provide a GC-DFB-LD capable of easily and reproducibly controlling the presence or absence and intensity of a refractive index distribution without depending on the accuracy of a processing process, and a manufacturing method thereof. To provide.
- a GC-DFB-LD includes a first layer having a predetermined refractive index and a predetermined forbidden band width, having a periodic structure, and a period of the first layer.
- the first layer functions as a light emitting layer or an absorption layer.
- the GC-DFB-LD of the present invention functions as an intrinsic GC-DFB-LD, and naturally only embeds the periodic structure of the first layer flatly in the second layer. It is formed without any dependence on accuracy.
- the GC-DFB-LD of the first embodiment is characterized in that the multilayer structure including the first layer and the second layer has a refractive index coupling coefficient of 5 cm- 1 or less.
- the refractive index coupling coefficient ⁇ i of the multilayer structure including the first layer and the second layer in which the periodic structure of the first layer is buried flat is 5 cm ⁇ 1 or less.
- Refractive index The effect of the coupling component is sufficiently small that the refractive indices of both layers are considered to be approximately equal.
- the first layer is configured to generate stimulated emission light, and the second layer is in close contact with the first layer. It is characterized by containing nitrogen as well as being provided.
- the first layer having the periodic structure and generating stimulated emission light has a wider forbidden band than the first layer, and the stimulated emission light from the first layer is formed around the first layer.
- a transparent second layer is provided in close contact therewith.
- the carrier is efficiently contained in the first layer.
- the periodic structure of the second layer is formed in close contact with the first layer, the first and second layers are adjusted by adjusting the nitrogen mixed crystal ratio of the second layer. It is possible to control the intensity of the periodic change of the equivalent refractive index in the laminated structure including. Therefore, in the gain-diffraction grating type GC-DFB-LD, it can be easily performed without considering the shapes of the first and second layers, in other words, without depending on the precision of the processing process. The intensity of the periodic change of the refractive index can be controlled easily and with good reproducibility.
- the GC-DFB-LD according to the third embodiment includes a third layer that generates stimulated emission light, and the first layer is located near one surface of the third layer, and Absorbed stimulated emission light generated from the third layer, the second layer is provided in close contact with the first layer and contains nitrogen.
- the forbidden band width is wider than that of the first layer around the first layer having the periodic structure and absorbing the stimulated emission light, so that the stimulated emission light from the third layer can be prevented.
- a clear second layer is provided in close contact.
- the periodic structure of the second layer is formed, so that the nitrogen mixed crystal ratio of the second layer is adjusted, whereby the equivalent refractive index in the multilayer structure including the first and second layers is adjusted.
- the magnitude of the period change of the control becomes controllable. Therefore, in the absorptive diffraction grating type GC-DFB-LD, the reproducibility is easy and reproducible without considering the shapes of the first and second layers, in other words, without depending on the precision of the processing process.
- the intensity of the periodic change of the refractive index can be controlled well.
- the GC-DFB-LD of the fourth embodiment is characterized in that the surface of the multilayer structure composed of the first layer and the second layer is made flat.
- the periodic structure of the first layer is embedded by the second layer, and the surface of the multilayer structure including the first layer and the second layer is flat. Therefore, the intensity of the periodic change in the refractive index set by adjusting the nitrogen mixed crystal ratio does not change depending on the surface shape of the multilayer structure.
- the GC-DFB-LD of the fifth embodiment is characterized in that the second layer contains at least one of In and Sb at a predetermined mixed crystal ratio.
- the second layer contains at least one of In and Sb at a predetermined mixed crystal ratio. Therefore, the change in the lattice constant caused by mixing the appropriate amount of nitrogen in the second layer to adjust the refractive index is canceled by the mixed crystal of In or Sb. In this way, an intrinsic GC-DFB-LD having better properties is obtained.
- the first layer has a plane orientation of (10 10
- the periodic structure is formed by crystal growth on the (0) plane or on a plane crystallographically equivalent to the (100) plane. It is characterized in that it is formed in a direction crystallographically equivalent to the [10] and [00-11] directions.
- the nitrogen in the growth layer is not affected by the irregularities of the underlayer.
- the mixed crystal becomes uniform, and the control of the refractive index coupling coefficient is performed more precisely. In this way, an intrinsic GC-DFB-LD having better properties is obtained.
- the method for producing a GC-DFB-LD according to the second invention includes a step of forming a first layer having a periodic structure by using a group III-V compound semiconductor; The method is characterized in that the method includes a step of forming a second layer so that the periodic structure of the first layer is buried flat by a III-V compound semiconductor having a wide band gap and containing nitrogen. .
- the first layer having a periodic structure since the first layer having a periodic structure is formed of a III-V compound semiconductor, it functions as a light emitting layer if sandwiched between p / n reverse conductivity type cladding layers, while the p-type Alternatively, if it is embedded in any of the n-type cladding layers, it functions as an absorption layer. Then, a second layer made of a group III-V compound semiconductor containing nitrogen and having a wider forbidden band width is formed in close contact with the light emitting layer or the absorption layer having the periodic structure. Therefore, the periodic structure is formed in the second layer, and the period of the equivalent refractive index in the multilayer structure including the first and second layers is adjusted by adjusting the nitrogen mixed crystal ratio of the second layer. The intensity of the change becomes controllable. In this way, the intensity of the periodic change of the refractive index can be easily and reproducibly controlled without depending on the precision of the processing process.
- the method of manufacturing GC-DFB-LD of the first embodiment is characterized in that the formation of the second layer is performed by crystal growth at a growth rate of 1 ⁇ / hour or less.
- the second layer in which the periodic structure of the first layer is buried flat, is grown at a growth rate of 1 / x m / hour or less.
- the method of manufacturing GC-DFB-LD of the second embodiment is characterized in that the refractive index of the second layer is made substantially equal to the refractive index of the first layer.
- the method of manufacturing a GC-DFB-LD according to the third embodiment is characterized in that the refractive index coupling coefficient of the laminated structure including the first layer and the second layer is set to 5 cm ⁇ 1 or less. It is.
- the refractive index coupling coefficient of the laminated structure including the first and second layers Since / c, is 5 cm- 1 or less, the refractive indices of the two layers are considered to be substantially equal, and the effect of the refractive index coupling component is sufficiently small.
- an intrinsic GC-DFB-LD is easily and reproducibly formed without depending on the accuracy of the processing process.
- the method of manufacturing a GC-DFB-LD according to the fourth embodiment is characterized in that the refractive index in the second layer is set by adjusting the mixed crystal ratio of nitrogen. I have.
- the refractive index of the second layer is easily and reproducibly controlled by merely adjusting the nitrogen mixed crystal ratio of the second layer, and the refractive index of the first layer is adjusted. It can be set almost equal to
- the method of manufacturing a GC-DFB-LD according to the fifth embodiment includes forming the first layer on a (100) plane or a plane crystallographically equivalent to the (100) plane. Crystal growth on the substrate and forming the periodic structure in the [010] direction or the [00-1] direction or a crystallographically equivalent direction to the above [010] and [00-1] directions. It is characterized by performing
- the nitrogen in the growth layer is not affected by the irregularities of the underlayer.
- the mixed crystal becomes uniform, and the control of the refractive index coupling coefficient is performed more precisely. That is, the intensity of the periodic change of the refractive index can be controlled easily and with good reproducibility and controllability.
- FIG. 1 is a longitudinal sectional view of the GC-DFB-LD of the present invention.
- FIG. 2 is a perspective view of a laminated structure.
- FIG. 3 is a diagram showing the temperature dependence of the oscillation wavelength in the GC-DFB-LD shown in FIG.
- FIG. 4 is a diagram showing the temperature dependence of the oscillation wavelength of the GC-DFB-LD of Comparative Example 1.
- 5A and 5B are diagrams showing changes in the refractive index and the forbidden band width when In or N is mixed with GaAs.
- FIG. 6A and 6B are diagrams showing the distribution of the band diagram and the equivalent refractive index in the direction of the resonator in the GC-DFB-LD of FIG. 1 or Comparative Example 1.
- FIG. 6A and 6B are diagrams showing the distribution of the band diagram and the equivalent refractive index in the direction of the resonator in the GC-DFB-LD of FIG. 1 or Comparative Example 1.
- FIG. 7 is a diagram showing a correlation between a nitrogen mixed crystal ratio in the GC-DFB-LD shown in FIG. 1 and ⁇ n eq in the resonator.
- FIGS. 8A, 8B, and 8C are longitudinal cross-sectional views of main parts near the active layer in the GC-DFB-LD of Modifications 1 to 3.
- FIG. 8A, 8B, and 8C are longitudinal cross-sectional views of main parts near the active layer in the GC-DFB-LD of Modifications 1 to 3.
- 9A, 9B, and 9C are longitudinal cross-sectional views of a main part near the active layer in GC-DFB-LD of Modification Example 4.
- FIG. 10 is a longitudinal sectional view of a GC-DFB-LD different from FIG.
- FIGS. ⁇ - ⁇ , ⁇ - C, and 11 C are perspective views of the laminated structure during the ⁇ $ forming process of the GC-DF-LD shown in FIG.
- FIG. 12 is a vertical cross-sectional view of a main part near the diffraction grating in the GC-DFB-LD different from FIGS.
- Fig. 13 is a vertical cross-sectional view of the main part near the diffraction grating in the GC-DFB-LD, which is different from Figs. 1, 10, and 12.
- Fig. 14 is a vertical cross-sectional view of the main part near the diffraction grating in the GC-DFB-LD, which is different from Fig. 1, Fig. 10, Fig. 12, and Fig. 13.
- Fig. 15 is a vertical cross-sectional view of the main part near the diffraction grating in the GC-DFB-LD, which is different from Figs. 1, 10, and Figs.
- FIG. 16 is a vertical cross-sectional view of a main part near a diffraction grating in a GC-DFB-LD different from FIGS. 1, 10, and 12 to 15.
- FIG. 17 shows a different GC-DFB-LD from Figs. 1, 10, and 12 to 16.
- FIG. 3 is a vertical sectional view of a main part near a diffraction grating.
- FIG. 18 is a perspective view of the laminated structure after the diffraction grating is imprinted during the process of forming the GC-DFB-LD shown in FIG.
- FIG. 19 is a longitudinal sectional view of a main part of a conventional GC-DFB-LD. BEST MODE FOR CARRYING OUT THE INVENTION
- the present embodiment relates to a gain-diffraction grating GC-DFB-LD, in which a transparent layer in which a small amount of nitrogen is mixed is formed adjacent to a periodically formed well layer (light emitting layer). It is characterized in that by forming it, an intrinsic GC-DFB-LD is obtained.
- FIG. 1 schematically shows a cross-sectional structure of a gain-diffraction grating GC-DFB-LD according to the present embodiment.
- the configuration, material, and layer thickness of each part are as follows.
- n-type GaAs 100 ⁇ m
- FIG. 2 is a perspective view of the laminated structure during the process of forming the GC-DFB-LD 10 shown in FIG.
- a method of manufacturing the GC-DFB-LD 10 shown in FIG. 1 will be described with reference to FIG.
- the first crystal growth using the metalorganic chemical vapor deposition method is performed to form the lower cladding layer 12 to the upper barrier layer 16.
- Each layer is sequentially laminated.
- the n-type GaAs substrate 11 uses the (100) plane.
- trimethylaluminum, trimethylgallium, trimethylindium, arsine, and dimethylhydrazine were used as the raw materials for Al, Ga, In, As, and N.
- the laminated structure after the first crystal growth is taken out of the crystal growth chamber, and the surface thereof is subjected to a two-beam interference exposure method to form a lattice photoresist mask having a period of 0.28 ⁇ and a duty ratio of 0.5 (see FIG. Next, hydrochloric acid and hydrogen peroxide solution are mixed at a ratio of 1:50, and the above-mentioned area where the photoresist mask is not formed is exposed from the surface with a cleaning solution diluted 5 times with pure water.
- the thickness of the upper barrier layer 16 is 20 nm
- the thickness of each of the well layers 14 a and 14 b is 10 nm
- the thickness of the intermediate barrier layer 15 is 20 nra Therefore, the total film thickness from the upper barrier layer 16 to the lower well layer 14a is 6 Onm. Therefore, when the photoresist mask is removed, as shown in FIG. 2B, a diffraction grating 17 in which the two well layers 14a and 14b are periodically divided in the extending direction of the n-type GaAs substrate 11 is obtained. can get.
- the multilayer structure shown in FIG. 2B is put into the crystal growth chamber again, and a second crystal growth is performed on the above-mentioned diffraction grating 17 to make contact from the buried layer 18 as shown in FIG. 2C. Grow each layer up to layer 20. At this time, the buried layer 18 It is necessary to perform crystal growth by selecting crystal growth conditions so that the nitrogen distribution in the only layer 18 is uniform and the interface between the buried layer 18 and the upper clad layer 19 is flat.
- the stacked structure after the second crystal growth is taken out of the crystal growth chamber, and a current confinement layer 23 made of silicon nitride is formed on the surface as shown in FIG. 2C.
- the p-electrode 21 is formed on the upper surface of the multilayer structure, and the n-electrode 22 is formed on the lower surface. Then, the laser light emitting end face is cleaved to obtain a gain diffraction grating type GC-DFB-LD10.
- FIG. 3 shows the temperature dependence of the oscillation wavelength of this GC-DFB-LD10.
- the submode suppression ratio is 2 OdB or more, and the same longitudinal mode (m (0)) oscillates at a completely single wavelength.
- no stop band was observed in the oscillation spectrum, indicating that the component of the refractive index coupling was zero.
- the lower barrier layer 13 ′, the intermediate barrier layer 15, the upper barrier layer 16 and the buried layer 18 are made of i-GaAsN.
- the material in the other layers is exactly the same, just by replacing with GaAs.GC-DFB-LD fabricated c
- the GC-DFB-LD in Comparative Example 1 also oscillated at a single wavelength of 98 Onm at a threshold current density of 0.5 kA m 2 .
- This GC-DFB-LD Figure 4 shows a typical example of the temperature dependence of the oscillation wavelength.
- oscillation occurs in a single longitudinal mode (m (0)) from the element temperature of + 10 ° C to + 50 ° C.
- the element temperature is lower than + 10 ° C or higher than + 50 ° C, it shifts to oscillation in another adjacent longitudinal mode (m (+ l), m (-1)) Oscillations in the mode hopping and in the Fabry-Bello mode ( ⁇ - ⁇ ) were also observed, causing instability in the oscillation wavelength.
- a stop band exists in the oscillation spectrum, and that the gain coupling and the refractive index coupling are mixed, which causes instability of the oscillation wavelength.
- the light is periodically divided like the diffraction grating 17.
- the barrier layer having a wide forbidden band width adjacent to the InGaAs well layer 14 is characterized by being composed of a slight (0.48% in the first embodiment) mixed crystal of nitrogen. That is, by slightly mixing nitrogen in the barrier layer, the refractive index is adjusted to a predetermined value without greatly changing the forbidden band width. This will be described with reference to FIGS.
- FIG. 5A shows changes in the refractive index and the forbidden band width when In is mixed with GaAs.
- FIG. 5B shows how the refractive index and the band gap change when N is mixed with GaAs. 5A and 5B, In used in the well layer 14 in the first embodiment. 2 Ga. 8 As (point a in FIG. 5A) and GaAs used for the barrier layers 13, 15, 16 and the buried layer 18 adjacent to the well layer 14. 995 2N. . . 48 (point b in Fig. 5B) has the same refractive index.
- GaAs Q9952N used for the barrier layers 13, 15, 16, and the buried layer 18 is related to the above-mentioned band gap . It can be seen from FIG.
- the gain region is periodic.
- the well layer 14, the barrier layers 13, 15, 16, and the buried layer 18 all have the same refractive index, despite the fact that the No perturbation has occurred.
- the shape of the diffraction there is no need to consider the balance of the refractive index with that of 18, etc., and even if the diffraction grating 17 is buried even flat, essentially no refractive index coupling occurs, making it possible to easily obtain an intrinsic GC-DEB-LD You can.
- Comparative Example 1 since nitrogen is not mixed in the layer 18 ′ surrounding the well layer 14 ′ having a narrow bandgap, as shown in FIG.
- the period of the equivalent refractive index n eq changes synchronously with the period change of the band structure.
- the refractive index increases as the bandgap becomes narrower.
- the rate of change in that case is almost the same without depending on the material system.
- the rate of change of the refractive index due to the change of the forbidden band width when the mixed crystal ratio of In is changed is about 0.4 [per eV].
- the change rate of the refractive index when the mixed crystal ratio of A1 is changed is about 0.4 [per eV].
- the barrier layers 13, 15, 16 and the buried layer 18 are slightly mixed with nitrogen.
- the rate of change of the refractive index when the nitrogen mixed crystal ratio was changed was about 1.4 [per eV].
- the change rate of the refractive index is several times larger than that of the material system.
- the forbidden band width is slightly reduced, but the effect of the increase in the refractive index is larger than that.
- it can be said that it is a special mixed crystal system that can obtain a material with a very high refractive index while keeping the forbidden band width relatively wide.
- a special refractive index change rate in a material in which only a small amount of nitrogen is mixed is positively used, and an InGaAs well having a narrow band gap and a high refractive index is used.
- the layer is surrounded by a GaAsN-based material having a wide forbidden band, and a diffraction grating structure in which a refractive index distribution does not occur is obtained by adjusting the nitrogen mixed crystal ratio of the GaAsN-based material.
- the nitrogen mixed crystal ratio is periodically distributed in the buried layer 18 on the diffraction grating 17 in which a plurality of planes appear periodically and repeatedly.
- a refractive index distribution is generated inside the buried layer 18 that matches the period of the concave-convex shape of the diffraction grating 17 which is the base. In that case, it is impossible to achieve the object of the present embodiment of obtaining a configuration of a diffraction grating having no refractive index distribution by adjusting the nitrogen mixed crystal ratio.
- the present inventor has set the growth rate during crystal growth to 1 ⁇ m / hour or less in order to eliminate the above-mentioned distribution of the nitrogen mixed crystal ratio in the grown crystal corresponding to the irregular shape of the underlying crystal. It was found that setting a slower rate was effective. This is presumed to be because if the above growth rate is sufficiently slow, the surface species of the raw material species supplied during crystal growth are sufficiently diffused, and the atoms constituting the crystal are sufficiently randomly mixed. You.
- sufficiently slowing the growth rate to cause sufficient surface diffusion of the raw material species is effective in promoting flattening of the upper surface of the buried layer 18.
- the crystal growth proceeds one by one before the surface diffusion of the raw material species has not sufficiently occurred, so that the initial irregularities are maintained even after the crystal growth. Flattening is not promoted.
- a sufficiently slow growth rate of 1 ⁇ / hr or less is essential.
- Ga In is often used as a barrier layer for an InGaAs well layer.
- GaAsN having a slightly narrower forbidden band width is used as the barrier layers 13, 15, 16 and the buried layer 18 instead of GaAs. Therefore, this raises a concern that the band offset with respect to the well layer is reduced. While with force, GaAs respect I n 0 2 Ga 0 8 As well layer 1 4.
- the lattice constant of the barrier layer deviates from the lattice constant of the GaAs substrate 11. There is a concern that defects will occur.
- the above G a As 0. 9952 N.
- the device lifetime was more than 5000 hours at device temperature of 80 ° C and output of 10 mW, which was sufficient.
- an intrinsic GC-DFB-LD in which the periodic fluctuation of the equivalent refractive index is zero is described as an example.
- periodic fluctuation of the equivalent refractive index is described as zero
- the refractive index coupling coefficient / which represents the degree of refractive index coupling caused by the periodic variation of the refractive index
- the periodic variation of the equivalent refractive index is as follows.
- Fig. 7 shows the structure of the gain-diffraction grating GC-DFB-LD10 shown in Fig. 1 using the GaAsN mixed crystal (lower barrier layer 13, intermediate barrier layer 15, upper barrier layer 16, The correlation between the nitrogen mixed crystal ratio in the buried layer 18) (horizontal axis in Fig.
- An eq (vertical axis in Fig. 7) representing the periodic change strength of the equivalent refractive index n eq in the resonator is shown. Show.
- An eq is the equivalent refractive index n eq (Y) in the convex section of the diffraction grating 17 shown by Y-Y ′ in FIG. Difference from equivalent refractive index n (Z) ( ⁇ n eq
- the magnitude of the refractive index coupling coefficient K i has a strong correlation with the absolute value of ⁇ n eq . If the nitrogen mole fraction of "0.0048" corresponds to the first 'embodiment, the period change of the equivalent refractive index n of the resonator as can be seen from Figure 7 delta n p "is” 0 ", bending The configuration does not involve the bending coupling. In contrast, when the nitrogen mole fraction of "0" corresponds to the above Comparative Example 1, configured with a refractive index coupled from a periodic change delta n eq of the equivalent refractive index n eq in the resonator is present Becomes
- the nitrogen mixed crystal ratio of the above GaAsN mixed crystal is set to an arbitrary value between “0” and “0.0045”, the GC-DFB-LD in which the degree of the refractive index coupling is set to an arbitrary value becomes Obtainable.
- the nitrogen mixed crystal ratio is set to a value larger than “0.000048”, an anti-phase type gain diffraction grating in which a portion having a high equivalent refractive index n eq matches a portion having a low gain can be obtained.
- the layer that generates stimulated emission light or the layer that absorbs stimulated emission light is given a periodic structure, and a layer in which nitrogen is mixed is provided adjacent to the layer, and the nitrogen mixed crystal ratio is varied.
- various characteristic gain diffraction gratings can be obtained. That is, it is possible to easily control the characteristics of GC-DFB-LD.
- the gain diffraction grating in which the barrier layers 13, 15, 16 and the buried layer 18 are formed of GaAsN, and the well layer 14 is formed of InGaAs As an example of the configuration of the type GC-DFB-LD, the configuration in which the periphery is surrounded by GaAsN after the InGaAs well layer 14 is periodically divided has been described. However, as the configuration of the gain diffraction grating in the present invention, the configurations shown in the following modified examples 1 to 4 are also possible.
- FIG. 8A shows a vertical cross section of a main portion near an active layer sandwiched between upper and lower clad layers in a gain grating type G C-DFB-LD of the first modification.
- the configuration, material, and film thickness of each part are as follows.
- Well layer 33 i-In 02 Ga 08 As, 9 nm
- the upper, lower, left and right sides of the InGaAs well layer 14 are all adjacent to the GaAsN material.
- the lower barrier layer 32 adjacent to the lower portion of the InGaAs well layer 33 is made of a GaAs material instead of a GaAsN material.
- the etching for forming the diffraction grating 37 does not etch the upper surface of the lower barrier layer 32.
- Fig. 8B shows a vertical cross section of the main part near the active layer sandwiched between the upper and lower cladding layers in the gain 1 "raw diffraction grating type GC-DFB-LD of the second modification.
- the film thickness is as follows.
- -Embed layer 4 5 i-GaAs, 5 Onm (the thinnest part)
- the upper, lower, left, and right sides of the InGaAs well layer 14 are all adjacent to the GaAsN material.
- the second modification only the side buried layer 44 adjacent to the side of the InGaAs well layer 43 is made of a GaAsN material.
- the gain grating type GC-DFB-LD having the above configuration, there is no perturbation of the refractive index.
- the upper and lower end surfaces of the InGaAs well layer 43 come into contact with a material having a larger forbidden band width than GaAsN (GaAs in Modification 2), improving the efficiency of confining carriers in the InGaAs well layer 43. Can be done.
- the GaAsN side buried layer 44 on the side surface of the InGaAs well layer 43 is formed by forming a silicon nitride mask (not shown) on the top of the diffraction grating 47 in advance and performing selective growth. It is formed by regrowth so as to be in contact with the side surface of the InGaAs well layer 43.
- FIG. 8C shows a vertical cross section of a main part near the active layer sandwiched between upper and lower cladding layers in the gain grating type GC-DFB-LD of the third modification.
- the configuration, material, and film thickness of each part are as follows.
- -Upper cladding layer 5 6 P type Al. 3 Ga 07 As, 1.0 / im
- a multilayer film including an InGaAs well layer 14 is stacked on a flat substrate 11, and after the InGaAs well layer 14 is etched and divided into a diffraction grating shape. Embedded with GaAsN.
- the GaAsN guide layer 52 serving as a base is formed with an uneven shape, and a GaAs
- the N-barrier layer 53InGaAs well layer 54 and the GaAsN buried layer 55 are regrown to form a diffraction grating 57. Therefore, a periodic distribution is generated in the film thickness of the InGaAs well layer 54 reflecting the unevenness of the underlying GaAsN guide layer 52, and a perturbation of gain is obtained.
- the upper and lower portions of the GaAs well layer 54 are all surrounded by GaAsN material. Therefore, there is no perturbation of the refractive index, and an intrinsic GC-DFB-LD is obtained.
- FIG. 9 shows a vertical cross section of a main part near an active layer sandwiched between upper and lower clad layers, showing a process of forming a gain diffraction grating GC-DFB-LD of Modification Example 4.
- the configuration, material, and film thickness of each part are as shown in FIG. 9C.
- 'Upper cladding layer 6 7 p-type Al 0. 3 Ga 0. 7 As, 1. 0 ⁇ m
- the structure shown in FIG. 9C is manufactured through the steps from FIG. 9A to FIG. 9C. That is, first, as shown in FIG. 9A, after the respective layers up to the guide layer 62 are laminated on the substrate by the first crystal growth, a periodic diffraction grating dielectric mask 69 is formed on the surface thereof. Form. Then, a periodic structure is formed on the guide layer 62 by etching.
- the GaAsN guide layer 62 is provided with an uneven shape, and a quantum well structure composed of an InGaAs well layer 64 and GaAsN barrier layers 63 and 65 is formed thereon. Despite the regrowth, a stronger gain perturbation than in Modification 3 is obtained because the active layer 64 is divided.
- the upper, lower, left and right sides of the GaAs well layer 64 are all surrounded by GaAsN material. Therefore, there is no perturbation of refractive index, and intrinsic GC-DFB-LD is obtained. Also, if the width of the concave portion of the periodic structure 68 is made sufficiently small and the width of the well layer 64 is reduced to about 1 Onm or less, the active layer (well layer) 64 can function as a quantum wire. Become.
- This embodiment relates to an absorptive diffraction grating type GC-DFB-LD, in which an absorption layer is periodically formed in a guide layer close to an active layer, and a small amount of nitrogen is mixed in the absorption layer. It is characterized in that intrinsic GC-DFB-LD is obtained by adjoining the transparentized layer.
- FIG. 10 schematically shows a cross-sectional structure of the absorptive diffraction grating type GC-DFB-LD 70 of the present embodiment.
- the composition, material, and layer thickness of each part are as follows.
- n-type GaAs 100 ⁇ m
- Type 03 9952 1 ⁇ . . . 48 , 20nm (the thinnest part)
- FIG. 11 is a perspective view of the laminated structure during the process of forming the GC-DFB-LD 70 shown in FIG.
- a method of manufacturing the GC-DFB-LD 70 shown in FIG. 10 will be described with reference to FIG.
- metalorganic vapor phase epitaxy was performed on an n-type GaAs substrate 71.
- Each layer from the lower cladding layer 72 to the upper barrier layer 77 is successively laminated by the first crystal growth using.
- the n-type GaAs substrate 71 uses the (100) plane.
- trimethylaluminum, trimethylgallium, trimethylindium, arsine, and dimethylhydrazine were used as the raw materials for Al, Ga, In, As, and N.
- the stacked structure after the first crystal growth is taken out of the crystal growth chamber, and a two-beam interference exposure method is applied to the surface of the stacked structure to form a lattice-shaped photoresist mask with a circumference of 0.228 ⁇ and a duty ratio of 0.5 (see Fig. (Not shown).
- hydrochloric acid and hydrogen peroxide solution were mixed at a ratio of 1:50, and the area where the photoresist mask was not formed was exposed from the surface with an etching solution diluted 5 times with pure water.
- the thickness of the upper barrier layer 77 is 2 Ontn, and the thickness of the absorption layer 76 is 10 nm. Therefore, the total thickness from the upper barrier layer 77 to the absorption layer 76 is 3 Onm. is there. Therefore, when the photoresist mask is removed, a diffraction grating 78 in which the absorption layer 76 is periodically divided in the extending direction of the n-type GaAs substrate 71 is obtained as shown in FIG. 11B.
- the laminated structure shown in FIG. 11B is put into the crystal growth chamber again, and the second crystal growth is performed on the diffraction grating 78, as shown in FIG. Grow each layer up to layer 81.
- the buried layer 79 is grown at a growth rate of 1 ⁇ / hour or less so that the interface between the buried layer 79 and the upper cladding layer 80 becomes flat.
- the stacked structure after the second crystal growth is taken out of the crystal growth chamber, and a current confinement layer 84 of silicon nitride is formed on the surface of the stacked structure as shown in FIG. 11C.
- the ⁇ electrode 82 is formed on the upper surface of the multilayer structure, and the ⁇ -type electrode 83 is formed on the lower surface. Then, the laser light emitting end face is cleaved to obtain an absorptive diffraction grating type GC-DFB-LD70.
- the second embodiment is characterized in that a layer adjacent to the n-type In Q2 G 3 ⁇ 48 As absorption layer 76 periodically divided by the diffraction grating 78 is slightly mixed with nitrogen. .
- the intrinsic refractive index can be set to a predetermined value without greatly changing the forbidden band width.
- GC-DFB-LD is realized. More specifically, as described in detail in the first embodiment, the InGaAs used for the absorption layer 76 and the barrier layer 75 77 and the buried layer 79 adjacent to the absorption layer 76 were used.
- the nitrogen mixed crystal ratio of the barrier layers 75 and 77 and the buried layer 79 is adjusted so that GaAsN has the same refractive index.
- the GaAs 9952 N used for the barrier layer 7577 and the buried layer 79 is about 1.
- the diffraction grating 78 is an absorption grating formed by embedding the opaque absorption layer 76 with the transparent barrier layer 7577 and the buried layer 79. Layer 76, barrier layers 75 and 77, and buried layer 79 all have the same refractive index, and there is no refractive index perturbation.
- the second embodiment as in the case of the conventional structure in which the refractive index perturbation of the absorbing layer is canceled by providing a refractive index perturbation having the opposite phase in the vicinity, There is no need to consider the shape of 8 and the balance of the refractive index with the buried layer 79, etc., and even if the diffraction grating 78 is buried flat, essentially no refractive index coupling occurs, and the intrinsic GC-DEB-LD Can be obtained.
- GaInAs in which nitrogen is not mixed is used as a light emitting layer or an absorption layer, and the light emitting layer or the absorption layer is embedded with GaAsN in which nitrogen is mixed.
- the GC-DFB-LD with the configuration has been described.
- a GC-DFB-LD in which each of the light emitting layer or the absorbing layer and the buried layer adjacent thereto is made of a material in which nitrogen is mixed and mixed will be described.
- FIG. 12 shows a vertical cross section of a main part near the diffraction grating in the GC-DFB-LD of the present embodiment.
- the configuration, material, and layer thickness of each part are as follows.
- the diffraction grating 95 in the present embodiment functions as a gain diffraction grating if the narrow bandgap layer 93 is used as a light emitting layer and sandwiched between p / n opposite conductivity type cladding layers as in the case of the first embodiment. . Further, as in the case of the second embodiment, if the narrow bandgap layer 93 is embedded as an absorption layer in either a p-type or n-type cladding layer, it functions as an absorptive diffraction grating.
- the narrow band gap layer 93 that functions as a light emitting layer or an absorption layer is set to have a lower nitrogen mixed crystal ratio than each layer adjacent thereto.
- each layer surrounding the narrow bandgap layer 93 and having a high nitrogen mixed crystal ratio is made of a material whose refractive index increases greatly as the bandgap narrows.
- the nitrogen mixed crystal ratio of each layer is adjusted so as not to cause a distribution of the refractive index.
- a small amount of In is simultaneously mixed and crystallized in the narrow bandgap layer 93 and the barrier layers 92 and 94 and the buried layer 96 adjacent to the narrow bandgap layer 93.
- the change in lattice constant when adjusting the refractive index by mixing an appropriate amount of nitrogen in each of the layers 92, 93, 94, and 96 can be reduced by mixing a small amount of In. Can be countered. Therefore, better GC-DFB-LD can be obtained.
- the GC-DFB-LD incorporating the diffraction grating 95 with the above configuration is completely unitary even if the diffraction grating 95 is an gain diffraction grating or an absorption diffraction grating, with a submode suppression ratio of 20 dB or more. Oscillates at one wavelength. In addition, no stop band was observed in the oscillation spectrum, and the refractive index coupling component was found to be zero. In addition, it can be seen that single-wavelength oscillation occurs with a probability of 97% in spite of the fact that the anti-reflection coating is not applied to the laser light emitting end face, and the yield for single-wavelength laser production is extremely high. There was found. These features are unique to intrinsic GC-DFB-LD without index coupling components.
- the diffraction gratings 17, 37, 47, 7, 7, 8, 8, 78 and 95 are constituted by layers in which In or N is mixed with GaAs.
- GC-DF B-LD explained.
- a GC-DFB-LD composed of a combination of AlGaAs material and nitrogen mixed crystal will be described.
- FIG. 13 shows a vertical cross section of a main part near the diffraction grating in the GC-DFB-LD of the present embodiment.
- the configuration, material, and layer thickness of each part are as follows.
- the diffraction grating 105 in the present embodiment has a gain 1 ⁇ 2 ⁇ diffraction grating when the narrow bandgap layer 103 is sandwiched between the p / n reverse conductivity type cladding layers as the light emitting layer as in the first embodiment. Act as a child. Also, as in the second embodiment, if the narrow bandgap layer 103 is embedded as an absorption layer in either the ⁇ -type or ⁇ -type cladding layer, it functions as an absorptive diffraction grating. As the clad layer, any material having a low refractive index, a wide band gap, and substantially lattice-matched to the substrate can be selected.
- the diffraction grating 105 is added to the barrier layers 102, 104 and the buried layer 106 adjacent to the narrow bandgap layer 103 functioning as the light emitting layer or the absorption layer. Nitrogen is mixed. Therefore, similarly to the case described in the first and second embodiments, the narrow bandgap layer 103 having a narrow bandgap and a high refractive index is surrounded by a material having a wide bandgap, but the distribution of the refractive index is not changed. The nitrogen mixture ratio of each layer is selected so as not to occur, and an intrinsic GC-DFB-LD is obtained.
- the GC-DFB-LD that incorporates the diffraction grating 105 with the above configuration, even if the diffraction grating 105 is a gain diffraction grating or an absorption diffraction grating, is completely unitary at a side mode suppression ratio of 2 Od B or more. It oscillates at the wavelength. In addition, no stop band was observed in the oscillation spectrum, and it was found that the component of the refractive index coupling was zero. Also, it was found that single-wavelength oscillation occurred with a probability of 97% despite the fact that the anti-reflection coating was not applied to the laser light emitting end face, and the yield for the production of single-wavelength lasers was extremely high. Turned out to be high. These characteristics are unique to intrinsic GC-DFB-LD that does not contain refractive index coupling components.
- the intrinsic GC-DFB-LD can be easily realized by mixing nitrogen in the layer adjacent to the light emitting layer or the absorption layer.
- the diffraction gratings corresponding to the first to fourth modifications of the first embodiment can be modified.
- the narrow band gap layer 103 functioning as a light emitting layer or an absorption layer can be mixed with a smaller amount of nitrogen than in an adjacent layer.
- a GC-DFB-LD constituted by a combination of a material obtained by mixing nitrogen with an AlInGaP-based material will be described.
- FIG. 14 shows a vertical cross section of a main part near the diffraction grating in the GC-DFB-LD of the present embodiment.
- the configuration, material, and layer thickness of each part are as follows.
- the barrier layer 112, 114, and the buried layer adjacent to the narrow bandgap layer 113 which functions as the light emitting layer or the absorption layer. Since an appropriate amount of nitrogen is mixed in 1 16, the narrow band gap layer 1 13 with a narrow band gap and a high refractive index is surrounded by a material with a wide band gap, but the refractive index is The nitrogen mixture ratio of each layer is selected so that no distribution occurs, and an intrinsic GC-DFB-LD is obtained. In that case, the GC-DFB-LD oscillates at a completely single wavelength at a side mode suppression ratio of 2 OdB or more. In addition, it was found that the component of the refractive index coupling was zero, and that single-wavelength oscillation occurred at a probability of 97% even though the non-reflection coating was not applied to the laser light emitting end face. .
- intrinsic GC-DFFB-LD can be easily realized by mixing nitrogen in a layer adjacent to the light emitting layer or the absorbing layer. It is needless to say that also in the present embodiment, the diffraction gratings corresponding to the first to fourth modifications of the first embodiment can be modified. Further, similarly to the third embodiment, it is also possible to mix a smaller amount of nitrogen in the narrow bandgap layer 113 functioning as a light emitting layer or an absorption layer than in an adjacent layer.
- FIG. 15 shows a vertical cross section of a main part near the diffraction grating in the GC-DFB-LD of the present embodiment.
- the configuration, material, and layer thickness of each part are as follows.
- the narrow bandgap layer 123 having a narrow bandgap and a high refractive index is surrounded by a material having a wide bandgap, and the refractive index is distributed.
- Intrinsic GC-DFB-LD is obtained by selecting the nitrogen mixed crystal ratio of each layer so as not to cause cracks. In that case, the GC-DFB-LD oscillates at a completely single wavelength at a submode suppression ratio of 20 dB or more. The component of the refractive index coupling is zero, and single-wavelength oscillation occurs with a probability of 97%. Note that, also in the present embodiment, the deformation of the diffraction grating corresponding to the first to fourth modifications is possible. In addition, it is possible to mix less nitrogen in the narrow bandgap layer 123 functioning as a light emitting layer or an absorption layer than in an adjacent layer.
- a GC-DFB-LD composed of a combination of an InGaAsP-based material that is substantially lattice-matched to an InP substrate and a mixed crystal of nitrogen will be described.
- FIG. 16 shows a vertical cross section of a main part near the diffraction grating in the GC-DFB-LD of the present embodiment.
- the configuration, material, and layer thickness of each part are as follows.
- the narrow bandgap layer 133 having a narrow bandgap and a high refractive index is surrounded by a material having a wide bandgap, but the refractive index is distributed.
- the intrinsic GC-DFB-LD is obtained by selecting the nitrogen mixed crystal ratio of each layer so as not to cause cracks. In that case, the GC-DFB-LD oscillates at a completely single wavelength at a side mode suppression ratio of 2 OdB or more.
- the component of the refractive index coupling is zero, and single-wavelength oscillation occurs with a probability of 97%.
- the deformation of the diffraction grating corresponding to the first to fourth modifications is possible. Also, it is possible to mix an appropriate amount of nitrogen only in an adjacent layer without mixing nitrogen in the narrow bandgap layer 133 functioning as a light emitting layer or an absorption layer.
- FIG. 17 shows a vertical cross section of a main part near the diffraction grating in the GC-DFB-LD of the present embodiment.
- the configuration, material, and layer thickness of each part are as follows.
- FIG. 18 shows that at least the lower wide bandgap layer 141, the lower barrier layer 142, the narrow bandgap layer 143, and the upper barrier layer 144 are formed on the GaAs substrate in the manufacturing process of the GC-DFB-LD of this embodiment.
- a perspective view of the laminated structure 140 immediately after the diffraction grating 145 is imprinted on the surface thereof after fabrication is shown.
- This embodiment is characterized in that the diffraction grating 145 is stamped in the [0 10] direction (or in the [00-1] direction orthogonal thereto) using the (100) plane of the GaAs substrate.
- the (100) plane Nitrogen is more likely to be incorporated into the film than when crystal growth is performed, and on the other hand, nitrogen is less likely to be incorporated on the surface inclined in the [01-1] direction (referred to as surface B). Therefore, when the diffraction grating 145 is imprinted in the [01 1] direction or the [01-1] direction, the flat portions of the tops and valleys of the uneven shape of the diffraction grating 145 are (100) planes.
- the inclined portion becomes the A-plane or the B-plane, and a periodic distribution is generated in the mixed crystal ratio of nitrogen in the film grown on the diffraction grating 145, reflecting the uneven shape of the diffraction grating 145.
- the inventor of the present application does not have the above-described problem when growing a crystal in which nitrogen is mixed and crystallized on a plane inclined in the [010] direction or the [00-1] direction orthogonal thereto. I found that. This is because the [010] direction or the [00-1] direction orthogonal to it is at a 45 degree angle to the [01 1] direction and the [01-11] direction, and therefore, it is inclined to the [010] direction. It seems that the surface has an intermediate property between the A and B surfaces.
- the diffraction grating 145 is imprinted in the [010] direction or in the [00-1] direction orthogonal thereto, the surface of the diffraction grating 145 that is inclined in the [010] direction or in the direction orthogonal thereto is exposed. That is, the mixed crystal ratio of nitrogen in the film grown on the diffraction grating 145 is independent of the growth rate during crystal growth. A uniform distribution can be obtained without reflecting the uneven shape of the diffraction grating 145.
- the plane orientation of the substrate is not necessarily the (100) plane, but may be any plane that is crystallographically equivalent to the (100) plane. In this case, it goes without saying that the direction in which the diffraction grating 145 is imprinted may be the [010] direction, the [00-1] direction orthogonal thereto, or a direction crystallographically equivalent thereto.
- the refractive index is reduced.
- the nitrogen mixture ratio of each layer is selected so that no distribution occurs, and intrinsic GC-DFB-LD is obtained.
- the GC-DFB-LD oscillates completely at a single wavelength with a side mode suppression ratio of 20 dB or more.
- the component of the refractive index coupling is zero and 97
- Single-wavelength oscillation occurs with a probability of%. Note that, also in the present embodiment, the deformation of the diffraction grating corresponding to the first to fourth modifications is possible. Further, the narrow bandgap layer 143 functioning as a light-emitting layer or an absorption layer can be mixed with a smaller amount of nitrogen than in an adjacent layer.
- the diffraction gratings 125, 135, and 145 in the sixth, seventh, and eighth embodiments are also sandwiched between p / n reverse conductivity type cladding layers with the narrow bandgap layers 123, 133, and 143 as light emitting layers. In this case, it functions as a gain diffraction grating.
- the narrow band gap layers 123, 133, and 143 are embedded in the p-type or n-type cladding layer as an absorbing layer, they function as an absorptive diffraction grating.
- the cladding layer can be made of any material having a low refractive index and a wide bandgap, and which is substantially lattice-matched to the substrate.
- a suitable amount of nitrogen is mixed and crystallized in the barrier layers 122, 124 and the buried layer 126 adjacent to the narrow bandgap layer 123 to obtain a refractive index.
- a small amount of Sb is simultaneously mixed and crystallized. By doing so, it is possible to cancel the change in lattice constant due to the mixed crystal of nitrogen, and to obtain a better GC-DFB-LD.
- the effect of simultaneously forming a mixed crystal of Sb is the same even with the mixed crystal of In, as described in the third embodiment. The same effects can be obtained. Needless to say, it is also possible to mix both Sb and In.
- the material constituting the semiconductor laser is not limited to the material system or the mixed crystal ratio used in each of the above embodiments.
- the present invention is applicable to any II-V semiconductor material system such as (Al, Ga, In, B, T1)-(P, As, Sb, N, Bi). Can be used.
- various modifications can be made to the combination of material types, such as a structure in which only the diffraction grating portion is made of a group IV-V semiconductor and a material for the cladding layer and the current confinement layer are made of a group II-VI semiconductor.
- the crystal growth method and the raw materials to be used are not limited to those specifically shown in each of the above embodiments and modifications, and various methods can be applied.
- the manufacturing method, configuration, and position of the diffraction grating are not limited by the above embodiments and modified examples.
- the configurations of the gain diffraction grating and the absorption diffraction grating those shown in the above-described embodiments and modified examples are merely examples, and various modifications are possible.
- the trapezoidal shape has been described as the shape of the diffraction grating, a rectangular shape, a triangular shape, a sawtooth wave shape, a sine wave shape, an inverted trapezoidal shape, or the like may be used.
- the diffraction grating When an LD is used as a monolithic light source for an optical integrated circuit, it is effective to draw the diffraction grating directly by electron beam exposure. Also, the diffraction grating may have a phase shift. The phase of the diffraction grating in the center of the element becomes discontinuous. The multi-shift type, in which multiple phase shifts are distributed in the resonator, the phase shifts gradually. It is possible to apply various phase shift methods, such as a graded shift type that changes the width of a stripe-shaped refractive index waveguide and a stripe width shift type that realizes an effective phase shift.
- the active layer having a periodic structure in the gain diffraction grating and the absorption layer having a periodic structure in the absorptive diffraction grating may be a quantum crystal having an arbitrary number of wells or a bulk crystal having no quantum effect. also good c, facet reflectivity of the laser device, thus can be controlled to coat thin films using a variety of materials.
- one end face can be coated with an anti-reflection coating, and the other end face can be coated with a reflection coating to achieve high output and high efficiency.
- Various configurations can be adopted, such as a window structure.
- the shape and manufacturing method of the striped waveguide structure for controlling the current confinement and the lateral electric field.
- the broad stripe type stripe structure is used in each of the above embodiments and modifications, various modifications such as a ridge waveguide type and a buried hetero type (Buried Heterostructure BH) can be applied.
- the gain grating and the absorption grating obtained in each of the above embodiments and modifications are excellent not only as GC-DFB-LDs but also as wavelength filters for selectively transmitting or amplifying only specific wavelengths. It shows the properties. It is also possible to apply the above-described configuration of the diffraction grating section to a light control element utilizing this fact.
- the diffraction grating of the present invention may be incorporated as a part of an optical integrated circuit in which various optical devices are integrated.
- the direction described as “up” is a direction away from the substrate, and the direction described as “down” is a direction approaching the substrate. Crystal growth proceeds from “below” to “above”. Further, the conductivity type of the substrate and the conductivity type of the upper cladding layer ⁇ the lower cladding layer can be replaced with a type opposite to that shown in each of the above embodiments and modifications.
- the GC-DFB-LD of the first invention has a periodic structure of the first layer having a refractive index substantially equal to that of the first layer and a forbidden band wider than that of the first layer. Since it is buried flat with a second layer having a width, it can be used as an intrinsic GC-DFB-LD. Can work.
- the intrinsic GC-DFB-LD can be formed easily and with good reproducibility without depending on the precision of the processing process at all by simply embedding the periodic structure of the first layer flat with the second layer. .
- the refractive index coupling coefficient ⁇ of the laminated structure including the first and second layers is set to 5 cm- 1 or less, the influence of the refractive index coupling component Is sufficiently small that the refractive indices of both layers can be considered to be substantially equal.
- the GC-DFB-LD of the second embodiment is provided with a second layer having a wider forbidden band than the first layer, in close contact with the first layer that generates stimulated emission light.
- the carrier can be efficiently contained in the first layer.
- the second layer containing nitrogen is provided in close contact with the first layer having a periodic structure, the periodic structure is also formed in the second layer.
- the refractive index of a nitrogen mixed crystal of a III-V compound semiconductor can be controlled by changing the nitrogen mixed crystal ratio. Therefore, by adjusting the nitrogen mixed crystal ratio of the second layer, it is possible to control the intensity of the periodic change of the equivalent refractive index in the laminated structure including the first and second layers. .
- the present invention in the gain-diffraction grating type GC-DFB-LD, without considering the shapes of the first and second layers, in other words, the accuracy of the processing process
- the intensity of the periodic change of the refractive index can be controlled easily and with good reproducibility without depending on. Therefore, stable single longitudinal mode oscillation characteristics can be obtained even when the ambient temperature changes, and the manufacturing yield can be dramatically improved.
- a second layer containing nitrogen is provided in close contact with the first layer having a periodic structure for absorbing stimulated emission light from the third layer. Therefore, a periodic structure is also formed in the second layer.
- the refractive index of a nitrogen mixed crystal of a III-V compound semiconductor can be controlled by changing the nitrogen mixed crystal ratio. Therefore, by adjusting the nitrogen mixed crystal ratio of the second layer, it is possible to control the intensity of the periodic change of the equivalent refractive index in the laminated structure including the first and second layers.
- the processing in the absorptive diffraction grating type GC-DFB-LD, without considering the shapes of the first and second layers, in other words, the processing
- the intensity of the periodic change in the refractive index can be easily and reproducibly controlled without depending on the accuracy of the process. Therefore, stable single longitudinal mode oscillation characteristics can be obtained even when the ambient temperature changes, and the manufacturing yield can be dramatically improved.
- the surface of the multilayer structure composed of the first layer and the second layer is made flat, it is set by adjusting the nitrogen mixed crystal ratio. It is possible to prevent the intensity of the periodic change of the refractive index from being changed by the surface shape of the multilayer structure.
- the second layer contains at least one of In and Sb at a predetermined mixed crystal ratio, it is suitable for the second layer.
- the change in the lattice constant caused by adjusting the refractive index by mixing crystals of an appropriate amount of nitrogen can be counteracted by the mixed crystals of In or Sb. Therefore, it is possible to obtain Shinju GC-DFB-LD having more excellent characteristics.
- the GC-DFB-LD of the sixth embodiment is obtained by growing the first layer on a (100) plane or a plane crystallographically equivalent to a (100) plane.
- the periodic structure is formed in the [010] direction or the [00-1] direction or in the crystallographically equivalent direction to the [010] or [0 0-1] direction.
- the second layer in which nitrogen is mixed and crystallized, is grown on the periodic structure in the first layer
- the mixed crystal of nitrogen in the growth layer is uniformly formed without being affected by the unevenness of the underlayer. Become. Therefore, the refractive index coupling coefficient can be controlled more precisely, and an intrinsic GC-DFB-LD having more excellent characteristics can be obtained.
- the method for manufacturing a GC-DFB-LD according to the second aspect of the present invention is a method for manufacturing a GC-DFB-LD, in which the periodic structure of the first layer made of a group III-V compound semiconductor that functions as a light emitting layer or an absorbing layer has a wider band gap. Since the second layer made of a ⁇ -V compound semiconductor containing nitrogen is buried flat, a periodic structure can be formed in the second layer, and the first and second layers can be formed by adjusting the nitrogen mixed crystal ratio. It is possible to control the intensity of the periodic change of the equivalent refractive index in the laminated structure including the two layers. Therefore, the intensity of the periodic change in the refractive index can be easily and reproducibly controlled without depending on the accuracy of the processing process. That is, according to the present invention, it is possible to form a GC-DFB-LD capable of obtaining stable single longitudinal mode oscillation characteristics even with a change in ambient temperature. In addition, the production yield of GC-DFB-LD can be significantly improved.
- the second layer is formed by growing a crystal at a growth rate of 1 / im / hour or less.
- the periodic distribution of the nitrogen mixed crystal ratio caused by the periodic structure can be eliminated. Therefore, the refractive index distribution in the second layer can be made more uniform. Further, flattening of the second layer can be promoted, and the periodic structure of the first layer can be embedded more evenly.
- the refractive index of the second layer is made substantially equal to the refractive index of the first layer, so that it does not depend on the precision of the processing process.
- An intrinsic GC-DFB-LD can be easily and reproducibly formed.
- the method of manufacturing a GC-DFB-LD according to the third embodiment is configured such that the refractive index coupling coefficient / ⁇ of the laminated structure including the first layer and the second layer is set to 5 cm- 1 or less. Therefore, it can be considered that the refractive indexes of the two layers are substantially equal. Therefore, the intrinsic GC-DFB-LD can be easily and reproducibly formed without depending on the precision of the processing process.
- the setting of the refractive index in the second layer is performed by adjusting the mixed crystal ratio of nitrogen.
- the refractive index of the second layer can be controlled easily and with good reproducibility only by adjusting the mixed crystal ratio of nitrogen in the layer, and can be set substantially equal to the refractive index of the first layer.
- the method of manufacturing a GC-DFB-LD according to the fifth embodiment includes forming the first layer on a (100) plane or a plane crystallographically equivalent to the (100) plane. Crystal growth on the substrate and forming the periodic structure in the [010] direction or the [00-1] direction or a crystallographically equivalent direction to the above [010] and [00-1] directions. Therefore, when growing the second layer in which nitrogen is mixed and crystallized on the periodic structure in the first layer, the nitrogen mixed in the growth layer is not affected by the irregularities of the underlayer. The crystallization becomes uniform. Therefore, it is necessary to control the refractive index crystal coefficient more precisely. Therefore, the intensity of the periodic change of the refractive index can be controlled easily and with good reproducibility and controllability.
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Description
Claims
Priority Applications (4)
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KR1020027012063A KR100632308B1 (ko) | 2000-03-13 | 2001-02-07 | 이득결합 분포귀환형 반도체레이저장치 및 그의 제조방법 |
DE60138691T DE60138691D1 (de) | 2000-03-13 | 2001-02-07 | Dfb-halbleiterlaserbauelement mit verstärkungs-kopplung und verfahren zu seiner herstellung |
EP01902789A EP1265326B1 (en) | 2000-03-13 | 2001-02-07 | Gain-coupled distributed feedback semiconductor laser device and production method therefor |
US10/221,363 US7016391B2 (en) | 2000-03-13 | 2001-02-07 | Gain-coupled distributed feedback semiconductor laser device and production method therefor |
Applications Claiming Priority (2)
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JP2000068500 | 2000-03-13 | ||
JP2000-68500 | 2000-03-13 |
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WO2001069735A1 true WO2001069735A1 (fr) | 2001-09-20 |
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ID=18587550
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PCT/JP2001/000838 WO2001069735A1 (fr) | 2000-03-13 | 2001-02-07 | Dispositif laser a semi-conducteur a retroaction repartie et a couplage de gain et son procede de production |
Country Status (5)
Country | Link |
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US (1) | US7016391B2 (ja) |
EP (1) | EP1265326B1 (ja) |
KR (1) | KR100632308B1 (ja) |
DE (1) | DE60138691D1 (ja) |
WO (1) | WO2001069735A1 (ja) |
Cited By (5)
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WO2003058685A2 (de) * | 2002-01-08 | 2003-07-17 | Forschungsverbund Berlin E.V. | Verfahren zur herstellung eines braggschen gitters in einer halbleiterschichtenfolge mittels ätzen und halbleiterbauelement |
EP1394911A2 (en) * | 2002-08-01 | 2004-03-03 | Northrop Grumman Corporation | Fabrication process of a semiconductor diffraction grating |
JP2009302416A (ja) * | 2008-06-17 | 2009-12-24 | Anritsu Corp | 半導体レーザ,半導体レーザモジュールおよびラマン増幅器 |
WO2015170590A1 (ja) * | 2014-05-07 | 2015-11-12 | 日本碍子株式会社 | グレーティング素子の実装構造の製造方法 |
JP2017034034A (ja) * | 2015-07-30 | 2017-02-09 | 浜松ホトニクス株式会社 | 分布帰還型横マルチモード半導体レーザ素子 |
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US6922426B2 (en) * | 2001-12-20 | 2005-07-26 | Finisar Corporation | Vertical cavity surface emitting laser including indium in the active region |
US7257143B2 (en) * | 1998-12-21 | 2007-08-14 | Finisar Corporation | Multicomponent barrier layers in quantum well active regions to enhance confinement and speed |
US7167495B2 (en) * | 1998-12-21 | 2007-01-23 | Finisar Corporation | Use of GaAs extended barrier layers between active regions containing nitrogen and AlGaAs confining layers |
US20030219917A1 (en) * | 1998-12-21 | 2003-11-27 | Johnson Ralph H. | System and method using migration enhanced epitaxy for flattening active layers and the mechanical stabilization of quantum wells associated with vertical cavity surface emitting lasers |
US7286585B2 (en) * | 1998-12-21 | 2007-10-23 | Finisar Corporation | Low temperature grown layers with migration enhanced epitaxy adjacent to an InGaAsN(Sb) based active region |
CN101432936B (zh) * | 2004-10-01 | 2011-02-02 | 菲尼萨公司 | 具有多顶侧接触的垂直腔面发射激光器 |
US7860137B2 (en) * | 2004-10-01 | 2010-12-28 | Finisar Corporation | Vertical cavity surface emitting laser with undoped top mirror |
JP4951267B2 (ja) * | 2006-04-27 | 2012-06-13 | 日本オプネクスト株式会社 | 半導体レーザ素子の製造方法 |
CN103346475B (zh) * | 2013-05-31 | 2015-07-15 | 中国科学院半导体研究所 | 单片集成耦合腔窄线宽半导体激光器 |
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Cited By (11)
Publication number | Priority date | Publication date | Assignee | Title |
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WO2003058685A2 (de) * | 2002-01-08 | 2003-07-17 | Forschungsverbund Berlin E.V. | Verfahren zur herstellung eines braggschen gitters in einer halbleiterschichtenfolge mittels ätzen und halbleiterbauelement |
WO2003058685A3 (de) * | 2002-01-08 | 2003-11-27 | Forschungsverbund Berlin Ev | Verfahren zur herstellung eines braggschen gitters in einer halbleiterschichtenfolge mittels ätzen und halbleiterbauelement |
EP1394911A2 (en) * | 2002-08-01 | 2004-03-03 | Northrop Grumman Corporation | Fabrication process of a semiconductor diffraction grating |
EP1394911A3 (en) * | 2002-08-01 | 2005-06-08 | Northrop Grumman Corporation | Fabrication process of a semiconductor diffraction grating |
JP2009302416A (ja) * | 2008-06-17 | 2009-12-24 | Anritsu Corp | 半導体レーザ,半導体レーザモジュールおよびラマン増幅器 |
WO2015170590A1 (ja) * | 2014-05-07 | 2015-11-12 | 日本碍子株式会社 | グレーティング素子の実装構造の製造方法 |
CN106233176A (zh) * | 2014-05-07 | 2016-12-14 | 日本碍子株式会社 | 光栅元件的安装结构的制造方法 |
JPWO2015170590A1 (ja) * | 2014-05-07 | 2017-04-20 | 日本碍子株式会社 | グレーティング素子の実装構造の製造方法 |
US9874694B2 (en) | 2014-05-07 | 2018-01-23 | Ngk Insulators, Ltd. | Production method for mounting structure for grating elements |
CN106233176B (zh) * | 2014-05-07 | 2019-08-16 | 日本碍子株式会社 | 光栅元件的安装结构的制造方法 |
JP2017034034A (ja) * | 2015-07-30 | 2017-02-09 | 浜松ホトニクス株式会社 | 分布帰還型横マルチモード半導体レーザ素子 |
Also Published As
Publication number | Publication date |
---|---|
EP1265326A1 (en) | 2002-12-11 |
KR20020081450A (ko) | 2002-10-26 |
EP1265326A4 (en) | 2005-12-07 |
US20030039287A1 (en) | 2003-02-27 |
KR100632308B1 (ko) | 2006-10-11 |
DE60138691D1 (de) | 2009-06-25 |
EP1265326B1 (en) | 2009-05-13 |
US7016391B2 (en) | 2006-03-21 |
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