JP3753793B2 - Group 3 nitride compound semiconductor light emitting device - Google Patents

Description

[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a semiconductor device using a group 3 nitride semiconductor. In particular, the present invention relates to a light emitting element with improved light emission luminance.
[0002]
[Prior art]
Conventionally, a material using an AlGaInN-based compound semiconductor is known as a material for light emitting elements in the blue and short wavelength regions. Since the compound semiconductor is a direct transition type, it has attracted attention because of its high emission efficiency and the use of blue and green as one of the three primary colors of light.
[0003]
AlGaInN semiconductors can also be made p-type by doping Mg and irradiating an electron beam, or by heat treatment. As a result, a light emitting diode (LED) having a double heterostructure using an AlGaN p-conducting cladding layer, a Zn and Si-doped InGaN light emitting layer, and a GaN n layer is known. This light emitting diode has a buffer layer on a sapphire substrate, an n ^{+ -type} GaN layer doped with silicon at a high concentration, a clad layer composed of an n-type GaN layer doped with silicon, a light-emitting layer composed of InGaN, and a clad layer of p-type AlGaN , A first contact layer of p-type GaN and a second contact layer of p ^{+ -type} GaN.
[0004]
[Problems to be solved by the invention]
However, the light emitting diode having such a structure has a problem that the light emission intensity is still small. Accordingly, as a result of repeated studies on the crystallinity of the light emitting element, the present inventors have newly found the following. An n ^{+ -type} GaN layer to which silicon is added at a high concentration is formed on the buffer layer, and the upper layer is sequentially formed thereon. As a result, it has been found that as a result of the n ^{+ -type} GaN layer containing a large amount of impurities, the crystallinity is not good, and therefore the crystallinity of each layer formed thereon is not good. Therefore, if the first layer formed on the substrate is a layer with a low impurity concentration except for the buffer layer, the crystallinity of each layer formed on the layer will be improved, and the emission luminance and light emission will be improved. It has been found that efficiency is improved.
[0005]
Therefore, the present invention has been made based on the above findings, and an object of the present invention is to improve light emission luminance and light emission efficiency by improving crystallinity of each layer of a light emitting element.
[0006]
[Means for Solving the Problems]
The invention according to claim 1 is a light emitting device having an n layer, a light emitting layer, and a p layer made of a group III nitride semiconductor formed on a substrate, a buffer layer formed on the substrate, and a buffer layer thickness 100 formed on the angstroms to 2 mu and a layer of undoped a m, the impurity concentration of silicon which is formed on the layer of additive-free is ^{1 × 10 17 ~1 × 10 20} / cm 3 N-type high impurity concentration layer having a thickness of 0.5 to 10 μm, a p-type contact layer, a contact electrode provided on the high impurity concentration layer, and nickel provided on the contact layer And a transparent electrode comprising a double layer of gold.
[0007]
In the above structure, an n layer to which an impurity is added at a low concentration may be formed between the n-type high impurity concentration layer and the light emitting layer. Since the impurity concentration of the base layer for growing the light emitting layer is lowered, the crystallinity of the layer is good, and therefore the crystallinity of the light emitting layer grown thereon is also good.
According to a second aspect of the present invention, there is provided a light emitting device having an n layer, a light emitting layer, and a p layer made of a group III nitride semiconductor formed on a substrate, a buffer layer formed on the substrate, a layer of undoped thickness formed on the buffer layer is 100 Å~ 2 μ m, the silicon concentration which is formed on the layer of undoped is ^{1 × 10 17 ~1 × 10 20} / an n-type high impurity concentration layer having a thickness in the range of cm ³ and having a thickness of 0.5 to 10 μm, and an n layer having a lower impurity concentration than the high impurity concentration layer, provided between the high impurity concentration layer and the light emitting layer. It is characterized by having.
According to a third aspect of the present invention, in the light emitting device according to the second aspect, a p-type contact layer, a contact electrode provided on the high impurity concentration layer, and a transparent electrode provided on the contact layer It further has these.
According to a fourth aspect of the present invention, in the light emitting device according to the third aspect, the transparent electrode is composed of a double layer of nickel and gold .
According to a fifth aspect of the present invention, in the light emitting device according to any one of the first to fourth aspects, the light emitting layer has a multiple quantum well structure.
According to a sixth aspect of the present invention, in the light emitting device according to any one of the first to fourth aspects, the light emitting layer has a single quantum well structure.
According to a seventh aspect of the present invention, in the light emitting device according to any one of the first to sixth aspects, the impurity-free layer is made of GaN.
According to an eighth aspect of the present invention, in the light emitting device according to any one of the first to seventh aspects, the high impurity concentration layer is made of GaN.
[0008]
In the above structure, the carrier concentration of the layer to which no impurities are added is desirably 2 × 10 ¹⁸ / cm ³ or less. At this time, the crystallinity of each layer formed thereon is improved. Also, the thickness of the layer without impurities is preferably 100 to 2 μm. If it is thinner than 100 mm, the effect of improving the crystallinity of each layer formed on it is low, and if it exceeds 2 μm, it is desirable because the thickness of each layer that can be grown on it without cracking is limited. Absent.
[0009]
In the above configuration, the carrier concentration of the n-type high impurity concentration layer is preferably 1 × 10 ¹⁶ to 1 × 10 ¹⁹ / cm ³ . A contact electrode is formed on this layer. Therefore, it is desirable that this layer has a lower resistivity. However, if the carrier concentration is 1 × 10 ¹⁹ / cm ³ or more, the crystallinity is deteriorated and the crystallinity of the layer formed thereon is lowered, which is not desirable. If the carrier concentration is 1 × 10 ¹⁶ / cm ³ or less, it is not desirable because the resistance cannot be lowered with an appropriate layer thickness. The n-type high impurity concentration layer preferably has a thickness of 0.5 to 10 μm. If it is thinner than 0.5 μm, the layer is exposed by etching, and it becomes difficult to form a contact electrode on the layer, which is not desirable. On the other hand, if it is thicker than 10 μm, it is difficult to grow each layer formed thereon without generating cracks.
[0010]
[0011]
[Action and effect of the invention]
As described above, since a layer underlying the growth of the light emitting layer was changed to an impurity-free additive pressurizing the layers, thereby improving the crystallinity of the layer. Accordingly, the crystallinity of each layer formed on the impurity-free layer is improved, and in particular, the crystallinity of the light emitting layer is improved. As a result, the light emission luminance and the light emission efficiency are improved. Further, to form a high impurity concentration layer of high impurity concentration n-type on the layer of the undoped, in order to provided a contact electrode in the layer, the carrier never passes through a layer of undoped For this reason, voltage drop and resistance loss due to resistance are suppressed, and luminous efficiency is improved.
[0012]
DETAILED DESCRIPTION OF THE INVENTION
Hereinafter, the present invention will be described based on specific examples. The present invention is not limited to the following examples.
FIG. 1 shows an overall view of a light emitting device 100 according to an embodiment of the present invention. The light emitting device 100 has a sapphire substrate 1 on which a 0.05 μm AlN buffer layer 2 is formed.
[0013]
On the buffer layer 2, an n layer (first layer) made of silicon (Si) -doped GaN having a film thickness of about 0.6 μm and a silicon concentration of 2 × 10 ¹⁸ / cm ³ and an electron concentration of 1 × 10 ¹⁸ / cm ³ is sequentially formed. Low impurity concentration layer) 31, high carrier concentration n ⁺ layer (high impurity concentration) made of silicon (Si) -doped GaN with a film thickness of about 4.0 μm, silicon concentration 4 × 10 ¹⁸ / cm ³ , and electron concentration 2 × 10 ¹⁸ / cm ³ (Concentration layer) 3, n-layer (second low impurity concentration layer) made of silicon (Si) -doped GaN with a silicon concentration of about 0.5 μm and a silicon concentration of 1 × 10 ¹⁸ / cm ³ and an electron concentration of 5 × 10 ¹⁷ / cm ³ 4. Thickness of about 100 nm, light emitting layer of In _0.20 Ga _0.80 N doped with zinc (Zn) and silicon (Si) doped to 5 × 10 ¹⁸ / cm ³ , thickness of about 10 nm, hole concentration 2 × 10 ¹⁷ / cm ³ , Magnesium (Mg) concentration 5 × 10 ¹⁹ / cm ³ doped Al _0.08 Ga _0.92 N p-conducting clad layer 71, film thickness about 35 nm, hole concentration 3 × 10 ¹⁷ / cm ³ of magnesium (Mg) concentration of 5 × 10 ¹⁹ / cm ³ first contact layer 72 made of doped GaN, thickness of about 5 nm, magnesium hole concentration ^{6 × 10 17 / cm 3 (} Mg) concentration of 1 × 10 ²⁰ / cm ³ A p ⁺ conductivity type second contact layer 73 made of doped GaN is formed. Then, a transparent electrode 9 made of a Ni / Au double layer is formed on the entire upper surface of the second contact layer 73, and a bonding pad 10 made of a Ni / Au double layer is formed at the corner of the transparent electrode 9. Has been. An electrode 8 made of Al is formed on the n ⁺ layer 3.
[0014]
Next, a method for manufacturing the semiconductor element having this structure will be described.
The light emitting device 100 was manufactured by vapor phase growth by metal organic chemical vapor deposition (hereinafter referred to as MOVPE).
The gases used were ammonia (NH ₃ ), carrier gas (H ₂ ), trimethyl gallium (Ga (CH ₃ ) ₃ ) (hereinafter referred to as “TMG”), trimethyl aluminum (Al (CH ₃ ) ₃ ) (hereinafter referred to as “TMG”) It referred to as "TMA"), trimethylindium (an In (CH _{3) 3)} (hereinafter referred to as "TMI"), silane (SiH ₄₎ diethylzinc _{(Zn (C 2 H 5)} 2) (hereinafter "DEZ" And cyclopentadienyl magnesium (Mg (C ₅ H ₅ ) ₂ ) (hereinafter referred to as “CP ₂ Mg”).
[0015]
First, a single crystal sapphire substrate 1 is mounted on a susceptor mounted in a reaction chamber of an M0VPE apparatus with the a-plane cleaned by organic cleaning and heat treatment as the main surface. Next, the sapphire substrate 1 was baked at a temperature of 1100 ° C. while flowing H ₂ at normal pressure at a flow rate of 2 liter / min for about 30 minutes into the reaction chamber.
[0016]
Next, the temperature is lowered to 400 ° C., H ₂ is supplied at 20 liter / min, NH ₃ is supplied at 10 liter / min, and TMA is supplied at 1.8 × 10 ⁻⁵ mol / min for about 90 seconds to provide an AlN buffer layer 2 Was formed to a thickness of about 0.05 μm. Next, the temperature of the sapphire substrate 1 is maintained at 1100 ° C., H ₂ is 20 liter / min, NH ₃ is 10 liter / min, TMG is 1.12 × 10 ⁻⁴ mol / min, 0.86 ppm with H ₂ gas. Diluted silane is introduced at 20 × 10 ⁻⁹ mol / min for 36 minutes, silicon (Si) doping with a film thickness of about 0.6 μm, an electron concentration of 1 × 10 ¹⁸ / cm ³ , and a silicon concentration of 2 × 10 ¹⁸ / cm ³ An n layer 31 made of GaN was formed.
[0017]
Next, the temperature of the sapphire substrate 1 is maintained at 1150 ° C., H ₂ is 20 liter / min, NH ₃ is 10 liter / min, TMG is 1.7 × 10 ⁻⁴ mol / min, diluted to 0.86 ppm with H ₂ gas. silane was introduced 40 minutes 20 × 10 ^-8 mol / min, a film thickness of about 4.0 [mu] m, an electron concentration 1 × 10 ¹⁸ / cm ^3, the silicon of the silicon concentration ^{4 × 10 18 / cm 3 (} Si) doped GaN A high carrier concentration n ⁺ layer 3 was formed.
[0018]
After the above high carrier concentration n ⁺ layer 3 is formed, the temperature is subsequently maintained at 1100 ° C., H ₂ is 20 liter / min, NH ₃ is 10 liter / min, and TMG is 1.12 × 10 ⁻⁴ mol / min. Silane diluted to 0.86 ppm with H ₂ gas was introduced at 10 × 10 ⁻⁹ mol / min for 30 minutes, film thickness of about 0.5 μm, electron concentration 5 × 10 ¹⁷ / cm ³ , silicon concentration 1 × 10 ¹⁸ An n layer 4 made of silicon (Si) -doped GaN of / cm ³ was formed.
[0019]
Subsequently, the temperature is maintained at 800 ° C., N ₂ or H ₂ is 20 liter / min, NH ₃ is 10 liter / min, TMG is 0.2 × 10 ⁻⁴ mol / min, and TMI is 1.6 × 10 ⁻⁴ mol / min. Silane diluted to 0.86 ppm with H ₂ gas at 10 × 10 ⁻⁸ mol / min and DEZ at 2 × 10 ⁻⁴ mol / min for 30 minutes to supply 100 nm thick silicon and zinc, Each of the light emitting layers 5 made of In _0.20 Ga _0.80 N doped to 5 × 10 ¹⁸ / cm ³ was formed.
[0020]
Subsequently, the temperature is maintained at 1100 ° C., N ₂ or H ₂ is 20 liter / min, NH ₃ is 10 liter / min, TMG is 1.12 × 10 ⁻⁴ mol / min, and TMA is 0.47 × 10 ⁻⁴ mol / min. Then, CP ₂ Mg was introduced at 2 × 10 ⁻⁵ mol / min for 0.6 minutes to form a clad layer 71 made of magnesium (Mg) -doped Al _0.08 Ga _0.92 N having a thickness of about 10 nm. The magnesium concentration of the cladding layer 71 is 5 × 10 ¹⁹ / cm ³ . In this state, the clad layer 71 is still an insulator having a resistivity of 10 ⁸ Ωcm or more.
[0021]
Next, the temperature is maintained at 1100 ° C., N ₂ or H ₂ is 20 liter / min, NH ₃ is 10 liter / min, TMG is 1.12 × 10 ⁻⁴ mol / min, and CP ₂ Mg is 2 × 10 The first contact layer 72 made of GaN doped with magnesium (Mg) having a film thickness of about 35 nm was formed at a rate of ⁻⁵ mol / min for 40 seconds. The magnesium concentration of the first contact layer 72 is 5 × 10 ¹⁹ / cm ³ . In this state, the first contact layer 72 is still an insulator having a resistivity of 10 ⁸ Ωcm or more.
[0022]
Next, the temperature is maintained at 1100 ° C., N ₂ or H ₂ is 20 liter / min, NH ₃ is 10 liter / min, TMG is 1.12 × 10 ⁻⁴ mol / min, and CP ₂ Mg is 4 × 10. ^A p ⁺ second contact layer 73 made of magnesium (Mg) -doped GaN having a thickness of about 5 nm was formed at a ^{rate of −5} mol / min for 18 seconds. The magnesium concentration of the second contact layer 73 is 1 × 10 ²⁰ / cm ³ . In this state, the second contact layer 73 is still an insulator having a resistivity of 10 ⁸ Ωcm or more.
[0023]
Next, the second contact layer 73, the first contact layer 72, and the clad layer 71 were uniformly irradiated with an electron beam using an electron beam irradiation apparatus. The electron beam irradiation conditions are an acceleration voltage of about 10 KV, a data current of 1 μA, a beam moving speed of 0.2 mm / sec, a beam diameter of 60 μmφ, and a degree of vacuum of 5.0 × 10 ⁻⁵ Torr. By this electron beam irradiation, the second contact layer 73, the first contact layer 72, and the cladding layer 71 have a hole concentration of 6 × 10 ¹⁷ / cm ³ , 3 × 10 ¹⁷ / cm ³ , and 2 × 10 ¹⁷ / cm, respectively. ^3. A p-conductivity semiconductor with resistivity of 2 Ωcm, 1 Ωcm, and 0.7 Ωcm was obtained. A wafer having a multilayer structure was thus obtained.
[0024]
Next, as shown in FIG. 2, a Ti (titanium) layer 111 having a thickness of 1000 mm is formed on the second contact layer 73 by vacuum deposition, and a Ni (nickel) layer 112 is formed thereon with a thickness of 1 μm. Form. Then, a photoresist 12 is applied on the Ni layer 112, and by photolithography, as shown in FIG. 2, on the second contact layer 73, a photoresist at the electrode formation site A ^′ for the high carrier concentration n ⁺ layer 3 is applied. 12 was removed. Next, as shown in FIG. 3, the Ti layer 111 and the Ni layer 112 not covered with the photoresist 12 were removed by wet etching with an acid.
[0025]
Next, after dry etching the second contact layer 73, the first contact layer 72, the clad layer 71, the light emitting layer 5, and the n layer 4 at portions not covered by the Ti layer 111 and the Ni layer 112 with BCl ₃ gas. Subsequently, dry etching was performed with Ar. In this step, as shown in FIG. 4, a hole A for extracting an electrode from the high carrier concentration n ⁺ layer 3 was formed. Thereafter, the photoresist 12, the Ti layer 111, and the Ni layer 112 as a mask were removed.
[0026]
Next, after uniformly applying a photoresist, a window was opened in a portion where the transparent electrode 9 was to be formed by a photolithography process. Thereafter, two layers of Ni / Au were uniformly deposited and the photoresist was removed, that is, the transparent electrode 9 was formed on the second contact layer 73 by a lift-off method. Then, two layers of Ni / Au were vapor-deposited on a part of the transparent electrode 9 to form a pad 10. On the other hand, for the n ⁺ layer 3, an electrode 8 was formed by vapor-depositing aluminum by the same process. Thereafter, the wafer processed as described above was cut for each element to obtain a light emitting diode having the structure shown in FIG. The light emitting device had a driving current of 20 mA, an emission peak wavelength of 430 nm, and an emission intensity of 1500 mCd. The emission intensity has tripled compared to the conventional LED.
[0027]
The surface morphology of the uppermost second contact layer 73 in the case where the GaN n layer 31 was provided to form the light emitting device having the above-described structure was observed with a microscope. The surface micrograph is shown in FIG. Further, unlike the conventional light emitting device, the n ⁺ layer 3 is formed directly on the buffer layer 2 without providing the n layer 31, and the second contact layer 73 as the uppermost layer when the light emitting device is formed. The surface morphology was observed with a microscope. The surface micrograph is shown in FIG. Both are 200 × photomicrographs.
[0028]
As can be seen from this photograph, it is understood that the crystallinity is improved when the n layer 31 is provided and each layer is laminated thereon.
[0029]
In the above embodiment, the n layer 4 is formed between the high carrier concentration n ⁺ layer 3 and the light emitting layer 5, but when the impurity carrier concentration of the high carrier concentration n ⁺ layer 3 is relatively low, The light emitting layer 5 may be grown directly on the carrier concentration n ⁺ layer 3.
In the above embodiment, silicon is added to the n layer 31 at 2 × 10 ¹⁸ / cm ^{3 so} as to have an electron concentration of 1 × 10 ¹⁸ / cm ³ , but it may be not added. When the silicon concentration is 2 × 10 ¹⁸ / cm ³ and the electron concentration is less than 1 × 10 ¹⁸ / cm ³ , it has been confirmed that the crystallinity of each layer grown thereon is good.
[0030]
Further, although the thickness of the n layer 31 is 0.6 μm, since the n layer 31 exists to improve the crystallinity of each layer that grows on the n layer 31, the crystallinity is improved in the range of 100 μm to 2 μm. It has been confirmed that there is an effect.
In the above embodiment, the carrier concentration of the high carrier concentration n ⁺ layer 3 is 2 × 10 ¹⁸ / cm ³ and the silicon concentration is 4 × 10 ¹⁸ / cm ³ , but the carrier concentration is 1 × 10 ¹⁶ to 1 × 10 ^19. / cm ³ and silicon concentration in the range of 1 × 10 ¹⁷ to 1 × 10 ²⁰ / cm ³ , the crystallinity of the layer grown thereon can be improved and the resistance can be reduced. Further, although the thickness of the high carrier concentration n ⁺ layer 3 is 4.0 μm, the thickness of the high carrier concentration n ⁺ layer 3 is optimally in the range of 0.5 to 10 μm from the same viewpoint as the carrier concentration.
[0031]
The n layer 4 has a silicon concentration of 1 × 10 ¹⁸ / cm ³ and an electron concentration of 5 × 10 ¹⁷ / cm ³ , but a silicon concentration of 2 × 10 ¹⁶ to 2 × 10 ¹⁹ / cm ^{3 of} electron concentration 1 × 10 ¹⁶ to 1 × 10 ¹⁹ / cm ³ is an appropriate range. Further, the thickness is 0.5 μm, but 0.5 to 2 μm is desirable. When the film thickness is 0.5 μm or less, the emission intensity decreases, and when the film thickness is 2 μm or more, the series resistance becomes too high, and heat is generated when a current is applied, which is undesirable.
[0032]
In the above embodiment, the contact layer has a two-layer structure, but may have a one-layer structure.
In _0.20 Ga _0.80 N was used for the light emitting layer 5, but any composition ratio of constituent elements can be used as long as it is a binary, ternary or quaternary InGaAlN group III nitride semiconductor. For the cladding layer 71, the first contact layer 72, and the second contact layer 73, a semiconductor having a wider band gap than the light emitting layer 5 is required. These layers can also use binary, ternary, and quaternary group III nitride semiconductors. Similarly, the n-layer 31, the n ⁺ -layer 3, and the n-layer 4 can be made of a binary, ternary, or quaternary group III nitride semiconductor having an arbitrary composition ratio of the general formula InGaAlN.
[0033]
The silicon concentration and zinc concentration of the light emitting layer 5 are preferably 1 × 10 ¹⁷ to 1 × 10 ²⁰ / cm ³ , respectively. If it is 1 × 10 ¹⁷ / cm ³ or less, the light emission efficiency is lowered due to insufficient emission center, and if it is 1 × 10 ²⁰ / cm ³ or more, the crystallinity is deteriorated and the Auger effect is generated. The range of 1 × 10 ¹⁸ to 1 × 10 ¹⁹ / cm ³ is more preferable. The concentration of silicon (Si) is preferably 10 times to 1/10, more preferably about 1 to 1/10 or less, compared to zinc (Zn).
[0034]
In the above embodiment, the light emitting layer 5 is a single layer, but the general formula Al _x1 Ga _y1 In _1-x1-y1 N (0 ≦ x1 ≦ 1 _, 0 ≦ y1 ≦ 1,0 ≦ x1 + y1 <1 ) Well layer and a barrier layer of the general formula Al _x2 Ga _y2 In _1-x2-y2 N (0 ≤x2 ≤1 _, 0 ≤y2 ≤1,0 ≤x2 + y2 ≤1) You may comprise in a well structure. In that case, a donor impurity and an acceptor impurity may be added simultaneously to the well layer or the barrier layer, or a donor impurity or acceptor impurity may be added to the well layer, and an acceptor impurity or donor impurity may be added to the barrier layer. You may do it. Further, the present invention can be used for a laser diode in addition to a light emitting diode.
[0035]
As the acceptor impurities, the group 2 elements beryllium (Be), magnesium (Mg), zinc (Zn), cadmium (Cd), and mercury (Hg) may be used. When a group 2 element is used as an acceptor impurity, carbon (C), silicon (Si), germanium (Ge), tin (Sn), and lead (Pb) that are group 4 elements can be used as donor impurities. . When a group 4 element is an acceptor impurity, a group 6 element of sulfur (S), selenium (Se), or tellurium (Te) can also be used as a donor impurity. The p-type can be formed by electron beam irradiation, thermal annealing, heat treatment in N ₂ plasma gas, or laser irradiation.
The impurity concentration of the first low impurity concentration layer is desirably 4 × 10 ¹⁸ / cm ³ or less. If the impurity concentration exceeds 4 × 10 ¹⁸ / cm ³ , the crystallinity of each layer formed thereon is lowered, which is not desirable. Also, the layer formed closer to the substrate may be an n-conducting n-layer or a p-conducting p-layer, but in terms of p-type activation, the layer closer to the substrate should be an n-layer. Easy to manufacture. When the layer closer to the substrate is an n-layer, the above carrier concentration means the electron concentration, and the above impurity means the donor impurity. Further, when the layer closer to the substrate is a p-layer, the above carrier concentration means the hole concentration, and the above impurity means the acceptor impurity. The numerical ranges of the carrier concentration, impurity concentration, and layer thickness are desirable ranges for both the n layer and the p layer.
[Brief description of the drawings]
FIG. 1 is a configuration diagram illustrating a configuration of a light emitting diode according to a first specific example of the present invention.
FIG. 2 is a cross-sectional view showing a manufacturing process of the light-emitting diode of the same example.
FIG. 3 is a cross-sectional view showing a manufacturing process of the light-emitting diode of the example.
FIG. 4 is a cross-sectional view showing a manufacturing process of the light-emitting diode of the same example.
FIG. 5 is a photomicrograph observing the surface state of the uppermost layer when a first low impurity concentration layer (n layer) is formed in the light emitting diode.
FIG. 6 is a photomicrograph of the surface state of the uppermost layer when the first low impurity concentration layer (n layer) is not formed in the light emitting diode.
[Explanation of symbols]
100: Semiconductor element 1 ... Sapphire substrate 2 ... Buffer layer 31 ... n layer (first low impurity concentration layer)
3. High carrier concentration n ⁺ layer (high impurity concentration layer)
4 ... n layer (second low impurity concentration layer)
DESCRIPTION OF SYMBOLS 5 ... Light emitting layer 6 ... Cap layer 71 ... Cladding layer 72 ... 1st contact layer 73 ... 2nd contact layer 8 ... Electrode 9 ... Transparent electrode 10 ... Pad

Claims (8)

In a light emitting device having an n layer, a light emitting layer, and a p layer made of a group III nitride semiconductor formed on a substrate,
A buffer layer formed on the substrate;
A layer of undoped thickness formed on the buffer layer is 100 Å~ 2 μ m,
An n-type high impurity concentration layer in which the silicon concentration formed on the impurity-free layer is in the range of 1 × 10 ¹⁷ to 1 × 10 ²⁰ / cm ³ and the thickness is 0.5 to 10 μm;
a p-type contact layer;
A contact electrode provided on the high impurity concentration layer;
A light emitting device comprising: a transparent electrode comprising a double layer of nickel and gold provided on the contact layer. In a light emitting device having an n layer, a light emitting layer, and a p layer made of a group III nitride semiconductor formed on a substrate,
A buffer layer formed on the substrate;
A layer of undoped thickness formed on the buffer layer is 100 Å~ 2 μ m,
An n-type high impurity concentration layer in which the silicon concentration formed on the impurity-free layer is in the range of 1 × 10 ¹⁷ to 1 × 10 ²⁰ / cm ³ and the thickness is 0.5 to 10 μm;
A light emitting element comprising: an n layer provided between the high impurity concentration layer and the light emitting layer and having an impurity concentration lower than that of the high impurity concentration layer. a p-type contact layer;
A contact electrode provided on the high impurity concentration layer;
The light emitting device according to claim 2, further comprising: a transparent electrode provided on the contact layer. The light emitting device according to claim 3, wherein the transparent electrode comprises a double layer of nickel and gold. The light emitting device according to claim 1, wherein the light emitting layer has a multiple quantum well structure. The light emitting device according to claim 1, wherein the light emitting layer has a single quantum well structure. The light emitting element according to claim 1, wherein the impurity-free layer is made of GaN. The light emitting device according to claim 1, wherein the high impurity concentration layer is made of GaN.

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