JP2007161944A - Phosphor - Google Patents
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- JP2007161944A JP2007161944A JP2005362978A JP2005362978A JP2007161944A JP 2007161944 A JP2007161944 A JP 2007161944A JP 2005362978 A JP2005362978 A JP 2005362978A JP 2005362978 A JP2005362978 A JP 2005362978A JP 2007161944 A JP2007161944 A JP 2007161944A
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- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 title claims abstract description 45
- 230000003746 surface roughness Effects 0.000 claims abstract description 19
- 229910010272 inorganic material Inorganic materials 0.000 claims abstract description 6
- 239000011147 inorganic material Substances 0.000 claims abstract description 6
- 239000013078 crystal Substances 0.000 claims description 45
- 239000011521 glass Substances 0.000 claims description 34
- 230000005284 excitation Effects 0.000 claims description 25
- 239000002223 garnet Substances 0.000 claims description 22
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 12
- 229910018068 Li 2 O Inorganic materials 0.000 claims description 11
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 10
- 229910005793 GeO 2 Inorganic materials 0.000 claims description 10
- 239000006104 solid solution Substances 0.000 claims description 7
- 229910005191 Ga 2 O 3 Inorganic materials 0.000 claims description 6
- 239000000126 substance Substances 0.000 claims description 5
- 229910052688 Gadolinium Inorganic materials 0.000 claims description 4
- 230000000295 complement effect Effects 0.000 claims description 2
- 238000000151 deposition Methods 0.000 claims 1
- 239000011347 resin Substances 0.000 abstract description 22
- 229920005989 resin Polymers 0.000 abstract description 22
- 230000006866 deterioration Effects 0.000 abstract description 12
- 230000000694 effects Effects 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 239000002131 composite material Substances 0.000 description 7
- 239000011248 coating agent Substances 0.000 description 6
- 238000000576 coating method Methods 0.000 description 6
- 238000004031 devitrification Methods 0.000 description 6
- 238000000295 emission spectrum Methods 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 230000007774 longterm Effects 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 238000004904 shortening Methods 0.000 description 4
- 239000000470 constituent Substances 0.000 description 3
- 238000002425 crystallisation Methods 0.000 description 3
- 230000008025 crystallization Effects 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 229910052733 gallium Inorganic materials 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 238000004017 vitrification Methods 0.000 description 3
- 229910052771 Terbium Inorganic materials 0.000 description 2
- 229910052769 Ytterbium Inorganic materials 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 239000003086 colorant Substances 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000004973 liquid crystal related substance Substances 0.000 description 2
- 229910052749 magnesium Inorganic materials 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 2
- 230000001376 precipitating effect Effects 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 229910052706 scandium Inorganic materials 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000004040 coloring Methods 0.000 description 1
- 239000006059 cover glass Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000007496 glass forming Methods 0.000 description 1
- 230000017525 heat dissipation Effects 0.000 description 1
- 230000020169 heat generation Effects 0.000 description 1
- 238000005286 illumination Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910052697 platinum Inorganic materials 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000000634 powder X-ray diffraction Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000002035 prolonged effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000004044 response Effects 0.000 description 1
- 238000001228 spectrum Methods 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/04—Glass compositions containing silica
- C03C3/062—Glass compositions containing silica with less than 40% silica by weight
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/04—Glass compositions containing silica
- C03C3/062—Glass compositions containing silica with less than 40% silica by weight
- C03C3/064—Glass compositions containing silica with less than 40% silica by weight containing boron
- C03C3/068—Glass compositions containing silica with less than 40% silica by weight containing boron containing rare earths
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/04—Glass compositions containing silica
- C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
- C03C3/095—Glass compositions containing silica with 40% to 90% silica, by weight containing rare earths
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Geochemistry & Mineralogy (AREA)
- Life Sciences & Earth Sciences (AREA)
- Organic Chemistry (AREA)
- Ceramic Engineering (AREA)
- Crystallography & Structural Chemistry (AREA)
- Dispersion Chemistry (AREA)
- Glass Compositions (AREA)
- Luminescent Compositions (AREA)
- Led Device Packages (AREA)
Abstract
Description
本発明は、蛍光体に関するものである。 The present invention relates to a phosphor.
１９９３年に発表された青色の発光ダイオード（ＬＥＤ：Ｌｉｇｈｔ Ｅｍｉｔｔｉｎｇ Ｄｉｏｄｅ）により光の３原色ＲＧＢ（Ｒ：赤色、Ｇ：緑色、Ｂ：青色）のＬＥＤが揃い、これらのＬＥＤを並べて用いることによって白色光を得ることが提案されている。しかし、三色のＬＥＤの発光出力が異なるため、各色個別の駆動回路が必要であり、制御性に問題があった。また、各色の発光ダイオードの色劣化速度が異なるため、白色光の長期安定性に問題があった。 The LEDs of the three primary colors RGB (R: red, G: green, B: blue) are aligned by blue light-emitting diodes (LEDs: Light Emitting Diodes) announced in 1993, and these LEDs are used side by side to produce white. It has been proposed to obtain light. However, since the light emission outputs of the three color LEDs are different, a drive circuit for each color is necessary, and there is a problem in controllability. Further, since the color deterioration rates of the light emitting diodes of the respective colors are different, there is a problem in long-term stability of white light.
これを解決するために、青色ＬＥＤチップと、青色ＬＥＤチップから発せられた青色光線によって黄色発光するＹＡＧ蛍光体を組合せたＬＥＤが開発された（例えば、特許文献１：特開２０００−２０８８１５号公報参照。）。これは、１種類のＬＥＤで白色光が得られるため、低コストで、白色光の長期安定性にも優れる。また、この白色ＬＥＤは、従来の照明装置等の光源に比べ、長寿命、高効率、高安定性、低消費電力、高応答速度、環境負荷物質を含まない等の利点を有しているため、現在、ほとんどの携帯電話やデジタルカメラ等の液晶バックライトにはこの形態の白色ＬＥＤが使用されている。今後はこの白色ＬＥＤは、白熱電球や蛍光灯に替わる次世代の光源として照明用途への応用が期待されている。
しかし、特許文献１に記載の白色ＬＥＤは、青色の光を発光する発光素子の上に、粉末状の蛍光体と樹脂からなる複合体（コーティング部材）が設けられた構造を有し、発光素子から発せられた青色の励起光を粉末状の蛍光体に当てることによって、蛍光体から発せられた黄色の蛍光と、樹脂を透過した青色の励起光とが混色して、粉末状の蛍光体と樹脂とからなる複合体（コーティング部材）が白色光を発するが、長期使用時に、この樹脂がＬＥＤチップの発熱、あるいはそれから発せられる光によって、徐々に劣化して変色あるいは変形し、これが白色発光ダイオードの発光強度や寿命を低下させる原因となっている。 However, the white LED described in Patent Document 1 has a structure in which a composite (coating member) made of a powdered phosphor and a resin is provided on a light emitting element that emits blue light. When the blue excitation light emitted from the phosphor is applied to the powdered phosphor, the yellow fluorescence emitted from the phosphor and the blue excitation light transmitted through the resin are mixed, and the powdered phosphor A composite (coating member) made of a resin emits white light, but during long-term use, the resin gradually deteriorates and discolors or deforms due to heat generated from the LED chip or light emitted from the LED chip. This is a white light emitting diode. This is a cause of lowering the light emission intensity and life of the product.
また、粉末状の蛍光体と樹脂とからなる複合体（コーティング部材）がＬＥＤチップを覆うように固定されるため、その樹脂の塗布条件によっては粉末状の蛍光体と樹脂とからなる複合体（コーティング部材）の厚みにばらつきが生じやすく、それが発光色の配光性を低下させる原因となっている。また、特許文献１に記載の白色ＬＥＤは、蛍光体を固定するための樹脂や、ＬＥＤチップ及びコーティング部材全体を保護するための樹脂からなるモールド部材が必要となり、複雑な構造を有する。 In addition, since a composite (coating member) made of powdered phosphor and resin is fixed so as to cover the LED chip, a composite made of powdered phosphor and resin (depending on the application condition of the resin) Variations in the thickness of the coating member) are likely to occur, which causes a reduction in the light distribution of the luminescent color. Further, the white LED described in Patent Document 1 requires a mold member made of a resin for fixing the phosphor and a resin for protecting the LED chip and the entire coating member, and has a complicated structure.
このように、白色ＬＥＤは、耐熱性や耐光性に優れることが要求され、さらに屋外や水中等の厳しい環境での使用を考えると耐候性に優れることも必要である。 As described above, the white LED is required to be excellent in heat resistance and light resistance, and is also required to be excellent in weather resistance in consideration of use in severe environments such as outdoors and underwater.
本発明は、耐熱性、耐光性及び耐候性に優れ、従来の樹脂の劣化による発光ダイオード等のデバイスの発光強度劣化や短寿命化を抑制できる塊状蛍光体を提供することを目的とする。 An object of the present invention is to provide a bulk phosphor that is excellent in heat resistance, light resistance, and weather resistance, and that can suppress deterioration in light emission intensity and shortening of lifetime of a device such as a light emitting diode due to deterioration of a conventional resin.
本発明の塊状蛍光体は、無機材料のみから構成され、その表面粗さ（Ｒａ）が０．０５〜３μｍの範囲内にあることを特徴とする。 The bulk phosphor of the present invention is composed only of an inorganic material and has a surface roughness (Ra) in the range of 0.05 to 3 μm.
このような構成によれば、耐熱性、耐光性及び耐候性に優れ、従来の樹脂の劣化による発光ダイオード等のデバイスの発光強度劣化や短寿命化を抑制できる。すなわち、蛍光体が有機物質である樹脂を含まず、耐熱性、耐光性及び耐候性に優れた無機材料のみから構成され、これを発光ダイオード等のデバイスに使用した場合、樹脂を使用せずにデバイスを構成できるため、従来の発光ダイオードにおいて見られるようなＬＥＤチップの発熱、あるいはそれから発せられる光による樹脂の着色や変形による劣化がない。その結果、発光ダイオード等のデバイスの発光強度が劣化し難く寿命が長くなる。また、高温の厳しい環境下においても、例えば１５０℃の高温下で６００時間保持しても、発光ダイオードの発光特性が変化し難くなる。また、太陽光等からの紫外線に曝されても、樹脂を含まないため樹脂による着色や劣化がない。また、厳しい長期間の高温高湿環境下（２０００時間、温度８５℃、湿度８５％）においても、発光ダイオードの発光特性が変化し難くなる。 According to such a structure, it is excellent in heat resistance, light resistance, and weather resistance, and can suppress the light emission intensity degradation and lifetime shortening of devices, such as a light emitting diode, by the deterioration of the conventional resin. That is, the phosphor does not contain an organic resin and is composed of only an inorganic material having excellent heat resistance, light resistance and weather resistance. When this is used for a device such as a light emitting diode, the resin is not used. Since the device can be configured, there is no deterioration due to the coloration or deformation of the resin due to the heat generation of the LED chip as seen in conventional light emitting diodes or the light emitted therefrom. As a result, the light emission intensity of a device such as a light-emitting diode is unlikely to deteriorate and the life is prolonged. Further, even in a severe environment of high temperature, for example, even if it is held at a high temperature of 150 ° C. for 600 hours, the light emission characteristics of the light emitting diode are difficult to change. Further, even when exposed to ultraviolet rays from sunlight or the like, the resin is not contained, and therefore, there is no coloring or deterioration due to the resin. In addition, the light-emitting characteristics of the light-emitting diode hardly change even under a severe long-term high-temperature and high-humidity environment (2000 hours, temperature 85 ° C., humidity 85%).
しかも、塊状蛍光体は、表面粗さ（Ｒａ）が０．０５〜３μｍの範囲内にあるため、それを用いた発光ダイオードの発光効率が高い。すなわち、表面粗さが０．０５μｍよりも小さいと、反射による損失が大きくなり発光効率は低下する。逆に表面粗さ（Ｒａ）が３μｍよりも大きいと散乱による損失が大きくなり発光効率が低下する。表面粗さの好ましい範囲は０．１〜０．５μｍ、より好ましい範囲は０．１５〜０．２５μｍである。 Moreover, since the bulk phosphor has a surface roughness (Ra) in the range of 0.05 to 3 μm, the light emitting diode using the phosphor has high luminous efficiency. That is, when the surface roughness is less than 0.05 μm, the loss due to reflection increases and the light emission efficiency decreases. On the other hand, if the surface roughness (Ra) is larger than 3 μm, the loss due to scattering increases and the light emission efficiency decreases. A preferable range of the surface roughness is 0.1 to 0.5 μm, and a more preferable range is 0.15 to 0.25 μm.
上記した構成において、塊状蛍光体が、紫外光線又は可視光線からなる励起光を入射すると、該励起光よりも長波長の蛍光を発すると、これを用いた発光ダイオード等のデバイスの構造が簡単になるため好ましい。 In the above-described configuration, when the bulk phosphor emits excitation light composed of ultraviolet light or visible light, and emits fluorescence having a wavelength longer than that of the excitation light, the structure of a device such as a light emitting diode using the light can be simplified. Therefore, it is preferable.
上記した構成において、可視光線からなる励起光を入射すると、該励起光の色相に対して補色の蛍光を発し、かつ該励起光を一部透過すると、それ自身を透過した透過励起光と蛍光との混色により、白色光を発光するため、白色発光デバイスに好適に使用できる。 In the configuration described above, when excitation light composed of visible light is incident, fluorescence of complementary color is emitted with respect to the hue of the excitation light, and when part of the excitation light is transmitted, transmitted excitation light and fluorescence transmitted through itself Since white light is emitted by the color mixture, it can be suitably used for a white light emitting device.
上記した構成において、前記可視光線からなる励起光は、中心波長が４３０〜４９０ｎｍの光線であり、前記蛍光は、中心波長が５３０〜５９０ｎｍの光線であると、白色光を得やすいため好ましい。 In the above-described configuration, it is preferable that the excitation light composed of visible light is light having a central wavelength of 430 to 490 nm, and the fluorescence is light having a central wavelength of 530 to 590 nm because white light can be easily obtained.
上記した構成において、塊状蛍光体が、板状体からなると、従来の白色発光ダイオードにおける粉末状の蛍光体と樹脂からなる複合体の代替材料として、あるいはその板状体の下面に青色ＬＥＤを複数個設置することによって、発光機能と拡散機能を兼ね備えた面発光デバイスの構成部材として利用することが可能である。また、青色発光ダイオードチップ上に固定せずにカバーガラスとして用いるだけで白色光を発し、シンプルな構造の白色発光ダイオードを構成することも可能である。また、厚みを一定にすることが容易となり、均質な白色光を得ることができる。また、厚みを変化させるだけで、励起光強度と蛍光強度とのバランスを自由に変化させることができるため、所望の色度あるいは色温度の白色光が得られる。 In the above-described configuration, when the massive phosphor is made of a plate-like body, a plurality of blue LEDs are used as an alternative material for the composite of powdered phosphor and resin in the conventional white light emitting diode, or on the lower surface of the plate-like body. By installing them individually, it can be used as a constituent member of a surface emitting device having both a light emitting function and a diffusing function. Further, it is possible to form a white light emitting diode having a simple structure by emitting white light only by using it as a cover glass without being fixed on the blue light emitting diode chip. Moreover, it becomes easy to make thickness constant and uniform white light can be obtained. Further, since the balance between the excitation light intensity and the fluorescence intensity can be freely changed simply by changing the thickness, white light having a desired chromaticity or color temperature can be obtained.
上記した構成において、板状体の蛍光体の肉厚が０．１ｍｍ〜２ｍｍであると、色温度の高い白色光から低い白色光までの所望の白色光が得られるため好ましい。肉厚が０．１ｍｍよりも薄いと、励起光に対する蛍光強度が小さく、全体として青みが強く白色光が得られ難い。肉厚が２ｍｍよりも厚いと、逆に励起光に対して蛍光強度が強く、黄色味が強く白色が得られにくい。より好ましい肉厚は、０．１〜１ｍｍであり、さらに好ましくは０．３ｍｍ〜０．７ｍｍである。 In the above-described configuration, it is preferable that the thickness of the plate-like phosphor is 0.1 mm to 2 mm because desired white light from white light having a high color temperature to low white light can be obtained. When the wall thickness is less than 0.1 mm, the fluorescence intensity with respect to the excitation light is small, and the whole is strongly bluish and it is difficult to obtain white light. If the wall thickness is thicker than 2 mm, on the contrary, the fluorescence intensity is strong with respect to the excitation light, and the yellow color is strong and it is difficult to obtain white. More preferable thickness is 0.1-1 mm, More preferably, it is 0.3 mm-0.7 mm.
上記した構成において、前記板状体の表裏面のうち少なくとも一方の面の表面粗さ（Ｒａ）が０．０５〜３μｍであれば、高い発光効率が得られるため好ましい。 In the above configuration, it is preferable that the surface roughness (Ra) of at least one of the front and back surfaces of the plate-like body is 0.05 to 3 μm because high luminous efficiency can be obtained.
また、上記した構成において、塊状蛍光体が、結晶化ガラスからなると、用途に応じて、任意形状、例えば、板形状、球形状、非球面レンズ形状、ロッド形状、円筒形状、円板形状、ファイバー形状等に容易に成形して使用することが可能となる。 In the above-described configuration, when the bulk phosphor is made of crystallized glass, it has an arbitrary shape, for example, a plate shape, a spherical shape, an aspheric lens shape, a rod shape, a cylindrical shape, a disc shape, a fiber, depending on the application. It can be easily formed into a shape and used.
また、上記した構成において、前記結晶化ガラスが、１２０ＭＰａ以上の曲げ強度を有していることが好ましい。このようにすれば蛍光体を大型化しても割れることがなく、また、加工プロセスにおける割れの問題も生じ難い。 In the above configuration, the crystallized glass preferably has a bending strength of 120 MPa or more. In this way, even if the phosphor is increased in size, it does not break, and the problem of cracking in the processing process hardly occurs.
また、上記した構成において、前記結晶化ガラスが、２．００Ｗ／ｍ／Ｋ以上の熱伝導率を有していることが好ましい。このようにすれば、蛍光体が放熱性に優れ、励起用青色ＬＥＤチップと接した状態で使用する場合、ＬＥＤチップからの熱を放出しやすい。 In the above-described configuration, the crystallized glass preferably has a thermal conductivity of 2.00 W / m / K or more. In this way, the phosphor is excellent in heat dissipation, and when used in contact with the excitation blue LED chip, it is easy to release heat from the LED chip.
上記した構成において、前記結晶化ガラスが、Ｃｅ3+を含有したガーネット結晶を析出してなると、ガーネット結晶中に含まれるＣｅ3+が発光中心となり、青色の励起光を吸収し、黄色の蛍光を発するようになり、青色の励起光の一部が透過し、透過励起光と蛍光の混色により白色光を発する蛍光体となる。 In the above configuration, the crystallized glass and formed by precipitating garnet crystal containing Ce 3+, Ce 3+ contained in the garnet crystal becomes a luminescent center, absorbs the blue excitation light, yellow fluorescence Thus, a part of the blue excitation light is transmitted, and a phosphor that emits white light by mixing the transmitted excitation light and the fluorescence is obtained.
上記した構成において、前記結晶化ガラスが、非晶質ガラスを熱処理することによってガーネット結晶を析出してなると、ガーネット結晶が結晶化ガラスのマトリックスガラス中に泡を巻き込むことなく分散して存在する。そのため、蛍光や透過励起光の一部があらゆる方向に散乱して、蛍光体自身が散乱板の役目も果たし、白色光が広角度に広がる。また、マトリックスガラス中又はマトリックスガラスと析出結晶の界面には、二種以上の異なる材料の複合体中又は異なる材料の界面に見られるような泡がないため、蛍光や透過励起光のうち、析出結晶によって散乱しない蛍光や透過励起光が透過しやすく、そのため発光効率が高くなる。 In the above-described configuration, when the crystallized glass is formed by precipitating garnet crystals by heat-treating amorphous glass, the garnet crystals are dispersed and present in the crystallized glass matrix glass without entraining bubbles. Therefore, a part of the fluorescence and transmitted excitation light is scattered in all directions, the phosphor itself also serves as a scattering plate, and white light spreads over a wide angle. In addition, there are no bubbles in the matrix glass or at the interface between the matrix glass and the precipitated crystal, as seen in the composite of two or more different materials or at the interface between different materials. Fluorescence that is not scattered by the crystal or transmitted excitation light is likely to be transmitted, so that the luminous efficiency is increased.
尚、ガーネット結晶とは、一般的にはＡ3Ｂ2Ｃ3Ｏ12で表される結晶（Ａ＝Ｍｇ、Ｍｎ、Ｆｅ、Ｃａ、Ｙ、Ｇｄ、Ｔｂ、Ｙｂ等：Ｂ＝Ａｌ、Ｃｒ、Ｆｅ、Ｇａ、Ｓｃ等：Ｃ＝Ａｌ、Ｓｉ、Ｇａ、Ｇｅ等）であり、上記したガーネット結晶として、特に、ＹＡＧ結晶（Ｙ3Ａｌ5Ｏ12結晶）又はＹＡＧ結晶固溶体であると、所望の黄色の蛍光を発するため好ましい。ＹＡＧ結晶固溶体としては、Ｙの一部をＧｄ、Ｓｃ、Ｃａ、Ｔｂ、Ｙｂ及びＭｇからなる群から選択された少なくとも１種の元素で、及び／又はＡｌの一部をＧａ、Ｓｉ、Ｇｅ及びＳｃからなる群から選択された少なくとも１種の元素で置換したＹＡＧ結晶固溶体であってもよい。 The garnet crystal is generally a crystal represented by A 3 B 2 C 3 O 12 (A = Mg, Mn, Fe, Ca, Y, Gd, Tb, Yb, etc .: B = Al, Cr, Fe, Ga, Sc, etc .: C = Al, Si, Ga, Ge, etc.), and the above garnet crystal is particularly desired to be a YAG crystal (Y 3 Al 5 O 12 crystal) or a YAG crystal solid solution. This is preferable because it emits yellow fluorescence. As a YAG crystal solid solution, a part of Y is at least one element selected from the group consisting of Gd, Sc, Ca, Tb, Yb and Mg, and / or a part of Al is Ga, Si, Ge and It may be a YAG crystal solid solution substituted with at least one element selected from the group consisting of Sc.
発光中心となるＣｅ2Ｏ3は、結晶化ガラス中に０．０１〜５モル％含有することが好ましい。Ｃｅ2Ｏ3の含有量が０．０１モル％よりも少ないと、発光中心成分としての役割を果たし難く、蛍光強度が充分でない。また、５モル％よりも多いと、濃度消光により発光効率が低くなるため好ましくない。Ｃｅ2Ｏ3の好ましい範囲は０．０１〜４モル％であり、より好ましくは０．３〜３モル％である。 Ce 2 O 3 serving as an emission center is preferably contained in the crystallized glass in an amount of 0.01 to 5 mol%. When the content of Ce 2 O 3 is less than 0.01 mol%, it is difficult to serve as a luminescent center component, and the fluorescence intensity is not sufficient. On the other hand, if it exceeds 5 mol%, the light emission efficiency is lowered by concentration quenching, which is not preferable. The preferred range of ce 2 O 3 is 0.01 to 4 mol%, more preferably from 0.3 to 3 mol%.
本発明の塊状蛍光体は、例えば、モル％で、ＳｉＯ2＋Ｂ2Ｏ3 １０〜６０％、Ａｌ2Ｏ3＋ＧｅＯ2＋Ｇａ2Ｏ3 １５〜５０％、Ｙ2Ｏ3＋Ｇｄ2Ｏ3＋Ｔｂ2Ｏ3＋Ｙｂ2Ｏ3 ５〜３０％、Ｌｉ2Ｏ ０〜２５％、Ｃｅ2Ｏ3 ０．０１〜５％含有する結晶化ガラスからなることが好ましい。 The bulk phosphor of the present invention is, for example, in mol%, SiO 2 + B 2 O 3 10-60%, Al 2 O 3 + GeO 2 + Ga 2 O 3 15-50%, Y 2 O 3 + Gd 2 O 3 + Tb 2. It is preferably made of crystallized glass containing 5 to 30% of O 3 + Yb 2 O 3 , 0 to 25% of Li 2 O, and 0.01 to 5% of Ce 2 O 3 .
また、本発明の塊状蛍光体は、モル％でＳｉＯ2 １０〜５０％、Ａｌ2Ｏ3 １５〜４５％、Ｙ2Ｏ3 ５〜３０％、ＧｅＯ2 ０〜１５％、Ｇｄ2Ｏ3 ０〜２０％、Ｌｉ2Ｏ ０〜１５％、ＣａＯ＋ＭｇＯ＋Ｓｃ2Ｏ3 ０〜３０％、Ｃｅ2Ｏ3 ０．０１〜５％含有してなる結晶化ガラスからなることがより好ましい。 In addition, the bulk phosphor of the present invention is SiO 2 10-50%, Al 2 O 3 15-45%, Y 2 O 3 5-30%, GeO 2 0-15%, Gd 2 O 3 0 in mol%. ~20%, Li 2 O 0~15% , CaO + MgO + Sc 2 O 3 0~30%, more preferably consisting of Ce 2 O 3 0.01~5% content was formed by crystallized glass.
次に、本発明の結晶化ガラスの組成を限定した理由を次に示す。 Next, the reason why the composition of the crystallized glass of the present invention is limited will be described below.
ＳｉＯ2とＢ2Ｏ3は、ガラスの網目形成酸化物で、母ガラス作成時にともに失透を抑制する成分であり、ＳｉＯ2とＢ2Ｏ3の含有量は合量で１０〜６０モル％であることが好ましい。ＳｉＯ2とＢ2Ｏ3の合量が１０モル％よりも少ないとガラス化せず、６０モル％よりも多いと所望の結晶が析出しにくくなる。ＳｉＯ2とＢ2Ｏ3の合量の好ましい範囲は、３０〜４７モル％である。ＳｉＯ2の含有量は１０〜５０モル％であることが好ましい。ＳｉＯ2が１０モル％よりも少ないとガラス化しにくく、５０モル％よりも多いと所望の結晶が析出しにくくなる。 SiO 2 and B 2 O 3 are glass network-forming oxides and are components that suppress devitrification at the time of making the mother glass. The total content of SiO 2 and B 2 O 3 is 10 to 60 mol%. It is preferable that When the total amount of SiO 2 and B 2 O 3 is less than 10 mol%, it does not vitrify, and when it exceeds 60 mol%, desired crystals are difficult to precipitate. A preferable range of the total amount of SiO 2 and B 2 O 3 is 30 to 47 mol%. The content of SiO 2 is preferably 10 to 50 mol%. When SiO 2 is less than 10 mol%, it is difficult to vitrify, and when it is more than 50 mol%, desired crystals are hardly precipitated.
Ａｌ2Ｏ3とＧａ2Ｏ3とＧｅＯ2も、ガーネット結晶の構成成分であるとともに、化学的耐久性を向上させる成分であり、Ａｌ2Ｏ3とＧａ2Ｏ3とＧｅＯ2の含有量は合量で１５〜５０モル％であることが好ましい。Ａｌ2Ｏ3とＧａ2Ｏ3とＧｅＯ2の含有量が合量で１５モル％よりも少ないと、ガーネット結晶が析出しにくく、また、化学的耐久性が低下する。また５０モル％よりも多いと、ガラス化しにくくなるとともにガーネット結晶が析出しにくくなるため好ましくない。Ａｌ2Ｏ3とＧａ2Ｏ3とＧｅＯ2の合量の好ましい範囲は、２０〜４０モル％である。Ａｌ2Ｏ3の含有量は１５〜４５モル％であることが好ましい。Ａｌ2Ｏ3含有量が１５モル％よりも少ないと、ガーネット結晶が析出しにくく、また、化学的耐久性が低下しやすい。また４５モル％よりも多いと、ガラス化しにくくなるとともに、異種結晶が析出するため好ましくない。また、ＧｅＯ2はガーネット結晶中に一部固溶し、結晶析出量を増加させる効果を有する。ＧｅＯ2の含有量は０〜１５モル％であることが好ましい。 Al 2 O 3 , Ga 2 O 3, and GeO 2 are also constituents of the garnet crystal and are components that improve chemical durability. The contents of Al 2 O 3 , Ga 2 O 3, and GeO 2 are as follows: The total amount is preferably 15 to 50 mol%. If the total content of Al 2 O 3 , Ga 2 O 3 and GeO 2 is less than 15 mol%, garnet crystals are difficult to precipitate and the chemical durability is lowered. On the other hand, if it is more than 50 mol%, it is difficult to vitrify and garnet crystals are difficult to precipitate. A preferable range of the total amount of Al 2 O 3 , Ga 2 O 3 and GeO 2 is 20 to 40 mol%. The content of Al 2 O 3 is preferably 15 to 45 mol%. If the Al 2 O 3 content is less than 15 mol%, garnet crystals are difficult to precipitate and the chemical durability tends to decrease. On the other hand, when it is more than 45 mol%, it is difficult to vitrify and a different crystal is precipitated, which is not preferable. Further, GeO 2 has a partly solid solution in the garnet crystal and has an effect of increasing the amount of crystal precipitation. The GeO 2 content is preferably 0 to 15 mol%.
Ｙ2Ｏ3、Ｇｄ2Ｏ3、Ｔｂ2Ｏ3及びＹｂ2Ｏ3は、ガーネット結晶の構成成分であるとともに、Ｃｅの均一分散能を向上させ、濃度消光を抑制する成分であり、Ｙ2Ｏ3、Ｇｄ2Ｏ3、Ｔｂ2Ｏ3及びＹｂ2Ｏ3の含有量は合量で５〜３０モル％であることが好ましい。Ｙ2Ｏ3、Ｇｄ2Ｏ3、Ｔｂ2Ｏ3及びＹｂ2Ｏ3の含有量が合量で５モル％よりも少ないと、ガーネット結晶が析出しにくく、３０モル％よりも多いと、ガラス化しにくくなるため好ましくない。Ｙ2Ｏ3、Ｇｄ2Ｏ3、Ｔｂ2Ｏ3及びＹｂ2Ｏ3の合量の好ましい範囲は、１０〜２５モル％である。Ｙ2Ｏ3含有量は５〜３０モル％であることが好ましい。Ｙ2Ｏ3の含有量が５モル％よりも少ないと、ガーネット結晶が析出しにくく、３０モル％よりも多いと、ガラス化しにくくなると共に、異種結晶が析出するため好ましくない。また、Ｇｄ2Ｏ3は蛍光波長を長波長化する効果や、母ガラスを作成する際ガラス化範囲を広げる効果も有する。Ｇｄ2Ｏ3の含有量は０〜２０モル％であることが好ましい。Ｇｄ2Ｏ3が２０モル％よりも多い場合はガーネット結晶が析出しにくくなる。Ｔｂ2Ｏ3はガラス化範囲を広げる効果や蛍光波長を調整する効果を有する。Ｔｂ2Ｏ3の含有量は０〜３０モル％であることが好ましい。３０モル％よりも多い場合はガーネット結晶が析出しにくくなる。Ｙｂ2Ｏ3はガラス化範囲を広げる効果や蛍光波長を調整する効果とともに、蛍光体の熱的安定性を向上させる働きがある。Ｙｂ2Ｏ3の含有量は０〜３０モル％であることが好ましい。３０モル％よりも多い場合はガーネット結晶が析出しにくくなる。 Y 2 O 3 , Gd 2 O 3 , Tb 2 O 3 and Yb 2 O 3 are components of the garnet crystal, are components that improve the uniform dispersibility of Ce and suppress concentration quenching, and Y 2 The total content of O 3 , Gd 2 O 3 , Tb 2 O 3 and Yb 2 O 3 is preferably 5 to 30 mol%. If the total content of Y 2 O 3 , Gd 2 O 3 , Tb 2 O 3 and Yb 2 O 3 is less than 5 mol%, garnet crystals are difficult to precipitate, and if it is more than 30 mol%, glass This is not preferable because it becomes difficult to convert. A preferable range of the total amount of Y 2 O 3 , Gd 2 O 3 , Tb 2 O 3 and Yb 2 O 3 is 10 to 25 mol%. The Y 2 O 3 content is preferably 5 to 30 mol%. If the content of Y 2 O 3 is less than 5 mol%, garnet crystals are difficult to precipitate, and if it is more than 30 mol%, it is difficult to vitrify and foreign crystals precipitate, which is not preferable. Gd 2 O 3 also has the effect of increasing the fluorescence wavelength and the effect of expanding the vitrification range when preparing the mother glass. The content of Gd 2 O 3 is preferably 0 to 20 mol%. When the amount of Gd 2 O 3 is more than 20 mol%, garnet crystals are hardly precipitated. Tb 2 O 3 has the effect of expanding the vitrification range and the effect of adjusting the fluorescence wavelength. The content of Tb 2 O 3 is preferably 0 to 30 mol%. When the amount is more than 30 mol%, garnet crystals are hardly precipitated. Yb 2 O 3 has the effect of improving the thermal stability of the phosphor as well as the effect of expanding the vitrification range and the effect of adjusting the fluorescence wavelength. The content of Yb 2 O 3 is preferably 0 to 30 mol%. When the amount is more than 30 mol%, garnet crystals are hardly precipitated.
Ｌｉ2Ｏは、結晶サイズを粗大化させず、また析出結晶量を減少させずに網目修飾酸化物としてガラスの粘性を調整する成分であり、Ｌｉ2Ｏの含有量は０〜２５モル％であることが好ましい。Ｌｉ2Ｏが２５モル％よりも多いとガラス成型時に多量の失透が発生しガラス化しにくく、結晶化のための熱処理を行なっても失透が消失せず好ましくない。特にＬｉ2Ｏが２モル％よりも多いと、ガーネット結晶が析出しやすくなるため好ましい。Ｌｉ2Ｏの好ましい範囲は、２〜１６モル％であり、さらに好ましい範囲は、２．５〜４．８モル％である。またＬｉ2Ｏが４モル％よりも少ない場合、及びＬｉ2Ｏが４モル％以上であってもＳｉＯ2とＢ2Ｏ3の合量が４０．５モル％以上である場合には、ガラス成形時に全く失透が見られないためより好ましい。尚、Ｌｉ2Ｏが４モル％よりも多く且つＳｉＯ2とＢ2Ｏ3の合量が４０．５モル％よりも少ない場合には、ガラス成形時に少量の失透が見られることがあるが、この失透は結晶化のための熱処理によって消失し、緻密なガーネット結晶が析出するため特に問題はない。 Li 2 O is a component that adjusts the viscosity of the glass as a network-modifying oxide without coarsening the crystal size and reducing the amount of precipitated crystals, and the content of Li 2 O is 0 to 25 mol%. Preferably there is. When the amount of Li 2 O is more than 25 mol%, a large amount of devitrification occurs during glass molding and it is difficult to vitrify, and devitrification does not disappear even when heat treatment for crystallization is performed. In particular, when Li 2 O is more than 2 mol%, garnet crystals are likely to precipitate, which is preferable. A preferable range of Li 2 O is 2 to 16 mol%, and a more preferable range is 2.5 to 4.8 mol%. Further, when Li 2 O is less than 4 mol%, and when Li 2 O is 4 mol% or more, the total amount of SiO 2 and B 2 O 3 is 40.5 mol% or more, glass It is more preferable because no devitrification is observed at the time of molding. When Li 2 O is more than 4 mol% and the total amount of SiO 2 and B 2 O 3 is less than 40.5 mol%, a small amount of devitrification may be observed during glass forming. This devitrification disappears by heat treatment for crystallization, and a dense garnet crystal is precipitated, so that there is no particular problem.
ＣａＯ、ＭｇＯ、Ｓｃ2Ｏ3はガーネット結晶中に固溶し、Ｃｅの発光波長を調整することができる成分である。ＣａＯ、ＭｇＯ、Ｓｃ2Ｏ3は合量で０〜３０モル％含有することが好ましい。３０モル％よりも多いと失透する。 CaO, MgO, and Sc 2 O 3 are components that can be dissolved in the garnet crystal to adjust the emission wavelength of Ce. CaO, MgO, and Sc 2 O 3 are preferably contained in a total amount of 0 to 30 mol%. When it exceeds 30 mol%, it devitrifies.
上記した成分以外にも、Ｎａ2Ｏ、ＣａＯ、ＭｇＯ、Ｋ2Ｏ等を単独又は合量で１５モル％まで添加できる。 In addition to the above components, Na 2 O, CaO, MgO, K 2 O, etc. can be added alone or in a total amount up to 15 mol%.
以上のように本発明の塊状蛍光体によれば、それを発光ダイオード等のデバイスに用いた場合、無機材料のみから構成され、樹脂を使用せずにデバイスを構成できるため、耐熱性、耐光性及び耐候性に優れ、従来の樹脂の劣化によるデバイスの発光強度劣化や短寿命化を防止できる。しかも、その表面粗さ（Ｒａ）が０．０５μｍ〜３μｍの範囲内にあるため、それを用いた発光ダイオードの発光効率が高い。また、用途に応じて、任意形状、例えば、板形状、球形状、非球面レンズ形状、ロッド形状、円筒形状、円板形状、ファイバー形状等に容易に成形して使用することが可能となる。 As described above, according to the bulk phosphor of the present invention, when it is used for a device such as a light-emitting diode, it is composed of only an inorganic material, and the device can be constructed without using a resin. Moreover, it is excellent in weather resistance, and can prevent deterioration of the light emission intensity and shortening of the lifetime of the device due to deterioration of the conventional resin. And since the surface roughness (Ra) exists in the range of 0.05 micrometer-3 micrometers, the light emission efficiency of the light emitting diode using it is high. Further, it can be easily formed into an arbitrary shape, for example, a plate shape, a spherical shape, an aspherical lens shape, a rod shape, a cylindrical shape, a disk shape, a fiber shape, etc. depending on the application.
以下、実施例について説明する。 Examples will be described below.
表１は本発明の実施例１〜８及び比較例１、２を示したものである。 Table 1 shows Examples 1 to 8 and Comparative Examples 1 and 2 of the present invention.
実施例の結晶化ガラスは以下のようにして作製した。 The crystallized glass of the example was produced as follows.
まず、表１に示した組成となるように調合したガラス原料を白金坩堝に入れ、１６５０℃にて３時間溶融した後、融液をカーボン板上に流し出すことによって結晶性ガラスを得た。次いでこれらの結晶性ガラスを表１中に示す結晶化温度で０．５〜２０時間熱処理することによって実施例１〜８及び比較例１、２の結晶化ガラスを得た。 First, a glass raw material prepared to have the composition shown in Table 1 was put in a platinum crucible, melted at 1650 ° C. for 3 hours, and then the melt was poured onto a carbon plate to obtain a crystalline glass. Next, the crystallized glasses of Examples 1 to 8 and Comparative Examples 1 and 2 were obtained by heat-treating these crystalline glasses at the crystallization temperature shown in Table 1 for 0.5 to 20 hours.
得られた結晶化ガラスを所望の形状に加工した後、研磨紙を用いて所望の表面粗さに仕上げた。表面粗さ（Ｒａ）は（株）東京精密製のサーフコム７５６Ａを用いて測定した。 The obtained crystallized glass was processed into a desired shape, and then finished to a desired surface roughness using abrasive paper. The surface roughness (Ra) was measured using Surfcom 756A manufactured by Tokyo Seimitsu Co., Ltd.
析出結晶種は、粉末Ｘ線回折法により同定し、表１において、析出結晶としてＹＡＧ結晶が析出したものについては“ＹＡＧ”とし、ＹＡＧ結晶固溶体が析出したものについては“ＹＡＧs.s.”とした。表１からわかるように、実施例１、２ではＹＡＧ結晶が析出し、実施例３〜８及び比較例１、２ではＹＡＧ結晶固溶体が析出していた。 Precipitated crystal seeds were identified by powder X-ray diffraction method. In Table 1, “YAG” was used when YAG crystals were deposited as precipitated crystals, and “YAGs.s.” was used when YAG crystal solid solutions were precipitated. did. As can be seen from Table 1, YAG crystals were precipitated in Examples 1 and 2, and YAG crystal solid solutions were precipitated in Examples 3 to 8 and Comparative Examples 1 and 2.
表１中の発光特性は次のようにして評価した。同じ厚みで異なる表面粗さを有するサンプルの後方から、青色ＬＥＤによって各サンプルを励起し、サンプル前方から発せられる光を積分球内で測定し、その発光スペクトルを得た。得られたスペクトルから発光効率を算出しその値が高いものについては、発光特性“〇”、低いものについては発光特性"דとした。図１は実施例５の発光スペクトルを示している。図１からわかるように、実施例５の発光スペクトルでは、中心波長が４３０〜４９０ｎｍにある透過励起光および、中心波長が５３０〜５９０ｎｍにある蛍光が観察された。他の実施例及び比較例についても同様形状の発光スペクトルが得られた。実施例１〜８については発光効率が高く発光特性は"〇"であった。また、実施例２の結晶化ガラスを、研磨方法を変えて表面粗さを変えた試料の発光効率を測定したところ、図２に示すように、実表面粗さ（Ｒａ）が、０．０５〜３μｍにおいて、高い発光効率を示すことがわかる。一方、比較例１及び２は、実施例５と同じ組成で表面粗さのみ異なるものであるが、比較例１については、表面粗さが大きく発光効率が低かった。また、比較例２については、表面粗さが小さく発光効率が小さかった。 The light emission characteristics in Table 1 were evaluated as follows. Each sample was excited by a blue LED from the back of the sample having the same thickness and different surface roughness, and the light emitted from the front of the sample was measured in an integrating sphere to obtain its emission spectrum. The light emission efficiency is calculated from the obtained spectrum, and the light emission characteristic is “◯” for the high value and the light emission characteristic “×” for the low value. FIG. 1 shows the emission spectrum of Example 5. As can be seen from FIG. 1, in the emission spectrum of Example 5, transmitted excitation light having a center wavelength of 430 to 490 nm and fluorescence having a center wavelength of 530 to 590 nm were observed. The emission spectrum of the same shape was obtained also about the other Example and the comparative example. In Examples 1 to 8, the light emission efficiency was high and the light emission characteristic was “◯”. In addition, when the crystallized glass of Example 2 was measured for the light emission efficiency of the sample with the surface roughness varied by changing the polishing method, the actual surface roughness (Ra) was 0.05 as shown in FIG. It can be seen that high luminous efficiency is exhibited at ˜3 μm. On the other hand, Comparative Examples 1 and 2 had the same composition as Example 5 but differed only in surface roughness, but Comparative Example 1 had a large surface roughness and low luminous efficiency. In Comparative Example 2, the surface roughness was small and the light emission efficiency was low.
また、実施例５について１５０℃で６００時間熱処理した際、熱処理前の発光強度に対する熱処理後の発光強度が９７％以上であり、耐熱性に優れていた。また、実施例２について、温度８５℃、湿度８５％の環境下で２０００時間処理する前の発光強度に対する処理後の発光強度が９３％以上であり、耐候性に優れていた。 Further, when heat treatment was performed at 150 ° C. for 600 hours in Example 5, the light emission intensity after the heat treatment with respect to the light emission intensity before the heat treatment was 97% or more, and the heat resistance was excellent. Moreover, about Example 2, the light emission intensity after a process with respect to the light emission intensity before processing for 2000 hours in the environment of temperature 85 degreeC and humidity 85% was 93% or more, and was excellent in the weather resistance.
以上説明したように、本発明の塊状蛍光体は、耐熱性、耐光性及び耐候性に優れ、樹脂の劣化による発光ダイオード等のデバイスの発光強度劣化や短寿命化を抑制できるため、照明装置、車載用、表示板、液晶用バックライト、医療器具等に使用される発光ダイオードにおける粉末状の蛍光体と樹脂からなる複合体（コーティング部材）の代替材料として、あるいは発光機能と拡散機能を兼ね備えた大面積面発光デバイスの構成部材として好適である。 As described above, the bulk phosphor of the present invention is excellent in heat resistance, light resistance and weather resistance, and can suppress deterioration in light emission intensity and shortening of the life of a device such as a light emitting diode due to deterioration of the resin. As an alternative material for composites (coating members) made of powdered phosphor and resin in light-emitting diodes used in in-vehicle devices, display panels, liquid crystal backlights, medical devices, etc., or has both a light emission function and a diffusion function It is suitable as a constituent member of a large area surface light emitting device.
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