JP3128044B2 - Ceramic composite materials - Google Patents
Ceramic composite materialsInfo
- Publication number
- JP3128044B2 JP3128044B2 JP06240792A JP24079294A JP3128044B2 JP 3128044 B2 JP3128044 B2 JP 3128044B2 JP 06240792 A JP06240792 A JP 06240792A JP 24079294 A JP24079294 A JP 24079294A JP 3128044 B2 JP3128044 B2 JP 3128044B2
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- composite material
- ceramic composite
- degrees
- polycrystalline
- plane
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Description
【０００１】[0001]
【産業上の利用分野】本発明は室温から高温までの広い
範囲にわたって機械的強度が大きくかつ耐クリ−プ特性
が良好であり、さらに耐酸化性が優れており、高温に曝
される構造材料として好適に使用することのできる、セ
ラミックス複合材料に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a structural material which has high mechanical strength and good creep resistance over a wide range from room temperature to high temperature, has excellent oxidation resistance, and is exposed to high temperatures. The present invention relates to a ceramic composite material that can be suitably used as a ceramic composite.
【０００２】[0002]
【従来の技術】高温下で用いられるセラミックス材料と
してＳｉＣあるいはＳｉ3 Ｎ4 が期待され、その実用化
が研究されてきたが、これらの材料は高温特性が充分で
はなく、実用化する上で問題となっている。その代替材
料としてＳＥＰ社の化学気相含浸法によるＳｉＣ／Ｓｉ
Ｃ複合材料が脚光を浴び、現在では世界最高の高温材料
と考えられており、その研究開発が進められているが、
その使用温度範囲は１４００℃以下とされている。2. Description of the Related Art SiC or Si 3 N 4 is expected as a ceramic material used at high temperatures, and its practical use has been studied. However, these materials do not have sufficient high-temperature characteristics and have problems in practical use. It has become. As an alternative material, SiC / Si by chemical vapor impregnation of SEP
C-composite material is in the spotlight and is currently considered to be the world's best high-temperature material.
The operating temperature range is set to 1400 ° C. or less.
【０００３】Journal of the American Ceramics Soci
ety ７６巻１号２９〜３２ペ−ジ（１９９３年）には、
Ａｌ2 Ｏ3 −Ｙ3 Ａｌ5 Ｏ12共晶で示されるアルミナと
イットリア・アルミナ・ガ−ネット（以下において「Ｙ
ＡＧ」ということがある。）とからなる複合体が開示さ
れている。さらに、この文献には、上記複合体の製法と
して、Ａｌ2 Ｏ3 とＹ2 Ｏ3 との混合粉末を溶融し、つ
いでルツボ内で一方向に溶解凝固する方法が開示されて
いる。[0003] Journal of the American Ceramics Soci
ety Vol. 76 No. 1 pp. 29-32 (1993)
Alumina represented by eutectic Al 2 O 3 —Y 3 Al 5 O 12 and yttria alumina garnet (hereinafter referred to as “Y
AG ". ) Is disclosed. Further, this document discloses a method for producing the above composite, in which a mixed powder of Al 2 O 3 and Y 2 O 3 is melted, and then melted and solidified in one direction in a crucible.
【０００４】上記文献２９ペ−ジ右欄９〜１０行の記載
及び同ペ−ジ図１及び図２から、上記複合体は、多結晶
からなり、粒界相を有していることがわかる。換言する
と、この複合体はコロニ−の集合体から構成されてい
る。このことは、例えば、上記文献３０ペ−ジ左欄最終
行〜同右欄１行の「破壊は通常Ａｌ2 Ｏ3 −ＹＡＧ界面
に沿って走る亀裂を有するコロニ−境界に沿っており」
との記載からも裏付けられる。そして、このコロニ−境
界が上記文献３０ペ−ジの図２中において他の部分に比
較して組織が大きくなっている部分で示されている。From the description on page 29, right column, lines 9 to 10 of the document and FIGS. 1 and 2, it can be seen that the composite is composed of polycrystal and has a grain boundary phase. . In other words, this complex is composed of an aggregate of colonies. This can, for example, the document 30 Paix - "- is along the boundary colonies with destruction running along the usual Al 2 O 3-YAG surface crack" di left column, last line - the same right column, line 1
This is supported by the description. This colony boundary is shown in FIG. 2 on page 30 of the above-mentioned document where the tissue is larger than the other parts.
【０００５】[0005]
【発明が解決しようとする課題】前記文献に開示されて
いる複合材料は、例えば図４に示されるように、歪み速
度と一定にした場合の応力は１５３０℃及び１６５０℃
でサファイア繊維のそれとほぼ同程度である。さらに、
本発明者の実験によると、上記文献に記載の複合体は、
複合体内部に気泡あるいはボイドを含有しており、高温
において機械的強度が急激に低下することが認められ
た。As shown in FIG. 4, for example, as shown in FIG. 4, when the strain rate is constant and the stress is constant at 1530 ° C. and 1650 ° C.
About the same as that of sapphire fiber. further,
According to the experiments of the present inventors, the complex described in the above-mentioned literature is:
It was confirmed that the composite contained bubbles or voids, and the mechanical strength was rapidly reduced at high temperatures.
【０００６】本発明の目的は、多結晶α−Ａｌ2 Ｏ3 と
多結晶ＹＡＧとからなり、室温から高温にわたって優れ
た機械的強度及びクリ−プ特性を有し、特に高温におけ
るこれら特性が飛躍的に改善されたセラミックス複合材
料を提供することにある。An object of the present invention is composed of a polycrystalline α-Al 2 O 3 and polycrystal YAG, excellent mechanical strength and chestnut over hot from room - has up properties, in particular those characteristics at elevated temperatures dramatically An object of the present invention is to provide a ceramic composite material that has been improved in terms of quality.
【０００７】[0007]
【課題を解決するための手段】本発明の上記目的は、多
結晶α−Ａｌ2 Ｏ3 と多結晶Ｙ3 Ａｌ5 Ｏ12とからな
り、コロニ−が存在せず、大気中１５００℃での三点曲
げ強度が５００ＭＰａ以上であるセラミックス複合材料
によって達成される。SUMMARY OF THE INVENTION An object of the present invention is to provide a polycrystalline α-Al 2 O 3 and a polycrystalline Y 3 Al 5 O 12 which are free of colonies and which are used at 1500 ° C. in the atmosphere. Achieved by a ceramic composite material having a three-point bending strength of 500 MPa or more.
【０００８】以下に本発明のセラミックス複合材料を詳
細に説明する。Hereinafter, the ceramic composite material of the present invention will be described in detail.
【０００９】図１は後述する実施例１で得られたセラミ
ックス複合材料の凝固方向に対して直角な面からのＸ線
回折を示す図である。FIG. 1 is a diagram showing X-ray diffraction from a plane perpendicular to the solidification direction of the ceramic composite material obtained in Example 1 described later.
【００１０】図１にはＹＡＧの（２１１）面、（３２
１）面、（４００）面、（４２０）面、（４２２）面、
（４３１）面、（５２１）面、（５３２）面、（６３
１）面、（６４０）面、（７２１）面、（６５１）面及
び（７５２）面からの回折に相当する２θ＝１８．１
度、２７．８度、２９．７８度、３３．２６度、３６．
６３度、３８．２２度、４１．１８度、４６．６２度、
５１．６度、５５．２８度、５６．２６度、６０．７度
及び６９．０６度のピ−クが観察される。FIG. 1 shows the (211) plane of YAG and the (32) plane of YAG.
1) plane, (400) plane, (420) plane, (422) plane,
(431) plane, (521) plane, (532) plane, (63) plane
2θ = 18.1 corresponding to diffraction from the 1), (640), (721), (651), and (752) planes
Degrees, 27.8 degrees, 29.78 degrees, 33.26 degrees, 36.
63 degrees, 38.22 degrees, 41.18 degrees, 46.62 degrees,
Peaks of 51.6 degrees, 55.28 degrees, 56.26 degrees, 60.7 degrees and 69.06 degrees are observed.
【００１１】さらに、図１には、Ａｌ2 Ｏ3 の（０１
２）面、（１１０）面、（０２４）面及び（２１１）面
からの回折に相当する２θ＝２６．６２度、３７．７８
度、５２．７度及び５９．７８度のピ−クが観察され
る。このことから、本発明のセラミックス複合材料は多
結晶α−Ａｌ2 Ｏ3 と多結晶ＹＡＧとから構成されてい
ることがわかる。Further, FIG. 1 shows that (01) of Al 2 O 3
2θ = 26.62 degrees, 37.78 corresponding to diffraction from the (2), (110), (024), and (211) planes
Degrees, 52.7 degrees and 59.78 degrees peaks are observed. This indicates that the ceramic composite material of the present invention is composed of polycrystalline α-Al 2 O 3 and polycrystalline YAG.
【００１２】図２は後述する実施例１で得られたセラミ
ックス複合材料の光学顕微鏡写真であり、前記した公知
文献の図１及び図２に見られるような、コロニ−、粒界
相あるいは粗大粒子は観察されない。なお、コロニ−と
は粗大粒子で特徴付けられる粒界で囲まれた領域を意味
する。FIG. 2 is an optical micrograph of the ceramic composite material obtained in Example 1 to be described later. As shown in FIGS. 1 and 2 of the above-mentioned known literature, a colony, a grain boundary phase or a coarse particle is shown. Is not observed. The colony means a region surrounded by grain boundaries characterized by coarse particles.
【００１３】他方、図３は後述する比較例１で得られた
複合材料の光学顕微鏡写真であり、この複合材料は前記
した公知文献の図１及び図２に示されているようなコロ
ニ−、粒界相あるいは粗大粒子を有していることがわか
る。On the other hand, FIG. 3 is an optical micrograph of the composite material obtained in Comparative Example 1 to be described later. This composite material has a colony as shown in FIGS. It turns out that it has a grain boundary phase or coarse particles.
【００１４】本発明のセラミックス複合材料は、多結晶
α−Ａｌ2 Ｏ3 と多結晶ＹＡＧとが微細なレベルで均質
に海島構造を形成しており、多結晶α−Ａｌ2 Ｏ3 が海
を、多結晶ＹＡＧが島を、それぞれ、形成している。海
島の大きさは凝固条件を変更することによって制御が可
能であるが、一般には１〜５０μｍである。In the ceramic composite material of the present invention, the polycrystalline α-Al 2 O 3 and the polycrystalline YAG form a sea-island structure uniformly at a fine level, and the polycrystalline α-Al 2 O 3 forms the sea. , Polycrystalline YAG form islands, respectively. The size of the sea-island can be controlled by changing the coagulation conditions, but is generally 1 to 50 μm.
【００１５】Ａｌ2 Ｏ3 とＹＡＧとは、Ａｌ2 Ｏ3 ５５
容積％、ＹＡＧ４５容積％で共晶を形成するが、本発明
のセラミックス複合材料においては、原料粉末のＡｌ2
Ｏ3及びＹＡＧ粉末の配合割合を変えることにより、多
結晶α−Ａｌ2 Ｏ3 約２０〜８０容積％、多結晶ＹＡＧ
約８０〜２０容積％の範囲内でその分率を変化させるこ
とができる。Al 2 O 3 and YAG are Al 2 O 3 55
Volume%, forms a eutectic with YAG45 volume%, in the ceramic composite material of the present invention, the raw material powder Al 2
By changing the mixing ratio of O 3 and YAG powder, about 20 to 80% by volume of polycrystalline α-Al 2 O 3
The fraction can vary within the range of about 80 to 20% by volume.
【００１６】本発明のセラミックス複合材料は、例えば
以下の方法によって調製することができる。最初にα−
Ａｌ2 Ｏ3 粉末及びＹ2 Ｏ3 粉末を、所望する成分比率
のセラミックス複合材料を生成する割合で混合して、混
合粉末を調製する。混合方法については特別の制限はな
く、乾式混合法及び湿式混合法のいずれも採用すること
ができる。湿式混合法を用いる際の媒体としては、メタ
ノ−ル、エタノ−ルのようなアルコ−ルが一般に使用さ
れる。ついで、この混合粉末を公知の溶解炉、例えばア
−ク溶解炉を用いて、両原料が溶解する温度、例えば１
８００〜２５００℃に加熱して溶解する。The ceramic composite material of the present invention can be prepared, for example, by the following method. First α-
The Al 2 O 3 powder and the Y 2 O 3 powder are mixed at a ratio that produces a ceramic composite material having a desired component ratio to prepare a mixed powder. There is no particular limitation on the mixing method, and any of a dry mixing method and a wet mixing method can be employed. As a medium for using the wet mixing method, alcohols such as methanol and ethanol are generally used. Then, the mixed powder is melted in a known melting furnace, for example, an arc melting furnace, at a temperature at which both raw materials are melted, for example, at 1 °
Heat to 800 to 2500 ° C to dissolve.
【００１７】引き続き、上記の溶解物をそのままルツボ
に仕込み一方向に凝固させて、本発明のセラミックス複
合材料を調製する。別の方法として、上記の溶解物を一
旦凝固させた後に粉砕し、粉砕物をルツボに仕込み、つ
いで溶解させて一方向に凝固させる方法も採用すること
ができる。Subsequently, the above-mentioned melt is charged into a crucible as it is and solidified in one direction to prepare a ceramic composite material of the present invention. As another method, a method in which the above-mentioned melt is once solidified and then pulverized, the pulverized material is charged in a crucible, and then dissolved and solidified in one direction can be adopted.
【００１８】溶解凝固の際の雰囲気圧力は、通常１０-3
torr以下である。また、一方向に凝固させるときのルツ
ボの移動速度、換言するとセラミックス複合材料の成長
速度は通常２００mm／時間より大きくかつ１０００mm／
時間以下である。雰囲気圧力及び移動速度以外の調製条
件ははそれ自体公知の方法の条件と同様である。Atmospheric pressure during melting and solidification is usually 10 −3.
It is less than torr. Further, the moving speed of the crucible when solidifying in one direction, in other words, the growth speed of the ceramic composite material is usually larger than 200 mm / hour and 1000 mm / hour.
Less than an hour. The preparation conditions other than the atmospheric pressure and the moving speed are the same as those of the method known per se.
【００１９】溶解凝固の際の雰囲気圧力が条件範囲外に
なると、コロニ−が生成し、かつボイドがコロニ−界面
に生成しやすくなり、機械的強度及びクリ−プ特性の優
れた複合材料を得ることが困難になる。If the atmospheric pressure during the melt-solidification is out of the range, colonies are formed and voids are easily formed at the colony interface, and a composite material having excellent mechanical strength and creep characteristics is obtained. It becomes difficult.
【００２０】一方向凝固させる装置としては、垂直方向
に設置された円筒状の容器内にルツボが上下方向に移動
可能に収納されており、円筒状容器の略中央部外側に加
熱用の誘導コイルが取り付けられており、容器内空間を
減圧にするための真空ポンプが設置されている、それ自
体公知の装置を使用することができる。As an apparatus for one-way solidification, a crucible is housed in a vertically disposed cylindrical container so as to be movable in a vertical direction, and an induction coil for heating is provided outside a substantially central portion of the cylindrical container. And a device known per se in which a vacuum pump for reducing the pressure in the container is installed can be used.
【００２１】[0021]
【実施例】以下に実施例及び比較例を示す。EXAMPLES Examples and comparative examples are shown below.
【００２２】実施例１ α−Ａｌ2 Ｏ3 粉末（住友化学工業製、商品名ＡＫＰ−
３０）及びＹ2 Ｏ3 粉末（信越化学工業製、微粉タイ
プ）を、前者対後者のモル比が８２％対１８％になる割
合で、エタノ−ルを用いて湿式ボ−ルミルによって混合
し、得られたスラリからロ−タリエバポレイタを用いて
エタノ−ルを除去した。Example 1 α-Al 2 O 3 powder (AKP-, trade name, manufactured by Sumitomo Chemical Co., Ltd.)
30) and Y 2 O 3 powder (fine powder type, manufactured by Shin-Etsu Chemical Co., Ltd.) were mixed by a wet ball mill using ethanol at a ratio of the former to the latter being 82% to 18%, Ethanol was removed from the obtained slurry using a rotary evaporator.
【００２３】こうして得られたα−Ａｌ2 Ｏ3 及びＹ2
Ｏ3 からなる混合粉末をチャンバ−内に設置されたルツ
ボに仕込み、１０-5torrの雰囲気圧力に維持して、高周
波コイルを用いてルツボを１８５０〜１９００℃に加熱
して、金型内の混合粉末を溶解した。つぎに、上記と同
一の雰囲気圧力下にルツボを２２０mm／時間の速度で降
下させ一方向凝固させて、セラミックス複合材料を得
た。The thus obtained α-Al 2 O 3 and Y 2
The mixed powder composed of O 3 is charged into a crucible installed in a chamber, and the crucible is heated to 1850 to 1900 ° C. using a high-frequency coil while maintaining the atmospheric pressure at 10 −5 torr, and The mixed powder was dissolved. Next, the crucible was lowered at a speed of 220 mm / hour under the same atmospheric pressure as described above and was unidirectionally solidified to obtain a ceramic composite material.
【００２４】この複合材料の凝固方向に垂直な面からの
Ｘ線回折図を図１に示す。図１には多結晶ＹＡＧと多結
晶α−Ａｌ2 Ｏ3 の回折ピ−クが観察され、上記複合材
料が多結晶から構成されていることがわかる。FIG. 1 shows an X-ray diffraction diagram of the composite material taken from a plane perpendicular to the solidification direction. FIG. 1 shows diffraction peaks of polycrystalline YAG and polycrystalline α-Al 2 O 3 , indicating that the composite material is composed of polycrystalline.
【００２５】また、この複合材料の光学顕微鏡写真を図
２に示す。図２から、この複合材料はコロニ−あるいは
粒界相を有しておらず、さらに気泡又はボイドが存在し
ない均一な海島構造を取っていることがわかる。FIG. 2 shows an optical microscope photograph of this composite material. From FIG. 2, it can be seen that this composite material has no colony or grain boundary phase, and has a uniform sea-island structure without bubbles or voids.
【００２６】この複合材料の機械的強度を表１に示す。
表１において、三点曲げ強度及び圧縮クリ−プ特性はい
ずれも大気中で測定した値である。また、この複合材料
を１７００℃の大気中に１００時間保持した後の重量増
は０．００４mg／cm3 であった。Table 1 shows the mechanical strength of this composite material.
In Table 1, the three-point bending strength and the compression creep property are values measured in the air. Further, the weight increase after keeping the composite material in the air at 1700 ° C. for 100 hours was 0.004 mg / cm 3 .
【００２７】実施例２ チャンバ−内の雰囲気圧力及びルツボの降下速度を、そ
れぞれ、１０-3torr及び３００mm／時間に変えた以外は
実施例１を繰り返して、セラミックス複合材料を得た。
この複合材料の凝固方向に垂直な面からのＸ線回折図は
図１と同じであり、上記複合材料が多結晶から構成され
ていることが判明した。Example 2 A ceramic composite material was obtained by repeating Example 1 except that the atmosphere pressure in the chamber and the crucible lowering speed were changed to 10 -3 torr and 300 mm / hour, respectively.
The X-ray diffraction pattern from a plane perpendicular to the solidification direction of this composite material was the same as that in FIG. 1, and it was found that the composite material was composed of polycrystal.
【００２８】また、この複合材料の光学顕微鏡写真か
ら、この複合材料はコロニ−あるいは粒界相を有してお
らず、さらに気泡又はボイドが存在しない均一な海島構
造をとっていることが観察された。From an optical micrograph of this composite material, it was observed that this composite material had no colony or grain boundary phase and had a uniform sea-island structure free of bubbles or voids. Was.
【００２９】この複合材料の機械的特性を表１に示す。
また、この複合材料を１７００℃の大気中に１００時間
保持した後の重量増は０．００５mg／cm3 であった。Table 1 shows the mechanical properties of this composite material.
Further, the weight increase after keeping the composite material in the air at 1700 ° C. for 100 hours was 0.005 mg / cm 3 .
【００３０】比較例１ チャンバ−内の圧力を常圧にした以外は実施例１を繰り
返して、セラミックス複合材料を調製した。得られた複
合材料の光学顕微鏡写真を図３に示す。Comparative Example 1 A ceramic composite material was prepared by repeating Example 1 except that the pressure in the chamber was changed to normal pressure. An optical microscope photograph of the obtained composite material is shown in FIG.
【００３１】図３から、この複合材料はコロニ−又は粒
界相、並びに気泡を有していることがわかる。この複合
材料の機械的特性を表１に示す。また、この複合材料を
１７００℃の大気中に１００時間保持した後の重量増は
０．０２mg／cm3 であった。FIG. 3 shows that the composite material has a colony or grain boundary phase and bubbles. Table 1 shows the mechanical properties of this composite material. Further, the weight increase after keeping the composite material in the atmosphere at 1700 ° C. for 100 hours was 0.02 mg / cm 3 .
【００３２】[0032]
【表１】 [Table 1]
【図１】図１は実施例１で得られた複合材料のＸ線回折
図である。FIG. 1 is an X-ray diffraction diagram of the composite material obtained in Example 1.
【図２】図２は実施例１で得られた複合材料の粒子構造
を示す図面に代える光学顕微鏡写真である。FIG. 2 is an optical microscope photograph instead of a drawing showing the particle structure of the composite material obtained in Example 1.
【図３】図３は比較例１で得られた複合材料の粒子構造
を示す図面に代える光学顕微鏡写真である。FIG. 3 is an optical microscope photograph instead of a drawing showing the particle structure of the composite material obtained in Comparative Example 1.
───────────────────────────────────────────────────── フロントページの続き (58)調査した分野(Int.Cl.7，ＤＢ名) C04B 35/60 C04B 35/10 C30B 29/20 - 29/28 ──────────────────────────────────────────────────続 き Continued on front page (58) Field surveyed (Int. Cl. 7 , DB name) C04B 35/60 C04B 35/10 C30B 29/20-29/28
Claims (1)
Ｏ12とからなり、コロニ−が存在せず、大気中１５００
℃での三点曲げ強度が５００ＭＰａ以上であることを特
徴とするセラミックス複合材料。A polycrystalline α-Al 2 O 3 and a polycrystalline Y 3 Al 5
O 12 , no colonies, 1500 in air
A ceramic composite material having a three-point bending strength at 500C of 500 MPa or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP06240792A JP3128044B2 (en) | 1993-11-12 | 1994-09-09 | Ceramic composite materials |
Applications Claiming Priority (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP31724293 | 1993-11-12 | ||
| JP19347194 | 1994-07-15 | ||
| JP6-193471 | 1994-07-15 | ||
| JP5-317242 | 1994-07-15 | ||
| JP06240792A JP3128044B2 (en) | 1993-11-12 | 1994-09-09 | Ceramic composite materials |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0881257A JPH0881257A (en) | 1996-03-26 |
| JP3128044B2 true JP3128044B2 (en) | 2001-01-29 |
Family
ID=27326772
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP06240792A Expired - Fee Related JP3128044B2 (en) | 1993-11-12 | 1994-09-09 | Ceramic composite materials |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3128044B2 (en) |
Families Citing this family (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1211312C (en) * | 1996-07-01 | 2005-07-20 | 宇部兴产株式会社 | Ceramic composite material and porous ceramic material |
| CN1738781A (en) | 2003-01-20 | 2006-02-22 | 宇部兴产株式会社 | Ceramic composite material for optical conversion and use thereof |
| JP4420021B2 (en) | 2004-06-24 | 2010-02-24 | 宇部興産株式会社 | White light emitting diode device |
| EP1811580A4 (en) | 2004-10-21 | 2012-05-23 | Ube Industries | Light emitting diode element, board for light emitting diode and method for manufacturing light emitting diode element |
| JP5029362B2 (en) | 2005-08-10 | 2012-09-19 | 宇部興産株式会社 | Light emitting diode substrate and light emitting diode |
| US8357262B2 (en) | 2005-08-31 | 2013-01-22 | Kyocera Corporation | Corrosion-resistant member, treatment apparatus and sample treatment method using the member, and method for manufacture of corrosion-resistant member |
| WO2007083828A1 (en) | 2006-01-19 | 2007-07-26 | Ube Industries, Ltd. | Ceramic composite light converting member and light emitting device using the same |
| JP5157909B2 (en) | 2006-09-25 | 2013-03-06 | 宇部興産株式会社 | Ceramic composite for light conversion and light emitting device using the same |
| KR101425183B1 (en) | 2010-03-31 | 2014-07-31 | 우베 고산 가부시키가이샤 | Ceramic composites for light conversion, process for production thereof, and light-emitting devices provided with same |
| EP2650082B1 (en) | 2010-12-10 | 2022-02-02 | Ube Industries, Ltd. | Ceramic composite for photoconversion, and method for manufacture thereof |
| KR101471641B1 (en) | 2010-12-16 | 2014-12-10 | 우베 고산 가부시키가이샤 | Ceramic composite for photoconversion, method for producing same, and light-emitting device comprising same |
| KR20140051209A (en) | 2011-07-08 | 2014-04-30 | 우베 고산 가부시키가이샤 | Method for producing ceramic composite for photoconversion |
| CN104245881B (en) | 2012-03-30 | 2015-11-25 | 宇部兴产株式会社 | Light conversion ceramic composite and use its light-emitting device |
-
1994
- 1994-09-09 JP JP06240792A patent/JP3128044B2/en not_active Expired - Fee Related
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| Publication number | Publication date |
|---|---|
| JPH0881257A (en) | 1996-03-26 |
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