JPH07187893A - Ceramic composite material - Google Patents
Ceramic composite materialInfo
- Publication number
- JPH07187893A JPH07187893A JP6193470A JP19347094A JPH07187893A JP H07187893 A JPH07187893 A JP H07187893A JP 6193470 A JP6193470 A JP 6193470A JP 19347094 A JP19347094 A JP 19347094A JP H07187893 A JPH07187893 A JP H07187893A
- Authority
- JP
- Japan
- Prior art keywords
- composite material
- al2o3
- polycrystalline
- yag
- ceramic composite
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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- Compositions Of Oxide Ceramics (AREA)
- Crystals, And After-Treatments Of Crystals (AREA)
Abstract
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ープ特性
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 The present invention has a large mechanical strength and a good creep resistance over a wide range from room temperature to a high temperature, and has excellent oxidation resistance, and is suitable as a structural material exposed to a high temperature. The present invention relates to a ceramic composite material that can be used for.
【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Ｓｉ３Ｎ４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 has been expected as a ceramic material used under high temperature and its practical application has been studied. However, these materials have insufficient high temperature characteristics and are problematic in practical application. Has become. As an alternative material, SiC / Si produced by SEP's chemical vapor impregnation method
C composite material has been in the limelight, and it is currently considered to be the highest temperature material in the world.
The operating temperature range is set to 1400 ° C or lower.
【０００３】Ｊｏｕｒｎａｌ ｏｆ ｔｈｅ Ａｍｅｒ
ｉｃａｎ Ｃｅｒａｍｉｃｓ Ｓｏｃｉｅｔｙ７６巻１
号２９〜３２ページ（１９９３年）には、Ａｌ２Ｏ３−
Ｙ３Ａｌ５Ｏ１２共晶で示されるアルミナとイットリア
・アルミナ・ガーネット（以下において「ＹＡＧ」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、Ａｌ
２Ｏ３とＹ２Ｏ３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。Journal of the Amer
ican Ceramics Society Volume 76 1
No. 29-32 (1993), Al 2 O 3 −
A composite composed of alumina represented by a Y 3 Al 5 O 12 eutectic and yttria-alumina garnet (hereinafter sometimes referred to as “YAG”) is disclosed.
Further, in this document, as a method for producing the above composite, Al
A method is disclosed in which a mixed powder of 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ページ右欄９〜１０行の記載
及び同ページ図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ー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ページ左欄最終
行〜同右欄１行の「破壊は通常Ａｌ２Ｏ３−ＹＡＧ界面
に沿って走る亀裂を有するコロニー境界に沿っており」
との記載からも裏付けられる。そして、このコロニー境
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 and FIG. 1 and FIG. In other words, this complex is composed of colony aggregates. This means, for example, in the above-mentioned document, page 30, left column, last line to right column, 1 line, "Fracture is usually along a boundary of a colony having a crack that runs along the Al 2 O 3 -YAG interface."
It is also supported by the statement. This colony boundary is shown in FIG. 2 on page 30 of the above-mentioned document by a portion where the tissue is larger than other portions.
【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。In the composite material disclosed in the above-mentioned document, for example, as shown in FIG. 4, the stress at a constant strain rate is 1530 ° C. and 1650 ° C.
It is about the same as that of sapphire fiber. further,
According to the experiments of the present inventor, the composites described in the above documents are
It was found that the composite contained air bubbles or voids, and the mechanical strength sharply decreased at high temperature.
【０００６】本発明の目的は、単結晶α−Ａｌ２Ｏ３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ープ特性を有し、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 that it is composed of single crystal α-Al 2 O 3 and polycrystalline YAG and has excellent mechanical strength and creep properties from room temperature to high temperatures, and these properties are remarkably high at high temperatures. An object is to provide an improved ceramic composite material.
【０００７】[0007]
【課題を解決するための手段】本発明の上記目的は、単
結晶α−Ａｌ２Ｏ３と多結晶Ｙ３Ａｌ５Ｏ１２とからな
り、コロニーが存在せず、大気中１５００℃での三点曲
げ強度が６００ＭＰａ以上及び／又は１６００℃での圧
縮クリープ強度が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。The above object of the present invention consists of single-crystal α-Al 2 O 3 and polycrystalline Y 3 Al 5 O 12 , is free of colonies, and is at room temperature at 1500 ° C. This is achieved by a ceramic composite material having a point bending strength of 600 MPa or more and / or a compression creep strength at 1600 ° C. 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。図１及び図２は、それぞれ、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
して直角な面及び約９度傾けた面（直角な面ではＡｌ２
Ｏ３の回折ピークが得られないので約９度傾けた面から
測定した。）からのＸ線回折を示す図である。The ceramic composite material of the present invention will be described in detail below. 1 and 2 are a plane perpendicular to the solidification direction of the ceramic composite material obtained in Example 1 to be described later and a plane tilted by about 9 degrees (in the plane perpendicular to Al 2
Since the diffraction peak of O 3 cannot be obtained, the measurement was performed from the surface tilted by about 9 degrees. FIG. 3 is a diagram showing an X-ray diffraction from FIG.
【０００９】図１にはＹＡＧの（２１１）面、（２２
０）面、（４２２）面、（４３１）面、（５４１）面、
（７２１）面及び（６５１）面からの回折に相当する２
θ＝１８．０６度、２０．８８度、３６．５８度、３
８．１６度、４９．１度、５６．２２度及び６０．６４
度のピークが観察される。In FIG. 1, (211) plane of YAG, (22
0 plane, (422) plane, (431) plane, (541) plane,
2 corresponding to diffraction from the (721) plane and the (651) plane
θ = 18.06 degrees, 20.88 degrees, 36.58 degrees, 3
8.16 degrees, 49.1 degrees, 56.22 degrees and 60.64 degrees
A peak of degree is observed.
【００１０】図２には、Ａｌ２Ｏ３についてはその（１
１０）面からの回折に相当する２θ＝３７．８度のピー
クのみが観察され、他方、ＹＡＧについてはその（２２
０）面、（４４０）面、（６４０）面及び（６６０）面
からの回折に相当する２θ＝２０．７４度、４２．５度
及び５４．９２度のピークが観察される。図１及び図２
から、本発明のセラミックス複合材料は単結晶α−Ａｌ
２Ｏ３と多結晶ＹＡＧとから構成されていることがわか
る。FIG. 2 shows that for Al 2 O 3 (1
Only the peak at 2θ = 37.8 degrees corresponding to diffraction from the (10) plane is observed, while for YAG its (22
Peaks at 2θ = 20.74 degrees, 42.5 degrees and 54.92 degrees corresponding to diffraction from the (0) plane, the (440) plane, the (640) plane and the (660) plane are observed. 1 and 2
Therefore, the ceramic composite material of the present invention is a single crystal α-Al.
It can be seen that it is composed of 2 O 3 and polycrystalline YAG.
【００１１】図３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、コロニー、粒界
相あるいは粗大粒子は観察されない。なお、コロニーと
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. 3 is an optical micrograph of the ceramic composite material obtained in Example 1 described later, showing that colonies, grain boundary phases or coarse particles as shown in FIGS. Not observed. The colony means a region surrounded by grain boundaries characterized by coarse particles.
【００１２】他方、図４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
ニー、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. 4 is an optical microscope photograph of the composite material obtained in Comparative Example 1 described later, which shows that the composite material has colonies and grains as shown in FIGS. It can be seen that it has a boundary phase or coarse particles.
【００１３】本発明のセラミックス複合材料は、単結晶
α−Ａｌ２Ｏ３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、単結晶α−Ａｌ２Ｏ３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５〜５０μｍである。In the ceramic composite material of the present invention, the single crystal α-Al 2 O 3 and the polycrystalline YAG form a sea-island structure uniformly at a fine level, and the single crystal α-Al 2 O 3 forms the sea. , Polycrystalline YAG forms islands, respectively. The size of the sea island can be controlled by changing the coagulation conditions, but it is generally 5 to 50 μm.
【００１４】Ａｌ２Ｏ３とＹＡＧとは、Ａｌ２Ｏ３５５
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、単
結晶α−Ａｌ２Ｏ３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
A eutectic is formed at a volume% of YAG of 45% by volume, but in the ceramic composite material of the present invention, Al 2 of the raw material powder is used.
By changing the compounding ratio of O 3 and YAG powder, single crystal α-Al 2 O 3 about 20 to 80% by volume, and polycrystalline YAG
The fraction can be changed within the range of about 80 to 20% by volume.
【００１５】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−
Ａｌ２Ｏ３粉末及びＹ２Ｏ３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
ノール、エタノールのようなアルコールが一般に使用さ
れる。ついで、この混合粉末を公知の溶解炉、例えばア
ーク溶解炉を用いて、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 in 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 either a dry mixing method or a wet mixing method can be adopted. Alcohols such as methanol and ethanol are generally used as a medium when the wet mixing method is used. Then, using a known melting furnace, for example, an arc melting furnace, the mixed powder is melted at a temperature, for example, 1
It is heated to 800 to 2500 ° C. and melted.
【００１６】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 the crucible as it is and solidified in one direction to prepare the ceramic composite material of the present invention. As another method, it is also possible to adopt a method in which the above-mentioned melted product is once solidified and then crushed, the crushed product is charged into a crucible, and then the melted product is melted and solidified in one direction.
【００１７】溶解凝固の際の雰囲気圧力は、通常１０
−３ｔｏｒｒ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５０ｍｍ／時間より大きくかつ２０
０ｍｍ／時間である。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。The atmospheric pressure during melting and solidification is usually 10
It is -3 torr or less. In addition, 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 50 mm / hour and 20
It is 0 mm / hour. The preparation conditions other than the atmospheric pressure and the moving speed are the same as those of the method known per se.
【００１８】溶解凝固の際の雰囲気圧力が条件範囲外に
なると、コロニーが生成し、かつボイドがコロニー界面
に生成しやすくなり、機械的強度及びクリープ特性の優
れた複合材料を得ることが困難になる。If the atmospheric pressure during dissolution and solidification is out of the range of the conditions, colonies are easily formed and voids are easily formed at the colony interface, making it difficult to obtain a composite material having excellent mechanical strength and creep properties. Become.
【００１９】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 a device for unidirectional solidification, a crucible is housed in a vertically arranged cylindrical container so as to be movable in the vertical direction, and an induction coil for heating is provided outside the substantially central portion of the cylindrical container. It is possible to use a device known per se, which is attached with a vacuum pump for reducing the pressure inside the container.
【００２０】[0020]
【実施例】以下に実施例及び比較例を示す。EXAMPLES Examples and comparative examples will be shown below.
【００２１】実施例１ α−Ａｌ２Ｏ３粉末（住友化学工業製、商品名ＡＫＰ−
３０）及びＹ２Ｏ３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、エタノールを用いて湿式ボールミルによって混合
し、得られたスラリからロータリエバポレイタを用いて
エタノールを除去した。Example 1 α-Al 2 O 3 powder (manufactured by Sumitomo Chemical Co., Ltd., trade name AKP-
30) and Y 2 O 3 powder (manufactured by Shin-Etsu Chemical Co., Ltd., fine powder type) were mixed by a wet ball mill with ethanol in a ratio of the former to the latter to be 82% to 18%, and the resulting slurry The ethanol was removed using a rotary evaporator.
【００２２】こうして得られたα−Ａｌ２Ｏ３及びＹ２
Ｏ３からなる混合粉末をチャンバー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６０ｍｍ／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 α-Al 2 O 3 and Y 2 thus obtained
A mixed powder of O 3 was charged into a crucible installed in the chamber, the atmospheric pressure was maintained at 10 −5 torr, and the crucible was heated from 1850 to 1900 using a high frequency coil.
It heated at 0 degreeC and melt | dissolved the mixed powder in a metal mold | die. Next,
Under the same atmosphere pressure as above, the crucible was lowered at a speed of 60 mm / hour and unidirectionally solidified to obtain a ceramic composite material.
【００２３】この複合材料の凝固方向に垂直な面及び約
９度傾けた面からのＸ線回折図を図１及び図２に示す。
図１には多結晶ＹＡＧからの回折ピークが観察され、図
２には、Ａｌ２Ｏ３については単結晶α−Ａｌ２Ｏ３の
（１１０）面からの回折ピークのみが観察される。この
ことから、上記複合材料が単結晶α−Ａｌ２Ｏ３と多結
晶ＹＡＧとから構成されていることがわかる。The X-ray diffraction patterns from the plane perpendicular to the solidification direction of this composite material and the plane inclined by about 9 degrees are shown in FIGS. 1 and 2.
In Figure 1 the diffraction peak was observed from the polycrystalline YAG, FIG. 2, for the Al 2 O 3 only a diffraction peak from (110) plane of the single crystal α-Al 2 O 3 is observed. From this, it is understood that the composite material is composed of single crystal α-Al 2 O 3 and polycrystalline YAG.
【００２４】また、この複合材料の光学顕微鏡写真を図
３に示す。図３から、この複合材料はコロニーあるいは
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。An optical micrograph of this composite material is shown in FIG. It can be seen from FIG. 3 that this composite material has no colony or grain boundary phase and has a uniform sea-island structure with no bubbles or voids.
【００２５】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ープ特性はい
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０．００７ｍｇ／ｃｍ３であった。The mechanical strength of this composite material is shown in Table 1.
In Table 1, the three-point bending strength and the compression creep property are both values measured in the atmosphere. Further, the weight increase after keeping this composite material in the air at 1700 ° C. for 100 hours was 0.007 mg / cm 3 .
【００２６】実施例２ チャンバー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１００ｍｍ／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。Example 2 A ceramic composite material was obtained by repeating Example 1 except that the atmospheric pressure in the chamber and the descending speed of the crucible were changed to 10 −3 torr and 100 mm / hour, respectively.
【００２７】この複合材料の凝固方向に垂直な面及び約
９度傾けた面からのＸ線回折図は、前者が図１と、後者
が図２と同一であり、上記複合材料が単結晶α−Ａｌ２
Ｏ３と多結晶ＹＡＧとから構成されていることが判明し
た。The X-ray diffractograms of the composite material from the plane perpendicular to the solidification direction and the plane inclined by about 9 degrees are the same as those in FIG. 1 for the former and FIG. 2 for the latter, and the above composite material is a single crystal α. -Al 2
It was found to be composed of O 3 and polycrystalline YAG.
【００２８】この複合材料の光学顕微鏡写真から、この
複合材料はコロニー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 the optical micrograph of this composite material, it was observed that this composite material did not have colonies or grain boundary phases, and had a uniform sea-island structure with no bubbles or voids.
【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０．００７ｍｇ／ｃｍ３であっ
た。The mechanical properties of this composite material are shown in Table 1.
Further, the weight increase after keeping this composite material in the air at 1700 ° C. for 100 hours was 0.007 mg / cm 3 .
【００３０】比較例１ チャンバー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Ｘ線回折図を図４に示す。Comparative Example 1 A ceramic composite material was prepared by repeating Example 1 except that the pressure inside the chamber was set to normal pressure. The X-ray diffraction pattern of the obtained composite material is shown in FIG.
【００３１】図４から、この複合材料はコロニー又は粒
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。From FIG. 4 it can be seen that this composite material has colonies or grain boundary phases, as well as bubbles. The mechanical properties of this composite material are shown in Table 1. Further, the weight increase after keeping this 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Ｘ線回折
図である。FIG. 2 is an X-ray diffraction pattern of the composite material obtained in Example 1.
【図３】図３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. 3 is an optical microscope photograph replacing a drawing showing the particle structure of the composite material obtained in Example 1.
【図４】図４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. 4 is an optical microscope photograph replacing 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 (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ３０Ｂ 21/02 Ｃ０４Ｂ 35/60 Ｂ ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 6 Identification code Office reference number FI technical display location C30B 21/02 C04B 35/60 B
Claims (1)
Ｏ１２とからなり、コロニーが存在せず、大気中１５０
０℃での三点曲げ強度が６００ＭＰａ以上及び／又は１
６００℃での圧縮クリープ強度が５００ＭＰａ以上であ
ることを特徴とするセラミックス複合材料。1. Single crystal α-Al 2 O 3 and polycrystalline Y 3 Al 5
Consisting of O 12 and no colonies, 150 in air
Three-point bending strength at 0 ° C is 600 MPa or more and / or 1
A ceramic composite material having a compressive creep strength at 600 ° C. of 500 MPa or more.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19347094A JP3264106B2 (en) | 1993-11-12 | 1994-07-15 | Ceramic composite materials |
| US08/335,919 US5484752A (en) | 1993-11-12 | 1994-11-08 | Ceramic composite material |
| DE69408939T DE69408939T2 (en) | 1993-11-12 | 1994-11-09 | Ceramic composite |
| EP94117640A EP0654456B1 (en) | 1993-11-12 | 1994-11-09 | Ceramic composite material |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5-317243 | 1993-11-12 | ||
| JP31724393 | 1993-11-12 | ||
| JP19347094A JP3264106B2 (en) | 1993-11-12 | 1994-07-15 | Ceramic composite materials |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07187893A true JPH07187893A (en) | 1995-07-25 |
| JP3264106B2 JP3264106B2 (en) | 2002-03-11 |
Family
ID=26507908
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP19347094A Expired - Fee Related JP3264106B2 (en) | 1993-11-12 | 1994-07-15 | Ceramic composite materials |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3264106B2 (en) |
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| US5902763A (en) * | 1995-01-19 | 1999-05-11 | Ube Industries, Inc. | Fused ceramic composite |
| US5981415A (en) * | 1996-07-01 | 1999-11-09 | Ube Industries, Ltd. | Ceramic composite material and porous ceramic material |
| JP2003034572A (en) * | 2001-07-23 | 2003-02-07 | Ngk Spark Plug Co Ltd | Alumina ceramic sintered body, method for producing the same, and cutting tool |
| US7633217B2 (en) | 2004-06-24 | 2009-12-15 | Ube Industries, Ltd. | White-light light emitting diode device |
| US7863636B2 (en) | 2005-08-10 | 2011-01-04 | Ube Industries, Ltd. | Substrate for light-emitting diode, and light-emitting diode |
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| WO2011125422A1 (en) | 2010-03-31 | 2011-10-13 | 宇部興産株式会社 | Ceramic composites for light conversion, process for production thereof, and light-emitting devices provided with same |
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| WO2013008751A1 (en) | 2011-07-08 | 2013-01-17 | 宇部興産株式会社 | Method for producing ceramic composite for photoconversion |
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- 1994-07-15 JP JP19347094A patent/JP3264106B2/en not_active Expired - Fee Related
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|---|---|---|---|---|
| US5902763A (en) * | 1995-01-19 | 1999-05-11 | Ube Industries, Inc. | Fused ceramic composite |
| US5981415A (en) * | 1996-07-01 | 1999-11-09 | Ube Industries, Ltd. | Ceramic composite material and porous ceramic material |
| EP0816537A3 (en) * | 1996-07-01 | 2000-03-15 | Ube Industries Limited | Ceramic composite material and porous ceramic material |
| JP2003034572A (en) * | 2001-07-23 | 2003-02-07 | Ngk Spark Plug Co Ltd | Alumina ceramic sintered body, method for producing the same, and cutting tool |
| EP2497758A2 (en) | 2003-01-20 | 2012-09-12 | Ube Industries, Ltd. | Ceramic composite material for optical conversion and use thereof |
| US8900480B2 (en) | 2003-01-20 | 2014-12-02 | Ube Industries, Ltd. | Ceramic composite material for light conversion and use thereof |
| US7633217B2 (en) | 2004-06-24 | 2009-12-15 | Ube Industries, Ltd. | White-light light emitting diode device |
| EP1760794A4 (en) * | 2004-06-24 | 2010-11-17 | Ube Industries | WHITE LIGHT EMITTING DIODE DEVICE |
| US7935973B2 (en) | 2004-10-21 | 2011-05-03 | Ube Industries, Ltd. | Light-emitting diode, light-emitting diode substrate and production method of light-emitting diode |
| US7863636B2 (en) | 2005-08-10 | 2011-01-04 | Ube Industries, Ltd. | Substrate for light-emitting diode, and light-emitting diode |
| US8608978B2 (en) | 2006-01-19 | 2013-12-17 | Ube Industries, Ltd. | Ceramic composite light-converting member and light-emitting device using the same |
| US8093799B2 (en) | 2006-09-25 | 2012-01-10 | Ube Industries, Ltd. | Ceramic composite for phototransformation and light emitting device using the same |
| WO2011125422A1 (en) | 2010-03-31 | 2011-10-13 | 宇部興産株式会社 | Ceramic composites for light conversion, process for production thereof, and light-emitting devices provided with same |
| WO2012077599A1 (en) | 2010-12-10 | 2012-06-14 | 宇部興産株式会社 | Ceramic composite for photoconversion, and method for manufacture thereof |
| US9543480B2 (en) | 2010-12-10 | 2017-01-10 | Ube Industries, Ltd. | Ceramic composite for light conversion and method for manufacture thereof |
| WO2012081566A1 (en) | 2010-12-16 | 2012-06-21 | 宇部興産株式会社 | Ceramic composite for photoconversion, method for producing same, and light-emitting device comprising same |
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