JPH0451508B2 - - Google Patents
Info
- Publication number
- JPH0451508B2 JPH0451508B2 JP58192470A JP19247083A JPH0451508B2 JP H0451508 B2 JPH0451508 B2 JP H0451508B2 JP 58192470 A JP58192470 A JP 58192470A JP 19247083 A JP19247083 A JP 19247083A JP H0451508 B2 JPH0451508 B2 JP H0451508B2
- Authority
- JP
- Japan
- Prior art keywords
- sintered body
- zirconia
- strength
- alumina
- spinel
- 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.)
- Expired - Lifetime
Links
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 claims description 44
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims description 16
- 239000000843 powder Substances 0.000 claims description 14
- 229910052596 spinel Inorganic materials 0.000 claims description 14
- 239000011029 spinel Substances 0.000 claims description 13
- 238000004519 manufacturing process Methods 0.000 claims description 7
- 239000002775 capsule Substances 0.000 claims description 5
- 238000001513 hot isostatic pressing Methods 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 3
- 229910026161 MgAl2O4 Inorganic materials 0.000 claims 1
- 229910052593 corundum Inorganic materials 0.000 claims 1
- 229910001845 yogo sapphire Inorganic materials 0.000 claims 1
- 238000000034 method Methods 0.000 description 12
- RKTYLMNFRDHKIL-UHFFFAOYSA-N copper;5,10,15,20-tetraphenylporphyrin-22,24-diide Chemical compound [Cu+2].C1=CC(C(=C2C=CC([N-]2)=C(C=2C=CC=CC=2)C=2C=CC(N=2)=C(C=2C=CC=CC=2)C2=CC=C3[N-]2)C=2C=CC=CC=2)=NC1=C3C1=CC=CC=C1 RKTYLMNFRDHKIL-UHFFFAOYSA-N 0.000 description 7
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 6
- 239000013078 crystal Substances 0.000 description 6
- 238000005452 bending Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 229910020068 MgAl Inorganic materials 0.000 description 4
- 239000011148 porous material Substances 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 238000000975 co-precipitation Methods 0.000 description 3
- 238000010304 firing Methods 0.000 description 3
- 239000011521 glass Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 238000005245 sintering Methods 0.000 description 3
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000013001 point bending Methods 0.000 description 2
- 239000011164 primary particle Substances 0.000 description 2
- 239000007858 starting material Substances 0.000 description 2
- RZVAJINKPMORJF-UHFFFAOYSA-N Acetaminophen Chemical compound CC(=O)NC1=CC=C(O)C=C1 RZVAJINKPMORJF-UHFFFAOYSA-N 0.000 description 1
- 206010027476 Metastases Diseases 0.000 description 1
- 229910052581 Si3N4 Inorganic materials 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 238000001354 calcination Methods 0.000 description 1
- 239000010987 cubic zirconia Substances 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 239000010432 diamond Substances 0.000 description 1
- 229910003460 diamond Inorganic materials 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000005538 encapsulation Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 230000009401 metastasis Effects 0.000 description 1
- 239000011812 mixed powder Substances 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000003672 processing method Methods 0.000 description 1
- 239000005297 pyrex Substances 0.000 description 1
- 238000007789 sealing Methods 0.000 description 1
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 description 1
- 229910010271 silicon carbide Inorganic materials 0.000 description 1
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Landscapes
- Compositions Of Oxide Ceramics (AREA)
Description
本発明は、ジルコニア−アルミナ（ZrO2−
Al2O3）またはジルコニア−スピネル（ZrO2−
MgAl2O4）から成る高強度ジルコニア系焼結体
の製造方法に関する。
近年、安定化剤としてY2O3を少量添加した正
方晶を含有するジルコニア焼結体（以下、Ｙ−
PSZと略記する）が、高強度、高靭性を発現する
ことから、この焼結体を切断工具、ダイス、ノズ
ル、ベアリングなどの機械構造材料として利用し
ようとする開発が活発化している。本発明によつ
てえられる焼結体は、このような機械構造材料と
しての用途の拡大、並びに使用に対する一段と高
い信頼性と耐久性を約束すべき著しく優れた強度
特性を具備したものである。
Ｙ−PSZは、すでに高強度焼結体として、よく
知られており、その高強度の原因は焼結体中に含
まれている正方晶ジルコニアが応力によつて、単
斜晶にマルテンサイト型転移をすることに起因し
ているとされている。本発明者等は、このＹ−
PSZの強度を詳細に調べた結果、強度は正方晶ジ
ルコニアの量と比例関係にあるのではなく、正方
晶の他に立方晶が少量含まれている場合に最高値
に達するという結果を得た。
この結果から推論して、立方晶ジルコニアの代
わりに弾性率、強度の大きいアルミナ（Al2O3）
又はスピネル（MgAl2O4）を添加することによ
つて、さらに高強度化が達成されるとする仮説を
もつに至つた。Ｙ−PSZ−Al2O3系焼結体につい
てはすでに文献（J.Mat.Sci.17、247−254
（1982））等で報告されているが、そこで報告され
ているホツトプレス焼結体の曲げ強度値は
1200MPaにも到達しておらず、ホツトプレスＹ
−PSZの値（1300−1700MPa）と比較しても低
く、上述の仮説に反するものであつた。しかしな
がら焼結体の強度は、出発原料並びにその製造方
法に大きく依存する。
そこで本発明者等は、ジルコニア−アルミナ系
またはジルコニア−スピネル系について、優れた
機械的強度特性を有する焼結体を得るべく検討し
た結果、イツトリアを少量添加した正方晶を含む
ジルコニアにアルミナまたはスピネルを特定割合
配合することにより、また熱間静水圧プレス処理
を行うことにより、Ｙ−PSZよりさらに著しく強
度特性の向上した焼結体が得られることを見い出
し本発明を完成させるに至つた。
すなわち、本発明は、1.5〜５モル％のイツト
リア（Y2O3）を含有するジルコニア（ZrO2）50
〜98重量％と、アルミナ（Al2O3）またはスピネ
ル（MgAl2O4）50〜２重量％とから成る1200〜
1500℃で予備焼結した予備焼結体、またはカプセ
ル中に真空封入した該組成の粉末成形体を圧力50
〜500MPa、温度1300〜1650℃で熱間静水圧プレ
ス処理することにより該ジルコニア系焼結体を製
造する方法を提供するものである。
以下本発明をさらに詳細に説明する。
本発明によつてえられる焼結体は、1.5〜５モ
ル％のY2O3を含有するジルコニア50〜98重量％
とアルミナまたはスピネル50〜２重量％から成る
ものである。ジルコニア中のY2O3含量は、1.5モ
ル％未満では、正方晶からなる焼結体が得られ
ず、また５モル％をこえると、正方晶が減少し、
立方晶が主体となるため、転移による高強度化が
得られず、不適当である。ジルコニアへのアルミ
ナまたはスピネルの添加量が２重量％未満の場合
には、添加による強度上昇効果が得難く、また、
50重量％をこえると正方晶ジルコニアに起因する
強化機構が減少し、期待したほどの強度が得られ
ない。
添加されるアルミナまたはスピネルは片方ずつ
でも、両方でも何らさしつかえない。
本発明によれば、３点曲げ強度1700MPa以上
のジルコニア焼結体がえられる。ここで規定した
３点曲げ強度値とは、JISR1601−1981に基づき
幅４mm、厚さ３mm、長さ40mmの試験体をスパン長
さ30mm、クロスヘツドスピード0.5mm／minの条
件で曲げ破壊したとき得られる強度の10体以上の
平均値を意味する。
該ジルコニア系焼結体の製造方法は、熱間静水
圧プレス（以下HIPと略記する）することを特徴
としている。HIP処理の方法としては粉末成形体
をガラス、金属などのカプセル中に真空封入した
のち、プレス焼成する方法とあらかじめ粉末成形
体を常圧で予備焼結した後、プレス装置によつて
再焼結する方法の２通りが知られている。本発明
からなる焼結体は、どちらの方法によつても作成
することが可能であるが、後者の方法を用いた方
が、カプセル封入の操作が不要であり、生産性に
於いても有利である。該HIP処理の条件は、圧力
50〜500MPa、温度1300〜1650としなければなら
ない。
以下、この製造方法についてさらに詳細に説明
する。
HIPに供する予備焼結体は、90％以上の相対密
度を有し、開気孔を含まないものでなければなら
ない。また、アルミナ又はスピネルの比率が20重
量％以下の場合には、予備焼成温度を1400℃以下
に、比率が20重量％以上の場合には1500℃以下に
設定することが望ましい。この理由は、1400℃あ
るいは1500℃より高い焼成温度で得られた焼結体
は、成長した大きな開気孔を含むようになり、
HIP処理による気孔除去が充分果せないからであ
る。従つて、1500℃以下の可能な限り低い焼成温
度で開気孔のない緻密な予備焼結体を得ること
が、この製造方法を実施する上で、重要な前提と
なる。このような予備焼結体を得るには、出発物
質として、焼結性に優れた微粉末を用いることが
好ましい方法である。ジルコニア原料として一次
粒子径200〜400Aの湿式法によつて得られた微粉
末を、またアルミナ、スピネル原料としては、湿
式法或いは共沈法によつて得られた高純度粉末を
用いることが望ましい。或いは、ジルコニウムと
アルミニウムを含む水溶液から共沈法によつて合
成した微粉末を用いることも望ましい方法と考え
られる。
また、ガラス、金属などのカプセル中にジルコ
ニアとアルミナまたはスピネルの微粉末を真空封
入した後、HIP処理することも可能である。
HIP処理の温度、圧力条件については、圧力
50MPa以下、温度1300℃以下の条件では期待さ
れる高強度焼結体は、得難い。また、温度1650℃
以上では、強度を得ることは可能であるが、焼結
体粒径が1μm以上に成長することに起因して、
200〜300℃に長時間保持した場合に焼結体に亀裂
が入るような熱的に不安定な焼結体となる。従つ
て、実際に、工業的に利用する材料としては、適
さない。
本発明からなる焼結体のなかで、特に、Y2O3
を２〜３モル％含有したジルコニアにアルミナを
10〜30重量％添加したHIP処理ジルコニア系焼結
体は、2000〜2500MPaに達する極めて高い平均
曲げ強度を与える。この値は、HIP処理を施さな
い焼結体のそれの約２倍に相当する。
このような驚異的な強度上昇は、アルミナ、窒
化ケイ素、炭化ケイ素などの他の材料ではまつた
く見い出すことができない。すなわち、本発明
は、このようなHIP処理の特異な効力と、アルミ
ナまたはスピネルの添加効果を見い出すことによ
つて、成し遂げられたものである。
本発明によつてえられるジルコニア系焼結体
は、従来品より以上に高強度であることから、従
来の切断工具、ダイス、ノズル、ベアリングなど
の機械構造材料は当然の事、これらの中でも特に
強耐久性を要求される分野にさらに有効に使用で
きるものである。
次に本発明を実施例に基づいて、詳細に説明す
るが、本発明はこれらに限定されるものではな
い。
実施例 １
共沈法によつて得られたY2O3を1.5〜５モル％
含む一次粒子径が230ÅのＹ−PSZ粉末と、平均
粒子径が0.4μmの高純度（99.99％）Al2O3粉末、
または0.1μmの高純度MgAl2O4粉末を、所望の組
成となるようにエタノール中で24時間湿式混合し
た後、乾燥行程を経て原料粉末を調製した。次い
で、上記原料粉末をラバープレス法によつて、厚
さ、幅、長さがそれぞれ４mm、40mm、56mmである
板状成形体とし、この成形体を1200〜1500℃の温
度で２時間（予備）焼結し、HIP処理用予備焼結
体とした。この予備焼結体を1300〜4600℃、50〜
200MPaの条件下で0.5時間、Arガス中でHIP処
理して本発明のジルコニア系焼結体を得た。この
ようにして作成した32組の焼結体について焼結体
密度、曲げ強度を行つた。これらの結果を表１に
示す。表１には比較のために、Ｙ−PSZ単身の予
備焼結体にHIP処理した焼結体及び、Ｙ−PSZ−
Al2O3系でHIP処理を行わない焼結体７組につい
ての結果も記した。
The present invention uses zirconia-alumina (ZrO 2 −
Al 2 O 3 ) or zirconia-spinel (ZrO 2 −
The present invention relates to a method for producing a high-strength zirconia-based sintered body made of MgAl 2 O 4 ). In recent years, zirconia sintered bodies ( hereinafter referred to as Y-
Because PSZ (abbreviated as PSZ) exhibits high strength and toughness, there is active development of using this sintered body as a mechanical structural material for cutting tools, dies, nozzles, bearings, etc. The sintered body obtained by the present invention has extremely excellent strength characteristics that should expand its use as a mechanical structural material and ensure even higher reliability and durability in use. Y-PSZ is already well known as a high-strength sintered body, and the reason for its high strength is that the tetragonal zirconia contained in the sintered body transforms into a monoclinic crystal into a martensitic type due to stress. It is thought to be caused by metastasis. The present inventors have discovered that this Y-
As a result of a detailed investigation of the strength of PSZ, we found that the strength is not proportional to the amount of tetragonal zirconia, but reaches its highest value when a small amount of cubic crystals are included in addition to tetragonal crystals. . Inferring from this result, alumina (Al 2 O 3 ) with high elastic modulus and strength is used instead of cubic zirconia.
Alternatively, we hypothesized that even higher strength could be achieved by adding spinel (MgAl 2 O 4 ). Y-PSZ-Al 2 O 3- based sintered body has already been described in the literature (J.Mat.Sci.17, 247-254
(1982), etc., but the bending strength values of hot-pressed sintered bodies reported therein are
It has not reached 1200MPa and hot press Y
- It was low compared to the PSZ value (1300-1700 MPa), which contradicted the above hypothesis. However, the strength of the sintered body largely depends on the starting material and the method for producing it. Therefore, the present inventors investigated the zirconia-alumina system or the zirconia-spinel system in order to obtain a sintered body with excellent mechanical strength characteristics, and found that alumina or spinel was added to the tetragonal zirconia containing a small amount of ittria. The present inventors have discovered that a sintered body with significantly improved strength properties compared to Y-PSZ can be obtained by blending a specific proportion of Y-PSZ and by performing a hot isostatic pressing treatment, thereby completing the present invention. That is, the present invention provides zirconia (ZrO 2 ) 50 containing 1.5 to 5 mol% ittria (Y 2 O 3 ).
~98% by weight and 50-2% by weight of alumina (Al 2 O 3 ) or spinel (MgAl 2 O 4 ).
A pre-sintered body pre-sintered at 1500℃ or a powder compact of the same composition vacuum-sealed in a capsule is heated to a pressure of 50℃.
The present invention provides a method for producing the zirconia-based sintered body by hot isostatic pressing at a temperature of ~500 MPa and a temperature of 1,300 to 1,650°C. The present invention will be explained in more detail below. The sintered body obtained by the present invention contains 50 to 98% by weight of zirconia containing 1.5 to 5 mol% of Y2O3 .
and 50 to 2% by weight of alumina or spinel. If the Y2O3 content in zirconia is less than 1.5 mol%, a sintered body consisting of tetragonal crystals cannot be obtained, and if it exceeds 5 mol%, the tetragonal crystals decrease,
Since it is mainly composed of cubic crystals, it is not possible to obtain high strength due to dislocation, making it unsuitable. If the amount of alumina or spinel added to zirconia is less than 2% by weight, it is difficult to obtain the effect of increasing the strength by adding it, and
If it exceeds 50% by weight, the strengthening mechanism caused by tetragonal zirconia will be reduced, and the expected strength will not be obtained. Either one or both of alumina or spinel may be added. According to the present invention, a zirconia sintered body having a three-point bending strength of 1700 MPa or more can be obtained. The three-point bending strength value specified here is based on JISR1601-1981 when a test specimen with a width of 4 mm, a thickness of 3 mm, and a length of 40 mm is broken by bending under the conditions of a span length of 30 mm and a crosshead speed of 0.5 mm/min. Means the average value of the strength obtained for 10 or more bodies. The method for producing the zirconia-based sintered body is characterized by hot isostatic pressing (hereinafter abbreviated as HIP). The HIP processing method involves vacuum sealing the powder compact in a capsule made of glass, metal, etc., and then press-firing it, or pre-sintering the powder compact under normal pressure, and then re-sintering it using a press machine. There are two known methods for doing this. The sintered body of the present invention can be produced by either method, but the latter method eliminates the need for encapsulation and is advantageous in terms of productivity. It is. The conditions for the HIP treatment are pressure
Must be 50~500MPa and temperature 1300~1650. This manufacturing method will be explained in more detail below. The pre-sintered body to be subjected to HIP must have a relative density of 90% or more and be free of open pores. Further, when the proportion of alumina or spinel is 20% by weight or less, it is desirable to set the pre-firing temperature to 1400°C or less, and when the proportion is 20% by weight or more, it is desirable to set the pre-calcination temperature to 1500°C or less. The reason for this is that sintered bodies obtained at sintering temperatures higher than 1400°C or 1500°C will contain large open pores that have grown.
This is because pores cannot be removed sufficiently by HIP treatment. Therefore, obtaining a dense pre-sintered body without open pores at the lowest possible firing temperature of 1500° C. or lower is an important premise for carrying out this manufacturing method. In order to obtain such a pre-sintered body, it is preferable to use a fine powder with excellent sinterability as a starting material. It is desirable to use a fine powder obtained by a wet method with a primary particle size of 200 to 400 A as the zirconia raw material, and a high purity powder obtained by a wet method or coprecipitation method as the alumina and spinel raw material. . Alternatively, it is considered to be a desirable method to use a fine powder synthesized from an aqueous solution containing zirconium and aluminum by a coprecipitation method. It is also possible to vacuum-seal fine powders of zirconia and alumina or spinel in a capsule made of glass, metal, etc., and then perform HIP treatment. For information on temperature and pressure conditions for HIP processing, please refer to
It is difficult to obtain the expected high-strength sintered body under conditions of 50 MPa or less and a temperature of 1300°C or less. In addition, the temperature is 1650℃
With the above, it is possible to obtain strength, but due to the grain size of the sintered body growing to 1 μm or more,
If kept at 200 to 300°C for a long time, the sintered body becomes thermally unstable, with cracks appearing in the sintered body. Therefore, it is not suitable as a material for actual industrial use. Among the sintered bodies of the present invention, especially Y 2 O 3
Alumina is added to zirconia containing 2 to 3 mol% of
HIP-treated zirconia-based sintered bodies containing 10 to 30% by weight give extremely high average bending strengths reaching 2000 to 2500 MPa. This value corresponds to approximately twice that of the sintered body without HIP treatment. Such an amazing increase in strength cannot be found with other materials such as alumina, silicon nitride, and silicon carbide. That is, the present invention was achieved by discovering the unique efficacy of such HIP treatment and the effect of adding alumina or spinel. Since the zirconia-based sintered body obtained by the present invention has higher strength than conventional products, it is of course suitable for mechanical structural materials such as conventional cutting tools, dies, nozzles, bearings, etc. It can be used more effectively in fields where strong durability is required. Next, the present invention will be explained in detail based on Examples, but the present invention is not limited thereto. Example 1 1.5 to 5 mol% of Y 2 O 3 obtained by coprecipitation method
Y-PSZ powder with a primary particle size of 230 Å, high purity (99.99%) Al 2 O 3 powder with an average particle size of 0.4 μm,
Alternatively, 0.1 μm high purity MgAl 2 O 4 powder was wet mixed in ethanol for 24 hours to obtain a desired composition, and then subjected to a drying process to prepare a raw material powder. Next, the raw material powder was molded into plate-shaped bodies with thickness, width, and length of 4 mm, 40 mm, and 56 mm, respectively, by a rubber press method, and this molded body was heated at a temperature of 1200 to 1500°C for 2 hours (preparation). ) was sintered and used as a preliminary sintered body for HIP treatment. This pre-sintered body is heated to 1300-4600℃, 50-
The zirconia-based sintered body of the present invention was obtained by HIPing in Ar gas under conditions of 200 MPa for 0.5 hours. The density and bending strength of the 32 sintered bodies thus prepared were measured. These results are shown in Table 1. For comparison, Table 1 shows sintered bodies obtained by HIPing a preliminary sintered body of Y-PSZ alone, and Y-PSZ-
The results for seven sets of Al 2 O 3 based sintered bodies that were not subjected to HIP treatment were also reported.
【表】【table】
【表】
実施例 ２
実施例１で用いたＹ−PSZとAl2O3の混合粉末
をラバープレス法によつて圧力3ton／cm2で角棒状
成形体（４×４×56mm）とした後、MO金属薄膜
によつて包み、パイレツクスがラスチユーブに入
れ、真空封入した。これらガラスカプセル中に入
れた成形体をホツトアイソスタテイツク装置に入
れ、Ar雰囲気中で800℃迄加熱した後、加圧を開
始し、1500℃、100MPa、0.5時間の条件で処理し
た。得られた焼結体をダイヤモンドホイールで研
削し、前述の方法に従つて、曲げ強度測定を行つ
た。[Table] Example 2 The mixed powder of Y-PSZ and Al 2 O 3 used in Example 1 was made into a rectangular bar-shaped body (4 x 4 x 56 mm) by a rubber press method at a pressure of 3 tons/cm 2. It was then wrapped in MO metal thin film, placed in a Pyrex tube, and vacuum sealed. These molded bodies placed in glass capsules were placed in a hot isostatic device and heated to 800°C in an Ar atmosphere, and then pressurization was started and treated at 1500°C, 100 MPa, and 0.5 hours. The obtained sintered body was ground with a diamond wheel, and the bending strength was measured according to the method described above.
Claims (1)
するジルコニア（ZrO2）50〜98重量％とアルミ
ナ（Al2O3）またはスピネル（MgAl2O4）50〜２
重量％とから成る1200〜1500℃で予備焼結した予
備焼結体、またはカプセル中に真空封入した該組
成の粉末成形体を圧力50〜500MPa、温度1300〜
1650℃で熱間静水圧プレス処理することを特徴と
するジルコニア系焼結体の製造方法。1 50-98% by weight of zirconia ( ZrO2 ) containing 1.5-5 mol% of ittria ( Y2O3 ) and 50-2% of alumina ( Al2O3 ) or spinel ( MgAl2O4 )
A pre-sintered body pre-sintered at 1200-1500°C, or a powder molded body of the composition vacuum-sealed in a capsule, is heated at a pressure of 50-500 MPa and a temperature of 1300-1300°C.
A method for producing a zirconia-based sintered body, characterized by hot isostatic pressing at 1650°C.
Priority Applications (7)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58192470A JPS6086073A (en) | 1983-10-17 | 1983-10-17 | High strength zirconia sintered body and manufacture |
| EP84307058A EP0140638B1 (en) | 1983-10-17 | 1984-10-15 | High-strength zirconia type sintered body and process for preparation thereof |
| DE8484307058T DE3472398D1 (en) | 1983-10-17 | 1984-10-15 | High-strength zirconia type sintered body and process for preparation thereof |
| AU34254/84A AU573631B2 (en) | 1983-10-17 | 1984-10-15 | High strength zirconia type sintered body |
| US06/661,968 US4587225A (en) | 1983-10-17 | 1984-10-17 | High-strength zirconia type sintered body |
| KR1019840006430A KR920007020B1 (en) | 1983-10-17 | 1984-10-17 | High-strength zirconia type sintered body |
| US06/704,037 US4774041A (en) | 1983-10-17 | 1985-02-21 | High-strength zirconia type sintered body and process for preparation thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP58192470A JPS6086073A (en) | 1983-10-17 | 1983-10-17 | High strength zirconia sintered body and manufacture |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6086073A JPS6086073A (en) | 1985-05-15 |
| JPH0451508B2 true JPH0451508B2 (en) | 1992-08-19 |
Family
ID=16291824
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP58192470A Granted JPS6086073A (en) | 1983-10-17 | 1983-10-17 | High strength zirconia sintered body and manufacture |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6086073A (en) |
Families Citing this family (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0667785B2 (en) * | 1985-07-15 | 1994-08-31 | 東レ株式会社 | Zirconia sintered body |
| JPS62143871A (en) * | 1985-12-17 | 1987-06-27 | 東北セラミツク株式会社 | Metal transfer or adhesion preventing tool |
| US5180696A (en) * | 1987-06-11 | 1993-01-19 | Hitachi Metals, Ltd. | High-toughness zro2 sintered body and method of producing same |
| JP2748388B2 (en) * | 1988-03-16 | 1998-05-06 | 住友電気工業株式会社 | High strength colored zirconia sintered body |
| JP2748389B2 (en) * | 1988-03-16 | 1998-05-06 | 住友電気工業株式会社 | High strength colored zirconia sintered body |
| JPH03112854A (en) * | 1989-09-25 | 1991-05-14 | Osaka Cement Co Ltd | Production of high strength alumina-zirconia system ceramic |
| JP3718541B2 (en) * | 1995-07-13 | 2005-11-24 | ファナック株式会社 | Vertical rotor |
| US8785008B2 (en) | 2006-07-25 | 2014-07-22 | Tosoh Corporation | Zirconia sintered bodies with high total light transmission and high strength, uses of the same, and process for producing the same |
| JP6093228B2 (en) * | 2013-04-09 | 2017-03-08 | 曙ブレーキ工業株式会社 | Friction material |
| JP7035220B2 (en) * | 2018-12-06 | 2022-03-14 | 日本碍子株式会社 | Ceramic sintered body and substrate for semiconductor devices |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5713077A (en) * | 1980-06-26 | 1982-01-23 | Mitsubishi Electric Corp | Reinforcing device for truss |
| JPS5832066A (en) * | 1981-08-13 | 1983-02-24 | 日本特殊陶業株式会社 | Tenacious zirconia sintered body |
-
1983
- 1983-10-17 JP JP58192470A patent/JPS6086073A/en active Granted
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5713077A (en) * | 1980-06-26 | 1982-01-23 | Mitsubishi Electric Corp | Reinforcing device for truss |
| JPS5832066A (en) * | 1981-08-13 | 1983-02-24 | 日本特殊陶業株式会社 | Tenacious zirconia sintered body |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6086073A (en) | 1985-05-15 |
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