JPH0570224A - Production of zirconia sintered body and zirconia sintered body - Google Patents
Production of zirconia sintered body and zirconia sintered bodyInfo
- Publication number
- JPH0570224A JPH0570224A JP3030438A JP3043891A JPH0570224A JP H0570224 A JPH0570224 A JP H0570224A JP 3030438 A JP3030438 A JP 3030438A JP 3043891 A JP3043891 A JP 3043891A JP H0570224 A JPH0570224 A JP H0570224A
- Authority
- JP
- Japan
- Prior art keywords
- sintered body
- powder
- zirconia sintered
- zro
- mixed
- 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.)
- Withdrawn
Links
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 title claims abstract description 42
- 238000004519 manufacturing process Methods 0.000 title claims description 8
- 239000000843 powder Substances 0.000 claims abstract description 34
- 239000002245 particle Substances 0.000 claims abstract description 17
- 238000001513 hot isostatic pressing Methods 0.000 claims description 11
- 239000003381 stabilizer Substances 0.000 claims description 9
- 239000011812 mixed powder Substances 0.000 claims description 7
- 238000005245 sintering Methods 0.000 claims description 5
- 238000000465 moulding Methods 0.000 claims 1
- 238000005728 strengthening Methods 0.000 abstract description 6
- 239000000203 mixture Substances 0.000 abstract description 4
- 230000002706 hydrostatic effect Effects 0.000 abstract 1
- 230000007547 defect Effects 0.000 description 19
- 238000000034 method Methods 0.000 description 11
- 239000011148 porous material Substances 0.000 description 11
- 238000002156 mixing Methods 0.000 description 7
- 238000013001 point bending Methods 0.000 description 4
- 239000012298 atmosphere Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002002 slurry Substances 0.000 description 2
- 238000007088 Archimedes method Methods 0.000 description 1
- 239000004372 Polyvinyl alcohol Substances 0.000 description 1
- 239000000853 adhesive Substances 0.000 description 1
- 230000001070 adhesive effect Effects 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000012300 argon atmosphere Substances 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 238000009694 cold isostatic pressing Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 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 1
- 230000006378 damage Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000005469 granulation Methods 0.000 description 1
- 230000003179 granulation Effects 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 229920002451 polyvinyl alcohol Polymers 0.000 description 1
- 230000000644 propagated effect Effects 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Compositions Of Oxide Ceramics (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、特に高い破壊靱性値を
有するジルコニア焼結体の製造方法とこれによって得ら
れるジルコニア焼結体に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a zirconia sintered body having a particularly high fracture toughness and a zirconia sintered body obtained thereby.
【０００２】[0002]
【従来の技術】一般にセラミックスにおいては、焼結体
の組織内に本来もっている破壊源の大きさ以下の欠陥が
均一に分散していると、破壊により伝播するクラック先
端近傍で前記欠陥が成長して非弾性領域が形成される。
そして、この領域の弾性率が減少し、これがクラック先
端付近の応力場の強さを小さくする効果をもつことによ
り、破壊靱性などの機械的性質が向上するのである。な
お、このような機構はマイクロクラック強化機構として
よく知られている。2. Description of the Related Art Generally, in ceramics, when defects having a size equal to or smaller than the original size of the fracture source are uniformly dispersed in the structure of the sintered body, the defects grow near the crack tip propagated by the fracture. An inelastic region is formed.
Then, the elastic modulus in this region decreases, and this has the effect of reducing the strength of the stress field near the crack tip, so that the mechanical properties such as fracture toughness are improved. Such a mechanism is well known as a microcrack strengthening mechanism.
【０００３】ところで、焼結体中に欠陥を分散する方法
としては、例えばジルコニア焼結体の場合、ZrO2粒子の
正方晶から単斜晶への相転移の際の体積変化を利用する
方法や、熱膨張係数の異なった粒子を分散させて、マト
リックスとの熱膨張差を利用する方法がよく知られてい
る。By the way, as a method of dispersing defects in a sintered body, for example, in the case of a zirconia sintered body, a method of utilizing a volume change at the time of a phase transition of ZrO 2 particles from a tetragonal crystal to a monoclinic crystal, It is well known to disperse particles having different thermal expansion coefficients and utilize the difference in thermal expansion from the matrix.
【０００４】[0004]
【発明が解決しようとする課題】しかしながら、前述し
たいずれの方法によっても、マトリックスを微少範囲で
破壊することによって欠陥を導入するため、欠陥の大き
さや量の制御には細心の注意が必要である。すなわち、
十分な破壊靱性の向上に気を取られて欠陥を導入し過ぎ
ると、欠陥の大きさが本来もっている破壊源の大きさ以
上になり、強度が低化してしまうのである。However, in any of the above-mentioned methods, defects are introduced by destroying the matrix in a minute range, and therefore, it is necessary to pay close attention to control the size and amount of defects. .. That is,
If too much attention is paid to the improvement of fracture toughness and defects are introduced too much, the size of the defects exceeds the size of the original fracture source, and the strength is reduced.
【０００５】また、これらの組織内では、ZrO2の体積変
化や分散粒子の熱膨張差によって生じた応力が欠陥の生
成により完全に緩和されるとは限らないので、それらの
応力が欠陥に残っていることにより、スロークラックグ
ロース現象が起こり、破壊が進行する恐れももある。以
上のことにより、マイクロクラック強化機構は比較的古
くから知られているものの、十分に実用化されていない
技術の一つなのである。Further, in these structures, the stress caused by the volume change of ZrO 2 and the difference in thermal expansion of the dispersed particles is not always completely relaxed by the generation of defects, so those stresses remain in the defects. As a result, a slow crack growth phenomenon occurs, and there is a possibility that destruction will progress. From the above, although the microcrack strengthening mechanism has been known for a relatively long time, it is one of the technologies that has not been sufficiently put into practical use.
【０００６】本発明は前記事情に鑑みてなされたもの
で、その目的とするところは、マイクロクラック強化機
構を利用することにより、高い破壊靱性値を有するジル
コニア焼結体を提供することにある。The present invention has been made in view of the above circumstances, and an object thereof is to provide a zirconia sintered body having a high fracture toughness value by utilizing a microcrack strengthening mechanism.
【０００７】[0007]
【課題を解決するための手段】本発明における請求項１
記載のジルコニア焼結体の製造方法では、安定化剤とし
てY2O3を２〜４モル％含む粒径０.１〜２.０μmのZrO2
粉末に、安定化剤としてY2O3を２〜４モル％含む粒径
０.０５μm以下のZrO2微粉末を２〜１０重量％混合して
混合粉末を得、次にこの混合粉末を造粒しさらに得られ
た造粒粉末を成形し、次いで得られた成形体を常圧で相
対密度９６〜９８％まで予備焼結し、その後１４８０℃
以下の温度にて熱間静水圧加圧処理することを前記課題
の解決手段とした。また、請求項２記載のジルコニア焼
結体では、請求項１記載の製造方法によって得られたこ
とを前記課題の解決手段とした。[Means for Solving the Problems] Claim 1 in the present invention
In the method for producing a zirconia sintered body described above, ZrO 2 having a particle size of 0.1 to 2.0 μm and containing 2 to 4 mol% of Y 2 O 3 as a stabilizer is used.
2 to 10% by weight of ZrO 2 fine powder having a particle size of 0.05 μm or less containing 2 to 4 mol% of Y 2 O 3 as a stabilizer is mixed with the powder to obtain a mixed powder, and then this mixed powder is prepared. The granulated powder obtained by granulation and further obtained is compacted, and then the compact obtained is pre-sintered at normal pressure to a relative density of 96 to 98%, and then 1480 ° C.
The hot isostatic pressing treatment at the following temperature was taken as a means for solving the above problems. Further, the zirconia sintered body according to claim 2 is obtained by the manufacturing method according to claim 1 as a means for solving the above-mentioned problems.
【０００８】以下、本発明のジルコニア焼結体の製造方
法及びこれによって得られるジルコニア焼結体を詳しく
説明する。本発明者は、ジルコニア焼結体にマイクロク
ラック強化機構を発現させる微小な欠陥を導入するため
に、従来からある微小範囲で破壊させる方法とは全く違
って、簡略な制御により導入することが可能な比較的大
きなクラックを閉気孔の形で焼結体中に導入し、その閉
気孔を熱間静水圧加圧（HIP）処理することによって本
来もっている破壊源の大きさより小さくし、マイクロク
ラック強化機構を発現させる欠陥とすることに思い至り
本発明を完成した。The method for producing a zirconia sintered body of the present invention and the zirconia sintered body obtained thereby will be described in detail below. The present inventor, in order to introduce a minute defect that expresses a microcrack strengthening mechanism in a zirconia sintered body, can be introduced by a simple control, which is completely different from the conventional method of breaking in a minute range. By introducing relatively large cracks in the form of closed pores into the sintered body and subjecting the closed pores to hot isostatic pressing (HIP), the size of the original fracture source is made smaller and micro cracks are strengthened. The present invention has been completed by convincing that the defect is a mechanism-expressing defect.
【０００９】比較的大きなクラックを導入する方法とし
て、本発明では、粒径０.１〜２.０μmの通常のZrO2粉
末に、粒径０.０５μm以下のZrO2微粉末を２〜１０重量
％混合する方法を採用した。すなわち、粒径が０.０５
μm以下のZrO2微粉末は、付着凝集力が大きいため充填
性が悪く、したがって予備焼結において粉末間の空隙が
満たされないまま焼結されるため、閉気孔が生成するの
である。ここで、通常のZrO2粉末へのZrO2微粉末の混合
については、ボールミルなどによる周知の混合方法が採
用できる。また、ZrO2微粉末の混合量を２〜１０重量％
としたのは、２重量％未満であると十分な数のクラック
が発生せず、一方１０重量％を越えると閉気孔とならず
開気孔となってしまい、この開気孔が後のHIP処理によ
って小さくならず好ましくないからである。なお、前記
通常のZrO2粉末およびZrO2微粉末については、いずれも
安定化剤としてY2O3を２〜４モル％含むものを使用す
る。ここで、Y2O3の添加量を２〜４モル％としたのは、
これより多くても少なくても得られる焼結体の曲げ強度
が低下するからである。As a method of introducing a relatively large crack, in the present invention, 2 to 10 parts by weight of ZrO 2 fine powder having a particle size of 0.05 μm or less is added to ordinary ZrO 2 powder having a particle size of 0.1 to 2.0 μm. % Mixing method was adopted. That is, the particle size is 0.05
The ZrO 2 fine powder having a particle size of μm or less has a large adhesive cohesive force and thus has a poor filling property. Therefore, in pre-sintering, the powder is sintered while the voids between the powders are not filled, so that closed pores are generated. Here, as for the mixing of the ZrO 2 fine powder with the ordinary ZrO 2 powder, a well-known mixing method using a ball mill or the like can be adopted. Moreover, the mixing amount of ZrO 2 fine powder is 2 to 10% by weight.
The reason is that if it is less than 2% by weight, a sufficient number of cracks do not occur, while if it exceeds 10% by weight, it becomes open pores instead of closed pores. It is not preferable because it does not become small. In addition, as for the above-mentioned ordinary ZrO 2 powder and ZrO 2 fine powder, those containing 2 to 4 mol% of Y 2 O 3 as a stabilizer are used. Here, the amount of Y 2 O 3 added is 2 to 4 mol%,
This is because the bending strength of the obtained sintered body decreases with more or less than this.
【００１０】このようにして通常のZrO2粉末へZrO2微粉
末を混合した後、得られた混合粉末を周知の方法で造粒
し、さらに得られた造粒粉末を所望形状に成形する。次
いで、得られた成形体を大気中常圧下において１３００
〜１４５０℃程度で、相対密度が９６〜９８％となるま
で予備焼結する。ここで、得られた予備焼結体には、前
述したようにZrO2微粉末を混合したことによる開気孔が
生成されている。なお、ここでの相対密度とは、理論密
度に対しての百分率をいう。After mixing the ZrO 2 fine powder with the ordinary ZrO 2 powder in this way, the obtained mixed powder is granulated by a known method, and the obtained granulated powder is shaped into a desired shape. Then, the obtained molded body is subjected to 1300 at atmospheric pressure under normal pressure.
Pre-sintering is performed at about 1450 ° C. until the relative density reaches 96 to 98%. Here, in the obtained pre-sintered body, open pores were generated by mixing the ZrO 2 fine powder as described above. The relative density here means the percentage with respect to the theoretical density.
【００１１】その後、予備焼結体を１４８０℃以下の温
度にて熱間静水圧加圧（HIP）処理する。この場合に、
１４８０℃完全に消滅してしまい、マイクロクラック強
化機構が働くなるため、HIP処理温度は１４８０℃以下
にする必要がある。なお、HIP処理の雰囲気について
は、アルゴン、窒素およびこれらと酸素との混合気体な
ど、通常採用される雰囲気が採用できる。Thereafter, the pre-sintered body is subjected to hot isostatic pressing (HIP) at a temperature of 1480 ° C. or lower. In this case,
The HIP treatment temperature must be 1480 ° C. or lower because it completely disappears at 1480 ° C. and the microcrack strengthening mechanism works. As the atmosphere for the HIP treatment, an atmosphere that is normally adopted, such as argon, nitrogen and a mixed gas of these and oxygen, can be adopted.
【００１２】[0012]
【作用】本発明における請求項２記載のジルコニア焼結
体によれば、組織内に本来もっている破壊源より小さく
なった閉気孔をもつため、マイクロクラック機構によっ
て高い破壊靱性値を有するものとなる。また、形成され
た閉気孔が応力を加えて生成させた欠陥ではないので、
微小欠陥のスロークラックグロースによる強度劣化の心
配がない。According to the zirconia sintered body according to the second aspect of the present invention, since it has closed pores smaller than the original fracture source in the structure, it has a high fracture toughness value due to the microcrack mechanism. .. In addition, since the formed closed pores are not defects generated by applying stress,
There is no concern about strength deterioration due to slow crack growth of minute defects.
【００１３】[0013]
【実施例】以下、この発明を実施例によりさらに具体的
に説明する。安定化剤としてY2O3を３モル％固溶した平
均粒径０.５６μmのZrO2粉末（粉末A）に、安定化剤と
してY2O3を３モル％固溶した最大粒径０.０１μm以下の
ZrO2粉末（粉末B）を加え、湿式媒体攪拌型混合機で３
０分間混合した。次に、この混合物にバインダーとして
ポリビニルアルコールを加えてスラリーとし、このスラ
リーより造粒物を得た。次いで、得られた造粒物を冷間
静水圧加圧（CIP）によって成形し、さらに得られた成
形体を常圧大気中において図１の表中に示す温度で４時
間予備焼結した。EXAMPLES The present invention will be described in more detail below with reference to examples. ZrO 2 powder (powder A) having an average particle size of 0.56 μm in which 3 mol% of Y 2 O 3 is dissolved as a stabilizer is dissolved in 3 mol% of Y 2 O 3 as a stabilizer, and the maximum particle size is 0. Less than 0.01 μm
Add ZrO 2 powder (powder B) and mix with a wet-medium agitating mixer.
Mix for 0 minutes. Next, polyvinyl alcohol was added to this mixture as a binder to form a slurry, and a granulated product was obtained from this slurry. Next, the obtained granulated product was molded by cold isostatic pressing (CIP), and the obtained molded product was pre-sintered at a temperature shown in the table of FIG. 1 for 4 hours in atmospheric pressure atmosphere.
【００１４】得られた予備焼結体の密度を水置換による
アルキメデス法によって測定した。さらに、測定値から
理論密度６.０８g／cm3として相対密度を計算し、その
結果を図１に示す。その後、予備焼結体をアルゴン雰囲
気中２０００気圧の加圧下にて図１に示す温度で２時間
熱間静水圧加圧（HIP）処理を行なった。得られた焼結
体について室温でJIS R1601による３点曲げ強度、SENB
法による破壊靱性値を測定した。得られた結果を図１に
示す。The density of the obtained pre-sintered body was measured by the Archimedes method with water substitution. Further, the relative density was calculated from the measured value as a theoretical density of 6.08 g / cm 3 , and the result is shown in FIG. 1. Then, the pre-sintered body was subjected to hot isostatic pressing (HIP) treatment for 2 hours at a temperature shown in FIG. 1 under a pressure of 2000 atm in an argon atmosphere. Three-point bending strength according to JIS R1601, SENB at room temperature for the obtained sintered body
The fracture toughness value was measured by the method. The obtained results are shown in FIG.
【００１５】また、比較のため図１に示す条件で焼結体
（No.３〜７）を作製し、本発明の実施例品（No.１〜
２）と同様に３点曲げ強度および破壊靱性値を測定し
た。図１の表中に示す結果より、本発明の実施例品であ
るNo.１およびNo.２は、１０MPam1/2以上の高い破壊靱
性値を示しているのに対し、比較例品のNo.３〜７はい
ずれも９MPam1/2以下の低い破壊靱性値であり、実施例
品が比較例品に比べ破壊靱性値が高いことが確認され
た。For comparison, sintered bodies (Nos. 3 to 7) were produced under the conditions shown in FIG.
The three-point bending strength and fracture toughness values were measured in the same manner as in 2). From the results shown in the table of FIG. 1, No. 1 and No. 2 which are the example products of the present invention show a high fracture toughness value of 10 MPam 1/2 or more, whereas the No. .3 to 7 are all low fracture toughness values of 9 MPam 1/2 or less, and it was confirmed that the example products have higher fracture toughness values than the comparative example products.
【００１６】ここで、No.３は予備焼結密度が大きく、
そのため内部に十分な数の欠陥が生成しないため同じ条
件でHIP処理しても破壊靱性値が大きくならないものと
推察される。また、No.４のようにHIP処理温度が高いと
内部に生成した欠陥が完全に消滅してしまうために破壊
靱性値が大きくならない。さらに、No.５のように粉末B
を加えないと、相対密度が９６％以上であってもHIP処
理によって小さくならない開気孔が残ってしまうため、
最終的には破壊靱性値、３点曲げ強度ともに小さな値と
なってしまうものと考えられる。また、No.６のように
粉末Bを加えず、相対密度が９６％未満のものや、粉末B
を多く入れたNo.７も同様の理由により、破壊靱性値、
３点曲げ強度ともに小さな値となってしまうものと考え
られる。Here, No. 3 has a large pre-sintering density,
Therefore, it is assumed that the fracture toughness value does not increase even if HIP treatment is performed under the same conditions because a sufficient number of defects are not generated inside. In addition, when the HIP treatment temperature is high as in No. 4, the defects generated inside disappear completely and the fracture toughness value does not increase. Furthermore, powder B as No. 5
If you do not add, the open pores that will not be reduced by HIP treatment will remain even if the relative density is 96% or more.
Ultimately, it is considered that the fracture toughness value and the three-point bending strength become small values. Moreover, powder B is not added like No. 6 and the relative density is less than 96%, or powder B
For the same reason, No. 7 containing a large amount of fracture toughness value,
It is considered that the three-point bending strength becomes small.
【００１７】[0017]
【発明の効果】以上説明したように本発明における請求
項１記載のジルコニア焼結体の製造方法は、通常のZrO2
粉末にZrO2微粉末を混合して予備焼結することにより、
閉気孔を生成せしめて組織内に本来もっている破壊源の
大きさよりも小さな欠陥を均一に分散させる方法である
から、マイクロクラック機構によって得られる焼結体の
破壊靱性値を高めることができる。また、閉気孔が応力
を加えて生成された欠陥ではないので、微小欠陥のスロ
ークラックグロースによる強度低下のおそれがなく、十
分な機械強度を有するジルコニア焼結体を製造すること
ができる。As described above, the method for producing a zirconia sintered body according to the first aspect of the present invention is the same as the conventional ZrO 2 method.
By mixing the powder with ZrO 2 fine powder and pre-sintering,
Since this is a method of forming closed pores and uniformly dispersing defects smaller than the original size of the fracture source in the structure, the fracture toughness value of the sintered body obtained by the microcrack mechanism can be increased. In addition, since the closed pores are not defects generated by applying stress, there is no fear of strength deterioration due to slow crack growth of minute defects, and a zirconia sintered body having sufficient mechanical strength can be manufactured.
【００１８】また、請求項２記載のジルコニア焼結体
は、請求項１記載の方法によって得られたものであるか
ら、破壊靱性値が高くしかも十分な機械強度を有するも
のとなる。Further, since the zirconia sintered body according to the second aspect is obtained by the method according to the first aspect, it has a high fracture toughness value and sufficient mechanical strength.
【図１】本発明の実施例品および比較例品の製造条件お
よび測定結果を示す表である。FIG. 1 is a table showing manufacturing conditions and measurement results of an example product and a comparative example product of the present invention.
Claims (2)
粒径０.１〜２.０μmのZrO2粉末に、安定化剤としてY2O
3を２〜４モル％含む粒径０.０５μm以下のZrO2微粉末
を２〜１０重量％混合して混合粉末を得、次にこの混合
粉末を造粒しさらに得られた造粒粉末を成形し、次いで
得られた成形体を常圧で相対密度９６〜９８％まで予備
焼結し、その後１４８０℃以下の温度にて熱間静水圧加
圧処理することを特徴とするジルコニア焼結体の製造方
法。1. A ZrO 2 powder having a particle size of 0.1 to 2.0 μm containing 2 to 4 mol% of Y 2 O 3 as a stabilizer, and Y 2 O as a stabilizer.
2 to 10% by weight of ZrO 2 fine powder containing 2 to 4 mol% of 3 and having a particle size of 0.05 μm or less is mixed to obtain a mixed powder, and then the mixed powder is granulated, and the obtained granulated powder is A zirconia sintered body characterized by being molded, then pre-sintered at a relative density of 96 to 98% under normal pressure, and then subjected to hot isostatic pressing at a temperature of 1480 ° C. or lower. Manufacturing method.
粒径０.１〜２.０μmのZrO2粉末に、安定化剤としてY2O
3を２〜４モル％含む粒径０.０５μm以下のZrO2微粉末
を２〜１０重量％混合して混合粉末を得、次にこの混合
粉末を造粒しさらに得られた造粒粉末を成形し、次いで
得られた成形体を常圧で相対密度９６〜９８％まで予備
焼結し、その後１４８０℃以下の温度にて熱間静水圧加
圧処理されて得られたことを特徴とするジルコニア焼結
体。 2. A ZrO 2 powder having a particle size of 0.1 to 2.0 μm containing 2 to 4 mol% of Y 2 O 3 as a stabilizer, and Y 2 O as a stabilizer.
2 to 10% by weight of ZrO 2 fine powder containing 2 to 4 mol% of 3 and having a particle size of 0.05 μm or less is mixed to obtain a mixed powder, and then the mixed powder is granulated, and the obtained granulated powder is It is characterized in that it is obtained by molding, then pre-sintering the obtained molded body at a normal pressure to a relative density of 96 to 98%, and then hot isostatic pressing at a temperature of 1480 ° C. or lower. Zirconia sintered body.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3030438A JPH0570224A (en) | 1991-02-25 | 1991-02-25 | Production of zirconia sintered body and zirconia sintered body |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3030438A JPH0570224A (en) | 1991-02-25 | 1991-02-25 | Production of zirconia sintered body and zirconia sintered body |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0570224A true JPH0570224A (en) | 1993-03-23 |
Family
ID=12303950
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3030438A Withdrawn JPH0570224A (en) | 1991-02-25 | 1991-02-25 | Production of zirconia sintered body and zirconia sintered body |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0570224A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2022075346A1 (en) | 2020-10-09 | 2022-04-14 | 第一稀元素化学工業株式会社 | Zirconia powder, zirconia sintered body, and production method for zirconia sintered body |
| CN115869089A (en) * | 2021-12-30 | 2023-03-31 | 苏州皓天医学技术有限公司 | All-ceramic tooth production process |
| WO2023190119A1 (en) | 2022-03-31 | 2023-10-05 | 第一稀元素化学工業株式会社 | Zirconia powder, sintered zirconia object, and method for producing sintered zirconia object |
-
1991
- 1991-02-25 JP JP3030438A patent/JPH0570224A/en not_active Withdrawn
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2022075346A1 (en) | 2020-10-09 | 2022-04-14 | 第一稀元素化学工業株式会社 | Zirconia powder, zirconia sintered body, and production method for zirconia sintered body |
| US12612338B2 (en) | 2020-10-09 | 2026-04-28 | Daiichi Kigenso Kagaku Kogyo Co., Ltd. | Zirconia powder, zirconia sintered body, and method for producing zirconia sintered body |
| CN115869089A (en) * | 2021-12-30 | 2023-03-31 | 苏州皓天医学技术有限公司 | All-ceramic tooth production process |
| WO2023190119A1 (en) | 2022-03-31 | 2023-10-05 | 第一稀元素化学工業株式会社 | Zirconia powder, sintered zirconia object, and method for producing sintered zirconia object |
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| A300 | Withdrawal of application because of no request for examination |
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