JPS59111976A - Zirconia ceramics - Google Patents
Zirconia ceramicsInfo
- Publication number
- JPS59111976A JPS59111976A JP57219427A JP21942782A JPS59111976A JP S59111976 A JPS59111976 A JP S59111976A JP 57219427 A JP57219427 A JP 57219427A JP 21942782 A JP21942782 A JP 21942782A JP S59111976 A JPS59111976 A JP S59111976A
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- Prior art keywords
- porcelain
- added
- sample
- mgo
- amount
- Prior art date
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- Compositions Of Oxide Ceramics (AREA)
Abstract
(57)【要約】本公報は電子出願前の出願データであるた
め要約のデータは記録されません。(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.
Description
【発明の詳細な説明】
産業上の利用分野
本発明は軸受や切削工具などに用いることができるジル
コニア磁器に関するものである。DETAILED DESCRIPTION OF THE INVENTION Field of Industrial Application The present invention relates to zirconia porcelain that can be used for bearings, cutting tools, and the like.
従来例の構成とその問題点
従来から、高強度セラミ、ツク材料の一つとして、ジル
コニアにイツトリア、カルシア、マグネシア等の安定化
剤を混合し、高温で焼成した安定化ジルコニア磁器が注
目されている。さらに最近になって、安定化剤の添加量
がより少なく、かつ上記の安定化ジルコニア磁器に比較
して、より高強度な部分安定化磁器が、高強度セラミッ
ク材料として最も適したものの一つとして注目されてき
ている。Structure of conventional examples and their problems Stabilized zirconia porcelain, which is made by mixing zirconia with stabilizers such as yttoria, calcia, and magnesia and firing it at high temperatures, has been attracting attention as a high-strength ceramic material. There is. Furthermore, recently, partially stabilized porcelain, which requires a smaller amount of stabilizer added and has higher strength than the above-mentioned stabilized zirconia porcelain, has been recognized as one of the most suitable high-strength ceramic materials. It is attracting attention.
しかしながら、この部分安定化ジルコニア磁器には大き
な欠点がある。それは、ある温度条件、例えば200〜
360’Cでの保持やあるいは、室温と高温(1000
’C付近)の間の温度変化の繰り返しを行なった場合に
、磁器の自然破壊がおこることである。この原因は、高
温焼成時に立方晶と正方晶の二相共存の磁器である部分
安定化ジルコニア磁器が、その中の一つの結晶相である
高温相の正方晶がよシ低温相の単斜晶に変化することに
よって大きな体積膨張が生じることにある。However, this partially stabilized zirconia porcelain has major drawbacks. It is under certain temperature conditions, for example 200~
Holding at 360'C or room temperature and high temperature (1000'C)
When the temperature changes repeatedly between 2000 and 2000, spontaneous destruction of the porcelain occurs. The reason for this is that during high-temperature firing, partially stabilized zirconia porcelain, which is a porcelain with two coexisting phases of cubic and tetragonal crystals, has one crystalline phase, tetragonal, which is a high-temperature phase, and monoclinic, a low-temperature phase. The reason for this is that a large volumetric expansion occurs due to the change in .
発明の目的
本発明の目的は、広い温度範囲において熱的に安定で、
かつ、高い強変を有するジルコニア磁器を提供すること
にある。OBJECT OF THE INVENTION The object of the invention is to provide a material that is thermally stable over a wide temperature range;
Another object of the present invention is to provide zirconia porcelain having a high tensile modulus.
発明の構成
本発明のジルコニア磁器は、ZrO2を主成分とし、Y
2O5を3〜emot% を添加し、これに対して、さ
らにAβ2銚を1〜6wt%、 SiO2を006〜0
.3wt%、 CaOを0.05〜0.3wt%およ
び、−MgOを0.05〜0.3wt%添加したもので
あり、これによって生じる複合添加物効果を用いて、部
分安定化ジルコニア磁器中の正方晶相から単斜晶相への
相転移を抑制することにより、磁器破壊が生じない磁器
を実現したものである。Structure of the Invention The zirconia porcelain of the present invention has ZrO2 as a main component and Y
Add 3~emot% of 2O5, and further add 1~6wt% of Aβ2 and add 006~0% of SiO2.
.. 3 wt%, 0.05 to 0.3 wt% of CaO, and 0.05 to 0.3 wt% of -MgO, and using the resulting composite additive effect, the By suppressing the phase transition from the tetragonal phase to the monoclinic phase, we have achieved porcelain that does not cause porcelain fracture.
実施例の説明 以下本発明の実施例について詳細に説明する。Description of examples Examples of the present invention will be described in detail below.
酸花ジルコニウムZrO2と酸化イ・ノトリウムY2O
6がそれぞれmoA%で95:5の比になるように均一
に混合した部分安定化ジルコニア磁器原料粉体を作成し
た。これに添加剤として、k120s。Acid flower zirconium ZrO2 and inotrium oxide Y2O
Partially stabilized zirconia porcelain raw material powder was prepared by uniformly mixing 6 and 6 at a ratio of 95:5 in terms of moA%. As an additive to this, k120s.
SiO2,Cab、 MgOを単独又は複合で添加して
、Al2O54wt%のみを添加したもの、 5iO2
0,1wt%のみを添加したもの、 CaOo、1wt
%のみを添加したもの、 MgOo、1wt%のみを添
加したもの、およびAβ2034wt%、 5iO2
0,1wt%を複合で添加したもty) 、 A120
54wt%、 5iO20,1wt%。SiO2, Cab, and MgO are added alone or in combination, and only 54 wt% of Al2O is added, 5iO2
Added only 0.1wt%, CaOo, 1wt
% only, MgOo, 1wt% only, and Aβ2034wt%, 5iO2
0.1 wt% added in combination), A120
54wt%, 5iO20, 1wt%.
MgO0,1wt%を複合で添加したもの、Aβ205
4W塙5iO2o、1wt%、 CaOO,1wt%、
MgO0,1wt%を複合で添加したもの、並びに添
加剤を全く含まないもの(Y2O5tsrnot%含む
)の8種類のジルコニア磁器粉体を作成した。Composite addition of 0.1 wt% MgO, Aβ205
4W Hanawa 5iO2o, 1wt%, CaOO, 1wt%,
Eight types of zirconia porcelain powders were prepared, including one to which 0.1 wt% of MgO was added in combination and one containing no additive at all (containing 5tsrnot% of Y2O).
これらの粉体を用いて、油圧プレスで板状に成形し、1
650℃で焼成して巾10朋×厚み2關×長さ35 m
inの板状のジルコニア磁器を作成した。Using these powders, form them into a plate shape using a hydraulic press, and
Baked at 650℃, width 10mm x thickness 2mm x length 35m
In plate-shaped zirconia porcelain was created.
このようにして作成した試料を250°Cの温度に保持
した恒温槽中に長時間(最高6000時間まで)放置し
た。これによって結晶相中の相変化をうながした。恒温
槽中に放置した試料は、一定時間ごとに取り出し、公知
の3点曲げ試験による曲げ強度を測定し、その結果から
磁器の劣化状態を判定した。The thus prepared sample was left in a constant temperature bath kept at a temperature of 250°C for a long time (up to 6000 hours). This promoted a phase change in the crystalline phase. The samples left in the thermostatic bath were taken out at regular intervals, and the bending strength was measured by a known three-point bending test, and the state of deterioration of the porcelain was determined from the results.
その結果を図面に示す。図中1は添加剤を4種類複合で
添加した本発明の一実施例の試料、2は添加剤を含まな
い試料、3〜6ばそれぞれA12’3゜SiO2,Ca
b、 MgOを単独で添加した試料、7はAl2O5と
5i02を複合添加した試料、8ばAl2O5゜SiO
2,MgOを複合添加した試料である。The results are shown in the drawing. In the figure, 1 is a sample of an embodiment of the present invention in which a combination of four types of additives is added, 2 is a sample containing no additives, and 3 to 6 are A12'3°SiO2, Ca, respectively.
b, Sample where MgO was added alone, 7: Sample where Al2O5 and 5i02 were added in combination, 8: Al2O5゜SiO
2. This is a sample with combined addition of MgO.
これらのうち2〜8の試料は、熱ニージンク時間が約1
000時間以内でその曲げ強度が極端に低くなる傾向が
ある。この現象が部分安定化ジルコニア磁器の結晶相転
移による磁器破壊現象である。Samples 2 to 8 of these have a thermal knee zinc time of approximately 1
The bending strength tends to become extremely low within 1,000 hours. This phenomenon is a porcelain destruction phenomenon due to crystal phase transition of partially stabilized zirconia porcelain.
また、添加剤を無添加あるいは1種類単独添加した場合
、または添加剤が3種類までの場合には、磁器破壊を防
止するほどの添加剤効果がないことがわかる。しかしな
がら、添加剤を4種類複合添加した1の試料では、熱エ
ージング時間が5000時間を経た後においても、曲げ
強度は全く初期値と変化していないことがわかる。すな
わち、k1203. SiO2,Cab、 HgOを複
合で添加することによって、明らかな添加剤効果が現わ
れている。Furthermore, it can be seen that when no additives are added, when only one type of additive is added, or when up to three types of additives are added, the additives do not have a sufficient effect to prevent porcelain destruction. However, it can be seen that in sample 1, in which four types of additives were added in combination, the bending strength did not change at all from the initial value even after 5000 hours of thermal aging. That is, k1203. By adding SiO2, Cab, and HgO in combination, a clear additive effect appears.
次に、Y2O6の量および添加剤であるk1203゜S
iO2,Cab、 MgOそれぞれの添加量を種々変化
サセタジノンコニア磁器について、上記と同様の検討を
行なった。その結果を次表に示す。Next, the amount of Y2O6 and the additive k1203°S
The same study as above was conducted on sasseta dinonconia porcelain in which the amounts of iO2, Cab, and MgO added were varied. The results are shown in the table below.
(以 下 余 白p
米比較例
上記表において、試料Nα1.2,3,22゜23はY
2O5量を変化させた試料であるが、このうち試料Nα
1のY2O3が少ない(2mot%)ものは、初期の曲
げ強度は47にノ・f/−と大きいが、熱エージング試
験(260’(:、 −5000時間)で磁器破壊が認
められた。また、試料N123のY2O3の多い(ym
o7%)1ものは、熱エージング試験による磁器破壊が
認められなかったが、初期の曲げ強度が小さい。一方、
試料Nα2,3.22のものは、熱エージング試験によ
る磁器破壊が認められず、また初期の曲げ強度も大きい
ことがわかる。(Margin below) Rice Comparative Example In the above table, samples Nα1.2, 3, 22°23 are Y
These are samples with varying amounts of 2O5, among which sample Nα
1 with a low Y2O3 content (2 mot%), the initial bending strength was as high as 47 f/-, but porcelain fracture was observed in the heat aging test (260' (:, -5000 hours). , sample N123 has a large amount of Y2O3 (ym
o7%) 1, no porcelain fracture was observed in the heat aging test, but the initial bending strength was low. on the other hand,
It can be seen that in sample Nα2, 3.22, no porcelain fracture was observed in the heat aging test, and the initial bending strength was high.
なお、試料Nα4〜21は、Y20gの添加量をs m
ot%に固定して、N[14〜Bけj、1203(7)
添加量。In addition, for samples Nα4 to 21, the addition amount of Y20g was s m
Fixed to ot%, N[14~Bkej, 1203(7)
Amount added.
NrL9〜13はSiO2の添加量、N1114〜17
は(aOの添加量、N[118〜21はMgC1)添加
量をそ□
れぞれ変化させた試料であるが、表から理解されるごと
く、k120s量の最も少ないNα4の試料は熱エージ
ング試験による磁器破壊が認められた。NrL9-13 is the amount of SiO2 added, N1114-17
are samples in which the added amounts of aO and N [118 to 21 are MgC1] were changed, but as can be understood from the table, the Nα4 sample with the least amount of k120s was subjected to the thermal aging test. porcelain destruction was observed.
同様に、5102量の少ないNαg 、 CaO量の少
ないNα14の試料およびNα18のMgO量の少ない
試料逆に、これらの添加剤の添加量が多いN[L8゜1
3.1了、21の試料では、熱エージング試験による磁
器破壊が認められなかったが、初期の曲げ強度が小さい
。Similarly, 5102 samples with a small amount of Nαg, Nα14 with a small amount of CaO, and Nα18 with a small amount of MgO conversely, N[L8゜1 with a large amount of these additives added.
In the sample No. 3.1 and No. 21, no porcelain fracture was observed in the heat aging test, but the initial bending strength was low.
一方、試料N(15〜7のAl2O5量が1〜6wt%
の範囲のもの、Nα1o〜12のSiO2量が。、06
〜0.3wt% の範囲のも(7) 、 NIL 15
〜1 eノca。On the other hand, sample N (Al2O5 amount of 15-7 is 1-6 wt%
The amount of SiO2 is in the range of Nα1o to 12. ,06
~0.3 wt% (7), NIL 15
~1 enoca.
量が0.05〜0.3 wt%の範囲のものおよびNα
19〜20のMgO量が0.05〜0.3 wt%の範
囲のものは、熱エージング試験による磁器破壊が認めら
れず、また初期の曲げ強度も大きいことがわかる。The amount ranges from 0.05 to 0.3 wt% and Nα
It can be seen that in samples No. 19 to 20 with an MgO content in the range of 0.05 to 0.3 wt%, no porcelain fracture was observed in the heat aging test, and the initial bending strength was high.
なお、前述の250℃でのエージ°ング試験で磁器破壊
が認められなかった試料を、実際に使用されると思われ
る温度範囲(RT〜600’C)で、昇・降温スピード
が300℃/n 、保持時間が6時間のくり返し温度変
化での熱エージング試験をs oo。In addition, for the sample in which no porcelain destruction was observed in the above-mentioned aging test at 250°C, the heating and cooling speed was 300°C/300°C in the temperature range expected to be actually used (RT ~ 600'C). n, thermal aging test with repeated temperature changes with a holding time of 6 hours.
時間まで行なったが、いずれの試料についても磁器破壊
が認められず、高い強度を有していた。Although the test was carried out for several hours, no porcelain fracture was observed in any of the samples, and they had high strength.
発明の効果
以上の説明から明らかなように、本発明のジルコニア磁
器はZrO2を主成分とし、Y2O3を3〜6 moz
%添加し、これに対して、さらにA12o5を1〜6w
t%、 SiO2を0.05〜0.3 w、t%、
CaOを0.05〜0.3 wt%、 MgOを0.0
6〜0.3 wt%t%したものであり、これらの添加
剤の複合添加効果によって、ジルコニア磁器の欠点であ
った200°C〜350℃の湿iでの熱エージングによ
る磁器破壊現象を克服できるため、その実用上の価値は
大なるものがある。Effects of the Invention As is clear from the above explanation, the zirconia porcelain of the present invention contains ZrO2 as a main component and Y2O3 in an amount of 3 to 6 moz.
%, and to this, 1 to 6 w of A12o5 was added.
t%, SiO2 0.05-0.3 w, t%,
CaO 0.05-0.3 wt%, MgO 0.0
6 to 0.3 wt%t%, and the combined addition effect of these additives overcomes the porcelain destruction phenomenon caused by thermal aging at 200°C to 350°C humidity, which was a drawback of zirconia porcelain. Therefore, its practical value is great.
図面は本発明のジルコニア磁器の25.0’cでの熱エ
ージング試験の結果を示す特性図である。
代理人の氏名 弁理士 中 尾 敏 男 ほか1名−4
(The drawing is a characteristic diagram showing the results of a thermal aging test at 25.0'c of the zirconia porcelain of the present invention. Name of agent: Patent attorney Toshio Nakao and 1 other person-4
(
Claims (1)
し、これに対して、さらにA4205を1〜ewt%、
SiO2を0.05〜0.3 wt%、 CaOを0
.05〜0.3wt%およびMgOを0.05〜0.3
wt%添加したことを特徴とするジルコニア磁器。The main component is ZrO2, 3~6m01% of Y2O is added, and 1~ewt% of A4205 is added.
SiO2 0.05-0.3 wt%, CaO 0
.. 05-0.3 wt% and 0.05-0.3 MgO
Zirconia porcelain characterized by wt% addition.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP57219427A JPS59111976A (en) | 1982-12-14 | 1982-12-14 | Zirconia ceramics |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP57219427A JPS59111976A (en) | 1982-12-14 | 1982-12-14 | Zirconia ceramics |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS59111976A true JPS59111976A (en) | 1984-06-28 |
Family
ID=16735220
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP57219427A Pending JPS59111976A (en) | 1982-12-14 | 1982-12-14 | Zirconia ceramics |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS59111976A (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4900492A (en) * | 1984-04-27 | 1990-02-13 | Max-Planck-Gesellschaft Zur Foerderung Der Wissenschaften E.V. | High-strength and temperature-stable formed bodies of zirconium dioxide |
JPH02157157A (en) * | 1988-12-12 | 1990-06-15 | Tosoh Corp | Zirconia sintered body having superior corrosion resistance and hot water resistrance |
JPH035365A (en) * | 1989-05-12 | 1991-01-11 | General Motors Corp <Gm> | Low-temperature sintering of toughened zirconia |
-
1982
- 1982-12-14 JP JP57219427A patent/JPS59111976A/en active Pending
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4900492A (en) * | 1984-04-27 | 1990-02-13 | Max-Planck-Gesellschaft Zur Foerderung Der Wissenschaften E.V. | High-strength and temperature-stable formed bodies of zirconium dioxide |
JPH02157157A (en) * | 1988-12-12 | 1990-06-15 | Tosoh Corp | Zirconia sintered body having superior corrosion resistance and hot water resistrance |
JPH035365A (en) * | 1989-05-12 | 1991-01-11 | General Motors Corp <Gm> | Low-temperature sintering of toughened zirconia |
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