JPS62123061A - Dielectric ceramic composition - Google Patents
Dielectric ceramic compositionInfo
- Publication number
- JPS62123061A JPS62123061A JP60247433A JP24743385A JPS62123061A JP S62123061 A JPS62123061 A JP S62123061A JP 60247433 A JP60247433 A JP 60247433A JP 24743385 A JP24743385 A JP 24743385A JP S62123061 A JPS62123061 A JP S62123061A
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- Prior art keywords
- composition
- dielectric ceramic
- fired
- ceramic composition
- partial pressure
- Prior art date
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- Compositions Of Oxide Ceramics (AREA)
- Ceramic Capacitors (AREA)
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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1100℃以下で焼成される高誘電率系誘電体
磁器組成物に関し、特に低酸素分圧雰囲気で焼成でき高
い抵抗率の得られる組成物に関する。DETAILED DESCRIPTION OF THE INVENTION Field of Industrial Application The present invention relates to a high dielectric constant dielectric ceramic composition that is fired at a temperature of 1100°C or lower, and in particular a composition that can be fired in a low oxygen partial pressure atmosphere and has a high resistivity. Regarding.
従来の技術
近年セラミックコンデンサにおいては素子の小型化、大
容量化への要求からI、W型セラミックコンデンサが急
速に普及しつつある。積層型セラミックコンデンサは内
部電極とセラミックを一体焼成する工程によって通常製
造される。従来より高誘電率系のセラミックコンデンサ
材料にはチタン酸バリウム系の材料が用いられてきたが
、焼成温度が1300℃程度と高いため、内部電極材料
としてはPt、Pdなどの高価な金属を用いる必要があ
った。BACKGROUND OF THE INVENTION In recent years, I- and W-type ceramic capacitors are rapidly becoming popular due to the demand for smaller elements and larger capacitance in ceramic capacitors. Multilayer ceramic capacitors are typically manufactured by a process of integrally firing internal electrodes and ceramics. Barium titanate-based materials have traditionally been used for high-permittivity ceramic capacitor materials, but because the firing temperature is as high as 1,300°C, expensive metals such as Pt and Pd are used as internal electrode materials. There was a need.
これに対し空気中1000℃以下で焼成でき内部電極と
して安価なAg系材料を用いることができる鉛複合ペロ
ブスカイト系材料や、低酸素分圧雰囲気中で焼成できN
iなとの卑金属材料を内部電極として使用できるチタン
酸バリウム系材料が開発されている。前者については発
明者らはすでにPbTi03−Pb(Mgs、3Nbq
t3)Os Pb(N i 1/2 Wl/2 )
Osを含む誘電体磁器組成物を提案している。後者につ
いては特公昭56−46641号公報に記載の材料など
が知られている。On the other hand, there are lead composite perovskite materials that can be fired in air at temperatures below 1000°C and inexpensive Ag-based materials can be used as internal electrodes, and N-based composite materials that can be fired in a low oxygen partial pressure atmosphere.
Barium titanate-based materials have been developed that allow use of base metal materials as internal electrodes. Regarding the former, the inventors have already developed PbTi03-Pb(Mgs, 3Nbq
t3) Os Pb (N i 1/2 Wl/2 )
A dielectric ceramic composition containing Os is proposed. Regarding the latter, materials such as those described in Japanese Patent Publication No. 56-46641 are known.
PbTiO3−Pb(Mgt/s Nb2ts )0+
−Pb(Nisz2Wl/2 )0+系固溶体は低温
で焼成でき、誘電率の温度変化率が同程度のチタン酸バ
リウム系材料に比べ高い誘電率が得られる。従ってこの
誘電体磁器組成物とAg系内部電極からなる積層コンデ
ンサは、素子の大容量、小型化、低コスト化が図れる利
点を有している。しかし近年さらに内部電極材料の低コ
スト化が図れるCuなどの卑金属を内部電極として用い
ることが求められている。このため、同時焼成したとき
Cuなどの金属が酸化しないような低酸素分圧雰囲気で
焼成したとき誘電体磁器の抵抗率が低下しない材料が必
要とされている。PbTiO3-Pb(Mgt/s Nb2ts)0+
The -Pb(Nisz2Wl/2)0+-based solid solution can be fired at a low temperature and has a higher dielectric constant than a barium titanate-based material with a similar rate of change in dielectric constant with temperature. Therefore, a multilayer capacitor made of this dielectric ceramic composition and an Ag-based internal electrode has the advantage that the device can have a large capacity, be small in size, and low in cost. However, in recent years, there has been a demand for using base metals such as Cu as internal electrodes, which can further reduce the cost of internal electrode materials. Therefore, there is a need for a material that does not reduce the resistivity of dielectric ceramics when fired in a low oxygen partial pressure atmosphere that does not oxidize metals such as Cu when fired simultaneously.
発明が解決しようとする問題点
PbTiC)+ −Pb(Mg+/3 Nb2ts
)Os −Pb(N i t t si W 1
/ 2 ) Os系固溶体は低酸素分圧雰囲気で焼成す
るとチ密に焼結せず、また抵抗率が小さくなる傾向があ
る。Problems to be solved by the invention PbTiC)+ -Pb(Mg+/3 Nb2ts
) Os −Pb(N it t si W 1
/2) When an Os-based solid solution is fired in a low oxygen partial pressure atmosphere, it does not sinter densely and tends to have a low resistivity.
本発明はPbTi03−Pb(Mgtz3NE12zs
)03−Pb(NitzQWl/2 )03系のもつ
高い誘電率と低温焼結性をそこなわず、低酸素分圧雰囲
気で焼成したとき抵抗値が高い誘電体磁器組成物を提供
することを目的としている。The present invention uses PbTi03-Pb (Mgtz3NE12zs
)03-Pb(NitzQWl/2) The purpose is to provide a dielectric ceramic composition that does not impair the high dielectric constant and low-temperature sinterability of the 03 series and has a high resistance value when fired in a low oxygen partial pressure atmosphere. It is said that
問題点を解決するための手段
本発明の誘電体磁器組成物は、(P ba Bab )
(Mgsz* Nb2z3)xTiz(Nitz2Wl
/2 )02+、+1゜で表され(ただしx+y+z=
1)、0.001≦ b ≦0.250,1.000≦
a+b≦1.200の範囲の組成である。Means for Solving the Problems The dielectric ceramic composition of the present invention has (P ba Bab )
(Mgsz* Nb2z3)xTiz(Nitz2Wl
/2 )02+, +1° (however, x+y+z=
1), 0.001≦ b ≦0.250, 1.000≦
The composition is in the range of a+b≦1.200.
作用
本発明の組成物においては、低酸素分圧雰囲気、110
0℃以下の焼成温度でチ密な焼成物が得られ、高い抵抗
率を有する信頼性の高い素子がえられる。Operation In the composition of the present invention, a low oxygen partial pressure atmosphere, 110
A dense fired product can be obtained at a firing temperature of 0° C. or lower, and a highly reliable device with high resistivity can be obtained.
実施例 出発原料には化学的に高純度なPbO,MgO。Example The starting materials are chemically highly pure PbO and MgO.
BaCO3、Nb2O5,TiO2,Ni○、WO2を
用いた。これらを純度補正をおこなったうえで所定量を
秤量し、メノウ製玉石を用い純水を溶媒としボールミル
で17時時間式混合した。これを吸引ろ過して水分の大
半を分離した後乾燥し、その後ライカイ機で充分解砕し
た後粉体量の5 w t%の水分を加え、直径60nm
+高さ約50mmの円柱状に成形圧力500kg/CI
l+2 で成形した。これをアルミナルツボ中に入れ
同質のフタをし、750℃〜880℃で多時間仮焼した
。次に仮焼物をアルミナ乳鉢で粗砕し、さらにメノウ製
玉石を用い純水を溶媒としてボールミルで17時間粉砕
し、これを吸引ろ過し水分の大半を分離した後乾燥した
。 以上の仮焼、粉砕、乾燥を数回くりかえした後この
粉末にポリビニルアルコール6wt%水溶液を粉体量の
6wt%加え、32メツシユふるいを通して造粒し、成
形圧力1000kg/cm2で直径13mm高さ約5酬
の円柱状に成形した。成形物は空気中で700℃まで昇
温し1時間保持しポリビルアルコール分をバーンアウト
した。これを上述の仮焼粉を体積の1/3程度敷きつめ
た上に200メツシユZrO2粉を約1 mm敷いたマ
・グネシャ磁器容器に移し、同質のフタをし、管状電気
炉の炉心管内に挿入し、炉心管内をロータリーポンプで
脱気したのちN2−H2混合ガスで置換し、酸素分圧(
PO2)が1. Ox 100−8atになるようN2
とH2ガスの混合比を調節しながら混合ガスを流し所定
温度まで400°C/hrで昇温し2時間保持後400
℃/hrで降温した。炉心管内のPo2は挿入した安定
化ジルコニア酸素センサーにより測定した。第2図に焼
成時のマグネシャ磁器容器の構造を、第3図に炉心管内
部をそれぞれ断面図で示す。BaCO3, Nb2O5, TiO2, Ni○, and WO2 were used. After correcting the purity of these, a predetermined amount was weighed, and mixed using an agate cobblestone and pure water as a solvent in a ball mill for 17 hours. This was filtered by suction to remove most of the water, then dried, and then thoroughly crushed using a Raikai machine. After adding 5 wt% of water to the powder amount, it was made into a powder with a diameter of 60 nm.
+ Molding pressure 500kg/CI into a cylindrical shape with a height of about 50mm
It was molded at l+2. This was placed in an alumina crucible, covered with a homogeneous lid, and calcined at 750°C to 880°C for many hours. Next, the calcined product was roughly crushed in an alumina mortar, and further crushed in a ball mill using agate cobblestones and pure water as a solvent for 17 hours, filtered under suction to remove most of the moisture, and then dried. After repeating the above calcining, crushing, and drying several times, 6 wt % of a 6 wt % aqueous solution of polyvinyl alcohol was added to the powder, and the powder was granulated through a 32-mesh sieve to a diameter of 13 mm in height at a compacting pressure of 1000 kg/cm2. It was molded into a cylindrical shape with 5 positions. The molded product was heated to 700° C. in air and held for 1 hour to burn out the polyvinyl alcohol content. This was transferred to a Ma-Gnesha porcelain container in which about 1/3 of the volume of the calcined powder was spread, and 200 mesh ZrO2 powder was spread to a thickness of about 1 mm, covered with a homogeneous lid, and inserted into the core tube of a tubular electric furnace. After degassing the inside of the reactor core tube with a rotary pump, the atmosphere was replaced with N2-H2 mixed gas, and the oxygen partial pressure (
PO2) is 1. N2 to make Ox 100-8at
The mixed gas was flowed while adjusting the mixing ratio of H2 gas and the temperature was raised to the specified temperature at 400°C/hr, and after holding for 2 hours,
The temperature was lowered at a rate of °C/hr. Po2 in the reactor core tube was measured by an inserted stabilized zirconia oxygen sensor. FIG. 2 shows the structure of the Magnesia porcelain container during firing, and FIG. 3 shows a cross-sectional view of the inside of the furnace tube.
第2図において1はマグネシア容器であり、その上部は
マグネシア容器蓋2で封じた。マグネシア容器1の下部
には仮焼粉3を配置し、その上にジルコニア紛4を配置
した。さらにその上に試料5を配置した。In FIG. 2, 1 is a magnesia container, the upper part of which is sealed with a magnesia container lid 2. Calcined powder 3 was placed at the bottom of magnesia container 1, and zirconia powder 4 was placed on top of it. Further, sample 5 was placed on top of it.
第2図のように準備されたマグネシア容器1を第3図の
ように炉心管6内に配置した。7は安定化ジルコニア酸
素センサーである。The magnesia container 1 prepared as shown in FIG. 2 was placed in the furnace core tube 6 as shown in FIG. 7 is a stabilized zirconia oxygen sensor.
焼成物は厚さ1 mmの円板状に切断し、両面にCr−
Auを蒸着し、誘電率、tanδを1kHzIV/mm
の電界下で測定した。また抵抗率は1 k V / m
mの電圧を印加後1分値から求めた。The fired product was cut into a disk shape with a thickness of 1 mm, and both sides were coated with Cr-
Au was deposited, and the dielectric constant and tan δ were set to 1kHzIV/mm.
Measured under an electric field of Also, the resistivity is 1 kV/m
The voltage of m was determined from the value 1 minute after application.
なお焼成温度は焼成物の密度がもっとも大きくなる温度
とした。The firing temperature was set to the temperature at which the density of the fired product was the highest.
表1に本発明の組成範囲および周辺組成の成分[a、b
、x、y、zは(Pb+ Bab)(Mg1z3Nb2
ts )xTiy(Ni1z2w、、2)z O2+a
+b と表したときの値1.低酸素分圧雰囲気で焼成
したときの焼成温度、誘電率、誘電率の温度変化率(2
0°Cに対する)、tanδ、抵抗率、密度を示した。Table 1 shows the composition range of the present invention and the peripheral composition components [a, b
, x, y, z are (Pb+Bab)(Mg1z3Nb2
ts ) x Tiy (Ni1z2w,,2)z O2+a
The value 1 when expressed as +b. Firing temperature, dielectric constant, temperature change rate of dielectric constant (2
), tan δ, resistivity, and density are shown.
第1図は表1に示した各試料を(P b n Ba b
)Ti○2+3+l) 、 (Pb aBa b)(
Mg1z3Nb2tz )Q2+、+b、(Pb a
Ba b)(Nix/2W12 )02+2+bを端成
分とする三角組成図中に示したもので、斜線の範囲が発
明の範囲である。Figure 1 shows each sample shown in Table 1 (P b n B a b
)Ti○2+3+l), (Pb aBa b)(
Mg1z3Nb2tz ) Q2+, +b, (Pb a
B a b ) (Nix/2W12 )02+2+b is shown in a triangular composition diagram having end members, and the shaded range is the scope of the invention.
発明範囲外の組成物では、a+bが1.000より小さ
いと低酸素分圧雰囲気で焼成したときチ密な焼結物が得
られない、もしくは抵抗率が低(なる難点を有しており
、1.200より大きくなると誘電率および抵抗率が低
下する難点を有する。またbが0.250より大きいと
誘電率が低下する。x、y、zが限定の範囲外の組成物
はキュリ一点が室温から大きくはずれ誘電率が低くなる
、もしくは誘電率の温度変化率が太きなる難点を有して
いる。発明の範囲内の組成物では前記の問題がいずれも
克服されている。Compositions outside the scope of the invention have the disadvantage that if a + b is less than 1.000, a dense sintered product cannot be obtained when fired in a low oxygen partial pressure atmosphere, or the resistivity is low. If b is larger than 1.200, the dielectric constant and resistivity will decrease.If b is larger than 0.250, the dielectric constant will decrease.For compositions in which x, y, and z are outside the specified ranges, a single point of Curie However, the compositions within the scope of the present invention overcome all of the above-mentioned problems.
なお焼成雰囲気として選択した低酸素分圧雰囲気PO2
; 1.0xlO−8atn+ は焼成温度におケル
銅の平衡酸素分圧より低く金属はほとんど酸化しないと
考えられる。Note that the low oxygen partial pressure atmosphere PO2 selected as the firing atmosphere
It is considered that 1.0xlO-8atn+ is lower than the equilibrium oxygen partial pressure of Kel copper at the firing temperature, and the metal is hardly oxidized.
発明の効果
本発明によれば、低酸素分圧雰囲気1100℃以下の焼
成で積層コンデンサ素子として高信頼性を得るためのチ
密で抵抗率の高い焼結体が得られ、内部電極としてCu
などの卑金属材料を用いることか可能になる優れた誘電
体磁器組成物でを実現できる。Effects of the Invention According to the present invention, a dense and highly resistive sintered body for obtaining high reliability as a multilayer capacitor element can be obtained by firing at 1100°C or lower in a low oxygen partial pressure atmosphere, and Cu is used as the internal electrode.
Excellent dielectric ceramic compositions can be realized by using base metal materials such as.
第1図は本発明に係る磁器組成物の成分組成を示す三角
組成図、第2図は焼成時に磁器を入れるマグネシャ容器
の断面図、第3図は焼成時の炉心管を示す断面図である
。
1;マグネシャ容器、2;マグネシャ容器蓋、3:仮焼
粉、4;ジルコニア粉、5;試料、6;炉心管。
7;安定化ジルコニア酸素センサー。
代理人の氏名 弁理士 中尾敏男 はが1名第1図
(Pba[1abXNi+/2W+/2)02+a+b
z (PbaBab
)Ti02+a+b第3図Fig. 1 is a triangular composition diagram showing the composition of the porcelain composition according to the present invention, Fig. 2 is a cross-sectional view of a magnesia container in which the porcelain is placed during firing, and Fig. 3 is a cross-sectional view showing the furnace tube during firing. . 1: Magnesia container, 2: Magnesia container lid, 3: Calcined powder, 4: Zirconia powder, 5: Sample, 6: Furnace tube. 7; Stabilized zirconia oxygen sensor. Name of agent Patent attorney Toshio Nakao 1 person Figure 1 (Pba[1abXNi+/2W+/2)02+a+b
z (PbaBab
)Ti02+a+bFigure 3
Claims (1)
/_3)_xTi_y(Ni_1_/_2W_1_/_
2)_z}O_2_+_a_+_bで表される組成式(
ただし、x+y+z=1)において 0.001≦b≦0.250 1.000≦a+b≦1.200 の範囲にあり、この範囲内の各a、bの値に対し(Pb
_aBa_b)(Mg_1_/_3Nb_2_/_3)
O_2_+_a_+_b、 Pb_aBa_b)TiO_2_+_a_+_b、 (Pb_aBa_b)(Ni_1_/_2W_1_/_
2)O_2_+_a_+_bを頂点とする三角座標にお
いて下記組成点、A、B、C、D、E、を頂点とする五
角形の領域内の組成物からなることを特徴とする誘電体
磁器組成物。 A;x=0.950 y=0.049 z=0.001 B;x=0.750 y=0.249 z=0.001 C;x=0.010 y=0.800 z=0.190 D;x=0.010 y=0.450 z=0.540 E;x=0.900 y=0.050 z=0.050[Claims] (Pb_3Ba_b) {(Mg_1_/_3Nb_2_
/_3)_xTi_y(Ni_1_/_2W_1_/_
2) Compositional formula represented by _z}O_2_+_a_+_b (
However, at
_aBa_b) (Mg_1_/_3Nb_2_/_3)
O_2_+_a_+_b, Pb_aBa_b) TiO_2_+_a_+_b, (Pb_aBa_b) (Ni_1_/_2W_1_/_
2) A dielectric ceramic composition comprising a composition within a pentagonal region whose vertices are the following composition points A, B, C, D, and E in triangular coordinates whose vertices are O_2_+_a_+_b. A; x=0.950 y=0.049 z=0.001 B; x=0.750 y=0.249 z=0.001 C; x=0.010 y=0.800 z=0. 190 D; x=0.010 y=0.450 z=0.540 E; x=0.900 y=0.050 z=0.050
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP60247433A JPS62123061A (en) | 1985-11-05 | 1985-11-05 | Dielectric ceramic composition |
US06/917,673 US4751209A (en) | 1985-10-11 | 1986-10-10 | Dielectric ceramic compositions |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP60247433A JPS62123061A (en) | 1985-11-05 | 1985-11-05 | Dielectric ceramic composition |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS62123061A true JPS62123061A (en) | 1987-06-04 |
JPH0324427B2 JPH0324427B2 (en) | 1991-04-03 |
Family
ID=17163366
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP60247433A Granted JPS62123061A (en) | 1985-10-11 | 1985-11-05 | Dielectric ceramic composition |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS62123061A (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01100051A (en) * | 1987-10-12 | 1989-04-18 | Mitsubishi Mining & Cement Co Ltd | Dielectric porcelain composition |
-
1985
- 1985-11-05 JP JP60247433A patent/JPS62123061A/en active Granted
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01100051A (en) * | 1987-10-12 | 1989-04-18 | Mitsubishi Mining & Cement Co Ltd | Dielectric porcelain composition |
Also Published As
Publication number | Publication date |
---|---|
JPH0324427B2 (en) | 1991-04-03 |
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