U.S. patent application number 11/353120 was filed with the patent office on 2006-10-05 for method for manufacturing dielectric ceramic powder, and multilayer ceramic capacitor obtained by using the ceramic powder.
Invention is credited to Sang Kyun Lee, Sang Pyo Lee, Seon Cheol Park, Sung Soo Ryu, Dong Sook Sinn, Dang Hyok Yoon.
Application Number | 20060221550 11/353120 |
Document ID | / |
Family ID | 36659852 |
Filed Date | 2006-10-05 |
United States Patent
Application |
20060221550 |
Kind Code |
A1 |
Ryu; Sung Soo ; et
al. |
October 5, 2006 |
Method for manufacturing dielectric ceramic powder, and multilayer
ceramic capacitor obtained by using the ceramic powder
Abstract
The invention relates to a method for manufacturing dielectric
ceramic powder and a multilayer ceramic capacitor using the ceramic
powder. According to the invention, BaCO.sub.3 powder is dispersed
into a solution of solvent and dispersant to prepare BaCO.sub.3
slurry and then the resultant BaCO.sub.3 slurry is wet-milled.
Also, TiO.sub.2 powder slurry is mixed into the wet-milled
BaCO.sub.3 slurry to form mixed slurry and then the mixed slurry is
dried into mixed powder. Finally, the dried mixed powder is
calcined to produce BaTiO.sub.3 powder.
Inventors: |
Ryu; Sung Soo; (Seoul,
KR) ; Park; Seon Cheol; (Suwon, KR) ; Lee;
Sang Pyo; (Kimhae, KR) ; Sinn; Dong Sook;
(Seoul, KR) ; Lee; Sang Kyun; (Suwon, KR) ;
Yoon; Dang Hyok; (Suwon, KR) |
Correspondence
Address: |
LOWE HAUPTMAN BERNER, LLP
1700 DIAGONAL ROAD
SUITE 300
ALEXANDRIA
VA
22314
US
|
Family ID: |
36659852 |
Appl. No.: |
11/353120 |
Filed: |
February 14, 2006 |
Current U.S.
Class: |
361/321.5 |
Current CPC
Class: |
C04B 2235/528 20130101;
C04B 2235/5436 20130101; C01P 2006/12 20130101; C01G 23/006
20130101; C04B 2235/3208 20130101; B82Y 30/00 20130101; C04B
2235/765 20130101; C04B 2235/3263 20130101; C04B 2235/5409
20130101; C04B 35/62625 20130101; C01P 2004/62 20130101; C04B
2235/3239 20130101; C04B 35/6261 20130101; H01G 4/1227 20130101;
C04B 2235/3215 20130101; C04B 35/4682 20130101; C01P 2004/04
20130101; C01P 2004/64 20130101; C04B 2235/5463 20130101; C04B
35/62675 20130101; C04B 2235/3225 20130101; C04B 2235/761
20130101 |
Class at
Publication: |
361/321.5 |
International
Class: |
H01G 4/06 20060101
H01G004/06 |
Foreign Application Data
Date |
Code |
Application Number |
Mar 29, 2005 |
KR |
10-2005-25891 |
Claims
1. A method for manufacturing dielectric ceramic powder comprising
steps of: dispersing BaCO.sub.3 powder into a solution of solvent
and dispersant to prepare a slurry and then wet-milling the slurry;
mixing TiO.sub.2 powder slurry into the wet-milled BaCO.sub.3
slurry to form mixed slurry and then drying the mixed slurry into
mixed powder; and calcining the dried mixed powder to produce
BaTiO.sub.3 powder.
2. The method according to claim 1, wherein the solvent comprises
distilled water or alcohol.
3. The method according to claim 1, wherein the dispersant is
polyacrylic, and added to 1.about.5 weight parts with respect to
the BaCO.sub.3 powder.
4. The method according to claim 1, wherein the BaCO.sub.3 powder
has a specific surface area ranging from 5 to 30 m.sup.2/g by BET
measurement.
5. The method according to claim 1, wherein BaCO.sub.3 powder is
dispersed into the solution to such an extent that the BaCO.sub.3
slurry contains 10 to 60 wt % BaCO.sub.3.
6. The method according to claim 1, wherein the BaCO.sub.3 slurry
is wet-milled to such an extent that BET specific surface area of
BaCO.sub.3 powder is at least 30 m.sup.2/g.
7. The method according to claim 1, wherein in the wet-milling
step, ammonia is added to reduce viscosity of the slurry.
8. The method according to claim 7, wherein the ammonia is added to
at least 0.1 weight parts with respect to the solvent.
9. The method according to claim 1, wherein the TiO.sub.2 powder
has a specific surface area of at least 20 m.sup.2/g.
10. The method according to claim 1, wherein the calcination
temperature ranges from 900 to 1100.degree. C.
11. The method according to claim 1, further comprising pulverizing
the produced BaTiO.sub.3 powder.
12. The method according to claim 11, wherein the pulverized
BaTiO.sub.3 powder has uniform particle size distribution, with
mean particle size of 150 nm to 250 nm, D10/D50 of at least 0.6 and
D90/D50 of up to 1.4 based on FE-SEM picture.
13. The method according to claim 11, wherein the pulverized
BaTiO.sub.3 powder has at least 5.0 m.sub.2/g of BET specific
surface area, and based on FE-SEM picture, a c/a ratio of C-axis to
a-axis of the powder crystal lattice is at least 1.009.
14. A method for manufacturing dielectric ceramic powder comprising
steps of: dispersing BaCO.sub.3 powder into a solution of solvent
and dispersant to prepare a slurry and then wet-milling the slurry;
mixing CaCO.sub.3 powder slurry and TiO.sub.2 powder slurry into
the wet-milled BaCO.sub.3 slurry to form mixed slurry, and then
drying the mixed slurry; and calcining the dried mixed powder to
produce BaCaTiO.sub.3 powder.
15. The method according to claim 14, wherein the solvent comprises
distilled water or alcohol.
16. The method according to claim 14, wherein the dispersant is
polyacrylic, and added to 1-5 weight parts with respect to the
BaCO.sub.3 powder.
17. The method according to claim 14, wherein the BaCO.sub.3 powder
has a specific surface area of 5 to 30 m.sup.2/g by BET
measurement.
18. The method according to claim 14, wherein BaCO.sub.3 powder is
dispersed into the solution so that the BaCO.sub.3 slurry contains
10 to 60 wt % BaCO.sub.3.
19. The method according to claim 14, wherein the BaCO.sub.3 slurry
is wet-milled to such an extent that the BaCO.sub.3 powder has a
specific surface area of at least 30 m.sup.2/g.
20. The method according to claim 14, wherein in the wet-milling
step, ammonia is added to reduce viscosity of the slurry.
21. The method according to claim 20, wherein the ammonia is added
to at least 0.1 weight parts with respect to the solvent.
22. The method according to claim 14, wherein the TiO.sub.2 powder
has a specific surface area of at least 20 m.sup.2/g.
23. The method according to claim 14, wherein the calcination
temperature ranges from 900 to 1100.degree. C.
24. The method according to claim 14, further comprising
pulverizing the produced BaCaTiO.sub.3 powder.
25. The method according to claim 24, wherein the pulverized
BaCaTiO.sub.3 powder has uniform particle size distribution, with
mean particle size of 150 nm to 250 nm, D10/D50 of at least 0.6 and
D90/D50 of up to 1.4 based on FE-SEM picture.
26. The method according to claim 24, wherein the pulverized
BaCaTiO.sub.3 powder has at least 5.0 m.sub.2/g of BET specific
surface area, and based on FE-SEM picture, a c/a ratio of C-axis to
a-axis of the powder crystal lattice is at least 1.009.
27. A multilayer ceramic capacitor comprising: a multilayer ceramic
structure having a plurality of dielectric layers and a plurality
of internal electrodes alternating with the dielectric layers; and
external electrodes provided at both ends of the multilayer
ceramic, electrically connected to at least one of the internal
electrodes, wherein the dielectric layers comprise the dielectric
ceramic powder manufactured according to claim 1.
28. The multilayer ceramic capacitor according to claim 27, wherein
the ceramic power has uniform particle size distribution, with mean
particle size of 150 nm to 250 nm, D10/D50 of at least 0.6 and
D90/D50 of up to 1.4 based on FE-SEM picture.
29. The multilayer capacitor according to claim 27, wherein the
ceramic powder has at least 5.0 m.sub.2/g of BET specific surface
area, and based on FE-SEM picture, a c/a ratio of c-axis to a-axis
of the powder crystal lattice is at least 1.009.
Description
CLAIM OF PRIORITY
[0001] This application claims the benefit of Korean Patent
Application No. 2005-25891 filed on Mar. 29, 2005, in the Korean
Intellectual Property Office, the disclosure of which is
incorporated herein by reference.
BACKGROUND OF THE INVENTION
[0002] 1. Field of the Invention
[0003] The present invention relates to a method for manufacturing
dielectric ceramic powder. More particularly, the present invention
relates to a method for manufacturing dielectric ceramic powder by
using wet-milled, BaCO.sub.3 as raw powder to prepare raw ceramic
powder via solid state reaction, thereby ensuring fine particle
size and uniform particle size distribution, and a multilayer
ceramic capacitor made from the ceramic powder.
[0004] 2. Description of the Related Art
[0005] The information society of the 21st century has seen an
increasing trend of digitalization, high-performance and
high-reliability and multimedia in products such as electronic
appliances, PC, HHP which chiefly utilize Multilayer Ceramic
Capacitor (MLCC), one of the necessary passive devices of the
electronics industry. Accordingly, MLCC parts have undergone
higher-capacity and minimization fast. But this requires sheet
lamination and fine BaTiO.sub.3 particles having uniform size
distribution as the dielectric power used. Also, tetragonality
indicated by a c/a ratio of c-axis to a-axis of BaTiO.sub.3 powder
crystal needs to be higher (more than 1.008).
[0006] BaTiO.sub.3 powder has been produced by hydrothermal
synthesis, alkoxide method, solid state reaction and the like.
[0007] In hydrothermal synthesis, jel-type titanium hydrate is
added to a great quantity of barium hydroxide to react at a high
temperature of about 150.degree. C. and under a high atmospheric
pressure of 10, thereby producing crystalline BaTiO.sub.3. This
method has the advantage of directly producing spherical crystal
BaTiO.sub.3 sized about 100 nm but has the disadvantage of
difficult design and maintenance of a reactor, and expensive
manufacturing cost. Furthermore, recently, BaTiO.sub.3 powder
produced by hydrothermal synthesis has revealed significant defects
such as oxygen vacancy and barium vacancy, which develop into pores
in the case of heat treatment, thus deteriorating properties of
BaTiO.sub.3 powder.
[0008] Meanwhile in synthesizing BaTiO.sub.3 via hydrolysis of
metal alkoxide, metal alkoaxide alcohol solution and Ba (OH)
aqueous solution are mixed in a tube-type static mixer to react at
a temperature of 80.degree. C. This method is advantageous due to
following reasons. Liquid phase employed herein as starting
material is more reactive than solid jel-type titanium hydrate used
in hydrothermal synthesis. This allows synthesizing at a relatively
low temperature, and easy adjustment of the synthesized powder
particle size to about 20 to 100 nm. However this method has
drawbacks in that a synthesis device is hard to configure, and
alkoxide reagent used as starting material is expensive.
Furthermore, material cost is expensive due to use of alcohol
solvent, and complicated process conditions such as synthesis
temperature hamper mass productions.
[0009] Therefore, to manufacture low-priced BaTiO.sub.3, solid
state reaction is most advantageous. In solid state reaction,
BaCO.sub.3 powder and TiO.sub.2 powder are used as starting powder.
The BaCO.sub.3 powder and TiO.sub.2 powder are mixed, and then
undergo solid phase reaction in a calcination process to be
synthesized into final BaTiO.sub.3 powder. To achieve lamination of
dielectric layers, dielectric material powder should have small
particle size and uniform particle distribution. But BaTiO.sub.3
manufactured by solid state reaction reportedly does not exhibit
uniform particle size distribution compared to BTO manufactured via
other methods described above. In the end, in sold state reaction,
one of essential factors for obtaining final uniform BaTiO.sub.3
powder concerns uniform dispersion of BaCO.sub.3 powder and
TiO.sub.2 powder in the early stage. Such technologies have been
consistently developed.
[0010] For example, conventional technologies are disclosed in
Korean Patent Application Publication Nos. 2002-0053749 and
2004-0038747. The Patent Application No. 2002-0053749 discloses
barium titanate powder obtained by mixing barium compound and
titanium dioxide having rutile ratio of up to 30% and BET specific
surface area of at least 5 m.sup.2/g and calcining the same.
Meanwhile, the Patent Application No. 2004-38747 teaches a
technology of absorbing organic polymer compound into barium
carbonate powder. According to inventions disclosed in the
aforesaid patent application publications, advantageously, barium
compound and titanium dioxide are mixed uniformly to enhance the
degree of mixing. However despite dispersion of each element, the
acicular shape of barium compounds remains unchanged, leading to
inevitable contact among barium compounds due to their
morphological properties. Consequently, there is a limit in
obtaining optimal degree of mixing with titanium dioxide.
[0011] Another conventional technology is disclosed in Korean
Patent Application Publication No. 2004-0020252. Herein, BaCO.sub.3
powder is dry-milled spherically, mixed with TiO.sub.2 powder, and
then calcined. However according to the aforesaid technology,
disadvantageously, such dry-milling does not reduce the number of
BaCO.sub.3 particles, and high stress placed on BaCO.sub.3 does not
disperse BaCO.sub.3 particles properly, thus leading to
agglomeration. Large specific surface area of powder, or small
particle size results in uniform dispersion, but BaCO.sub.3
according to the aforesaid technology does not diminish particle
numbers, rendering uniform mixing with TiO.sub.2 difficult. Thus,
BaTiO.sub.3 powder finally obtained agglomerates heavily among
primary particles and forms secondary particles relatively bigger
than primary particles, also causing uneven particle distribution
of powder. BaTiO.sub.3 powder with such properties may be hardly
dispersible when applied to the MLCC, and unsuitable for the
dielectric ceramic use for up to 1 .mu.m lamination to ensure a
high-capacity capacitor.
SUMMARY OF THE INVENTION
[0012] The present invention has been made to solve the foregoing
problems of the prior art and it is therefore an object of the
present invention to provide dielectric ceramic powder having fine
particles and uniform particle size distribution, and high
tetragonal crystalinity.
[0013] It is another object of the invention to provide a
multilayer ceramic capacitor obtained by using the dielectric
ceramic powder.
[0014] The invention will be explained hereunder.
[0015] As identified above, solid state reaction is the most
economical method for producing BaTiO.sub.3 powder having fine
particles and uniform particle size, and high tetragonality to
manufacture a high-capacity MLCC.
[0016] In solid state reaction, fine BaTiO.sub.3 powder may be
produced via BaCO.sub.3 powder and TiO.sub.2 powder having big
specific surface area. But the acicular shape of BaCO.sub.3 powder
obstructs uniform mixing with TiO.sub.2 powder even in the case of
mechanical mixing via beads mill equipment, and renders it
difficult to obtain uniform BaTiO.sub.3 powder after final
calcination. Further, despite uniform dispersion of fine BaCO.sub.3
and TiO.sub.2 powders, BaCO.sub.3 power particles grow easily in
the calcination process. Therefore the BaCO.sub.3 powder particles
grow even before reacting with TiO.sub.2 and reaching a temperature
at which BaTiO.sub.3 particles are formed, thus making uniform
reaction with TiO.sub.2 difficult.
[0017] This increases unevenness of particles in case where fine
BaTiO.sub.3 powder is produced via solid state reaction to laminate
dielectric layers.
[0018] Therefore, the inventors have conducted studies and
experiments to solve problems of the solid state reaction. As a
result, they confirmed that fine particles of BaCO.sub.3 powder
could be obtained effectively by wet-milling acicular-shaped
BaCO.sub.3 raw powder into a slurry and changing the particle shape
from acicular to spherical. Also, the inventors found that fine
BaTiO.sub.3 powder with high tetragonality and uniform particle
size distribution could be produced by mixing TiO.sub.2 powder
having a big specific surface area into such fine and spherical
BaCO.sub.3 slurry, drying and cacinating the mixed slurry.
[0019] According to an aspect of the invention for realizing the
object, there is provided a method for manufacturing dielectric
ceramic powder comprising steps of:
[0020] dispersing BaCO.sub.3 powder into a solution of solvent and
dispersant to prepare a slurry and then wet-milling the slurry;
[0021] mixing TiO.sub.2 powder slurry into the wet-milled
BaCO.sub.3 slurry to form mixed slurry and then drying the mixed
slurry into mixed powder; and
[0022] calcining the dried mixed powder to produce BaTiO.sub.3
powder.
[0023] According to another aspect of the invention for realizing
the object, there is provided a method for manufacturing dielectric
ceramic powder comprising steps of:
[0024] dispersing BaCO.sub.3 powder into a solution of solvent and
dispersant to prepare a slurry and then wet-milling the slurry;
[0025] mixing CaCO.sub.3 powder slurry and TiO.sub.2 powder slurry
into the wet-milled BaCO.sub.3 slurry to form mixed slurry, and
then drying the mixed slurry; and
[0026] calcining the dried mixed powder to produce BaCaTiO.sub.3
powder.
[0027] According to further another aspect of the invention for
realizing the object, there is provided a multilayer ceramic
capacitor comprising:
[0028] a multilayer ceramic structure having a plurality of
dielectric layers and a plurality of internal electrodes
alternating with the dielectric layers; and
[0029] external electrodes provided at both ends of the multilayer
ceramic, electrically connected to at least one of the internal
electrodes,
[0030] wherein the dielectric layers comprise the dielectric
ceramic powder manufactured according to the methods.
BRIEF DESCRIPTION OF THE DRAWINGS
[0031] The above and other objects, features and other advantages
of the present invention will be more clearly understood from the
following detailed description taken in conjunction with the
accompanying drawings, in which:
[0032] FIG. 1 illustrates a process for producing dielectric
ceramic powder of the invention;
[0033] FIG. 2a is a graph illustrating particle size change in
accordance with wet-milling duration of the invention;
[0034] FIG. 2b is a graph illustrating effects of ammonia addition
on viscosity of BaCO.sub.3 slurry in a wet-milling process of the
invention;
[0035] FIG. 3 is a sectional view illustrating a multilayer ceramic
capacitor manufactured via the dielectric ceramic powder of the
invention;
[0036] FIG. 4a is SEM picture of BaCO.sub.3 powder before wet
milling;
[0037] FIG. 4b is SEM picture of BaCO.sub.3 powder wet-milled
according to the invention;
[0038] FIG. 5a is FE-SEM picture illustrating mixed powder of
BaCO.sub.3 powder and TiO.sub.2 powder obtained without wet
milling;
[0039] FIG. 5b is FE-SEM picture illustrating mixed powder of
BaCO.sub.3 powder wet-milled according to the invention and
TiO.sub.2 powder;
[0040] FIG. 6a is FE-SEM picture of the mixed powder of FIG. 5a
which was heat-treated at a temperature of 900.degree. C.;
[0041] FIG. 6b is FE-SEM picture of the mixed powder of FIG. 5b
which was heat-treated at a temperature of 900.degree. C.;
[0042] FIG. 7a is FE-SEM picture illustrating morphology of
BaTiO.sub.3 powder manufactured according to a conventional solid
state reaction;
[0043] FIG. 7b is a graph illustrating particle size distribution
of BaTiO.sub.3 powder of FIG. 7a;
[0044] FIG. 8a is FE-SEM picture illustrating an example of
morphology of BaTiO.sub.3 powder produced according to the
invention;
[0045] FIG. 8b is a graph illustrating particle size distribution
of BaTiO.sub.3 powder of FIG. 8a;
[0046] FIG. 9a is FE-SEM picture illustrating another example of
morphology of BaTiO.sub.3 powder obtained according to the
invention;
[0047] FIG. 9b is a graph illustrating particle size distribution
of BaTiO.sub.3 powder of FIG. 9a.
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENT
[0048] Preferred embodiments of the present invention will now be
described in detail with reference to the accompanying
drawings.
[0049] FIG. 1 illustrates a process for manufacturing dielectric
ceramic powder of the invention. As shown in FIG. 1, according to
the invention, first, BaCO.sub.3 powder is dispersed into a
solution of solvent and dispersant to prepare BaCO.sub.3 slurry.
The dispersant, e.g. polyacrylic dispersant, is added to increase
dispersibility of powder. Preferably, the dispersant is added to
1-5 weight parts with respect to BaCO.sub.3 raw powder. The
BaCO.sub.3 raw powder is acicular, and preferably should have a
specific surface area of 5 to 30 m.sup.2/g by BET measurement.
[0050] Further, according to the invention, distilled water and
alcohol may be used as the solvent, but distilled water is
preferable.
[0051] More preferably, the BaCO.sub.3 powder is dispersed into the
solution to such an extent that that the BaCO.sub.3 slurry contains
10 to 60 wt % BaCO.sub.3. Less than 10 wt % BaCO.sub.3 out of the
BaCO.sub.3 slurry adversely affects productivity (mass
productivity). Also, BaCO.sub.3 in excess of 60 wt % out of the
BaCO.sub.3 slurry degrades dispersibility and impairs wet
milling.
[0052] Then, according to the invention, the BaCO.sub.3 slurry is
wet-milled. The wet-milling is carried out at a speed of 1800 rpm
via beads mill type equipment that uses zirconia beads with a
diameter of 0.3 mm. Preferably, the milling duration should be
limited to up to 20 hours. More preferably, the BaCO.sub.3 powder
is wet-milled so as to have a specific surface area of at least 30
m.sup.2/g by BET measurement.
[0053] With increase in milling time for BaCO.sub.3 slurry,
particle size of BaCO.sub.3 powder decreases, leading to continuous
increase in the specific surface area thereof. But as shown in FIG.
2(a), the specific surface area does not increase any more after 8
hours, increasing viscosity of slurry significantly. However,
increased viscosity renders continuous wet-milling process
difficult and thus it is necessary to reduce viscosity.
[0054] Therefore, according to the invention, to reduce viscosity
of slurry, as shown in FIG. 2(b), ammonia should be preferably
added in the wet-milling process. More preferably, the ammonia can
be added to at least 0.1 wt % with respect to the solvent.
[0055] Then, according to the invention, TiO.sub.2 powder slurry is
mixed into the wet-milled BaCO.sub.3 slurry to form mixed slurry.
TiO.sub.2 slurry can be easily manufactured by dispersing TiO.sub.2
powder into a solution of solvent and dispersant. The TiO.sub.2 raw
powder preferably have a specific surface area of at least 20
m.sup.2/g, and more preferably at least 45 m.sup.2/g.
[0056] At this time, to produce BaTiO.sub.3 powder in a following
process, TiO.sub.2 powder is mixed into a slurry to such an extent
that a Ba/Ti mole ratio becomes 1. In this mixing process, the
BaCO.sub.3 slurry and TiO.sub.2 slurry can be wet-mixed via
zirconia beads with a diameter of 0.3 mm.
[0057] Meanwhile, sheet lamination of a high-capacity MLCC
increases induced electric field, resultantly deteriorating IR and
TCC properties. Therefore, to solve this problem, if necessary,
TiO.sub.2 slurry and CaCO.sub.3 slurry as well may be mixed into
the wet-milled BaCO.sub.3 slurry. With such mixing of CaCO.sub.3
slurry, Ca-doped BaTiO.sub.3, or fine BaCaTiO.sub.3 powder can be
obtained in a following process.
[0058] Thereafter, the mixed slurry is dried to produce dried mixed
powder, preferably, at a temperature of up to 200.degree. C. The
invention is not limited to the aforesaid drying method but spray
drying method may be more preferable.
[0059] Also, if necessary, the dried powder may be coarsely crushed
via atomizer.
[0060] And the dried mixed powder is calcined to synthesize
dielectric ceramic powder such as BaTiO.sub.3 powder or
BaCaTiO.sub.3 powder. In a calcination process, BaCO.sub.3 powder
and TiO.sub.2 powder may undergo solid state reaction to form
BaTiO.sub.3 dielectric powder. Further, in case where CaCO.sub.3
powder is additionally mixed, Ca-doped BaCaTiO.sub.3 power can be
obtained. Preferably, the calciantion temperature ranges from 900
to 1100.degree. C.
[0061] Powders synthesized in this fashion have necking among
primary particles. To be used for the MLCC, typically, the mixed
powders could go through a process of separation from primary
particles undamaged. To this end, according to the invention, the
synthesized ceramic powder can be pulverized. The pulverizing
process can be carried out effectively through deagglomeration in
beads mill.
[0062] Typical solid state reaction is applied to the dielectric
ceramic powder manufactured according to the aforesaid process.
Still the dielectric ceramic powder may have uniform particle size
distribution, with mean particle size of 150 nm to 250 nm, D10/D50
of at least 0.6 and D90/D50 of up to 1.4. based on FE-SEM
picture
[0063] Also, the dielectric ceramic powder may have at least 5.0
m.sub.2/g of BET specific surface area, and based on FE-SEM
picture, a c/a ratio of c-axis to a-axis of the powder crystal
lattice is at least 1.009.
[0064] Meanwhile, organic binder, solvent and other additives may
be mixed with the dielectric ceramic powder obtained to prepare
ceramic slurry, and a dielectric layer for the MLCC, or green
sheets may be manufactured by using the ceramic slurry via a
general tape casting method. Y.sub.2O.sub.3, Mn.sub.3O.sub.4,
Cr.sub.2O.sub.3 and glass are used as additives.
[0065] FIG. 3 is a sectional view illustrating a multilayer ceramic
capacitor manufactured via the dielectric ceramic powder. As shown
in FIG. 3, the multilayer ceramic capacitor (MLCC) 10 includes a
multilayer ceramic structure having a plurality of dielectric
layers 1 and a plurality of internal electrodes 3 alternating with
the dielectric layers; and external electrodes 5 provided at both
ends of the multilayer ceramic structure.
[0066] To manufacture the capacitor 10, first, ceramic slurry
including the dielectric ceramic powder prepared as described above
is used to form the dielectric layers 1 through the typical tape
casting method. Then the internal electrodes 3 are formed on the
dielectric layers 1 via screen printing. Subsequently firing is
carried our for the multilayer ceramic structure including the
unfired dielectric layers 1, and then applying a conductive paste
on both ends of the multilayer ceramic structure and finally firing
it, thereby producing the multilayer ceramic capacitor 10 having
the external electrodes 5.
[0067] As described above, according to the invention, to uniformly
disperse and mix BaCO.sub.3 powder and TiO.sub.2 powder, before
mixing with TiO.sub.2 powder, only acicular-shaped BaCO.sub.3
powder is wet-milled to be made spherical. Spherical particle shape
or significant reduction in particle size allows uniform mixing
with TiO.sub.2. Also, dielectric ceramic powder having fine
particle size of 150 to 250 nm and high tetragonality can be
manufactured by reacting BaCO.sub.3 powder with TiO.sub.2 powder
before BaCO.sub.3 powder particles grow in a calcination
process.
[0068] Further, in case where the multilayer ceramic capacitor is
manufactured via the dielectric ceramic powder produced by the
aforesaid process, sheet lamination is ensured to effectively
realize higher-capacity of the MLCC while reducing the size
thereof.
[0069] The invention will be explained in detail with reference to
the unlimited examples which follow.
EXAMPLE 1
[0070] BaCO.sub.3 raw powder having a specific surface area of 20
m.sup.2/g was prepared. Some of BaCO.sub.3 raw powder was dispersed
into a mixed solution of distilled water and polyacrylic dispersant
to manufacture BaCO.sub.3 slurry. BaCO.sub.3 raw powder was
dispersed into the solution to such an extent that the BaCO.sub.3
slurry would contain 10 to 60 wt % BaCO.sub.3. The slurry was
wet-milled for 18 hours via beads mill type equipment that uses
zirconia beads with a diameter of 0.3 mm as milling media. During
wet-milling, considering a sudden increase in viscosity in
accordance with decrease in BaCO.sub.3 particle numbers, ammonia
was added after 8 hour milling to reduce viscosity. A specific
surface area of the wet-milled BaCO.sub.3 powder was 31 m.sup.2/g,
a significant increase from the initial one, and the particles had
almost a spherical shape.
[0071] Field Emission (FE-SEM) picture before and after wet-milling
BaCO.sub.3 is shown in FIG. 4(a-b). As shown in the aforesaid FIG.
4(a-b), wet-milling changed BaCO.sub.3 from acicular powder into
finer spherical powder.
[0072] Meanwhile, slurried TiO.sub.2 powder having a specific
surface area of 45 m.sup.2/g was mixed into the wet-milled
BaCO.sub.3 slurry, and then the mixed slurry was mixed via beads
mill. At this time, mixed powder was slurried so that BaTiO.sub.3
powder would have a Ba/Ti ratio of 1. Then for comparison,
BaCO.sub.3 raw powder, which was not wet-milled, was mixed with
TiO.sub.2 powder to produce mixed powder.
[0073] FIG. 5(a-b) shows FE-SEM picture of the final mixed powder.
FIG. 5(a) is FE-SEM picture illustrating BaCO.sub.3 powder mixed
with TiO.sub.2 powder without wet-milling, while FIG. 5(b) is
FE-SEM picture of wet-milled BaCO.sub.3 powder mixed with TiO.sub.2
power. As shown in FIG. 5 (a-b), when BaCO.sub.3 powder without
wet-milling was mixed with TiO.sub.2 powder, it leads to uneven
mixing but use of the wet-crushed BaCO.sub.3 powder led to uniform
mixing among each component.
[0074] Also, to confirm whether BaCO.sub.3 powder particles grow in
case of rising temperature during a calcination process, mixed
powders prepared as above were calcined and heat-treated at a
temperature ranging from 600.degree. C. to 1000.degree. C.
Consequently, as in FIG. 6(a), in case of using BaCO.sub.3 powder
without wet-milling, BaCO.sub.3 particles grew considerably at a
temperature of 900.degree. C., while as in FIG. 6(b), in case where
wet-milled BaCO.sub.3 powder was used, particle growth was not
observed, indicating that BaTiO.sub.3 powder can be
synthesized.
EXAMPLE 2
[0075] TABLE-US-00001 TABLE 1 Specific surface area Wet-milling of
(m.sup.2/g) Calcination No. BaCO.sub.3 BaCO.sub.3 TiO.sub.2
CaCO.sub.3 temp. (.degree. C.) 1 Not wet-milled 20 20 1020 2 Not
wet-milled 20 20 1040 3 Wet-milled 31 20 1020 4 Wet-milled 31 20
1040 5 Wet-milled 31 45 960 6 Wet-milled 31 45 990 7 Wet-milled 31
45 1020 8 Wet-milled 31 45 30 960 9 Wet-milled 31 45 30 990
[0076] BaCO.sub.3 raw powder having a specific surface area of 20
m.sup.2/g was prepared. Some of BaCO.sub.3 raw powder was dispersed
into a mixed solution of distilled water and polyarcrylic
dispersant to produce BaCO.sub.3 slurry. BaCO.sub.3 powder was
dispersed into the solution to such an extent that BaCO.sub.3
slurry would contain 10 to 60 wt % BaCO.sub.3. The resultant slurry
was wet milled for 18 hours via beads mill type equipment using
zirconia beads with a diameter of 0.3 mm as milling media.
Considering a sudden increase in viscosity in accordance with
decrease in BaCO.sub.3 particle numbers during a wet-milling
process, ammonia was added to reduce viscosity after 8-hour
milling. A specific surface area of the wet-milled BaCO.sub.3
powder is shown in Table 1 above.
[0077] Slurried TiO.sub.2 raw powder having different specific
surface area was mixed into the wet-milled BaCO.sub.3 slurry via
beads mill. The mixed powder was slurried so that BaTiO.sub.3
powder would have a Ba/Ti ratio of 1, and then the mixed powder was
obtained by spray drying.
[0078] Meanwhile, in manufacturing Ca-doped BaCaTiO.sub.3
dielectric ceramic powder, as shown in Table 1, slurried TiO.sub.2
powder and slurried CaCO.sub.3 powder having a specific surface
area of 30 m.sup.2/g were mixed into the wet-milled BaCO.sub.3. At
this time, to obtain (Ba.sub.0.98Ca.sub.0.02).sub.1.000TiO.sub.3
powder, each of TiO.sub.2 powder and CaCO.sub.3 powder were mixed
into a slurry form, and then dried by spraying dying to produce
mixed powder.
[0079] For comparison, as shown in Table 1, some of BaCO.sub.3 raw
powder having a specific surface area of 20 m.sup.2/g was wet-mixed
with TiO.sub.2 powder having a specific surface area of 20
m.sup.2/g without undergoing wet-milling. The powders were measured
and mixed so that resultant BaTiO.sub.3 powder would have a Ba/Ti
ratio of 1.
[0080] The resultant mixed powders were dried and calcined under
the conditions set forth in Table 1 to manufacture BaTiO.sub.3 or
BaCaTiO.sub.3 dielectric ceramic powder. Thereafter, the ceramic
powder was deagglomerated via beads mill to produce final
powder.
[0081] To examine properties of powders manufactured as above, BET
specific surface area was measured. Also, through XRD analysis, a
c/a ratio of c-axis to a-axis of the powder crystal lattice was
calculated to measure tetragonality, and the results are shown in
Table 2 below. Mean particle size (D.sub.mean) of powder was
measured via image analyzer based on FE-SEM picture. Further, to
investigate uniformity of particle size distribution, measurement
was conducted on 10% cumulative distribution D10, 50% cumulative
distribution D50, and 90% cumulative distribution D90, respectively
from small size distribution. The calculated results of D10/D50,
D90/D50 are shown in Table 2. TABLE-US-00002 TABLE 2 Particle size
Ceramic SSA* MPS* distribution Tetrago- No. powder (m.sup.2/g) (nm)
D10/D50 D90/D50 nality 1 BaTiO.sub.3 5.66 176 0.41 1.57 1.0070 2
BaTiO.sub.3 3.97 212 0.40 1.54 1.0097 3 BaTiO.sub.3 4.58 199 0.62
1.38 1.0097 4 BaTiO.sub.3 4.01 230 0.65 1.36 1.0103 5 BaTiO.sub.3
5.68 150 0.70 1.26 1.0093 6 BaTiO.sub.3 4.53 202 0.69 1.24 1.0105 7
BaTiO.sub.3 4.08 218 0.72 1.24 1.0105 8 BaCaTiO.sub.3 5.62 155 0.71
1.27 1.0091 9 BaCaTiO.sub.3 4.57 198 0.70 1.24 1.0103 *SSA:
Specific Surface Area *MPS: Mean Particle Size
[0082] As shown in Tables 1 and 2, for sample 1 in which BaCO.sub.3
was calcined at a temperature of 1020.degree. C. without
wet-milling, the particles were finely-sized with 176 nm but
tetragonality thereof was 1.007, which is lower than 1.008 or a
requirement for high-capacity dielectric powder. For sample 2 in
which BaCO.sub.3 was calcined at a temperature of 1040.degree. C.,
BaTiO.sub.3 having tetragonality of 1.0097 and size of about 212 nm
was synthesized.
[0083] In contrast, for sample 3, in which BaCO.sub.3 was
wet-milled and then mixed with 20 m.sup.2/g of TiO.sub.2,
BaCO.sub.3 particles were finely-sized with 199 nm and
tetragonality thereof was 1.0097, a high figure even at a
temperature of 1020.degree. C., which is lower than when BaCO.sub.3
was not wet-milled. Also, for sample 6 in which BaCO.sub.3 was
wet-milled and then mixed with TiO.sub.2 powder having a specific
area of 45 m.sup.2/g, BaTiO.sub.3 powder particles were sized 202
nm, with tetragonality of at least 1.010 at a temperature of 990C.
Further, for sample 5 in which BaCO.sub.3 was calcined at a
temperature of 960.degree. C., BaCO.sub.3 powder was obtained with
fine particle size of 150 nm and big specific surface area of 5.68
m.sup.2/g. Still, BaTiO.sub.3 powder obtained had high
tetragonality of 1.0093.
[0084] In addition, to compare particle uniformity based on
cumulative particle size distribution, the calculated values of
D10/D50, D90/D50 were considered. Herein, bigger D10/D50 value and
smaller D90/D50 value mean more uniform distribution. When the
calculated values are compared, wet-milled BaCO.sub.3 indicates
bigger D10/D50 and smaller D90/D50, and thus more uniform particle
size distribution than that without wet-milling. For mixed powders
(samples 5 to 7) in which wet-milled BaCO.sub.3 was mixed with
TiO.sub.2 having a specific surface area of 45 m.sup.2/g, the
particle size distributions were most uniform.
[0085] Further, Ca-added BaCaTiO.sub.3 powder (samples 8 to 9)
exhibited behavior similar to BaTiO.sub.3 powder. By calcining at a
temperature of 990.degree. C. and 960.degree. C., BaCaTiO.sub.3
powders having mean particle size of 198 nm and 155 nm,
respectively, could be produced with tetragonalitiy of at least
1.0091 overall.
[0086] FIGS. 7a, 8a and 9a are FE-SEM pictures of dielectric
ceramic powder corresponding to samples 2, 3 and 6. FIGS. 7b, 8b
and 9b are graphs illustrating particle size distribution measured
via image analyzer. As shown in the above FIGS. 7a, 7b, 8b and 9b,
compared to sample 2 which used BaCO.sub.3 without wet-milling,
sample 3 which used wet-milled BaCO.sub.3 powder indicated more
uniform particle size distribution. Further, the narrowest particle
size distribution was found in sample 6 which used wet-milled
BaCO.sub.3 powder and TiO.sub.2 powder having big specific surface
area.
[0087] As set forth above, according to the invention, BaTiO.sub.3
or BaCaTiO.sub.3 is manufactured via wet-milled BaCO.sub.3 powder
to produce uniform dielectric ceramic powder having fine particles
sized 150 to 250 nm and high tetragonality.
[0088] Also, the multilayer ceramic capacitor manufactured via
dielectric ceramic powder allows sheet lamination and enables
higher-capacity and minimization of the MLCC.
[0089] While the present invention has been shown and described in
connection with the preferred embodiments, it will be apparent to
those skilled in the art that modifications and variations can be
made without departing from the spirit and scope of the invention
as defined by the appended claims.
* * * * *