study on the formation process of al2o3-tio2 composite powders
TRANSCRIPT
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Powder Technology 15
Study on the formation process of Al2O3–TiO2 composite powders
Shiquan Liu *, Wenhong Tao, Jia Li, Zhongxi Yang, Futian Liu
School of Materials Science and Engineering, Jinan University, Jinan, Shandong 250022, China
Received 24 August 2004; received in revised form 23 March 2005; accepted 18 May 2005
Available online 14 July 2005
Abstract
Fine particles of anatase were suspended in solutions of ammonium alum with Al2O3/TiO2 molar ratios from 0.1:1 to 7:1. By spray drying
the suspensions and calcining the spray-dried powders, Al2O3–TiO2 composite particles were obtained. The results show that after the spray
drying, coatings of ammomium alum are formed on the surface of the anatase particles, leading to composite precursor powders (CCPs) with
larger particle sizes. Upon calcining the CCPs, ammomium alum pyrolyzes to amorphous Al2O3 and anatase transforms into rutile. Both are
mainly responsible for the observed particle size reductions as well as the densification of each composite particle. The in-situ formed a-
Al2O3 and rutile may have higher reactivities, forming aluminum titanate at 1150 -C, about 130 -C lower than the theoretical temperature for
the formation of Al2TiO5 by solid reaction. The reaction between a-Al2O3 and rutile starts from the interface between the anatase and the
alum coating and mainly takes place in the single particles formed by spray drying. The molar ratio of Al2O3 to TiO2 influences the final
crystalline phases in the composite powders, but not stoichiometrically.
D 2005 Elsevier B.V. All rights reserved.
Keywords: Al2O3–TiO2 composite particle; Aluminum titanate; Spray dyring; Calcination; Crystalline phase
1. Introduction Traditionally, Al O and TiO are ball-milled to form
Al2O3 ceramics have been widely used in many fields
because of their good mechanical properties, such as high
hardness and super abrasion resistance [1,2]. Recently,
researchers have tried to improve their performance through
additions of other oxides [3–6]. Xiao and his coworkers
found that protective coatings on metals, which were
prepared from Al2O3–TiO2 composite powders by flame-
spraying, have much better abrasion resistance than those
consisting of pure Al2O3 powders [6]. Wunderlich et al.
pointed out that nano-hybrid Al2O3–TiO2 might be applied
as catalysts [7]. In addition, ceramics made from Al2O3–
TiO2 composite powders show attractive perspectives.
Aluminum titanate ceramic is a good example. Owing to
its excellent thermal expansion behavior [8–10], it can be
used as thermal resistant materials, such as catalyst carriers
for purification of fume produced by cars, as containers and
tubes for storing or conveying high temperature steel liquid
and as protective tube for thermal couples, etc.
0032-5910/$ - see front matter D 2005 Elsevier B.V. All rights reserved.
doi:10.1016/j.powtec.2005.05.048
* Corresponding author. Tel.: +86 531 2201692; fax: +86 531 7974453.
E-mail address: [email protected] (S. Liu).
2 3 2
composite powder mixtures for the subsequent shaping and
sintering process [10]. Other authors have tried new
methods such as wet chemical synthesis and high temper-
ature oxidation [7,11,12]. We use spray drying, an industrial
technology, to form composite precursor powders (CPPs) of
ammonium alum and titania. After calcining the precursor
powders, Al2O3–TiO2 composite particles with different
crystalline phases are obtained. The most obvious character
of the spray drying is that the as-prepared powders are
uniformly spherical, which is beneficial to the following
conveying and shaping procedure in the manufacturing of
ceramic products. In addition, the spray drying introduces
less impurity and saves time and energy compared to the
traditional ball-milling. We also find that upon calcination
the in-situ formed components inside the CPPs show higher
chemical reactivities.
2. Experimental
Fine anatase powder produced by the sulfate process
(Yuxing Chemical Industrial Factory, Jinan) was suspended
5 (2005) 187 – 192
Table 1
Designed compositions of Al2O3–TiO2 composite powders
Sample no. AT1 AT2 AT3 AT4 AT5
Al2O3/TiO2 molar ratio 0.1:1 0.6:1 1:1 1.4:1 7:1
S. Liu et al. / Powder Technology 155 (2005) 187–192188
in the solutions of ammonium alum (Dagang Yizhong
Chemical Industrial Factory, Tianjing). The molar ratios of
Al2O3 to TiO2 (A/T ratio) were changed from 0.1:1 to 7:1
(see Table 1).
Spray drying was performed on a QP-3 spray-drier
(Research Institute of Chemical Industry, Beijing). The
conditions for the spray drying were as follows: pressure of
the atomizing air, 0.1–0.2 MPa; flow of feeding, 30 ml/min;
temperatures at the inlet and outlet of the spray-drier,
200T10 -C and 100T10 -C, respectively.Powders collected from the spray-drier were calcined in
an electrical furnace with a temperature precision of T5 -C.The temperatures were set at 700, 864, 1150 and 1368 -C,respectively, with a heating rate of 10 -C/min. The
calcined samples were cooled in air directly from high
temperatures.
X-ray diffractograms (XRD) were recorded on a D/max-
rA diffractometer (Rigaku, Japan) to identify the crystalline
phase in the calcined samples. A S-2500 Scanning Electron
Microscope (SEM) (Hitachi, Japan) equipped with an
Energy Dispersive Spectrum (EDS) analyzer (Oxford Co.,
Britain) was used to analyze the morphology and compo-
sition of the powders. The measurements of the powder
particle size and its distribution were performed on a FAM
Laser Particle Diameter Analyzer (Pike Instrument Co.,
Shanghai). Histograms of the particle size distribution
(PSD) based on the mass frequency were drawn according
to the original data. Modes, representing the values that
occur most frequently in the distributions, were labeled on
the histograms.
(a)
~200µm
Fig. 1. SEM graph (a) and EDS (b) of
3. Results and discussion
3.1. Formation of the composite precursor powders (CPPs)
upon spray drying
Most of the particles prepared by the spray drying are
dispersed and spherical (Fig. 1a).
A comparison among the mean particle sizes (d50) of the
original anatase and the spray-dried powder shows an
increase of d50 from 4.48 to 17.24 Am, indicating a
significant increment of the particle size. Taking AT3 as
an example, Figs. 2a and b depict the histograms of particle
size distribution of the original anatase powder and the
spray-dried powder. As compared with the columns in Fig.
2a, the heights of the first eight columns in Fig. 2b decrease
in contrast with increases of the height of the subsequent
columns, suggesting that after the spray drying, larger
particles are formed. It can also be seen that after the spray
drying, the mode shifts to a larger particle size value (Fig.
2b). Meanwhile, the particle size distribution becomes
broader, indicated by new columns in the size fractions
above 53.5 Am.
According to the mechanism of spray drying [6],
ammomium alum coating is supposed to be formed on the
surface of TiO2 particles. Moreover, EDS analysis (Fig. 1b)
reveals that these particles, bigger or smaller in size, all
contain elements of O, Al, S and Ti, indicating that spray
drying the suspension with anatase powder in the alum
solution successfully leads to the formation of composite
powder consisting of TiO2 and ammomium alum.
TGA analyses reveal that upon heating, the weight losses
of the CPPs depend on the A/T ratios (Fig. 3). The larger the
A/T ratio is, the more the weight loss is observed. Since the
weight loss is mainly due to the thermal decomposition of
alum in the CCP, this correlation between the weight losses
and the A/T ratios indicates that thicker alum coatings are
formed on the surface of anatase in the case of higher A/T
(b)
cps
15
10
5
0
1 2 3 4 5Energy (keV)
O
Al
S
Ti
the composite precursor powder.
21a
b
c
d
e
f
0
21
021
021
021
021
0
0.5-
1.9
1.9-
2.4
2.4-
3.0
3.0-
3.8
3.8-
4.8
4.8-
6.2
6.2-
7.9
7.9-
10.1
10.1
-13
13-1
6.7
16.7
-21.
621
.16-
28.1
28.1
-37.
637
.6-5
3.5
53.5
-87.
187
.1-1
859
Particle Size (µm)
Fre
quen
cy,
p
arti
cles
by
mas
s
mode
mode
mode
mode
mode
mode
Fig. 2. Histograms of the particle size distribution of the CCP and the
calcined samples of AT3.
Fig. 3. Weight losses versus A/T ratios.
S. Liu et al. / Powder Technology 155 (2005) 187–192 189
ratios. However, the correlation is not linear, because the
calculation of the weight loss of the CCP takes the mass of
inner anatase plus the alum coating as a whole, while the
former does not lose any weight except the adsorbed water
upon heating.
3.2. Reactions in the composite precursor powders (CPPs)
upon calcination
After being spray-dried, the CCP powders were first
calcined at 700 -C, 864 -C and 1150 -C for 2 h,
respectively. The results of the particle size analysis for
the calcined samples of AT3 are also depicted as histograms
in Fig. 2. Comparing Fig. 2c–e with Fig. 2b, we can see that
the modes of the calcined samples are shifting to smaller
size values, indicating that the powder particles are
becoming smaller upon increasing temperatures. Mean-
while, the PSDs are narrowing. The d50 values show
decreases from 17.24 for CCP to 15.12Y12.02Y7.03 Amafter calcinations. SEM observation reveals that most
particles in the sample calcined at 1150 -C for 2 h are still
spherical (Fig. 4a).
However, when the spry-dried powder was calcined at
1368 -C for 20 min, the histogram of PSD shows a
significant shift to the large size fractions, suggesting a
sharp increase of the particle size. The d50 value is increased
up to 26.07 Am, even larger than that for the spray-dried
powder. SEM observation reveals that particles in this case
are not spherical at all (Fig. 4b).
From the DTA curve of the spray-dried ammomium
alum powder (Fig. 5a), it can be seen that weight losses
mainly take place below 800 -C, no obvious weight
losses have been observed when the temperature is higher
than 1000 -C, suggesting that the pyrolysis of ammonium
alum is completed. That is to say, ammonium alum in
CCPs must have pyrolyzed to Al2O3. Similar results are
obtained for the CCPs of AT3 (Fig. 5b). Meanwhile, as it
will be illustrated later by the XRD results, some anatase
has transformed into rutile in the same temperature
region. since rutile is more densely compacted than
anatase, the phase transformation can result in a negative
volume change [13]. Therefore, it is supposed that the
decreases in the particle size under 900 -C are mainly
due to the pyrolysis of ammomium alum on the surface
of the anatase particles and the volume reduction caused
by the anatase-to-rutile transformation. At 1150 -C,densification which occurs inside each composite particle
should be mainly responsible for the particle size
reduction. At 1368 -C, possibly the inter-particle solid
Fig. 4. SEM graphs of the samples calcined at (a) 1150 -C and (b) 1368 -C.
Fig. 5. DTA-TG curves for (a) CCp of AT3, (b) spray-dried alum, (c)
annatase.
S. Liu et al. / Powder Technology 155 (2005) 187–192190
reactions and sintering effect finally lead to the non-
spherical morphology and the size increase of the
composite particles.
Fig. 6 shows the XRD patterns of the calcined AT3
powders. When the spray-dried powder is calcined at 700
-C, only the anatase phase is detected (Fig. 6a). Upon
raising the temperature to 864 -C, part of the anatase
transforms into rutile (Fig. 6b). This temperature is
significantly lower than that for the pure anatase-to-rutile
transformation [14,15]. This difference might be caused by
the composite effect of the two components in the CCP,
especially on the interface between the anatase and the alum
coating. It has been found that the incorporation of Al2O3
into anatase can accelerate the anatase-to-rutile transforma-
tion [16,17]. The reason is that Al3+ ions, with a valence
lower than Ti4+, can create oxygen vacancies due to the
necessity of charge balance, reducing the energy barrier for
the rearrangement of the Ti–O octahedra. Also this
composite effect may be responsible for the difference
between the thermal decomposition behaviors of a spray-
dried alum and the CCP. In our previous study [18], the
spray-dried ammomium alum powders were subsequently
pyrolyzed to crystalline Al2(SO4)3 and g- or u-Al2O3 in a
temperature region of ¨900 -C. However, for the CCP, as
indicated by the TGA result, the pyrolysis of ammonium
alum is completed under 864 -C. However, no similar
crystalline phases are detected, indicating that Al2O3 is in an
amorphous state.
With the temperature rising to 1150 -C, rutile is still the
main crystalline phase, but aluminum titanate (Al2O3ITiO2)
is detected along with a-Al2O3 (Fig. 6c) This temperature is
about 130 -C lower than the theoretical temperature for the
formation of Al2TiO5 through traditional solid reaction
between a-Al2O3 and rutile [10,19]. This might be due to
the higher reactivities of the rutile and a-Al2O3 formed in-
situ upon heating. Since the particles are still highly
dispersed (Fig. 4a), it is reasonable to believe that the
formation of Al2O3ITiO2 mainly takes place in every single
particle formed by the spray drying.
From Table 2, it can be seen that at a same calcining
temperature below 1150 -C, although the CCPs have
different A/T ratios, the crystalline phases in all calcined
Fig. 6. XRD patterns for the sample of AT3 calcined at : (a) 700 -C, 2 hr; (b) 864 -C, 2 hr; (c) 1150 -C, 2 hr; (d) 1368 -C, 20 min; (e) 1368 -C, 2 hr.
S. Liu et al. / Powder Technology 155 (2005) 187–192 191
samples are the same as those in AT3. However, when the
temperature is raised to 1368 -C, the reactions are
dominated by the formation of Al2O3ITiO2 as the main
crystalline phase at the loss of a-Al2O3 and rutile. The
final phases are dependent on the A/T ratios, but not
stoichiometrically. In the samples with A/T ratios smaller
than 1 (such as AT1 and AT2), a-Al2O3 totally disappears,
rutile, supposed as an unreacted component, still exists. It
is not difficult to understand that rutile co-exists with
Al2O3ITiO2 in these cases, because Al2O3 is relatively
inadequate for the formation of Al2O3ITiO2. But in AT3
with an A/T ratio of 1:1, rutile is also detected (Fig. 6d).
Even in the cases of AT4 and AT5, whose A/T ratios are
1.4 and 7, respectively, rutile is still found along with
unreacted a-Al2O3. Comparing the DTA curves in Fig. 6b
and c, we can see that each of them shows an
endothermal peak at exactly the same temperature,
1367.9 -C, indicative of the normal anatase-to-rutile
transformation. This proves that the inner part of the
anatase particles is still undergoing phase transformation,
although aluminum titanate (Al2O3ITiO2) has been iden-
tified to be formed at 1150 -C. It evidences that the
formation of Al2O3ITiO2 starts from the interface between
the anantase and the alum coatings inside the CCPs. Then
the completeness of the formation of Al2O3ITiO2 in each
Table 2
Crystalline phases in the calcined samples
Sample no. AT1 AT2 AT3 AT4 AT5
Calcining temperature/-C 700 Anatase Anatase Anatase Anatase Anatase
864 Anatase Anatase Anatase Anatase Anatase
Rutile Rutile Rutile Rutile Rutile
1150 Rutile Rutile Rutile Rutile Rutile
Al2O3ITiO2 Al2O3ITiO2 Al2O3ITiO2 Al2O3ITiO2 Al2O3ITiO2
a-Al2O3 a-Al2O3 a-Al2O3 a-Al2O3 a-Al2O3
1368 Al2O3ITiO2 Al2O3ITiO2, Al2O3ITiO2 Al2O3ITiO2 Al2O3ITiO2
Rutile Rutile Rutile Rutile Rutile
a-Al2O3 a-Al2O3
single particle relies on the solid diffusion and solid
reaction. Therefore, the thickness of the coating plays an
important role in the process of the formation of
Al2O3ITiO2. Increasing the A/T ratio results in a thicker
surface coating of alum on the surface of anatase. Then
the transformed rutile in the center part of a single CPP
particle is difficult to diffuse to the surface to react with
a-Al2O3. Consequently, rutile is still detected although it
is stoichiometrically inadequate for the formation of
Al2O3ITiO2. This result does not change when the soaking
time is prolonged from 20 min to 2 h at this temperature
(Fig. 6e).
4. Conclusions
1. The spray-dried composite precursor powder has a core–
shell structure with coatings of ammonium alum on the
surface of anatase particles. The thickness of the alum
coating increases with the increase of the Al2O3/TiO2
ratio.
2. Upon calcination of the spray-dried composite precursor
powder, pyrolysis of ammomium alum and the anatase to
rutile transformation as well as the densification of each
composite particle result in the particle size reductions.
S. Liu et al. / Powder Technology 155 (2005) 187–192192
3. During the calcination, ammonium alum pyrolyzes to
Al2O3 and anatase transforms into rutile. Al2O3ITiO2
forms at 1150 -C. The reaction between Al2O3 and rutile
mainly takes place in every single particle formed
through spray drying and starts from the interface.
4. The molar ratio of Al2O3 to TiO2 does not influence the
crystalline phases stoichiometrically in the final compo-
site Al2O3–TiO2 powders.
References
[1] S. Ashley, Mech. Eng. 118 (1996) 48.
[2] E. Medvedovski, J. Am. Ceram. Soc. Bull. 81 (2002) 27.
[3] M.F. Zawrah, J. Schneider, K.-H. Zum Gahr, Mater. Sci. Eng., A 332
(2002) 167.
[4] A. Mimaroglu, I. Taymaz, A. Ozel, S. Arslan, Surf. Coat. Technol.
169–170 (2003) 405.
[5] B. Smuk, M. Szutkowska, J. Walter, J. Mater. Process. Technol. 133
(2003) 195.
[6] H. Xiao, Q. Wang, J. Liu, New Tech. New Prog. 5 (1995) 30, (in
Chinese).
[7] W. Wunderlich, P. Padmaja, K.G.K. Warrier, J. Eur. Ceram. Soc. 24
(2004) 313.
[8] J. Kim, H.S. Kwak, Can. Metall. Q. 39 (2000) 387.
[9] M. Ishitsuka, T. Sato, T. Endo, M. Shimada, J. Am. Ceram. Soc. 70
(1987) 69.
[10] M. Takahashi, M. Fukuda, M. Fukuda, H. Fukuda, T. Yoko, J. Am.
Ceram. Soc. 85 (2002) 3025.
[11] D.M. Ibrahim, A.A. Mostafa, T. Khalil, Ceram. Int. 25 (1999) 697.
[12] L. Shi, Y. Zhu, A. Chen, C. Li, D. Cong, D. Fang, Chinese J. Mater.
Res. 14 (2000) 58, (supplement, in Chinese).
[13] A. Navrosky, O.J. Kleppa, J. Am. Ceram. Soc. 50 (1967) 626.
[14] H. Zhang, J.F. Banfield, Am. Mineral. 84 (1999) 528.
[15] P.I. Gouma, M.J. Mills, J. Am. Ceram. Soc. 84 (2001) 619–622.
[16] R.D. Shannon, J.A. Pask, J. Am. Ceram. Soc. 48 (1965) 391.
[17] S. Borkar1, S. Dharwadkar, J. Therm. Anal. Calorim. 78 (2004) 761.
[18] S. Liu, G. Song, Z. Yang, J. Wang, H. Dai, J. Chem. Ind. Eng. 53
(2002) 738, (in Chinese).
[19] M. Andrianainarivelo, R.J.P. Corrie, D. Leclercq, P.H. Mutin, D.
Vioux, Chem. Mater. 9 (1997) 1098.