growth of sno nanowires with uniform branched...
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Growth of SnO2 nanowires with uniform branched structures
J.X. Wang, D.F. Liu, X.Q. Yan, H.J. Yuan, L.J. Ci, Z.P. Zhou, Y. Gao, L. Song,L.F. Liu, W.Y. Zhou, G. Wang, S.S. Xie*
Institute of Physics, Center for Condensed Matter Physics, Chinese Academy of Sciences, P.O. Box 603-65#, Beijing 100080, China
Received 3 September 2003; received in revised form 5 December 2003; accepted 5 January 2004 by B. Jusserand
Abstract
SnO2 nanowires have been prepared using the active carbon reaction with the fine SnO2 powder at low temperature (700 8C).
These nanowires show rectangular cross-section, with their widths ranging from 10 to 50 nm. Branched nanowires with definite
included angle are also observed in these products. The morphology and microstructure of the single crystalline SnO2
nanowires and the branched nanowires are characterized by means of scanning electron microscopy (SEM), high-resolution
transmission electron microscopy (HRTEM), selective area electron diffraction (SAED) and Raman spectrum. In addition, the
possible growth mechanism of the SnO2 nanowires and branched nanowires is also discussed.
q 2004 Elsevier Ltd. All rights reserved.
PACS: 81.10; 81.05.Y
Keywords: A. Nanomaterials; A. Semiconducting materials; C. Crystal morphology
1. Introduction
Semiconductor metal oxide nanowires have attracted
significant attention of the researchers due to the funda-
mental importance and the wide range of their potential
applications in nanodevices [1–7]. As a wide band
semiconductor (Eg ¼ 3.6 eV at 300 K), SnO2 is a key
functional material that has been used extensively for gas
sensor, transparent conductor, and nanoelectronic device
[8–10]. Until now, considerable effort has been focused on
the synthesis and application of the SnO2 thin film or
nanoparticles [11–15]. Recently, SnO2 nanowires, nano-
belts and nanotubes are prepared by simple evaporation of
the source compound over 1000 8C [16–20]. SnO2 nano-
belts as gas sensor and field-effect transistor are also
reported [10,20]. In addition, the branched carbon nanotubes
(so call ‘Y’ shape or branched shape) materials have been
synthesized by different methods in many groups [21–23],
for example, Li et al. produced the branched carbon
nanotubes in template with branched nanochannels [23].
In this study, we prepared SnO2 nanowires using the active
carbon reaction with the fine SnO2 powder at low
temperature 700 8C. Moreover, branched SnO2 nanowires
and nanowires network structures, which have definite
included angle and high crystalline, were also observed. In
contrast with the synthesis methods previously reported
[16–19], both the straight nanowires and branched nano-
wires prepared in our method have the rectangular cross-
section. Furthermore, the growth mechanisms of these SnO2
nanostructures are also discussed.
2. Experiment
Our experiment was carried out in a high-temperature
tube furnace. Fig. 1 represents schematically the apparatus
we used. A horizontal quartz tube was mounted inside the
furnace. The mixture of active carbon powder 1.2 g and fine
SnO2 powder 5 g was placed on a quartz wafer and the
substrates for growth of nanowires were put on the place 3–
8 cm away from the quartz wafer. The substrates we used in
0038-1098/$ - see front matter q 2004 Elsevier Ltd. All rights reserved.
doi:10.1016/j.ssc.2004.01.003
Solid State Communications 130 (2004) 89–94
www.elsevier.com/locate/ssc
* Corresponding author. Tel.: þ86-10-82649081; fax: þ86-10-
82640215.
E-mail addresses: [email protected] (J.X. Wang),
[email protected] (S.S. Xie).
experiment were n-type silicon (2–3 V). A thin Au film was
deposited on the substrates using an ion sputter films
deposition system (Hitachi, E-1010). The thickness of Au
film was estimated to be approximately 5 nm. After the
wafer was inserted into the center of the quartz tube, the
quartz tube was first evacuated by a vacuum pump. Then
the furnace was rapidly heated up to 700 8C from the room
temperature under a N2 flow at a rate of about 100 sccm.
During the experiment, the pressure was kept at 200 Torr
and the heating last for 240 min. Subsequently, the furnace
was cooled to the room temperature naturally and the
products were collected on the substrates from different
regions I, II and III of the furnace (as shown in Fig. 1). All
these regions have the same temperature of 700 8C. It was
observed that thick white cotton-wool-like products are
deposited on the surface of the substrates. Then, these as-
prepared products were characterized by field emission
scanning electron microscopy (FESEM; Philips XL 30
FEG), transmission electron microscopy (HRTEM; JEOL
2010F at 200 kV), and energy-disperse X-ray spectrum.
Raman measurements were also carried out on a micro-
Raman spectrometer (JY T64000 France) at room tempera-
ture. The 514.5 nm emission from argon ion laser was used.
3. Result and discussion
Fig. 2(a) is a typical SEM image showing the general
view of the morphology of the as-prepared product in region
I (as shown in Fig. 1). It was found that large-scale wire-like
material is produced. High magnification SEM image (Fig.
2(b)) shows the wire-like materials have cross-rectangle
section. Unlike the SnO2 belts previously reported [4,20],
the width-to-thickness aspect ratio of these nanowires are
2:1–4:1, obviously smaller than that of nanobelts. Actually,
their width ranges from 20 to 60 nm and the length of these
nanowires varies from several tens to hundreds of
micrometers. All these nanowires are smooth and uniform
along the fiber axis.
A straight nanowire collected in region I with the
diameter almost 20 nm is displayed in TEM image (Fig.
3(a)). Inset shows a nanowire with a catalyst particle on its
tip. These catalyst particles are not easily found in the SEM
image, presumably because the nanowires are too long.
To provide the further insight of nanowires, HRTEM and
area diffraction (SAED) were used. Fig. 3(b) reveals that the
SnO2 nanowires are structurally uniform and single crystal-
line. The interplanar spacing is measured to be 0.34 nm,
which corresponds to the (110) plane of a rutile SnO2 lattice.
The inset SAED pattern of the nanowires in Fig. 3(b) was
recorded with the electron beam along [1̄13]. From SAED,
the growth direction of SnO2 nanowire is found to be [301],
different from previous reports [18].
Raman spectrum is exhibited (Fig. 4) to further
determine the characteristic of the nanowires. Rutile SnO2
belongs to the space group D4h and displays four Raman-
active modes in bulk SnO2. In Fig. 4, three fundamental
Raman scattering peaks at 472, 629 and 773 cm21can be
observed, respectively. The peak at 472 cm21 can be
assigned to the Eg, the peak at 629 cm21 can be indexed
to the A1g mode and the peak at the 773 cm21 can be
identified as the B2g mode. These peaks indicate the typical
feature of the rutile structure of the SnO2 nanowires. There
also exist two weak Raman peaks at 498 and 689 cm21.
These two peaks, which have not been detected in bulk
SnO2, were reported to be A2u mode and Eu(2) mode,
respectively [19]. The Raman activities of these two modes
Fig. 1. Schematic diagram of apparatus used in experiment.
Fig. 2. (a) SEM images of the SnO2 nanowires prepared using active carbon and SnO2 powder. (b) Enlarged SEM image which shows
rectangular cross-section.
J.X. Wang et al. / Solid State Communications 130 (2004) 89–9490
may be due to a size effect of the thin nanowires. In our case,
the peak at 540 cm21 has not been reported in the Raman
study of SnO2 nanowires. This peak is identified to be of S2
mode, which is believed to be the consequence of the
disorder activation of SnO2 nanowires.
Many models are proposed to describe the growth
mechanism of the one-dimensional materials, such as VLS
(vapor–liquid–solid) and VS (vapor–solid) mechanism
[24]. The inset image in Fig. 3(a) shows a particle on the tip
of the nanowire, which indicates the growth mechanism of
SnO2 nanowires in our experiment that can be considered to
be VLS. It is reported that the Sn droplets on the tips are
essential for the growth of the nanowires [16]. However, in
our experiment, EDX reveals that the top particles are
composed of Au, Sn and O, which indicates Au particles
also play an important role in the growth of SnO2 nanowires.
The following chemical reaction will take place during the
thermal evaporation process:
CðsÞ þ SnO2ðsÞ ¼¼ SnOðgÞ þ COðgÞ ð1Þ
COðgÞ þ SnO2ðsÞ ¼¼ SnOðgÞ þ CO2ðgÞ ð2Þ
2SnOðgÞ ¼¼ SnðlÞ þ SnO2ðsÞ ð3Þ
SnO2 powder is first reduced by active carbon powder at
700 8C, as the reaction (1) described. Then SnO2 powder
will continue to be reduced by the CO gas formed from
reaction (1). SnO vapor is the common resultant of these two
reactions. The SnO vapor can be transported to the
deposition zone by the carrying gas. As we all know SnO
is metastable, it will decompose into Sn and SnO2 above
600 8C, as shown in reaction (3). Considering the low
melting point of Tin (231.9 8C), Sn particles are still liquid
at reaction temperature. These Sn droplets fell on the
substrate and form Sn–Au alloyed droplets by reacting with
the Au particles. At the same time, these alloyed droplets
can provide the energetically favored sites for adsorption of
SnO vapor. Subsequently, the decomposition of SnO will
result in the precipitation of SnO2 and the SnO2 nanowires
are formed.
Except the single-crystalline nanowires, however, differ-
ent morphologies are found in the products collected from
different regions of the furnace. In region II (region II in Fig.
1), the products also display wire-like features similar to the
nanowires mentioned above, but among these nanowires,
many of them have the branched structures, which are
marked by arrow A–H in SEM image (Fig. 5(a)). Unlike the
Y-shape junction previously reported [21–23], these
branched nanowires are just formed by one stem nanowire
and one branch nanowire. Some of the nanowires were
connected by several junctions and resulted in a network of
the nanowires, (as the arrow A–H marked). Similar with the
Fig. 3. (a) A typical TEM image of SnO2 nanowires with diameter about 10 nm, inset is a nanowire with a catalyst particle on the tip. (b)
HRTEM image of the individual straight SnO2 nanowire, inset is the SAED pattern. The growth direction of the nanowire is [301].
Fig. 4. Raman spectrum of the SnO2 nanowires.
J.X. Wang et al. / Solid State Communications 130 (2004) 89–94 91
straight nanowires, both the stem and branch of the branched
nanowires have the rectangle cross-section, as shown in
enlarge SEM image (Fig. 5(b)). In addition, in the nearest
region from the reactant (region III in Fig. 1), the product
shows a sheet-like feature that is similar with the previously
reported [4], which we will described in another paper.
TEM images of branched nanostructures are shown in
Fig. 6. Fig. 6(a) is a typical TEM picture of the branched
nanowires. Both the stem and branch of the branched
nanowires are straight and uniform, and with the width of
about 20 nm. The induced angle between the arms is
measured to be 68 8C. In our TEM study, we have observed
more than 10 nanowires and found that almost all of the
branched nanowires have the constant included angles.
Moreover, some interesting structures are also found in the
as-prepared product. Fig. 6(b) shows a network of
nanowires in which the nanowires are parallel to each
other. Three angles among the three nanowires are also 688,
which are marked by the arrow a, b, and c in the image. A
structure with parallelogram-shape is displayed in Fig. 6(c).
Two parallelograms in different panels are formed by the
connection of the nanowires. The angle between two
nanowires (marked by E and F) is also found to have the
same value. These structures provide the strong evidence
that the branched SnO2 nanowires tend to form the junction
in a definite included angle.
Comparing with the straight nanowire, HRTEM image
of the branched nanowire in Fig. 7 shows that a thin
amorphous layer exists at the surface of the junction. On the
other hand, the clear lattice fringes indicate the single-
crystalline of the junction. The lattice fringe distances are
0.26 nm, which is coincidence with the d space (101) plane
of the rutile SnO2. The SAED pattern taken from the
junction of branched nanowires (inset in the Fig. 7) can be
indexed to be [010] zone axis of the rutile structured SnO2
crystal. Further analysis indicated that the growth direction
of the stem and branch are [1̄01] and [101] crystalline
orientations, respectively. This result can be confirmed by
the fact that the included angle is 688 between [1̄01] and
[101] crystalline orientation.
On the basis of the experimental data, a schematic
diagram of the crystal structures is used to describe the
structural relationship between the branch and stem
nanowire. As shown in Fig. 8, the rectangular parallelepiped
ABCO–DGFE represents unit cell for the rutile structured
SnO2 crystal and the spheres denote the Sn atoms (O atoms
are not drawn). The stem of branched nanowire is
represented by the hexahedron ABA1B1–LNPM and the
branch of branched nanowire is represented by the
hexahedron ABFE–JKIH; the growth orientations of these
hexahedrons are [1̄01] and [101], respectively. The plane
ABLN is indexed to be (101) plane while the OCGD is
indexed to be (1̄01) plane. These planes correspond to the
growing plane of the stem and branch nanowire, respect-
ively. In addition, because the nanowires shows rectangular
cross-section, the enclosed facet planes of the branched
nanowires can be determined in this diagram. The enclosed
facet planes of stem nanowire are ^ (010) and ^(101) while
those of branch nanowire are ^ (010) and ^ (ı̄01),
respectively.
Taking consideration of the growth mechanism of
branched nanowires, we suggest the growth of the stem of
branched nanowires may follow the same growth mechan-
ism as that of the straight nanowires with the rectangular
cross-section. When the stem SnO2 nanowires grows along
the (101) crystalline orientation, the outside faces of (101)
plane might consists of oxygen atoms with many dangling
bonds. As the grown nanowire is nearer to the reactants, the
dangling bonds of oxygen on the outside surface have more
chance to catch Sn atoms. Thus, some of the small Sn
droplets decomposed from SnO vapor can be attached on its
surface and formed the new growth sites. This point was
also supported by our SEM study. Some small droplets
attached in the surface of nanowires have been observed in
SEM observation. As we all know, because of the tetragonal
structure of the SnO2 crystal, (101) and (1̄01) plane are
kinetically identical in the growth of crystal, the same as
Fig. 5. (a) SEM image of branched nanowires, the junctions are
marked by arrow A–H. (b) High magnification SEM image of the
SnO2 nanowires also show the rectangle cross section.
J.X. Wang et al. / Solid State Communications 130 (2004) 89–9492
[101] and [1̄01] orientation. Moreover, because the (101)
plane and [101] orientation are, respectively, the close-
packed plane and close-packed orientation in rutile SnO2
crystal, these orientations are prior directions for growth of
crystal. Once the Sn droplets as the nucleation sites were
attached on the surface (101) plane of the stem nanowire, the
epitaxial growths of the branch nanowires will take place.
These branch nanowires grow along the definite directions
and then result in uniform branched nanowires. Here, the
growth process of these branch nanowires is similar to the
formation of the individual straight nanowire, but Sn
droplets replaced the Sn–Au alloy droplets as the catalyst
for the formation of the branch nanowire. If these growths
take place in several sites of the stem nanowire, the parallel
network is produced. Similarly, as the growths take place on
the top and end of the nanowires, the parallelograms
structure is formed.
In addition, the SnO2 fishbone nanostructures were
reported recently. In these structures the branches grow
perpendicularly from the main stem [25]; however, the
vertical structures were not observed in our specimen. The
k101l direction for growth of branched nanowires is
Fig. 6. TEM image of branched nanostructure (a) branched nanowire, (b) a parallel network of SnO2 nanowires. The angle marked by arrow a, b
and c are all 688 (c) a parallelogram structure formed by the connection of nanowires.
J.X. Wang et al. / Solid State Communications 130 (2004) 89–94 93
dominant under our experiment condition. This difference
may due to the using of Au catalyst particles and relatively
low growth temperature during the growth process.
Presumably different favored growth directions for SnO2
nanowire growth depend on different experiment con-
ditions. By controlling the experimental conditions in
order to favor different growth orientations, branched
nanowires with different included angles might be obtained.
These will be the subjects of further study in our laboratory.
4. Conclusion
In summary, we have demonstrated the synthesis of
single crystalline rutile SnO2 nanostructures in the forms of
nanowires and branched structures using the active carbon
and SnO2 powder at low temperature 700 8C. The
characteristics of these nanostructures were analyzed by
means of SEM, TEM, HRTEM, and Raman spectrum. The
branched nanowires, which were constructed by two
nanowires in the definite included angle, were observed in
the experiment. Both the individual straight nanowires and
the branched nanowires have the rectangle cross-section. In
addition, the growth mechanism of the SnO2 nanowires and
other nanostructures are also discussed in detail. Epitaxial
growth of branch nanowire from the kinetic equivalent
crystal planes and orientation may be the possible reasons
for the formation of the branched nanowires. These obtained
SnO2 nanostructures may have important application in
fabrication of the nano-devices.
Acknowledgements
The authors gratefully thank X.A. Yang and J.L. Jing for
the assistance in SEM and HRTEM work. This work is
supported in part by the national Natural Science Foun-
dation of China.
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Fig. 7. HRTEM image of the branched SnO2 nanowire, inset is the
SAED pattern taken along [010] axis. The growth directions of stem
and branch nanowire are [1̄01] and [101], respectively.
Fig. 8. A schematic diagram of the branched nanowire crystal
structure. Circles denote Sn atoms while O atoms are not drawn.
J.X. Wang et al. / Solid State Communications 130 (2004) 89–9494