Magnetic cobalt nanowire thin films

Article abstract of DOI:10.1021/jp045554t

Two-dimensional (2D) and three-dimensional (3D) magnetic cobalt nanowire thin films with tunable 3-10 nm wire diameters have been electrodeposited using mesoporous silica templates containing 2D hexagonal or 3D cubic pore channels. As compared to bulk cobalt films, the cobalt nanowire thin films exhibit enhanced coercivities and controllable magnetic anisotropy through tuning of the mesostructure and dimension of the nanowires. Such novel magnetic nanowire thin films may provide a new platform for high-density information storage applications.

Full text of DOI:10.1021/jp045554t

J. Phys. Chem. B 2005, 109, 1919-1922
1919
Magnetic Cobalt Nanowire Thin Films
Hongmei Luo, Donghai Wang, Jibao He, and Yunfeng Lu*
Department of Chemical and Biomolecular Engineering, Tulane UniVersity, New Orleans, Louisiana 70118
ReceiVed: September 30, 2004; In Final Form: NoVember 22, 2004
Two-dimensional (2D) and three-dimensional (3D) magnetic cobalt nanowire thin films with tunable 3-10
nm wire diameters have been electrodeposited using mesoporous silica templates containing 2D hexagonal
or 3D cubic pore channels. As compared to bulk cobalt films, the cobalt nanowire thin films exhibit enhanced
coercivities and controllable magnetic anisotropy through tuning of the mesostructure and dimension of the
nanowires. Such novel magnetic nanowire thin films may provide a new platform for high-density information
storage applications.
Introduction
3-10 nm) using mesoporous silica films as templates. Meso-
porous silica thin films can be readily prepared on conductive
The rapid development of information technology calls for
high-density information storage media. A possible strategy
toward this challenge is to reduce magnetic domain sizes by
using low-dimensional magnetic materials such as magnetic
nanoparticles, nanorods, or nanowires.1-3 It is expected that
patterned magnetic nanowire arrays may provide a recording
density on the order of 100 Gb/inch2.4 However, as the grain
size decreases, originally ferromagnetic particles may become
superparamagnetic and can no longer be used as the magnetic
storage media. For example, two-dimensional (2D) or three-
dimensional (3D) superlattices assembled from 2 to 11 nm cobalt
nanoparticles showed superparamagnetic behavior at room
temperature.5-8 Such a superparamagnetic behavior is due to
the overcoming of magnetic anisotropy by thermal energy that
randomizes the magnetization orientation. As compared to
magnetic nanoparticles, although nanowires have small wire
diameters, they may still show ferromagnetism at room tem-
perature because of the volume effect and enhanced magnetic
shape anisotropy.1-3,9 Fabrication of magnetic nanowire-based
devices therefore holds great promise for future high-density
information storage.
Various magnetic nanowires have been synthesized using
methods such as electron beam lithography, X-ray lithography,
scanning probe lithography, step growth methods, nano-imprint,
and templating approach.3,10 Among these methods, the template-
assisted electrodeposition is particularly attractive due to its
simplicity, low-cost, and high yield. It provides an efficient route
for fabricating isolated ferromagnetic nanowire columns with
small diameters that are determined by the pore diameter of
the templates.11,12 To date, arrays of ferromagnetic metals (e.g.,
Co, Ni, and Fe), alloys (e.g., NiFeCo and CoPt), and multilayer
(e.g., Cu/Co, Cu/Ni) nanowires have been prepared using porous
polycarbonate or anodized aluminum oxide (AAO) membranes
as templates.1-3,11-28 It has been demonstrated that a smaller
nanowire diameter often enhances the coercivity, a key factor
for data storage. However, these common templates often
contain pore diameters greater than 30 nm, limiting the synthesis
of nanowires with smaller diameters.
substrates through cooperative assembly of silicate and surfac-
tant using a simple sol-gel dip-coating or spin-coating process.29
The pore diameters are unimodally controllable from 2 to 20
nm, and these pore channels are organized into 2D hexagonal,
3D cubic, or other mesostructures.29,30 Furthermore, it may be
possible to align the pore channels parallel or perpendicular to
the substrate.31 These unique features allow precise controls over
nanowire diameters and their mesoscale arrangements.32-37
Although nanowires with diameters of 3-7 nm have been
synthesized using porous AAO, carbon nanotubes, or tobacco
mosaic virus as templates, there are no reports on their magnetic
properties.18,27,28,38,39
Experimental Section
Sample Preparation. The mesoporous silica templates were
prepared by spin-coating the silicate/surfactant sols on ITO-
glass substrates. The surfactants used included Pluronic P123
(EO20PO70EO20, EO ) -CH2CH2O-, PO ) -CH2(CH3)-
CHO-), CTAB (cetyltrimethylammonium bromide, CH3-
(CH2)15N+(CH3)3Br-), and Brij-58 (C16H33(OCH2CH2)20OH).
The sols were prepared by mixing 1 g of tetraethoxysilane
(TEOS, 98%), 0.2-0.3 g of surfactant, 0.4 g of 0.1 N HCl, and
4.2 g of ethanol at room temperature for 30 min. Spin-coated
thin films were calcined at 400 °C for 1 h in air to remove the
surfactant, resulting in mesoporous thin films with an average
thickness of 200 nm. Mesoporous silica thin films with 2D
hexagonal pore channels were prepared using CTAB and P123
as the pore-directing agents. Mesoporous silica thin films with
3D cubic pore channels were prepared using Brij-58 as the pore-
directing agent. Electrochemical deposition was performed in
a standard three-electrode glass cell consisting of a mesoporous
silica-coated ITO-glass cathode, a Pt gauze anode, and a Ag/
AgCl reference electrode. The electrolyte contained 20 v% of
methanol, Co salt (1.3 M CoSO4‚5H2O), and a buffering acid
(0.7 M H3BO3).11,13 Deposition was conducted at -1.2 V vs
Ag/AgCl at room temperature. The currents increased quickly
during the first 30 s and then became constant during deposition,
indicating the ions are steadily diffused through the porous
networks and deposited on the electrodes.
This research reports the electrochemical deposition of 2D
and 3D magnetic nanowires with smaller wire diameters (e.g.,
Sample Characterization. X-ray diffraction (XRD) patterns
were recorded on a Siemens D-500 diffractometer using Cu KR
* Corresponding author. Phone: (504) 865-5827. Fax: (504) 865-6744.
E-mail: ylu@tulane.edu.
10.1021/jp045554t CCC: $30.25 © 2005 American Chemical Society
Published on Web 01/13/2005

1920 J. Phys. Chem. B, Vol. 109, No. 5, 2005
Luo et al.
Figure 1. (a) Low-angle XRD patterns of the 2D hexagonal Co
nanowire thin films directed from P123 and CTAB surfactant, and 3D
cubic Co directed from Brij-58 surfactant, respectively. (b) Wide-angle
XRD pattern of the Co nanowire thin film directed from P123 surfactant.
radiation. Transmission electron microscopy (TEM) images and
selective area electron diffraction (SAED) patterns were obtained
on a JEOL 2010 TEM microscope equipped with Oxford Link
ISIS 6498 spectrometer for energy-dispersive X-ray (EDX)
analysis and operated at 200 kV. The samples for TEM were
prepared by scraping off the thin films from ITO-glass and
directly placing them onto a carbon-coated copper grid.
Magnetic characterization was carried out using the MPMS
Quantum design superconducting quantum interference device
magnetometer SQUID. The measurements were conducted using
an applied field parallel or perpendicular to the film plane at
room temperature. The bulk Co thin films were deposited on
an Au sputtered Si wafer with a Cr adhesion layer.
Figure 2. TEM images of (a) 2D hexagonal Co nanowire/silica directed
from P123 surfactant and (b) 3D Co nanowire/silica directed from Brij-
58 surfactant. Inset: SAED pattern of the Co nanowires showing the
polycrystalline nature of the nanowires.
example, the use of mesoporous silica templates with 2D
hexagonal or 3D cubic pore channels results in the formation
of 2D nanowires or 3D nanowire networks, respectively.37
Figure 1a shows the low-angle XRD patterns of Co nanowire
thin films prepared using P123, CTAB, and Brij-58 directed
mesoporous silica templates. The P123 directed Co nanowire
thin film shows a typical 2D hexagonal structure with an intense
(100) diffraction at the d spacing of 7.4 nm and a (200)
diffraction at 3.7 nm. The CTAB directed Co nanowire thin
film shows a similar 2D hexagonal structure with a (100)
diffraction at the d spacing of 3.6 nm and a (200) diffraction at
1.8 nm. The absence of (110) diffraction for the 2D hexagonal
structure of mesoporous silica is due to preferred orientation of
the pore channels parallel to the film plane.29 However, such
hexagonal pore channels may form a swirling mesostructure
due to the low bending energy of the surfactant tubules and the
Results and Discussion
The growth of the nanowires is initiated from the bottom
conductive electrodes. Metal precursors, such as the cobalt ions,
are continuously diffused through the porous channels and
deposited on the electrodes. Such a bottom-up growing process
gradually fills the pore channels of the templates with magnetic
cobalt, resulting in the formation of continuously macroscopic
nanowire thin films.37 Through controlling the mesostructure
of the mesoporous templates, cobalt nanowire thin films with
the replicated mesostructure can be easily achieved. For

Magnetic Cobalt Nanowire Thin Films
J. Phys. Chem. B, Vol. 109, No. 5, 2005 1921
Figure 3. Room-temperature magnetic hysteresis loops of (a) Co film on Au-Si; (b) 2D Co nanowire thin film directed from P123 surfactant; (c)
2D Co nanowire thin film directed from CTAB surfactant; and (d) 3D Co nanowire thin film directed from Brij-58 surfactant.
inability of the liquid-vapor interface to impose long-range
order on the tubule assembly process, which allows the transport
of Co ions into the electrodes. The Brij-58-directed Co nanowire
film shows a 3D cubic mesostructure with a (200) and (211)
diffraction at the d spacing of 3.75 and 2.95 nm, respectively.
Figure 1b shows a representative wide-angle XRD pattern of
the P123 directed Co nanowire thin film. Except for the ITO
substrate peaks (marked as o), the cobalt (100), (002), and (101)
hcp diffraction peaks indicate a crystalline structure.
Figure 2 shows the TEM images of (a) the 2D hexagonal Co
nanowires/silica directed from P123 surfactant and (b) the 3D
Co nanowires/silica directed from Brij-58 surfactant. The inset
SAED pattern indicates the polycrystalline nature of Co
nanowires, which is consistent with the wide-angle XRD pattern.
Figure 2a clearly shows the formation of nanowires swirling
within the silica template. Figure 2b shows the formation of
ordered Co nanowire arrays along the [111] direction of the
cubic mesostructure. The average nanowire diameters are
roughly equal to the average pore diameters of the templates,
which are about 3, 5, and 8 nm, when CTAB, Brij-58, and P123
are respectively used as the pore structure directing agents.29-37
Figure 3 shows the room-temperature magnetization hyster-
esis loops of (a) a bulk Co thin film, and (b) a Co nanowire
film prepared using P123, (c) CTAB, and (d) Brij-58 directing
agents. Comparison of the magnetization hysteresis loops clearly
suggests that the mesostructure of the nanowires significantly
affects the magnetic isotropy. As shown above, 2D nanowire
thin films directed from P123 or CTAB surfactants possess
nanowires that are preferably oriented parallel to the substrate
plane. Similar to the Co bulk thin film (a), such a shape
anisotropy results in uniaxial anisotropic magnetism (b,c). As
compared to the anisotropic 2D hexagonal mesostructure, the
isotropic 3D cubic Co nanowire thin film shows isotropic
magnetism (d). Although the magnetic signal is a little noisy,
the inset of Figure 3d clearly shows approximately equal
coercivity and remanent magnetization, which further confirms
the pure cubic structure formation.
The nanostructure endows the nanowire thin films (b-d) with
enhanced coercivity, as compared to the bulk Co film (a) that
shows a low coercivity on the order of 10 Oe.11,13 As shown in
Figure 3, the CTAB directed 3 nm Co nanowire thin film shows
a parallel coercivity of 140 Oe and a perpendicular coercivity
of 400 Oe. The Brij-58 directed 5 nm Co nanowire thin film
shows an identical parallel and perpendicular coercivity of 255
Oe. The P123 directed 8 nm Co nanowire thin film shows a
parallel coercivity of 385 Oe and a perpendicular coercivity of
890 Oe. It is well known that the coercivity of nanowires
strongly depends on the wire diameters. The CTAB and P123
directed nanowire thin films contain similar 2D hexagonal
mesostructure but different nanowire diameters. As shown
above, the P123 directed nanowires (8 nm diameter) show a
higher covercivity than the CTAB directed nanowires (3 nm
diameter). As we mentioned before, the most nanowires
investigated so far have diameters greater than 30 nm; the
coercivity increased with decreasing wire diameters. Only Zeng
et al. reported the magnetic properties of Fe, Co, and Ni
nanowires with diameters between 9 and 21 nm, and they found
the coercivity is closely related to the wire diameters and there

1922 J. Phys. Chem. B, Vol. 109, No. 5, 2005
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Acknowledgment. This work was supported by NASA
(Grant No. NAG-1-02070 and NCC-3-946), the office of Naval
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