strong uni-directional anisotropy in disordered nife2o4
TRANSCRIPT
Strong uni-directional anisotropy in disordered NiFe2O4
Y. Shia, J. Dinga,*, Z.X. Shenb, W.X. Sunb, L. Wangb
aDepartment of Materials Science, National University of Singapore, Lower Kent Ridge Road, Singapore, Singapore 119260bDepartment of Physics, National University of Singapore, Singapore, Singapore 119260
Received 31 March 2000; accepted 18 April 2000 by T. Tsuzuki
Abstract
High-energy mechanical milling of spinel NiFe2O4 leads to the formation of a disordered wustite-like structure. Cluster glass
behavior was found in the MoÈssbauer study. The investigation suggested ferrimagnetic clusters in an antiferromagnetic matrix.
The ferrimagnetic and antiferromagnetic exchange coupling results in a strong uni-directional anisotropy and a coercivity of
over 10 kOe after magnetic cooling. q 2000 Elsevier Science Ltd. All rights reserved.
Keywords: A. Magnetically ordered materials; B. Nanofabrications; E. Nuclear resonances
1. Introduction
Magnetic ferrites are found in many applications such as
permanent magnets, recording media, ferro¯uids and micro-
wave devices [1±4]. Recently, many publications have
reported interesting behaviors in ferrite materials, such as
change in saturation magnetization, spin glass or cluster
glass, high coercivity and shift in hysteresis loop [1,2,4±
6]. The mechanisms of these behaviors are not clear. Disor-
dered structure has been suggested [5,6]. The clari®cation of
the mechanisms is certainly of interest for research and
applications, e.g. magnetic recording [1±6].
Mechanical alloying (high-energy mechanical milling) is
a powerful method for the synthesis of amorphous and non-
equilibrium materials. Many ferrite materials prepared by
mechanical alloying have shown unique properties [3,4,7].
In this work, we have mechanically milled NiFe2O4 powder.
The structure and magnetic properties were studied.
2. Experimental
The starting powder for the mechanical milling was
NiFe2O4 powder, which was calcined at 13008C for 2 h
after chemical co-precipitation. NiFe2O4 powder together
with several steel balls was loaded in a hardened steel vial
before mechanical milling. The mechanical milling was
performed using a Spex 8000 for 32 h. The powder/steel
ball weight ratio was 1:5. After mechanical milling, the
as-milled powder was annealed at different temperatures
(400±10008C) for 1 h in air atmosphere.
The structure was examined by X-ray diffraction with
CuKa radiation, transmission electron microscopy and
Raman spectroscopy. The magnetic properties were studied
using a vibrating sample magnetometer (VSM) with a maxi-
mum ®eld of 90 kOe in the temperature range 4.2±293 K
and a 57Fe-MoÈssbauer spectrometer from room temperature
to 4.2 K.
3. Results and discussion
The calcined powder possessed a saturation magnetiza-
tion of 49 emu/g at room temperature. The MoÈssbauer spec-
trum and X-ray diffraction pattern were expected for the
spinel ferrite phase with a composition of NiFe2O4 [8].
Fig. 1 shows the X-ray diffraction patterns of the as-milled
powder and powders after annealing at different tempera-
tures. After mechanical milling, the diffraction peaks were
broad. The major peak ((311) plane) at 2u � 35:88 for the
spinel structure was absent. The broad diffraction peaks
could be well identi®ed with the wustite structure (FeO).
After annealing at 4008C, the major peak at 2u � 35:88 for
the spinel structure began to appear. After annealing at
6008C, the X-ray diffraction pattern could be described
with the spinel NiFe2O4 structure. Annealing at higher
Solid State Communications 115 (2000) 237±241
0038-1098/00/$ - see front matter q 2000 Elsevier Science Ltd. All rights reserved.
PII: S0038-1098(00)00176-9
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* Corresponding author. Tel.: 165-874-4317; fax: 165-776-
3604.
E-mail address: [email protected] (J. Ding).
temperatures (800 and 10008C) lead to sharp crystalline
peaks, indicating grain growth. The as-milled powder was
studied under a transmission electron microscope. Small
grains of approximately 10 nm exhibited diffuse electron
diffraction rings, indicating a disordered structure. These
diffuse rings could be described with the wustite structure.
Fig. 2 shows the Raman spectra of the as-milled and the
subsequently annealed powders. No signi®cant difference
between the as-milled powder and the powders annealed
at 10008C is evident. The broadened peaks of the as-milled
corresponded to the nanocrystalline structure. The Raman
result indicated that the as-milled powder should have a
structure similar to that of the powder annealed at 10008C(i.e. ordered NiFe2O4 structure).
Fig. 3 shows the saturation magnetization Ms of the as-
milled and subsequently annealed powders. The as-milled
powder exhibited a much lower saturation magnetization,
which is approximately 1/3 of that expected for NiFe2O4. Ms
increased with increasing annealing temperature. After
annealing at 10008C, Ms was measured to be 48 emu/g,
which is nearly the same as the starting powder before
milling and is well expected for NiFe2O4 [8].
Y. Shi et al. / Solid State Communications 115 (2000) 237±241238
Fig. 1. X-ray diffraction patterns of the as-milled and the subsequently annealed samples.
Fig. 2. Raman spectra of the as-milled and the subsequently
annealed samples.
Fig. 3. Saturation magnetization Ms versus the annealing tempera-
ture Ta.
Fig. 4 shows the MoÈssbauer spectra of the as-milled
powder taken at different temperatures. The MoÈssbauer
spectrum of the as-milled powder at room temperature
could be well ®tted with two non-magnetic doublets, indi-
cating superparamagnetism in consideration of the magnetic
result discussed above. With decreasing temperature, the
average hyper®ne ®eld increased, while the population of
the non-magnetic component decreased. This behavior is
typical for cluster glass [6]. At 4.2 K, the average hyper®ne
®eld was close to the average hyper®ne ®eld of NiFe2O4, but
with a much broader hyper®ne ®eld distribution.
All the results discussed above (X-ray diffraction, trans-
mission electron microscopy, Raman spectroscopy,
magnetic measurements and MoÈssbauer spectroscopy)
suggest a disordered structure after the high-energy mechan-
ical milling. The structure of the as-milled powder is
Y. Shi et al. / Solid State Communications 115 (2000) 237±241 239
Fig. 4. MoÈssbauer spectra of the as-milled and the subsequently annealed samples.
probably similar to the wustite structure. A possible conver-
sion between magnetite (Fe3O4) and wustite (FeO) has been
reported in thin ferrite ®lms [5]. In this work, XPS was used
for the study of the as-milled powder. Many Ni21 ions were
converted into Ni31, while some Fe31 changed into Fe21
after mechanical milling. This result is probably associated
with a disordered structure in the A and B sites of the spinel
structure. Similar results have been reported previously
[7,9].
Fig. 5 shows the zero-®eld-cooling (ZFC) and ®eld-cool-
ing (FC) curves of the as-milled powder, when the magne-
tization was measured under the maximum ®eld of 90 kOe.
At 5 K, the difference in magnetization was approximately
15% between FC and ZFC. This is a characteristic behavior
for cluster or spin glasses [6]. Recently, similar results have
been reported in other ferrite materials [1,2,5,6] that may
possess a disordered structure [5,6].
Fig. 6 shows the hysteresis loops taken at 5 K after ZFC
and FC, respectively. The hysteresis loop after ZFC exhib-
ited a relatively low coercivity and a symmetric hysteresis
loop. The hysteresis loop after FC was shifted. A coercivity
of over 10 kOe was measured. The high coercivity and the
large shift in the hysteresis loop are attributed to a large
exchange coupling [1,2].
From a combination of our magnetic and MoÈssbauer
results, we suggest that cluster glass [6] is the control-
ling mechanism in the mechanically alloyed NiFe2O4
powder. We may propose a tentative microstructure
for the powder after mechanical milling. The high-
energy mechanical milling of spinel NiFe2O4 results in
a disordered structure. This structure is associated with
both spinel and wustite [5]. There is probably a mixture
of ferrimagnetic clusters (spinel) in an antiferromagnetic
matrix (wustite). The interaction between the ferrimag-
netic clusters and the antiferromagnetic matrix results in
a large exchange anisotropy, which leads to the shifted
hysteresis loop and large coercivity (Fig. 6). At room
temperature, the ferromagnetic clusters exhibit superpar-
amagnetism, as found in our MoÈssbauer and magnetic
measurements.
4. Summary
Mechanical milling of NiFe2O4 lead to a disordered struc-
ture. In the X-ray diffraction patterns, the as-milled powder
exhibits broadened diffraction peaks which can be identi®ed
as wustite-like, while ordered spinel was reformed after heat
Y. Shi et al. / Solid State Communications 115 (2000) 237±241240
Fig. 5. Field-cooling (FC) and zero-®eld-cooling (ZFC) of the as-
milled powder. The sample was cooled under a magnetic ®eld of
90 kOe in the ®eld cooling. The magnetization was measured at
90 kOe.
Fig. 6. Hysteresis loops of the as-milled NiFe2O4 powder taken at 5 K after zero-®eld cooling (ZFC) and after ®eld cooling (FC).
treatment at a temperature of 6008C or higher. The as-milled
powder under a transmission electron microscope
consists of small grains with a grain size of approxi-
mately 10 nm. The diffuse electron diffraction rings can
be described with the wustite structure. However,
Raman spectroscopic study suggests that the as-milled
powder should have a structure similar to that of the
ordered NiFe2O4 structure.
A cluster glass behavior [6] was observed in the
MoÈssbauer spectra of the as-milled powder taken at
different temperatures. The spectrum taken at 4.2 K
possessed the average hyper®ne ®eld of ,51 T, which
is close to that of the ordered NiFe2O4 and is signi®-
cantly higher than that of wustite [10]. Cluster glass was
con®rmed in FC and ZFC curves. Shifted hysteresis
loop and high coercivity was measured at 5 K after
magnetic cooling. These results lead to a tentative
microstructure which cab be described as ferrimagnetic
clusters (based on spinel) in an antiferromagnetic matrix
(based on wustite).
References
[1] R.H. Kodama, A.E. Berkowitz, E.J. McNiff, S. Foner, Phys.
Rev. Lett. 77 (1996) 395.
[2] B. Martinez, T. Obradors, Ll. Balcells, A. Rounanet, C.
Monty, Phys. Rev. Lett. 80 (1998) 181.
[3] J. Ding, T. Reynold, W.F. Miao, P.G. McCormick, R. Street,
Appl. Phys. Lett. 65 (1994) 7074.
[4] J. Ding, W.F. Miao, R. Street, P.G. McCormick, J. Alloys
Compd. 281 (1998) 32.
[5] D.V. Dimitrov, K. Unruh, G.C. Hadjipanayis, Phys. Rev. B 59
(1999) 14499.
[6] A. Ito, K. Iwai, H. Kato, J. Phys. Soc. Jpn. 64 (1995) 1766.
[7] J.Z. Jiang, R. Lin, S. Morup, K. Nielsen, F.W. Poulsen, F.J.
Berry, R. Clasen, Phys. Rev. B 55 (1997) 11.
[8] S. Krupicka, P. Novak, Oxide spinels, in: E.P. Wohlfarth
(Ed.), Ferromagnetic Materials, Vol. 3, North-Holland,
Amsterdam, 1998, p. 189.
[9] J.Z. Jiang, P. Wynn, S. Morup, T. Okada, F.J. Berry, Nano-
struct. Mater. 12 (1999) 737.
[10] C.A. McCammon, D.C. Price, Phys. Chem. Mineral. 11
(1985) 250.
Y. Shi et al. / Solid State Communications 115 (2000) 237±241 241