improving room temperature magnetoresistance in derivatives of ferrimagnetic cacu3mn4o12 perovskite
TRANSCRIPT
Journal of Magnetism and Magnetic Materials 272–276 (2004) e1407–e1409
ARTICLE IN PRESS
*Corresp
91-372-062
(J. S!anchez
0304-8853/
doi:10.1016
Improving room temperature magnetoresistance in derivativesof ferrimagnetic CaCu3Mn4O12 perovskite
J. S!anchez-Ben!ıtez*, J.A. Alonso, A. de Andr!es, M.J. Mart!ınez-Lope, M.T. Casais,J.L. Mart!ınez
Instituto de Ciencia de Materiales de Madrid, CSIC. Cantoblanco, E-28049 Madrid, Spain
Abstract
Two series of derivatives of the complex CaCu3Mn4O12 perovskite have been prepared under moderate pressure
conditions (20 kbar), and characterized by neutron powder diffraction, magnetic and magnetotransport measurements.
In a susbtituted series with formula LnCu3Mn4O12 (Ln=rare earths) we observe a significant increment of TC and a
level of low field magnetoresistance at RT that compete with the best values described for the state-of-the art perovskite
oxide systems.
r 2004 Elsevier B.V. All rights reserved.
PACS: 75.47.�m
Keywords: Magnetoresistance; Ferrimagnetic oxide; Neutron diffraction; Magnetic structure
Half metallic ferromagnets have focused a lot of
attention as a source of magnetoresistive materials.
Recently, the complex perovskite CaCu3Mn4O12 [1] has
attracted the attention of the CMR community: it is
semiconducting, orders ferromagnetically at 355K, and
shows, at 300K, low-field magnetoresistance (MR)
values higher than hole-doped manganese perovskites
ones. The crystal structure of CaCu3Mn4O12 [2] has the
rare feature of containing Cu2+ (or other Jahn–Teller
transition metal cations, such as Mn3+) at the A
positions of the ABO3 perovskite. This Jahn–Teller
cation and Ca2+ are 1:3 ordered in a 2a0� 2a0� 2a0cubic cell of Im%3 symmetry (a0: unit cell of the
aristotype). This material, and other compounds of the
A0A3B4O12 family, have been prepared under high
pressure (70 kbar), necessary to stabilize the small A
cations in the perovskite.
onding author. Tel.: +34-91-334-9000; fax: +34-
3.
address: [email protected]
-Ben!ıtez).
$ - see front matter r 2004 Elsevier B.V. All rights reserve
/j.jmmm.2003.12.704
Recently, we have been able to synthesize some new
derivatives of CaCu3Mn4O12 at moderate pressures of
20 kbar, starting from very reactive precursors obtained
by wet-chemistry procedures, in the presence of KClO4
as oxidizing agent. These materials have been fully
characterized by neutron powder diffraction (NPD),
magnetic and magnetotransport measurements.
With the aim of improving the magnetotransport
properties of this promising system, we have prepared
and studied two series of compounds: (i) Cu2+ has been
replaced by Mn3+, in the series CaCu3�xMn4+xO12
(x ¼ 0:5; 1, 2, 3) and (ii) Ca2+ has been replaced by a
rare earth ion in the series LnCu3Mn4O12 (Ln= La3+,
Nd3+, Tb4+, Ce4+ and Th4+).
Both series present Mn valence mixing at the B
positions of the perovskite, induced by the introduction
of Mn3+ or Ln3+/4+ replacing divalent cations at the A
sublattice. The crucial difference of both series is that in
the last one the Cu sublattice is undisturbed.
Fig. 1 shows the magnetization vs. temperature of
some selected samples. As Mn3+ is introduced in the
first series, the Curie temperature (TC) shows a steep
decrease. Most interestingly, TC increases remarkably in
d.
ARTICLE IN PRESS
0 50 100 150 200 250 300 350 400
0
1
2
3
4
5
0 1 2 3 4 50
3
6
9
12
10.2 µB/f.u.
T = 5 K
CaCu2.5Mn4.5O12
M(µ
B/f.
u.)
Magnetic Field (T)
CaCu2Mn5O12
CaCuMn6O12
CaCu2.5Mn4.5O12
LaCu3Mn4O12
TbCu3Mn4O12
M(µ
B/f.
u.)
Temperature (K)
Fig. 1. Temperature dependence of the magnetization for some
selected samples. The inset shows the magnetization vs.
magnetic field plot at 5K of CaCu2.5Mn4.5O12.
0.0 0.5 1.00.0
0.5
1.0
1.5
2.0
2.5
3.0
~ 1 0 0 º
B site A site
M n 4 + M n 3 +
M n 4 + M n 3 + C u 2 + M n 3 +
C u 2 +
CeCu 3Mn 4
O 12NdCu3M
n4O 12
Ca 0.5La 0.5
Cu 3Mn 4
O 12
CaCu2Mn5O12
CaCu 2.5Mn 4.5
O 12
LaCu3Mn4O
12
- M
R %
Magnetic Field (T)
Fig. 2. The left panel shows the arrangement of magnetic
moments in the CaCu3�xMn4+xO12 (up) and LnCu3Mn4O12
(down) series. The right panel shows the magnetoresistance
curves at RT for some selected samples of both series.
J. S !anchez-Ben!ıtez et al. / Journal of Magnetism and Magnetic Materials 272–276 (2004) e1407–e1409e1408
the second series up to 395K for TbCu3Mn4O12. All the
samples, excepting CaMn7O12 (AF), show a magnetiza-
tion characteristic of a ferromagnet (illustrated at the
inset of Fig. 1). In the first series, the saturation
magnetizations are significantly higher than those
expected in a pure ferrimagnetic system. We have
developed a magnetic model for the complex magnetic
couplings of these compounds from the analysis of NPD
and magnetization data.
NPD patterns were collected at room temperature and
2K at the high-resolution D2B neutron diffractometer
of ILL-Grenoble. A wavelength of 1.594 (A was selected
from a Ge monochromator. Both crystallographic and
magnetic structures were refined from NPD by the
Rietveld method.
The left panel of Fig. 2 depicts a schematic micro-
scopic model on the relative arrangement of the
magnetic moments in the Mn and Cu sublattices of
both series. This model implies that magnetic moments
of Mn3+ in B position are oriented parallel to those of
Mn4+ of the same site. However, magnetic moments of
Mn3+ at Cu positions are not collinear to those of Cu,
but almost perpendicular.
As a result of this configuration, in the Ca-
Cu3�xMn4+xO12 series, the interactions between Mn
an Cu planes are disturbed because of the introduced
magnetic disorder. By contrast, in LnCu3Mn4O12, where
the Cu sublattice is not disturbed, the magnetic
configuration is purely ferrimagnetic and a remarkable
increase of TC is observed.
The CaCu3Mn4O12 pure sample displays a semicon-
ducting behavior in all the temperature range (0–400K)
(rRT ¼ 1800O cm), while a metallic behavior is observed
for most of the substituted samples at low temperature,
with very low resistivity values (0.05–0.5O cm). For
NdCu3Mn4O12 and TbCu3Mn4O12 we find a metallic
behavior up to 400K. This fact can be explained
through the band structure diagram proposed by Weth
and Picket [3], where Mn eg levels are involved in the
conduction band. When Mn3+ is introduced, the
compound is electron doped and the conduction band
is progressively occupied leading to a metallic ground
state. This also causes the strong decrease of several
orders of magnitude in the resistivity. In both series, a
transition in the electrical behavior is induced (metal–
insulator transition) around 180–300K that can be due
to the competition of different electronic transport
mechanisms not determined yet.
The right panel of Fig. 2 shows the magnetoresistance
(MR ¼ 100� ðrH � r0Þ=r0) curves at RT for some
selected samples. The most interesting feature of these
curves is the strong component of low-field MR
(LFMR) at room temperature.
MR values of LnCu3Mn4O12 series are higher than
those of CaCu3�xMn4+xO12 (right panel of Fig. 2).
LaCu3Mn4O12 reaches a MR value higher than 1% at
0.1 T and RT. The improved LFMR in the lanthanide
series is due to its direct relationship with the carriers
polarization degree. In the first series, the magnetic
moments of Mn3+ at Cu positions are set in an almost
perpendicular direction, thus the carriers polarization is
reduced, while this is not the case for the lanthanide-
substituted series. Moreover, the increase of TC in Ln
compounds favors the degree of polarization of the
carriers at RT. On the other hand, we observe the MR at
H ¼ 9T increases monotonically with decreasing tem-
perature and no anomaly is found around TC; indicatingthat the valence mixing does not seem to couple the
ARTICLE IN PRESSJ. S !anchez-Ben!ıtez et al. / Journal of Magnetism and Magnetic Materials 272–276 (2004) e1407–e1409 e1409
electronic transport to the magnetic order, as it occurs in
manganites.
We conclude that in the lanthanide-substituted series
we obtain both a substantial increment of TC and a
better low field MR, via an electron doping effect that
maintains undisturbed the Cu sublattice. The obtained
TC’s and the levels of LFMR compete with the best
values described for the state-of-the art perovskite oxide
systems.
We thank the financial support of CICyT to the
projects MAT 2003-01880, MAT 2001-0539 and CAM
07N/0080/2002 and we are grateful to ILL for making
all facilities available.
References
[1] Z. Zeng, M. Greenblatt, M.A. Subramanian, M. Croft,
Phys. Rev. Lett. 82 (1999) 3164.
[2] J. Chenavas, J.C. Joubert, M. Marezio, B. Bochu, J. Sol.
Stat. Chem. 14 (1975) 25.
[3] R. Weht, W.E. Pickett, Phys. Rev. B 65 (2001) 14415.