2. in-plane field. The results are shown in the inset of Fig. 2͑a͒,
where the as-grown and annealed piece both show similar TC
of ϳ66 K, identifying suppressed effect of annealing due to
GaAs capping.13
An alternative method of determining TC of
͑Ga,Mn͒As is through the peak of the temperature-
dependent resistivity, where the peak temperature is usually
within 10 K of the estimated TC from SQUID
measurements.16,17
The equivalence is demonstrated in Fig.
2͑a͒ by resistivity versus temperature data from 1 mm
ϫ2 mm mesas patterned on the same as-grown and annealed
pieces.
We fabricated wires of widths 1 m, 420, 220, and
120 nm for four probe resistivity measurement. We measured
the temperature-dependent resistivity, ͑T͒, of all the wires
and then annealed for an hour at 190 °C in flowing N2, and
then measured again, and then annealed again for another
hour. This cycle was repeated for 6 h of total annealing time,
but the samples degraded during a longer anneal which was
attempted after 6 h, and became unmeasurable. Typical data
are shown in Figs. 2͑b͒ and 2͑c͒ for the wires as-grown and
annealed for 6 h total.18
Compared to the results for the mac-
roscopic pieces of sample ͓Fig. 2͑a͔͒, there is a significant
effect of annealing on the nanowires. The increase in TC after
annealing is almost 45 K for the 120 nm wire, indicating the
effectiveness of outdiffusion of MnI towards the lateral free
surfaces. Though we have no explanation for the slightly
increased resistivity in our set of annealed wires compared to
the unpatterned as-grown sample, similar effects due to re-
construction of defect structures have been observed for con-
FIG. 3. ͑a͒ Curie temperature, ͑b͒ conductivity at T=300 K, and ͑c͒ rate of
change of conductivity ͑measured at T=300 K͒ for the different wires as a
function of total anneal time. Each of these wires is measured as-grown and
after every additional hour of annealing at 190 °C up to 6 h. The rate
change of conductivity was calculated based on the neighboring conductiv-
ity values of the corresponding annealing time.
FIG. 2. ͑a͒ Resistivity vs temperature ͑measured in van der Pauw geometry͒
of as-grown and annealed 1 mmϫ2 mm mesa patterned on
GaAs/͑Ga,Mn͒As͑50 nm͒/GaAs͑10 nm͒ heterostructures. The inset shows
magnetization vs temperature for the same sample measured in a magnetic
field of 50 Oe in-plane while warming after field cooling in a 1 T field. The
values of TC obtained from both measurements are consistent. ͑b͒ Tempera-
ture dependence of ͑four-probe͒ resistivity for unannealed wires, patterned
from the same sample. ͑c͒ The temperature dependence of the resistivity of
the same wires after six 1 h anneals.
08D501-2 Sheu et al. J. Appl. Phys. 99, 08D501 ͑2006͒
Downloaded 17 Apr 2006 to 146.186.190.234. Redistribution subject to AIP license or copyright, see http://jap.aip.org/jap/copyright.jsp
3. ditions such as higher annealing temperatures and longer an-
nealing times.6,7
In Fig. 3, we show the annealing time dependence of TC
and resistivity at 300 K. We note that after 6 h of annealing,
the increase in TC for the 120 nm wire is three times of the
1 m wire; at the same time, the resistivity at the ͑T͒ peak
is reduced to half that of the 1 m wire, confirming the
strong correlation between the enhancement of TC and de-
crease of resistivity, which was observed in uncapped
epilayers.7
Figure 3͑c͒ shows the rate change of conductivity versus
annealing time, indicating the MnI diffuse out faster in a
thinner wire in the initial stages of annealing, and the rate of
MnI removal decreases with annealing time. This is some-
what different from the results of in situ resistance monitor-
ing in uncapped epilayers, in which the thinner layers had a
slower rate of change of resistivity.9
Due to the limited time
interval of our measurements, we cannot rigorously test our
data against the one-dimensional diffusion model used in that
study. On the other hand, the higher rate of change of the
conductivity in thinner wires, suggests that a more complex
model would be required, perhaps due to the more complex
geometry presented by the wires. Another possibility is that
diffusion is different in the thinner epilayers studied previ-
ously or different in the lateral as opposed to the growth
direction ͑although different lateral directions appear to be
equivalent͒.15
In summary, we studied lateral diffusion of Mn intersti-
tials in a post-growth annealed series of GaAs-capped
͑Ga,Mn͒As wires of different widths. For different anneal-
ing time periods, our measurements indicate that the nar-
rower wires are fabricated, the more significant are the ef-
fects of Curie temperature enhancement, accompanied by a
larger resistivity decrease and higher rate change of conduc-
tivity.
This research has been supported by Grant Nos. ONR
N0014-05-1-0107, DARPA/ONR N00014-99-1093, -00-1-
0951, University of California-Santa Barbara Subcontract
KK4131, and NSF DMR-0305238 and DMR-0401486. This
work was performed in part at the Penn State Nanofabrica-
tion Facility, a member of the NSF National Nanofabrication
Users Network.
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The monotonically decreasing resistivity with wire width in the as-grown
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08D501-3 Sheu et al. J. Appl. Phys. 99, 08D501 ͑2006͒
Downloaded 17 Apr 2006 to 146.186.190.234. Redistribution subject to AIP license or copyright, see http://jap.aip.org/jap/copyright.jsp