Annealing Dependence of Exchange Bias in MnO/Ga1−xMnxAs Heterostructures

Journal of Superconductivity: Incorporating Novel Magnetism, Vol. 18, No. 3, June 2005 ( C 2005)
DOI: 10.1007/s10948-005-0019-9

Annealing Dependence of Exchange Bias
in MnO/Ga1−x Mnx As Heterostructures

K. F. Eid,1 O. Maksimov,1 M. B. Stone,1 P. Schiffer,1 and N. Samarth1

We discuss the annealing-dependence of exchange bias in Ga1−x Mnx As epilayers that are
overgrown with Mn. Although pure Mn is a known antiferromagnet, we find that the as-
grown Mn overlayer does not produce any exchange coupling with Ga1−x Mnx As. Rather,
our studies indicate that annealing in air is essential for creating the standard signatures of
exchange bias (a clear shift in the magnetization hysteresis loop and an increased coercive
field). We use X-ray photoelectron spectroscopy to characterize the compositional depth pro-
file of both as-grown and rapid thermal annealed samples. These studies demonstrate that the
cleanest exchange bias arises when the Mn overlayer is completely converted into MnO.
KEY WORDS: exchange bias; ferromagnetic semiconductor; antiferromagnet.

1. INTRODUCTION HE ). This occurs when the sample is cooled through
the blocking temperature (TB ) of the AF in the pres-
Ferromagnetic semiconductors derived from ence of either an external magnetic field or a net mag-
III–V semiconductors such as GaAs and InAs have netization in the ferromagnetic layer [9]. This shift
attracted significant attention recently within the is typically accompanied by an increase in the coer-
context of semiconductor-based “spintronics” [1,2]. cive field (HC ) of the ferromagnetic layer. This phe-
These materials present a unique opportunity for nomenon is the subject of intense study in a variety
controlling magnetism through electrical gates [3], of magnetic materials and is exploited in different ap-
and have also been incorporated in a variety of proof- plications [9].
of-principle device configurations [4–6]. The ability We have recently demonstrated the first success-
to exchange bias spintronic devices derived from ful exchange biasing of a ferromagnetic semiconduc-
these materials will add to their viability for future tor (Ga1−x Mnx As) by an overgrown antiferromagnet
applications, as well as offer a new system for ba- (MnO) [10]. In these experiments, metallic Mn is
sic scientific research. For example, it is known from first epitaxially grown on top of Ga1−x Mnx As in
studies of metallic ferromagnetic multilayer struc- an ultrahigh vacuum chamber. Upon removal from
tures that exchange biased read heads are more sta- the vacuum chamber, the Mn overlayer is uninten-
ble than hybrid sensors [7]. Exchange biased spin- tionally oxidized during removal of the wafer from
valves are also preferred for devices because of the the indium-bonded mounting block. Rutherford
desirable shape of their magnetoresistance curves backscattering (RBS) measurements clearly indicate
[8]. the presence of MnO, a well-known antiferromagnet
Exchange biasing of a ferromagnet by a vicinal that is presumably responsible for the exchange
antiferromagnet (AF) manifests itself as a shift of biasing effect. This conclusion is supported by the
the magnetization hysteresis loop, making it centered observation that Al-capped samples do not exhibit
about a nonzero magnetic field (the exchange field, any exchange bias since they are impervious to
oxidation. Furthermore, RBS studies also suggest
1 Department of Physics and Materials Research Institute, Penn- that the extreme reactivity between Mn and GaAs
sylvania State University, University Park, Pennsylvania 16802. requires a delicate balance between the need for

421
0896-1107/05/0600-0421/0 C 2005 Springer Science+Business Media, Inc.

422 Eid, Maksimov, Stone, Schiffer, and Samarth

oxidation and the preservation of a clean inter- ∼8 nm is deposited. Mn growth is performed at room
face. For instance, modest annealing at temperatures temperature in order to prevent inter diffusion and
around 230◦ C completely destroys the exchange bias. chemical reaction between Mn and Ga1−x Mnx As lay-
Given these circumstances, it is important to de- ers [11,12].
velop a better understanding of the oxidation of the The growth mode and surface reconstruction
Mn overlayer and to hence obtain systematic control are monitored in situ by reflection high-energy elec-
over the creation of exchange biased Ga1−x Mnx As tron diffraction (RHEED) at 12 keV. The thick-
devices. In this paper, we focus on the growth and ness of the Ga1−x Mnx As layer is calculated from
characterization of the antiferromagnetic MnO layer RHEED oscillations, while the thickness of the
and discuss the dependence and sensitivity of ex- Mn layer is estimated from RHEED oscillations of
change coupling on the annealing conditions. In par- MnAs whose growth rate is mainly determined by
ticular, we use a series of annealing experiments to the sticking coefficient of Mn. The Mn concentration
definitively demonstrate that metallic Mn grown on in Ga1−x Mnx As is x ∼ 0.06, estimated from the Mn
Ga1−x Mnx As does not by itself create exchange bias, flux.
and that the oxidation of the Mn layer to MnO is es- Magnetization measurements are performed us-
sential to produce an exchange coupling. ing a commercial superconducting quantum interfer-
ence device (SQUID) magnetometer. Samples were
measured with the magnetic field in plane along the
2. EXPERIMENTAL DETAILS (110) direction as a function of both temperature and
applied magnetic field. Surface morphology is inves-
Samples are grown by molecular beam epitaxy tigated using an atomic force microscope running in
(MBE) on “epi-ready” semi-insulating GaAs (100) a tapping mode. Si cantilevers with a spring constant
substrates that are bonded with indium to molyb- of 13–100 N/m and a nominal resonance frequency
denum blocks. Removal of the samples from the of 240–420 kHz are used. Images are recorded with
mounting block entails heating up the entire block to a resolution of 300 × 300 pixels at a scan rate of
melt the bonding layer of indium. In contrast to the 1 micrometer/s. The surface and sub-surface com-
usual mounting, when indium is uniformly dispersed position is examined by X-ray photoelectron spec-
under the entire wafer, for samples studied in this troscopy (XPS) using a Kratos Analytical Axis Ul-
communication only the edges of the sample wafer tra system. The Ga 2p3/2 , As 2p3/2 , Mn 2p3/2 , 2p1/2 ,
are indium bonded to the block. This procedure pro- 3p, and O 1s photoelectrons are excited using a
vides sufficient thermal contact during MBE growth monochromatic Al K X-rays (hv = 1486.6 eV). XPS
and allows the removal of a significant portion of the quantification is performed by applying the appropri-
wafer without any post-growth annealing. ate relative sensitivity factors (RSFs) for the Kratos
The MBE growth is performed in an Applied instrument to the integrated peak areas. These RSFs
EPI 930 system equipped with Ga, Mn, and As effu- take into consideration the X-ray cross-section and
sion cells. The substrates are deoxidized using stan- the transmission function of the spectrometer. Low
dard protocol, by heating to ∼580◦ C with an As energy (<5 eV) electrons are used for charge neu-
flux impinging on the surface. A 100 nm thick GaAs tralization. The charge-induced shifts are corrected
buffer layer is grown after the deoxidization. Then, using the binding energy of C–C hydrocarbon line
samples are cooled to ∼250◦ C for the growth of a (285.0 eV) as an internal standard.
5 nm thick low temperature GaAs layer, followed
by a 10 nm thick Ga1−x Mnx As layer (x ∼ 0.06). The
growth is performed under the group V rich condi- 3. RESULTS AND DISCUSSION
tions with a As:Ga beam equivalent pressure ratio
of ∼12:1. After the Ga1−x Mnx As growth, the sam- Figure 1a shows the (1×2) surface reconstruc-
ples are transferred in situ to an adjoining ultra high tion in a RHEED pattern for a Ga1−x Mnx As epi-
vacuum buffer chamber and the As cell is cooled layer prior to the Mn growth. Figure 1b and c shows
to the rest temperature of 110◦ C to avoid formation RHEED patterns for Mn deposited on Ga1−x Mnx As
of MnAs clusters during the Mn growth. When the with the incident electron beam along the [110] and
As pressure in the growth chamber decreases to an ¯
[110] directions. The RHEED pattern consists of
acceptable level, the wafers are reintroduced. Then, sharp, elongated streaks and its symmetry is sugges-
the Mn capping layer with a thickness of ∼4 nm or tive of the stabilization of a cubic phase of Mn. This

Annealing Dependence of Exchange Bias in MnO/Ga1−x Mnx As 423

Fig. 1. (a) RHEED patterns for Ga1−x Mnx As showing the two-fold reconstruction prior to Mn
growth; (b) and (c) RHEED patterns for Mn epilayers grown on Ga1−x Mnx As with different
incident directions of the electron beam.

indicates that, in contrast to previous reports [11], pieces from the same wafer: one piece is from the
Mn can be epitaxially grown at room temperature. A indium-free portion of the wafer and is not heated
representative atomic force microscope scan of the after removal from the vacuum chamber, while the
Mn surface is shown in Fig. 2. The epilayer is atom- other is from the indium-bonded portion and hence
ically ﬂat with a root mean square (rms) roughness undergoes a rapid thermal anneal to ∼220◦ C during
of ∼0.2 nm, similar to the rms values reported for sample removal. The zero magnetization at tempera-
Ga1−x Mnx As epilayers [13]. tures above TC indicates that the sample is of good
Figure 3a shows the temperature dependence of quality without MnAs clusters. Although we ob-
the magnetization for a sample with a Curie tem- serve no difference in the TC of the indium-free and
perature (TC ) of 85 K. The data is shown for two indium-mounted portions of the sample, we do note

Fig. 2. Tapping-mode atomic force microscope scan of an as-grown Mn/Ga1−x Mnx As heterostructure with
8 nm Mn thickness.


collected for the samples annealed to 200◦ C and
250◦ C, we only compare the 250◦ C annealed sam-
ple to the as-grown sample. Figure 4 depicts high-
resolution Mn 2p spectra for the as-grown and an-
nealed samples. Both the positions and the shapes of
the Mn 2p lines differ for the annealed and as grown
samples. The Mn 2p3/2 line for the as grown part is
centered at ∼641.0 eV. Its position is in agreement
with the binding energy of MnO (Mn2+ ), indicating
that the Mn at the surface is oxidized. (Metallic Mn0
has a 2p3/2 line at 639 eV, while lines from Mn2 O3
(Mn3+ ) and MnO2 (Mn4+ ) have binding energies of
∼641.7 eV and ∼642.5 eV, respectively [14].) The
observation of two satellite lines spaced by 5.5 eV
from 2p3/2 and 2p1/2 lines further supports this as-
signment. These satellite excitations are typical for
Fig. 3. Magnetization as a function of temperature and applied MnO [15,16] and are not present in either Mn2 O3 or
magnetic field for MnO/Ga1−x Mnx As heterostructures. Hystere- Mn2 O3 [17–20]. The Mn 2p3/2 line for the annealed
sis loops are measured at T = 10 K, field cooled from T = 200 K piece is visibly shifted to a slightly higher binding en-
with H = 1 kOe. (a) Temperature-dependent magnetization mea- ergy of ∼641.3 eV. The two satellite lines disappear
sured with H = 100 Oe for an indium-free portion of the as-grown
while a new satellite line at ∼663.5 eV appears, indi-
sample and for an indium-bonded portion. (b) Field-cooled hys-
teresis loop for indium-free portion of sample. (c) Field-cooled cating that the as-grown Mn has oxidized to Mn2 O3
hysteresis loop for indium-mounted portion of sample. (d) Field- [17].
cooled hysteresis loop for indium-free portion of sample after in- We also measure the compositional depth de-
tentional annealing at T = 200◦ C for 1 min. A diamagnetic back- pendence in ion milled samples using 4 keV Ar+ .
ground has been subtracted from the data shown. A paramagnetic
Figure 5a shows the relative percentage-depth profile
background has been subtracted from the data shown in panels
(a)–(c). of Mn, O, Ga, and As for the as-grown part. Even
prior to sputtering, As (Ga) 2p lines are detected.
This does not necessarily indicate As (Ga) diffusion
that the former has a smaller low-temperature satu- and is, most probably, due to the fact that the Mn film
rated moment compared to the latter. Figure 3b and c
shows the magnetization (M) of the bilayer structure
as a function of the applied magnetic field (H) after
the samples are cooled to the measuring temperature
(T = 10 K) in the presence of an external magnetic
field of 1 kOe. Figure 3b shows the magnetization
of an indium-free part of the wafer. The magnetiza-
tion curve is symmetric about zero applied field, in-
dicating absence of exchange bias. Figure 3c shows
a shifted hysteresis loop measured for an indium-
mounted portion of the sample. Finally, Fig. 3d shows
a hysteresis loop of an indium-free portion of the
sample that was intentionally annealed at 200◦ C for
1 min. The center of the hysteresis loop is also shifted
from zero. These results clearly demonstrate that an-
nealing is necessary to create exchange bias in the
Mn/Ga1−x Mnx As bilayer structures.
To further understand these results, we per-
form detailed XPS studies on the indium-free por-
tion of the wafer. We study the as-grown sample, as Fig. 4. The Mn 2p spectra acquired at the surface for the
well as pieces that are annealed for 1 min at 200◦ C (a) annealed and (b) as-grown In-free parts of the Mn/
and 250◦ C. Since qualitatively similar spectra were Ga1−x Mnx As heterostructure.

Annealing Dependence of Exchange Bias in MnO/Ga1−x Mnx As 425

centration after 250 s. A larger O content is present
with O being more uniformly distributed with an
O/Mn ratio of ∼1. Thus, the Mn film is more sig-
nificantly oxidized upon annealing. We furthermore
conclude that oxidation results in the expansion of
the crystal lattice (∼1.8 times assuming complete
conversion of Mn0 to MnO). Since the MnO film is
thicker, we do not see As (Ga) lines when the top
layers are studied.
This interpretation is further supported
if we consider Mn 2p lines as a function of
depth (Fig. 6). The Mn 2p3/2 line from the
annealed sample is characteristic for MnO. Its posi-
tion and shape remains constant and only the inten-
sity decreases due to a decrease in Mn content. Thus,
the annealed film is nearly uniformly oxidized with

Fig. 5. Relative concentration as a function of depth of Mn, O, As,
and Ga in the (a) as-grown and (b) annealed indium-free parts of
a Mn/Ga1−x Mnx As heterostructure. The nominal thickness of Mn
deposition is 8 nm.

thickness is comparable to the probing depth. The
data show that the As (Ga) content increases with
depth, while the Mn content decreases. The change is
linear and the content becomes constant after 150 s,
indicating the depth of the Ga1−x Mnx As interface. A
Significant amount of O is present close to the surface
with an O/Mn ratio of approximately 1. However, O
content drops rapidly with depth, and only traces are
present after 100 s with the O/Mn ratio consistently
less than 1/3. This suggests that only the top portion
of the film is oxidized and metallic Mn0 is present
closer to the Ga1−x Mnx As interface.
Figure 5b illustrates the relative percentage-
depth profile for the annealed piece of the indium-
free mounted sample. In contrast to the as-grown
part, we do not detect As (Ga) lines prior to sput-
tering, and the As (Ga) traces become evident only Fig. 6. The Mn 2p spectra acquired at the different depths
after sputtering for 100 s. This is followed by a linear for (a) annealed and (b) as-grown indium-free piece of a
change in content, and finally a stabilization in con- Mn/Ga1−x Mnx As heterostructure.


MnO being the dominant form of Mn throughout the REFERENCES
whole layer. In contrast, the Mn 2p3/2 line from the
as-grown part exhibits a low energy shoulder after 1. H. Ohno, in Semiconductor Spintronics and Quantum Com-
60 s and shifts to 639 eV after 90 s. Satellite lines putation, D. D. Awschalom, D. Loss, and N. Samarth, eds.
(Springer-Verlag, Berlin, 2002), p. 1.
also disappear at this point. This clearly indicates 2. S. A. Wolf, D. D. Awschalom, R. A. Buhrman, J. M.
that while the surface layers of the as-grown part Daughton, S. von Molnar, M. L. Roukes, A. Y. Chtchelka-
are oxidized, metallic Mn dominates in the bottom nova, and D. M. Treger, Science 294, 1488 (2001).
3. H. Ohno, D. Chiba, F. Matsukura, T. Omiya, E. Abe, T. Dietl,
layers. Y. Ohno, and K. Ohtani, Nature 408, 944 (2000).
4. Y. Ohno, D. K. Young, B. Beschoten, F. Matsukura, H. Ohno,
and D. D. Awschalom, Nature 402, 790 (1999).
5. M. Tanaka and Y. Higo, Phys. Rev. Lett. 87, art. no. (2001).
4. CONCLUSIONS 6. S. H. Chun, S. J. Potashnik, K. C. Ku, P. Schiffer, and N.
Samarth, Phys. Rev. B 66, 100408(R) (2002).
7. L. Thomas, J. Luning, A. Scholl, F. Nolting, S. Anders, J.
In summary, we have demonstrated that epitaxi- Stohr, and S. Parkin, Phys. Rev. Lett. 84, 3462 (2000).
ally grown Mn/Ga1−x Mnx As heterostructures do not 8. K. Nagasaka, Y. Seyama, L. Varga, Y. Shimizu, and A.
Tanaka, J. Appl.Phys. 89, 6943 (2001).
exhibit any exchange bias until the Mn layer has been ´
9. J. Nogues and I. Schuller, J. Magn. Magn. Mater. 192, 203
completely oxidized into MnO by thermal annealing (1999).
in air. XPS measurements as a function of depth show 10. K. F. Eid, M. B. Stone, K. C. Ku, O. Maksimov, P. Schiffer, N.
Samarth, T. C. Shih, and C. J. Palmstrom, Appl. Phys. Lett. 85,
that the as-grown Mn layer oxidizes partially into 1556 (2004). Also K. F. Eid, M. B. Stone, O. Maksimov, T. C.
MnO upon exposure to air, with some metallic Mn Shih, K. C. Ku, W. Fadgen, C. J. Palmstrom, P. Schiffer, and
regions close to the Mn/Ga1−x Mnx As interface, as N. Samarth, J. Appl. Phys. 97, 10D304 (2005).
11. X. Jin, Y. Chen, X. Lin, D. Dong, Y. Chen, M. Xu, W. Zhu, X.
well as some regions of Mn2 O3 at the surface. Rapid Wang, X. Shen, and L. Li, Appl. Phys. Lett. 70, 2445 (1997).
thermal annealing to ∼200◦ C completely converts 12. J. L. Hilton, B. D. Schultz, S. McKernan, and C. J. Palmstrøm,
the Mn layer into MnO, creating an exchange-biased Appl. Phys. Lett. 84, 3145 (2004).
13. T. Sadowski, J. Domagala, J. Bak-Misiuk, S. Kolesnik, K.
system. Swiatek, J. Kanski, and L. Ilver, Thin Solid Films 367, 165
(2000).
14. R. J. Iwanowski, M. H. Heinonen, and E. Janik, Chem. Phys.
Lett. 387, 110 (2004).
ACKNOWLEDGMENTS 15. F. Muller, R. de Masi, D. Reinicke, P. Steiner, S. Hufner, and
K. Stowe, Surface Sci. 520, 158 (2002).
16. S. P. Jeng, R. J. Lad, and V. E. Henrich, Phys. Rev. B 43, 11971
The research has been supported by DARPA/ (1991).
ONR under grants N00014-99-1093, and -00-1-0951, 17. S. A. Chambers and Y. Liang, Surface Sci. 420, 123 (1999).
by ONR N00014-99-1-0071 and by NSF DMR 01- 18. M. A. Stranick, Surface Sci. Spectra 6, 31 (1999).
19. M. A. Stranick, Surface Sci. Spectra 6, 39 (1999).
01318. We thank Dr Shallenberger for useful discus- 20. M. C. Militello and S. W. Gaarenstroom, Surface Sci. Spectra
sions and assistance with XPS measurements. 8, 200 (2001).

Annealing Dependence of Exchange Bias in MnO/Ga1−xMnxAs Heterostructures

More Related Content

What's hot

Similar to Annealing Dependence of Exchange Bias in MnO/Ga1−xMnxAs Heterostructures

More from Oleg Maksimov

Recently uploaded

Annealing Dependence of Exchange Bias in MnO/Ga1−xMnxAs Heterostructures