Upload
independent
View
0
Download
0
Embed Size (px)
Citation preview
1 23
Journal of Materials ScienceFull Set - Includes `Journal of MaterialsScience Letters' ISSN 0022-2461Volume 47Number 8 J Mater Sci (2012) 47:3658-3662DOI 10.1007/s10853-011-6212-2
Fabrication conditions and transformationbehavior of epitaxial Ni–Mn–Ga thin films
I. R. Aseguinolaza, I. Orue, A. V. Svalov,V. A. Chernenko, S. Besseghini &J. M. Barandiarán
1 23
Your article is protected by copyright and
all rights are held exclusively by Springer
Science+Business Media, LLC. This e-offprint
is for personal use only and shall not be self-
archived in electronic repositories. If you
wish to self-archive your work, please use the
accepted author’s version for posting to your
own website or your institution’s repository.
You may further deposit the accepted author’s
version on a funder’s repository at a funder’s
request, provided it is not made publicly
available until 12 months after publication.
Fabrication conditions and transformation behavior of epitaxialNi–Mn–Ga thin films
I. R. Aseguinolaza • I. Orue • A. V. Svalov •
V. A. Chernenko • S. Besseghini • J. M. Barandiaran
Received: 2 November 2011 / Accepted: 14 December 2011 / Published online: 28 December 2011
� Springer Science+Business Media, LLC 2011
Abstract Epitaxial Ni–Mn–Ga films have been grown
onto heated substrates by sputtering. Their chemical compo-
sition depends on the sputtering argon pressure. Represen-
tative epitaxial films of Ni52.3Mn26.8Ga20.9, 0.5 lm-thick,
transform martensitically at about 120 �C, accompanied by
sharp changes in the lattice parameter and resistivity, and
orders ferromagnetically below 98�. The observed high
transformation temperature, orthorhombic martensitic
structure, twinning mode and film morphology, indicate a
potential multifunctional behavior of the film, such as
high-temperature shape-memory effect and magnetic field
actuation.
Introduction
Ferromagnetic shape memory alloys (FSMAs), such as the
off-stoichiometric Ni–Mn–Ga Heusler compounds, are
subject of a continuing intense research, because of the
interesting underlying physics and potential applications.
The FSMAs exhibit a giant recoverable strain of about 10%
(that can be induced by temperature, mechanical stress, and
magnetic field) alongside remarkable magnetocaloric,
magnetoresistance and damping characteristics [1–3]. The
ferromagnetic ordering and martensitic transformation
(MT) are the fundamental ingredients governing these
outstanding properties.
In view of the large energy per mass rate, thin-film
technology has been already probed to obtain the best of
the properties of FSMAs on (nano-)microscale [4–14]. In
fact, both grain-textured and epitaxially grown single
crystalline Ni–Mn–Ga thin films, in a free-standing and/or
attached-to-the-substrate form, revealed expected func-
tionality [6–12]. Incidentally, magnetic field-induced strain
activation was possible owing to reduced internal geo-
metrical constraints in thin film samples where grain size is
comparable to plate thickness [4, 6, 11].
Thin-film technology of FSMAs is still under develop-
ment. In order to meet application conditions, one should
control crystal structure, crystallographic orientation, and
twinning substructure of the films alongside the transfor-
mation behaviour and magnetic properties. All these
characteristics depend on the constraints from substrate,
film thickness, and thermal treatment. For any technical
application, it is essential that the films display ferromag-
netism and martensitic structure at room temperature.
Magnetron sputtering has proved to be the most suitable
technique to fabricate Ni–Mn–Ga/substrate thin films. By
this technique, epitaxial growth has been achieved onto some
appropriate substrates, e.g., MgO(001) [5–14]. Alongside
the target composition, substrate type and temperature, the
sputtering power and argon pressure were reported to be the
significant factors in controlling properties of films deposited
onto cold substrates [15, 16]. In particular, the influences of
sputtering power on the transformation temperatures and
structure of martensitic phase in polycrystalline Ni–Mn–Ga
I. R. Aseguinolaza � A. V. Svalov � V. A. Chernenko (&) �J. M. Barandiaran
Departamento de Electricidad y Electronica, Universidad
del Paıs Vasco, P.O. Box 644, 48080 Bilbao, Spain
e-mail: [email protected]
I. Orue
SGiker, Vicerrectorado de Investigacion UPV/EHU,
Sarriena s/n, 48940 Leioa, Spain
V. A. Chernenko
Ikerbasque, Basque Foundation for Science, 48011 Bilbao, Spain
S. Besseghini
CNR-IENI, 23900 Lecco, Italy
123
J Mater Sci (2012) 47:3658–3662
DOI 10.1007/s10853-011-6212-2
Author's personal copy
films are explained by the variation of composition and the
corresponding valence electron concentration in the multi-
component alloy [15, 17]. In the case of Ni–Mn–Ga films
epitaxially grown on heated substrates, further advancement
needs also a detailed study of the influence of sputtering
parameters on their properties.
In this study, we report the preparation of epitaxial
Ni–Mn–Ga films by magnetron sputtering to address how
the composition and transformation behavior of the films
depend on the preparation parameters. We show that the
film composition and the related transformation behavior
are mainly controlled by the Ar pressure. The results of
extensive measurements of physical properties of a repre-
sentative film are presented to demonstrate its potential for
magnetic and high-temperature actuations.
Experimental
Thin films have been deposited by DC magnetron sput-
tering, using a Pfeiffer Vacuum Classic 500 station. Tar-
gets of Ni49.9Mn27.8Ga22.3 (at.%), each having the electron
concentration e/a = 7.61, were fabricated by a plasma-
melting technique and by subsequent spark-cutting the
ingot into disks of 50-mm diameter and 3-mm thickness.
The targets displayed the MT at 25 �C and the Curie
temperature, (TC), at 88 �C with few degrees of variation
across the target. Deposition parameters, such as sputtering
power and Ar pressures varied from 50 to 200 W and from
2.8 9 10-3 to 2.6 9 10-2 mbar, respectively. The base
pressure was always 4.1 9 10-7 mbar and the target-sub-
strate distance was 9 cm. Single crystalline plates of
MgO(001) were used as substrates. They were held either
at room temperature (RT), 400 �C or 500 �C during the
deposition. The RT and 400 �C deposited films were sub-
jected to subsequent annealing to obtain more ordered
structures. The thickness of the films was fixed at 0.5 lm.
Compositions of the target and films were determined
with an accuracy better than 0.5 at.% by energy-dispersive
X-ray spectroscopy (EDX), using a SEM (scanning elec-
tron microscope) Jeol JSM-6400. SEM was also used for
the microstructure observations in the secondary electron
mode [18].
Crystal structure of the thin films was examined by
X-ray diffraction (Philips X0Pert PRO), using CuKa radi-
ation. Diffractograms were taken at 35 different tempera-
tures from 30 to 200 �C, with a heating step of 5 �C. The
uncertainty in the relative change of lattice spacing was
better than 5 9 10-5nm.
Magnetic measurements were carried out in a vibrating
sample magnetometer recording in-plane and out-of-plane
hysteresis loops, M(H), in fields up to 1.8 T at RT, as well
as the temperature dependence of magnetization, M(T). In
the latter case, the applied magnetic field was 0.05 T, and
the temperature was varied from –120 to ?120 �C.
Electric resistivity, R(T), was measured in the temper-
ature range from 0 to 200 �C, at a rate of 1 �C/min, in the
four-probe configuration by using an in-house made set-up
with a temperature sensor in direct contact with the sample.
Results and discussion
Influence of substrate temperature and post-deposition
annealing
Depositions made at temperatures up to 400 �C resulted in
films showing typical features of magnetically and struc-
turally disordered compounds. To promote atomic order-
ing, a 500 �C post-deposition annealing was done, whereby
films showed ferromagnetism together with a certain
paramagnetic contribution as demonstrated by the pres-
ence of large slopes in the hysteresis loops at high fields.
Two TC, of about -10 and 60 �C, were detected in the
M(T) curve (not shown), presumably related to two dif-
ferent phases. A 700 �C annealing did not lead to any
improved properties either, showing even stronger para-
magnetic contribution at RT and a low TC (&-30 �C).
On the other hand, the depositions at 500 �C produced
highly ordered single-phase films, so that no additional heat
treatment was needed. Thus, all subsequent depositions
were made at this temperature.
Influence of Ar pressure and deposition power
Several series of films with different deposition pressure
have been fabricated, keeping other parameters constant.
Among them, a series of the three samples grown onto
heated MgO wafers, using 200 W power and Ar pressures
of 2.8 9 10-3, 1.1 9 10-2, and 2.6 9 10-2 mbar (films 1,
2, and 3, respectively) was the most indicative.
Figure 1 shows that the composition of the epitaxial
films depends on Ar pressure, and suffers a considerable
and systematic shift from the target one, enriching in Ni
and losing Mn and Ga. The trend shown by the experi-
mental points on the right panel of Fig. 1 can be used as a
guide for a proper calibration and control of the film
composition by sputtering.
Table 1 shows that the evolution of the TC versus
electron concentration follows the well-known general
trend, increasing as e/a decreases, although the absolute
values of TC deviate from those of the bulk [17]. The sat-
uration magnetization value is above 50 emu/g for films 2
and 3, which is close to the previous results [5]. However,
it is much smaller for film 1, pointing to its less homoge-
neous state in this case.
J Mater Sci (2012) 47:3658–3662 3659
123
Author's personal copy
The effect of sputtering power on the film composition
in the case of epitaxial growth was marginal comparatively
to Ar pressure, therefore, 150 W power was selected in all
further experiments as a technically optimal value.
Crystal structure and morphology
Hereafter we will focus on the results obtained on the
representative 0.5 lm-thick film of Ni52.3Mn26.8Ga20.9,
epitaxially grown on MgO(001), heated at 500 �C under
2.6 9 10-2 mbar pressure and 150 W power. The electron
concentration of this film, e/a = 7.73, is almost identical to
film 3 and belongs to the TC * TM zone (Fig. 1), which is
interesting for applications [19].
X-ray diffraction pattern of the film shows only one
single peak at 2h = 63.5�, which indicates a preferential
lattice orientation with the h100i axis along the film nor-
mal. Temperature-induced changes in the position and
intensity of this peak are depicted in Fig. 2, and unequiv-
ocally indicate a transformation from the cubic to the
martensitic phase. The value of lattice parameter (5.83 A)
and its small change when the sample transforms into cubic
phase (about 0.3%, Fig. 2) suggests that it corresponds to
the lattice parameter b of the quasi-orthorhombic 14 M
structure, in agreement with Refs [10, 11, 20]. The thermal
expansion coefficient can be evaluated from the slope in
the martensitic and austenitic phases to be equal to
38.0 9 10-6 K-1 and 12.0 9 10-6 K-1, respectively
(cf. Ref. [8]). The role played by the differences between
the MgO substrate and the Ni–Mn–Ga films, both the in
thermal expansion and lattice constant, has been already
highlighted in the context of internal biaxial tensile stresses
measured in the film plane [10].
The local surface topography was studied by scanning
electron microscopy (SEM), secondary electrons signal, and
one of the selected areas image was shown in Ref. [18]. The
twinning pattern in the martensite reflects a well-resolved
surface relief, and the twin boundaries aligned along or
perpendicular to h110iMgO directions confirm a quasi-single
crystalline nature of the film (in austenitic phase) and
the epitaxial relationship Ni–Mn–Ga(001)[110]//MgO(001)
[100] between austenite and substrate (see also [10, 11, 20]).
Fig. 1 (Color online) Leftpanel films composition as a
function of Ar pressure. Films
were deposited with 200 W on
MgO(001) heated at 500 �C.
Right panel compositions of
three films and target are shown
together with e/a isolines
providing a guide for a proper
calibration and control of the
composition by sputtering
process. TM and TC are the
martensitic and ferromagnetic
transitions temperatures,
respectively
Table 1 TC and saturation
magnetization of the films
obtained at various sputtering
Ar pressure and 200 W power
on heated (500 �C) substrate
MgO(001)
Film Argon pressure,
mbar
Composition,
at.%
e/a TC, �C TC, �C
(expected [17])
Ms, emu/g
(5 K)
1 2.8 9 10-3 Ni56.1Mn25.8Ga18.1 7.96 29 49 41
2 1.1 9 10-2 Ni54.0Mn26.4Ga19.6 7.84 44 71 54
3 2.6 9 10-2 Ni52.2Mn26.8Ga21.0 7.73 98 88 53
Fig. 2 (Color online) Temperature evolution of the lattice parameter
b and (400)-peak intensity of Ni52.3Mn26.8Ga20.9/MgO(001) film
composite during step-wise heating. Inset evidences an MT through a
conversion of (004)-peak in the cubic phase into (040)-peak in the
orthorhombic phase
3660 J Mater Sci (2012) 47:3658–3662
123
Author's personal copy
Repeated analysis of the twin morphology has forced us
to reconsider the previous description of the film micro-
structure given in Ref. [18]. X-rays measurements are
averaged along the full sample, and indicate that the b axis
of the orthorhombic structure is out of the film plane. This
means that, in average, the martensite exhibits ac twinning
in the film plane. Such a twinning implies that twin
boundaries should be perpendicular to the film plane (see
also Ref [21].) and the resulting surface topology would be
hardly resolved. On the other hand, local SEM observations
[18] show well-developed surface relief produced by out-
of-plane ac twinning in some parts of the film, indicating
that twin boundaries are aligned at 45� with respect to the
film plane (see also Ref [11].). Although this reconsidera-
tion has not impact in any deduction of Ref [18]. (the
micromagnetic structure and all the parameters of model in
Ref. [18] do not depend on the spatial coordinates), it
removes the apparent contradiction between X-rays results
and local SEM observations, by assuming a mixed type of
ac-twinning in the film with a dominance of the in-plane
orientation. Moreover, the micrograph given in Ref [18]
was useful to clarify the underlying physics of the FMR
anomalies, serving as a kind of microstructure probe.
Magnetic and resistivity measurements
The transformation and magnetic behavior of the films have
been studied by magnetization and resistivity measurements.
Typical results are shown in Fig. 3. The TC was determined
to be 98 �C. No evidences of MT appears in the M(T) curve,
because MT takes place in the paramagnetic zone. The MT
already observed by X-rays measurements are confirmed by
the large abrupt anomaly (about 25%, cf. Ref [17]) on the
resistivity curve in Fig. 3. This curve yields TM of about
120 �C and a transformation hysteresis of 8 �C. The
enhanced MT temperature and narrow temperature hyster-
esis are the prerequisites of advanced functional properties of
the studied films, such as a high-temperature shape-memory
effect.
The in-plane and out-of-plane hysteresis loops are
shown in Fig. 4. These loops show a significant difference
in the values of saturating magnetic fields. The shape
anisotropy alone is not enough to explain the difference in
saturating field. The estimated value of the shape anisot-
ropy field is about 0.5 T, whereas the actual saturating field
is about 1.1 T (Fig. 4). Thus, the difference must be
explained by the contribution of the magnetocrystalline
anisotropy of the film. This result agrees with the structural
characterization, which assumes the b axis (hard) to be out
of plane. The in-plane magnetic anisotropy was studied
in detail in Ref. [18]. The coercive field of the film was
determined from these loops as 0.02T for in-plane case,
and 0.03T for out-of-plane case. These relatively high
values of coercive field are associated with the films
imperfections, such as high-density twin boundaries, con-
strains, etc. Since the twin boundaries are fixed by the
substrate, they could only be activated by the application of
a magnetic field if the substrate is removed, and free-
standing films are produced.
Conclusions
We have found that the chemical composition of the
Ni–Mn–Ga films epitaxially grown onto MgO(001) substrates
heated at 500 �C depends mainly on the sputtering argon
pressure, enriching in Mn and Ga and depleting in Ni
Fig. 3 (Color online) Magnetization at 0.05 T and electric resistivity
as a function of temperature. The thermomagnetization curve shows
the TC. The resistivity abrupt change indicates the MT
Fig. 4 (Color online) In-plane (1) and out-of-plane (2) hysteresis
loops at room temperature
J Mater Sci (2012) 47:3658–3662 3661
123
Author's personal copy
contents as Ar pressure increases so, the transformation
behavior of the these films can be mainly tailored by
changing the Ar pressure. Deposition power in this case is
of minor influence. The relative influences of Ar pressure
and power are just opposite in the case of sputtering onto
cold substrates [15].
One of the representative Ni–Mn–Ga films epitaxially
grown on MgO(001) exhibits MT accompanied by sharp
changes in the lattice parameter and resistivity above the
TC. X-rays measurements showed an orthorhombic crystal
structure of the martensite, with the b axis out of plane,
which means, in average, ac twinning in the film plane with
boundaries perpendicular to it. Previous SEM observations
had shown evidences of out-plane-plane ac twinning as
well. Probably, a mixture of differently oriented twin
packets, with predominant in-plane ac twinning, better
represents the highly relaxed structure, self-accommodated
in the mechanical constraints imposed by the substrate. The
observed high transformation temperature and film mor-
phology are prerequisites for advanced multifunctional
behavior, such as high-temperature shape memory and
magnetic field actuation, respectively. A large resistivity
change (about 25%) measured at MT is also important, as it
can allow the sensorless mode of control for the actuation
of this film [22].
Acknowledgements The financial support from the Department of
Education, Basque Government (Project ETORTEK No. IE10-272),
and the Spanish Ministry of Science and Innovations (Project No.
MAT2008 06542-C04-02) is acknowledged. The discussions with
Prof. G. Jakob about twinning crystallography are very much appre-
ciated. Authors are very grateful to M. Pini and G.Carcano for
technical support.
References
1. Soderberg O, Ge Y, Sozinov A, Hannula S-P, Lindroos VK
(2006) In: Buschow J (ed) Handbook of magnetic materials, vol
16. Elsevier Science, Amsterdam, p 1
2. Chernenko VA (ed) (2008) Advances in shape memory materials.
Ferromagnetic shape memory alloys TTP, Zurich (Mat Sci Forum 583)
3. Nespoli A, Besseghini S, Pittaccio S, Villa E, Viscuso S (2010)
Sensors Actuat A 158:149
4. Dunand DC, Mullner P (2011) Adv Mater 23:216
5. Chernenko VA, Ohtsuka M, Kohl M, Khovailo VV, Takagi T
(2005) Smart Mater Struct 14:S245
6. Kohl M, Agarwal A, Chernenko VA, Ohtsuka M, Seemann K
(2006) Mater Sci Eng A 438–440:940
7. Kohl M, Brugger D, Ohtsuka M, Takagi T (2004) Sensor Actuat
A114:445
8. Besseghini S, Cavallin T, Chernenko V, Villa E, L’vov V, Oht-
suka M (2008) Acta Mater 56:1797
9. Khelfaoui F, Kohl M, Buschbeck J, Heczko O, Fahler S, Schultz L
(2008) Eur Phys J Special Topics 158:167
10. Thomas M, Heczko O, Buschbeck J, Schultz L, Fahler S (2008)
Appl Phys Lett 92:192515
11. Buschbeck J, Niemann R, Heczko O, Thomas M, Schultz L,
Fahler S (2009) Acta Mater 57:2516
12. Rumpf H, Feydt J, Levandovski D, Ludwig A, Winzek B, Quandt E,
Zhao P, Wuttig M (2003) Proc SPIE 5053:191
13. Jakob G, Eichhorn T, Kallmayer M, Elmers HJ (2007) Phys Rev B
76:174407
14. Recarte V, Perez-Landazabal JI, Sanchez-Alarcos V, Chernenko VA,
Ohtsuka M (2009) Appl Phys Lett 95:141908
15. Ohtsuka M, Itagaki K (2000) Int J Appl Electromagn Mech 12:49
16. Liu C, Cai W, An X, Gao LX, Gao ZY, Zhao LC (2006) Mater
Sci Eng A 986:438
17. Chernenko VA (1999) Scr Mater 40:523
18. Chernenko VA, Lvov VA, Golub V, Aseguinolaza IR, Barandi-
aran JM (2011) Phys Rev B 84:054450
19. Lanska N, Soderberg O, Sozinov A, Ge Y, Ullakko K, Lindroos VK
(2004) J Appl Phys 95:8074
20. Tillier J, Bourgault D, Pairis S, Ortega L, Caillault N, Carbone L
(2010) Phys Procedia 10:168
21. Mullner P, Chernenko VA, Kostorz G (2004) J Appl Phys
95:1531
22. Auernhammer D, Kohl M, Krevet B, Ohtsuka M (2009) Smart
Mater Struct 18:104016
3662 J Mater Sci (2012) 47:3658–3662
123
Author's personal copy