Film Structures of Fe/B-doped Carbon/Fe3Si Spin Valve ... · Film Structures of Fe/B-doped...
Transcript of Film Structures of Fe/B-doped Carbon/Fe3Si Spin Valve ... · Film Structures of Fe/B-doped...
Film Structures of Fe/B-doped Carbon/Fe3Si Spin Valve Junctions
Kazuki Kudo1, Kazutoshi Nakashima1, Satoshi Takeichi1, Rezwan Ahmed2, Seigi Mizuno2, Ken-ichiro Sakai3*, Masahiko Nishijima4, and Tsuyoshi Yoshitake1**
1 Department of Applied Science for Electronics and Materials, Kyushu University, Kasuga,
Fukuoka 816-8580, Japan 2 Department of Molecular and Material Sciences, Kyushu University, Kasuga,
Fukuoka 816-8580, Japan 3 Department of Control and Information Systems Engineering, National Institute of
Technology, Kurume College, Kurume, Fukuoka 830-8555, Japan 4 The Electron Microscopy Center, Technology Center for Research and Education
Activities, Tohoku University, Sendai, Miyagi 980-8577, Japan
E-mail: *[email protected]; **[email protected]
(Received January 24, 2017)
Fe/B-doped carbon/Fe3Si trilayered films were prepared on Si(111) substrates by physical vapor
deposition with a mask method, and the film-structures and magnetic properties of the films were
investigated. The Fe3Si and Fe layers were deposited by facing targets direct-current sputtering
(FTDCS), and the B-doped carbon layers were deposited by coaxial arc plasma deposition (CAPD)
with B-blended graphite targets. Here, since the B-doped carbon layers were deposited by CAPD
in the same manner as the deposition of B-doped ultrananocrystalline diamond/hydrogenated
amorphous carbon composite (UNCD/a-C:H) films, the interlayers should be B-doped UNCD/a-
C:H. The formation of a layered structure was confirmed by transmission electron microscopy
(TEM). The diffusion of Fe and Si atoms into the interlayer occurs in the range of several
nanometers. The shape of the magnetization curve has clear steps that evidently indicate the
formation of antiparallel alignment of magnetizations owing to the difference in the coercive forces
between the top Fe and bottom Fe3Si layers. It was experimentally demonstrated that B-doped
UNCD/a-C:H is applicable to Fe-Si system spin valves as interlayer materials.
1. Introduction
Spintronics devices that utilize both electric charge and spin of electrons have actively been studied.
Giant magnetoresistance (GMR) [1,2] and tunnel magnetoresistance (TMR) [3-8] effects are
representative phenomena utilizing the spin-dependent scattering of carriers.
Whereas GMR and TMR films employ nonmagnetic metal and insulator as interlayers,
respectively, there have been a few studies on spintronics devices comprising semiconductors. Spin
injection from ferromagnetic materials into semiconductors such as Si, Ge and GaAs, has been
widely investigated thus far [9-14]. Recently, spin injection into semiconducting graphene has
received much attention because of a long spin diffusion length being expected due to weak spin-
orbit interactions [15-17].
Our laboratory has structurally and electrically investigated ultrananocrystalline diamond
(UNCD)/hydrogenated amorphous carbon (a-C:H) composite (UNCD/a-C:H) films, comprising a
large number of nano-sized diamond grains and an a-C:H matrix, prepared by coaxial arc plasma
deposition (CAPD), thus far [18-22]. The UNCD/a-C:H films prepared by CAPD have the following
characteristics: (i) the production of p and n-type conduction accompanied by enhanced electrical
conductivities is possible by B and N doping, respectively; (ii) they can be grown on foreign solid
substrates; (iii) they can be grown at low substrate temperatures even on unheated substrates, while
JJAP Conf. Proc. , 011502 (2017) https://doi.org/10.7567/JJAPCP.5.0115025Proc. Asia-Pacific Conf. on Semiconducting Silicides and Related Materials 2016
© 2017 The Author(s). Content from this work may be used under the terms of the .Any further distribution of this work must maintain attribution to the author(s) and the title of the work, journal citation and DOI.
Creative Commons Attribution 4.0 license
chemical vapor deposition (CVD) requires high substrate temperatures of more than 700 °C for the
growth [23,24]. UNCD/a-C:H is a carbon-based semiconductor similarly to graphene, and it is a new
candidate as spin transport materials.
We have studied Fe-Si based artificial lattices and spin valves comprising ferromagnetic Fe3Si
and semiconducting FeSi2, prepared by sputtering, thus far [25-36]. Based on the preparation
techniques in our previous researches, spin valve junctions comprising ferromagnetic Fe3Si and Fe
layers and B-doped UNCD/a-C:H interlayers were prepared, and they were structurally investigated
by transmission electron microscopy (TEM). We report that it is possible for layered structures to be
formed owing to the low substrate temperature growth of B-doped UNCD/a-C:H interlayers.
2. Experimental methods
Fe (100 nm)/B-doped ultrananocrystalline diamond (10 nm)/Fe3Si (100 nm) trilayered spin valve
junction were deposited on p-type Si(111) substrates by a mask method, as shown in Fig. 1(a). First,
the Si(111) substrate with specific resistance range of 30008000 cm, produced by a floating zone
(FZ) method, was cleaned with 1 hydrofluoric acid and rinsed in deionized water before it was set
into the vacuum chamber of a facing target direct-current sputtering (FTDCS) apparatus. The bottom
Fe3Si layer (100 nm) was deposited on the Si(111) substrate at an Ar pressure of 1.33 101 Pa and
substrate temperature of 300 °C, by FTDCS using the 1st mask. Subsequently, after the exposure to
air for the mask exchange, the UNCD/a-C:H interlayer (10 nm) was deposited with the 2nd mask at
a H2 pressure of 53.3 Pa and substrate temperature of 300 °C by CAPD with a 10 at.% B-blended
graphite target. After the exposure to air for the mask exchange again, the top Fe layer (100 nm) was
deposited with the 3rd mask at an Ar pressure of 1.33 101 Pa and room temperature by FTDCS
apparatus. The optical top-view image of the resultant junction is shown in Fig. 1(b). The B content
of the UNCD/a-C:H interlayer was estimated to approximately 5 at. % from the X-ray photoemission
spectra. The microstructure of the trilayered films were structurally observed by TEM combined with
energy dispersive X-ray (EDX) spectroscopy. The magnetization curves of the junctions were
measured at room temperature using a vibrating sample magnetometer (VSM).
3. Results and discussion
Figure 2 shows the XRD pattern of the junction, measured in 2θ-θ. The junction exhibit diffraction
Fig. 1. (a) Schematic diagram of deposition procedure of spin valve junction comprising Fe3Si, B-doped
UNCD/a-C:H, and Fe trilayers and (b) optical top-view image of the spin valve junction.
(a) (b)
Fe3Si Fe
UNCD
011502-2JJAP Conf. Proc. , 011502 (2017) 5
peaks of Fe3Si-222 and Fe-110 and 200. In our previous study, we confirmed that Fe3Si oriented
grains are also in-plane ordered on Si(111) substrates, by X-ray diffraction (XRD) [35,36]. From a
pole figure pattern concerning the Fe3Si-422 plane with a rotation axis of Fe3Si [222], the in-plane
orientation of the Fe3Si layer was confirmed. Totally considering this results and our previous
research results [26], the bottom Fe3Si layer is epitaxially grown on the Si(111) substrate. Since the
top Fe layer exhibits Fe-110 and 220 peaks and it is deposited on the non-oriented UNCD/a-C:H
layer, the Fe layer should be non-oriented polycrystalline. Here, the Fe-110 peak might be buried in
the background pattern of the Si substrate.
Figure 3(a) shows the cross-sectional high-angle annular dark field scanning transmission
electron microscopic (HAADF-STEM) image of the junction. A trilayered structure is certainly
formed, in other words, the UNCD/a-C:H layer structurally acts as an interlayer that clearly separates
the top Fe layer from the bottom Fe3Si layer. Figure 3(b) shows a bright-field scanning transmission
electron microscopic (BF-STEM) image of an Fe3Si/Si(111) interface in the junction. The interface
is not sharp in atomic scale, which might be because of atomic interdiffusion induced by the
bombardment of sputtering species and the HF pretreatment of the Si substrate was imperfectly made.
Fig. 2. XRD pattern of junction comprising Fe, B-doped UNCD/a-C:H, and Fe3Si
layers, measured in 2θ-θ.
(a) (b)
Fig. 3. (a) Cross-sectional HAADF-STEM image of trilayered junction and (b) BF-
STEM image of interface between Fe3Si bottom-layer and B-doped UNCD/a-C:H
interlayer in the junction.
011502-3JJAP Conf. Proc. , 011502 (2017) 5
From the electron diffraction pattern, the epitaxial growth of the Fe3Si layer on the Si(111) substrate
was confirmed, as expected from the XRD measurement results. This is consistent with results in our
previous research, wherein Fe3Si thin films are epitaxially grown on Si(111) substrate even at room
temperature [26]. The cross-sectional HAADF-STEM image of a magnified area around the interlayer of the
junction and the EDX profile of C, O, Si, and Fe in the depth direction are shown in Fig. 4(a) and
4(b), respectively. The STEM image of the interlayer can be divided into three areas. At the side
areas of A and B, O atoms preferentially exist, which means that the interfaces are oxidized due to temporal exposures to air for the replacements of the masks. Additionally, C, Si, and Fe atoms coexist in
the areas of A and B. This is because of the diffusions of Fe and Si atoms into the interlayer. Surprisingly,
the center area between the A and B areas hardly contains all atoms. The TEM observation sample was
prepared by a focused ion beam (FIB) apparatus. As a probable reason for it, we consider that the center
C-rich areas were preferentially etched away by Ga ions bombardment during the FIB process. Since the
interlayer exists in layer structure, the UNCD/a-C:H layer should have been present before the FIB etching.
The magnetization curve of the junction measured at room temperature is shown in Fig. 5. The
magnetization curve has clear two steps that indicate the antiparallel alignment formation of
(a)
(b)
Fig. 4. (a) Cross-sectional HAADF-STEM image and (b) EDX profiles of C, O, Si, and Fe corresponding
to the depth direction in the STEM image.
57.5
C
O
Si
Fe
0Distance (nm)
Fe3Si layer Fe layerAB
011502-4JJAP Conf. Proc. , 011502 (2017) 5
magnetizations owing to the difference in the coercive forces between the top Fe and the bottom
Fe3Si layers. The polycrystalline Fe layer has a larger coercive force than that of the epitaxial Fe3Si
layer [37]. The spin valve behavior is realized, which proves that the UNCD/a-C:H layer act as an
interlayer for the spin valve action.
4. Conclusion
Trilayered junctions comprising Fe, B-doped UNCD/a-C:H, and Fe3Si layers were prepared on
Si(111) substrates by physical vapor deposition combined with a mask method, and the film-
structures and magnetic properties were investigated. The TEM observation revealed that the
interlayer exists in layered structure and it contains oxidized layers at interfaces with ferromagnetic
layers due to the exposure to air for the replacements of the masks. From the shape of the
magnetization curve, the formation of antiparallel alignment of magnetizations owing to the
difference in the coercive forces between the top Fe and bottom Fe3Si layers were confirmed. It was
experimentally demonstrated that UNCD/a-C:H is applicable to Fe-Si system spin valves as
interlayer materials although the diffusion of Si and Fe atoms from the ferromagnetic layers into the
interlayer occurs in the range of several nanometers.
Acknowledgment
This work was partially supported by JSPS KAKENHI Grant Number JP16K14391, JP15K21594,
Yoshida Grant from Yoshida Academic Education Promotion Association, and Tohoku University
Advanced Characterization Nanotechnology Platform in Nanotechnology Platform Project
sponsored by the Ministry of Education, Culture, Sports, Science and Technology (MEXT), Japan.
References
[1] G. Binasch, P. Grunberg, F. Saurenbach, and W. Zinn, Phys. Rev. B 39, 4828 (1989).
[2] M. N. Baibich, J. M. Broto, A. Fert, F. Nguyen Van Dau, F. Petroff, P. Etienne, G. Creuzet, A. Friederich,
and J. Chazelas, Phys. Rev. Lett. 61, 2472 (1988).
[3] M. Julliere, Phys. Lett. 54A, 225 (1975).
[4] S. Maekawa, and U. Gafvert, IEEE Trans. Magn. 18, 707 (1982).
[5] T. Miyazaki and N. Tezuka, J. Magn. Magn. Mater. 139, L231 (1995).
[6] J. S. Moodera, L. R. Kinder, T. M. Wong, and R. Meservey, Phys. Rev. Lett. 74, 3273 (1995).
Fig. 5. Magnetization curve of junction, measured at room temperature.
–20 0 20
–1
0
1
Magnetic field (Oe)
M/M
s
UNCD (10 nm)
Fe3Si (100 nm)
Fe (100 nm)
011502-5JJAP Conf. Proc. , 011502 (2017) 5
[7] S. Yuasa, T. Nagahama, A. Fukushima, Y. Suzuki, and K, Ando, Nat. Mater. 3, 868 (2004).
[8] S. S. P. Parkin, C. Kaiser, A. Panchula, P. M. Rice, B. Hughes, M. Samant, and S. H. Yang, Nat. Mater. 3,
862 (2004).
[9] I. Appelbaum, B. Huang, and D. J. Monsma, Nature 447, 295 (2007).
[10] B. Huang, D. J. Monsma, and I. Appelbaum, Phys. Rev. Lett. 99, 177209 (2007).
[11] B. T. Jonker, G. Kioseoglou, A. T. Hanbicki, and C. H. Li, Nat. Phys. 3, 542 (2007).
[12] Y. Ando, K. Kasahara, K. Yamane, K. Hamaya, K. Sawano, T. Kimura, and M. Miyao, Appl. Phys.
Express 3, 093001 (2010).
[13] K. Kasahara, Y. Fujita, S. Yamada, K. Sawano, M. Miyao, and K. Hamaya, Appl. Phys. Express 7, 033002
(2014).
[14] X. Lou, C. Adelmann, S. A. Crooker, E. S. Garlid, J. Zhang, K. S. M. Reddry, S. D. Flexner, C. J.
Palmstorm, and P. A. Crowell, Nat. Phys. 3, 197 (2007).
[15] M. Ohishi, M. Shiraishi, R. Nouchi, T. Nozaki, T. Shinjo, and Y. Suzuki, Jpn. J. Appl. Phys. 46, L605
(2007).
[16] D. Huertas-Hernando, F. Guinea, and A. Brataas, Phys. Rev. Lett. 103, 146801 (2009).
[17] V. K. Dugaev, E. Y. Sherman, and J. Barna´s, Phys. Rev. B 83, 085306 (2011).
[18] T. Yoshitake, A. Nagano, M. Itakura, N. Kuwano, T. Hara, and K. Nagayama, Jpn. J. Appl. Phys. 46, L936
(2007).
[19] T. Yoshitake, Y. Nakagawa, A. Nagano, R. Ohtani, H. Setoyama, E. Kobayashi, K. Sumitani, Y. Agawa,
and K. Nagayama, Jpn. J. Appl. Phys. 49, 015503 (2010).
[20] S. Ohmagari, T. Yoshitake, A. Nagano, R. Ohtani, H. Setoyama, E. Kobayashi, T. Hara, and K. Nagayama,
Jpn. J. Appl. Phys. 49, 031302 (2010).
[21] S. Ohmagari and T. Yoshitake, Jpn. J. Appl. Phys. 51, 090123 (2012).
[22] Y. Katamune, S. Ohmagari, S. Al-Riyami, S. Takagi, M. Shaban, and T. Yoshitake, Jpn. J. Appl. Phys. 52,
065801 (2013).
[23] S. Bhattacharyya, O. Auciello, J. Birrell, J. A. Carlisle, L. A. Curtiss, A. N. Goyette, D. M. Gruen, A. R.
Krauss, J. Schlueter, A. Sumant, and P. Zapol, Appl. Phys. Lett. 79, 1441 (2001).
[24] C. Popov, W. Kulisch, S. Boycheva, K. Yamamoto, G. Ceccone, and Y. Koga, Diamond Relat. Mater. 13,
2017 (2004).
[25] T. Yoshitake, T. Ogawa, D. Nakagauchi, D. Hara, M. Itakura, N. Kuwano, and Y. Tomokiyo, Appl. Phys.
Lett. 89, 253110 (2006).
[26] K. Takeda, T. Yoshitake, D. Nakagauchi, T. Ogawa, D. Hara, M. Itakura, N. Kuwano, Y. Tomokiyo, T.
Kajiwara, and K. Nagayama, Jpn. J. Appl. Phys. 46, 7846 (2007).
[27] K. Takeda, T. Yoshitake, Y. Sakamoto, T. Ogawa, D. Hara, M. Itakura, N. Kuwano, T. Kajiwara, and K.
Nagayama, Appl. Phys. Express 1, 021302 (2008).
[28] S. Hirakawa, T. Sonoda, K. Sakai, K. Takeda, and T. Yoshitake, Jpn. J. Appl. Phys. 50, 08JD06 (2011).
[29] K. Sakai, T. Sonoda, S. Hirakawa, K. Takeda, and T. Yoshitake, Jpn. J. Appl. Phys. 51, 028004 (2012).
[30] K. Sakai, Y. Noda, K. Takeda, M. Takeda, and T. Yoshitake, Phys. Status Solidi C 10, 1862 (2013).
[31] K. Sakai, Y. Noda, D. Tsumagari, H. Deguchi, K. Takeda, and T. Yoshitake, Phys. Status Solidi A 211,
323 (2014).
[32] K. Sakai, Y. Noda, T. Daio, D. Tsumagari, A. Tominaga, K. Takeda, and T. Yoshitake, Jpn. J. Appl. Phys.
53, 02BC15 (2014).
[33] K. Sakai, Y. Asai, M. Takeda, K. Ishibashi, Y. Noda, K. Takeda, and T. Yoshitake, JJAP Conf. Proc. 3,
011503 (2015).
[34] K. Sakai, Y. Asai, Y. Noda, T. Daio, A. Tominaga, K. Takeda, and T. Yoshitake, JJAP Conf. Proc. 3,
011502 (2015).
[35] Y. Asai, K. Sakai, K. Ishibashi, K. Takeda, and T. Yoshitake, JJAP Conf. Proc. 3, 011501 (2015).
[36] Y. Asai, K. Sakai, K. Ishibashi, K. Takeda, and T. Yoshitake, JJAP Conf. Proc. 3, 011504 (2015).
[37] K. Ishibashi, K. Nakashima, K. Sakai, and T. Yoshitake, APS Conf. Proc., 2015, GT1.00151.
011502-6JJAP Conf. Proc. , 011502 (2017) 5