1. technology and computing

Durham
UK-India
WorkshoponMagnetisationProcesses
19th-20thMarch2015
DurhamUniversity
UKIERI
UK - India Education
and Research Initiative
Durham UK–India Workshop on Magnetisation Processes 2015
Workshop Sponsors
UKIERI
UK - India Education
and Research Initiative
This workshop is supported by the British Council through the UK-India Education and Research Initiative (UKIERI) programme, grant ref IND/CONT/E/12-13/688 ‘Nano-Engineered Magnetic Materials for Spintronic Applications’ in partnership with DST India, with additional support from Mantis
Deposition Ltd., the XMaS UK CRG Beamline, and Durham University Physics Department.
We are very grateful for the support provided for this meeting, which has enabled us to waive registration fees for attendees, provide refreshments, lunch, and a drinks reception, and host invited speakers.
Durham UK–India Workshop on Magnetisation Processes 2015
Welcome!
We warmly welcome you to the Durham UK-India Workshop on Magnetisation Processes 2015.
This is a two-day workshop on thin-film and related magnetism, supported by the British Council
through the UK-India Education and Research Initiative (UKIERI) programme in conjunction with
the Indian department of science and technology (DST). It is funded through a collaborative research
grant between the Centre for Materials Physics at Durham University and the Ultrafast Nanomagnetics
group at S.N. Bose National Center for Basic Sciences, Kolkata, India.
Our programme consists of invited presentations from early stage rising star researchers and academics
from the UK and India. The plenary speaker is Professor Anjan Barman from SN Bose National Centre for Basic Sciences, Kolkata, India. After the first afternoon of talks there is a short panel discussion, where our Indian colleagues and visitors will describe the institutional and funding structure of
research in India, followed by a reception and poster session where other attendees will present posters
describing their recent research. Friday will consist of a full day of invited talks, with continuation of
the poster session over lunch.
We hope that you enjoy your visit to Durham and the workshop, and thank you for attending!
Prof. Del Atkinson & Dr Aidan Hindmarch
Cover & logo design Mustafa Tokac¸, cover image courtesy Durham University.
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Durham UK–India Workshop on Magnetisation Processes 2015
Durham City Map
Physics Department (Rochester building): #12
St. Chad’s College: #20
Durham rail station is located top center of the image above. Walking from the rail station to the Physics
Department will typically take 20-25 minutes. A taxi will take 5-15 minutes, depending on traffic.
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Durham UK–India Workshop on Magnetisation Processes 2015
Plenary Lecture
Thursday
Prof. Anjan Barman, S.N. Bose National Center for Basic Sciences . . . . . . . . . . . . . . .
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Invited Talks
Thursday
Chair: Prof. Del Atkinson
Dr Aidan Hindmarch, Durham University . . . . . . . . . . . . . . . . . . . . . . . . . . . . 11
Dr Pranaba Kishor Muduli, Indian Institute of Technology, Delhi . . . . . . . . . . . . . . . . 12
Dr Paul Keatley, University of Exeter . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 13
Friday session 1
Chair: Prof. Brian Tanner
Dr Tom Lancaster, Durham University . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 15
Dr Jaivardhan Sinha, S.N. Bose National Center for Basic Sciences . . . . . . . . . . . . . . . 16
Dr Oscar C´espedes, University of Leeds . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 17
Dr Andrew Ferguson, University of Cambridge . . . . . . . . . . . . . . . . . . . . . . . . . 18
Friday session 2
Chair: Prof. Anjan Barman
Dr Andrew Rushforth, University of Nottingham . . . . . . . . . . . . . . . . . . . . . . . . . 19
Dr Tom Hayward, University of Sheffield . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 20
Dr Dan Read, University of Cardiff . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 21
Friday session 3
Chair: Prof. Peter Hatton
Dr Subhankar Bedanta, National Institute of Science Education and Research . . . . . . . . . 22
Dr Will Branford, Imperial College London . . . . . . . . . . . . . . . . . . . . . . . . . . . 23
Dr Stuart Cavill, University of York . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 24
Dr Damien McGrouther, University of Glasgow . . . . . . . . . . . . . . . . . . . . . . . . . 25
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Durham UK–India Workshop on Magnetisation Processes 2015
Posters
From 16:15 on Thursday in the Bransden room
P1: Andrew Caruana, Loughborough University . . . . . . . . . . . . . . . . . . . . . . . . . 29
P2: Sinan Azzawi, Durham University . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 30
P3: Stuart Bowe, University of Nottingham . . . . . . . . . . . . . . . . . . . . . . . . . . . . 31
P4: Oto-obong Inyang, Durham University . . . . . . . . . . . . . . . . . . . . . . . . . . . . 32
P5: Christy Kinane, STFC ISIS Neutron Facility . . . . . . . . . . . . . . . . . . . . . . . . . 33
P6: John Sinclair, University of York . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 34
P7: Jeovani Brand˜ao, Durham University . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 35
P8: Ioan Polenciuc, University of York . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 36
P9: Christopher Cox, Loughborough University . . . . . . . . . . . . . . . . . . . . . . . . . 37
P10: Mustafa Tokac¸, Durham University . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 38
P11: David Burn, Imperial College London . . . . . . . . . . . . . . . . . . . . . . . . . . . 39
P12: Kowsar Shahbazi, University of Leeds . . . . . . . . . . . . . . . . . . . . . . . . . . . 40
P13: Jenny King, Durham University . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 41
P14: Richard Rowan-Robinson, Durham University . . . . . . . . . . . . . . . . . . . . . . . 42
P15: Jaivardhan Sinha, S.N. Bose National Center for Basic Sciences . . . . . . . . . . . . . . 43
P16: Anjan Barman, S.N. Bose National Center for Basic Sciences . . . . . . . . . . . . . . . 44
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Durham UK–India Workshop on Magnetisation Processes 2015
Plenary Lecture
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Durham UK–India Workshop on Magnetisation Processes 2015
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Durham UK–India Workshop on Magnetisation Processes 2015
Thursday 14:00-14:45
Investigation of Spin Dynamics Using All-Optical Techniques
Anjan Barman
Department of Condensed Matter Physics and Material Sciences, S. N. Bose National Centre
for Basic Sciences, Block JD, Sec. III, Salt Lake, Kolkata 700 098, India
abarman@bose.res.in
Spin waves are known for many decades while magnonics is an emerging topic with both
fundamental interest and application potential. Magnons with frequencies in the GHz and
sub-THz regimes have wavelengths in the nanoscale due to their smaller velocities, and
magnonics fits perfectly with nanotechnology. It promises a new era of all-magnetic
computation encircling on-chip information communication, processing and logic operations
in addition to storage and memory. For magnonics to become a viable and sustainable
technology it is essential to build a knowledge base of excitation, manipulation and detection
of spin waves in various 1-D and 2-D periodic magnetic structures.
Here, we present manipulation of spin waves in optically excited and detected spin dynamics
in two-dimensional ferromagnetic nanodots and nanoantidots lattices. Femtosecond laser
pulses are used to create hot electrons in metallic thin films and nanostructures followed by
thermalization of electron and spin populations yielding a sub-picosecond demagnetization.
This is followed by a two-step relaxation process and excitation of spin waves and its
damping, which are detected with a sub-100 fs temporal and sub-μm spatial resolutions by a
home-built time-resolved magneto-optical Kerr microscope.1 Various aspects of the dynamics
as a function of the lattice constant, lattice symmetry, and bias field strength and orientation
have been investigated and new observations such as magnonic mode splitting, bandgap
formation, tunability of bandgaps, dynamic dephasing and transition from collective to non
collective dynamics are discussed based upon the experimental data and numerical
simulations.2-4 We further discuss a novel way of determining spin Hall angle in
ferromagnetic/non-magnetic bilayers using time-resolved magneto-optics.5
We gratefully acknowledge financial supports from DST, Government of India and the
British Council for the DST-UKIERI joint project, Grant No. DST/INT/UK/P-44/2012. We
also acknowledge financial support from DST under Grant No. SR/NM/NS-09/2011(G).
1. A. Barman and A. Haldar, Solid State Physics 65, 1-108 (2014).
2. B. Rana et al., ACS Nano, 5, 9559 (2011).
3. R. Mandal et al., ACS Nano 6, 3397 (2012).
4. S. Saha et al., Advanced Functional Materials 23, 2378 (2013).
5. A. Ganguly et al., Appl. Phys. Lett. 105, 112409 (2014).
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Durham UK–India Workshop on Magnetisation Processes 2015
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Durham UK–India Workshop on Magnetisation Processes 2015
Invited Talks
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Durham UK–India Workshop on Magnetisation Processes 2015
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Durham UK–India Workshop on Magnetisation Processes 2015
Thursday 13:30-14:00
Crystal phase and interface dependent spin-mixing conductance in
polycrystalline cobalt thin-films
A.T. Hindmarch*1, M. Tokac1, S.A. Bunyaev2, G. N. Kakazei2, D.S. Schmool3, D. Atkinson1
(1) Centre for Materials Physics, Durham University, Durham, UK
(2) IFIMUP and IN, Departamento de Fisica e Astronomia, Universidade do Porto, Portugal
(3) Laboratorie PROMES CNRS UPR 8521 University of Perpignan Via Domitia, France
*Email: a.t.hindmarch@durham.ac.uk
A quantitative physical analysis of spin-currents traversing interfaces in ferromagnetic thin-film
multilayers will provide a deeper fundamental understanding applications of such nanoscale magnetic
systems in spintronics, magnonics, and spin-caloritronics. Precessional magnetization dynamics have
been used extensively to access interfacial spin transport where spin-current flows from precession in
a ferromagnetic thin-film, into an adjacent non-magnetic layer where it is dissipated under the
influence of the spin-orbit interaction resulting in an enhanced damping in the ferromagnetic layer – a
process known as spin-pumping.
In this talk I will describe growth of multi-layered thin films where we are able to control the
dominant crystal phase in a ferromagnetic cobalt film as a function of thickness; we induce a nonequilibrium fcc (111) texture through growth on suitable seed layers, and allow relaxation to a bulklike hcp (0001) phase with increasing film thickness. I will then outline some recent results from our
research group where we have been investigating transmission of pure spin-currents via ‘spinpumping’ under ferromagnetic resonance. Using measurements on sets of device structures with
different overlayers we show that the nature of the atomic scale structure in the vicinity of the
interface plays a dominant role in the transmission of pure-spin currents, creating significant
differences in the enhancement of precessional magnetisation damping.
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Thursday 15:00-15:30
Durham UK–India Workshop on Magnetisation Processes 2015
Recent advances in magnetic tunnel junction based spin torque nanooscillators
Pranaba Kishor Muduli*
Department of Physics, Indian Institute of Technology, Hauz Khas, New Delhi-110016, India
*Email: muduli@physics.iitd.ac.in
Spin transfer torque (STT) allows manipulation of magnetic moments in nano-sized magneto-resistive
devices using current instead of magnetic field.1, 2 In certain sample geometries and/or applied fields, STT
can maintain a steady precession of one or more magnetic moments.3 As a consequence, the device
resistance undergoes oscillation, either through giant magnetoresistance (GMR) or tunneling
magnetoresistance (TMR), producing an output voltage signal in the microwave frequency range. These
so-called Spin Torque Nano Oscillators (STNOs) are typically based either on nanocontacts on top of GMR
stacks, or nanopillars of GMR or TMR stacks. In this talk, I will first discuss nanocontacts devices based
on metallic spin-valves and show the experimental confirmation of spin torque induced propagating spin
waves,4 formation of magnetic droplet5 and synchronization of three nanocontact STOs fabricated close to
each other.6 I will then present our recent results on frequency noise measurements7 for understanding
coherence mechanisms in a magnetic tunnel junction (MTJ) based STNO and show how mode-hopping
mechanism generates a 1/f frequency noise. I will discuss how to reduce linewidth and enhance power of
the STNOs for practical applications by demonstrating parametric excitation and synchronization.8 Finally
I will show our first results on wireless communication of MTJ based STNOs up to a distance of 150 m
with a data rate of ~3 Mbps.
Acknowledgement:
Partial support by DST Fast-Track Project is gratefully acknowledged. Support from the Swedish
Foundation for Strategic Research (SSF) and the Swedish Research Council (VR) are gratefully
acknowledged.
References:
1.
2.
3.
4.
5.
6.
7.
8.
12
J. Slonczewski, J. Magn. Magn. Mater. 159, L1-L7 (1996).
L. Berger, Phys. Rev. B 54, 9353-9358 (1996).
S. I. Kiselev, J. C. Sankey, I. N. Krivorotov, N. C. Emley, R. J. Schoelkopf, R. A. Buhrman and
D. C. Ralph, Nature 425 (6956), 380-383 (2003).
S. Bonetti, V. S. Tiberkevich, G. Consolo, G. Finocchio, P. Muduli, F. Mancoff, A. N. Slavin and
J. Åkerman, Phys. Rev. Lett. 105 (21), 217204 (2010).
S. M. Mohseni, S. R. Sani, J. Persson, T. N. A. Nguyen, S. Chung, Y. Pogoryelov, P. K. Muduli,
E. Iacocca, A. Eklund, R. K. Dumas, S. Bonetti, A. Deac, M. A. Hoefer and J. Akerman, Science
339 (6125), 1295-1298 (2013).
S. Sani, J. Persson, S. M. Mohseni, Y. Pogoryelov, P. K. Muduli, A. Eklund, G. Malm, M. Kall,
A. Dmitriev and J. Akerman, Nat. Commun. 4, 2731 (2013).
R. Sharma, P. Durrenfeld, E. Iacocca, O. G. Heinonen, J. Akerman and P. K. Muduli, Appl. Phys.
Lett. 105 (13), 132404 (2014).
P. Durrenfeld, E. Iacocca, J. Akerman and P. K. Muduli, Appl. Phys. Lett. 104 (5), 052410
(2014).
Durham UK–India Workshop on Magnetisation Processes 2015
Thursday 15:30-16:00
Time-resolved scanning Kerr microscopy of magnetization dynamics at the
nanoscale
P.S. Keatley*1 and R.J. Hicken1
(1) School of Physics and Astronomy, University of Exeter, Exeter UK
*Email: p.s.keatley@exeter.ac.uk
Time-resolved scanning Kerr microscopy (TRSKM) is a powerful tool for the investigation of the
magnetization dynamics at sub-micrometer length scales with picosecond temporal resolution.[1,2] A
variety of measurement configurations allows a range of dynamic magnetic phenomena to be explored
including sub-gigahertz gyrotropic oscillations of magnetic vortices, picosecond magnetic reorientation in hard disk writers, domain wall dynamics and excitations in nanowires, non-uniform
confinement of spin waves in nanomagnets, and low-temperature ferromagnetic resonance of thin
films. Recently TRSKM has been used to understand the coupled response of vortices, domain walls,
and spin-waves that govern the behaviour of magnonic metamaterials for magnetic logic and signal
processing applications. At the same time, the influence of a spin-torque on these magnetic
excitations is of fundamental interest for spintronic devices for non-volatile memory elements and
microwave oscillators. In this presentation the results of TRSKM on individual nanomagnets are
presented, Figure 1. The influence of the precise shape, material parameters, and a spin-torque on the
confined spin waves modes of an individual nanomagnet will be discussed in addition to the effect of
nearest neighbour static and dynamic dipole interactions in pairs of nanomagnets. Finally, a summary
of recent developments in TRSKM for the detection of magnetisation dynamics in active spintronic
devices and for the prospect of sub-diffraction spatial resolution will be presented.
(a)
fK
300 nm
hRF (t)
Frequency
Frequency
(GHz) (GHz)
10
H
8 -f
K
6
10 (b)
4
8
2
6
+f K
(c)
4
2
-1.0 -0.5 0.0
-M z
0.5
1.0
0.5
+M z
0.0 -0.5 -1.0
Magnetic field (kOe)
Figure 1. (a) TRSKM measurements with coherent microwave field excitation on a pair of
NiFe(15 nm) discs with 300 nm diameter and edge-to-edge separation of 160 nm (inset). (b) Spinwave spectrum acquired from one of the discs showing respectively the higher and lower frequency
branches of the centre and edge modes, in agreement with micromagnetic simulations (c).
[1] P.S. Keatley, V.V. Kruglyak, P. Gangmei, and R.J. Hicken, Philosophical Transactions of the
Royal Society A: Mathematical, Physical and Engineering Sciences, 369, 3115 (2011).
[2] P.S. Keatley, P. Gangmei, M. Dvornik, R.J. Hicken, J. Grollier, C. Ulysse, J.R. Childress, and J.A.
Katine, Topics in Applied Physics, 125, 17 (2013).
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Durham UK–India Workshop on Magnetisation Processes 2015
14
Durham UK–India Workshop on Magnetisation Processes 2015
Friday 09:15-09:45
Using implanted muons to investigate order, disorder and excitations in
reduced dimensions
Tom Lancaster*1
(1) Department of Physics, Durham University, Durham DH1 3LE
*Email: Tom.Lancaster@durham.ac.uk
Implanted muons are a sensitive means of investigating magnetic order, disorder and dynamics and
the properties of magnetic textures. I will review the use of the technique in investigations of lowdimensional magnetic systems, concentrating on the case of molecular coordination polymers, which
are materials that can show two-, one- or even zero-dimensional behaviour. In favourable cases we
have been able to control the dimensionality of a system through chemical or physical means. I will
also describe the use of muons in investigating the skyrmion lattice, by exploiting the analogy
between skyrmion and vortex lattice physics.
15
Friday 09:45-10:15
Durham UK–India Workshop on Magnetisation Processes 2015
Perpendicular Magnetic Anisotropy and Magnetic Inhomogeneity in
Ta(N)/CoFeB/MgO
J. Sinha1, C. Banerjee1, A. K. Chaurasiya1, A. Ganguly1, M. Hayashi2 and A. Barman1
(1) Thematic Unit of Excellence on Nanodevice Technology, Department of Condensed Matter
Physics and Material Sciences, S. N. Bose National Centre for Basic Sciences, Salt Lake, Kolkata 700
098, India
(2) National Institute for Materials Science, Tsukuba 305-0047, Japan
Email: jaivardhan.sinha@bose.res.in
In-depth understanding of perpendicular magnetic anisotropy (PMA) in thin film with structure
inversion asymmetry is important to develop advanced spintronics devices [1]. The thin film
heterostructure CoFeB|MgO with Heavy Metal (HM- Ta, TaN) underlayer has drawn much attention
recently as it posses sufficient interface anisotropy to exhibit PMA [1,2]. Specially, Ta|CoFeB|MgO is
the main constituent of magnetic tunnel junction [1] and it has significant application potential in
recently discovered three terminal devices [3]. Though in this heterostructure interface anisotropy
primarily originates from CoFeB|MgO interface but the choice of underlayer significantly influences
the strength of PMA. It has been found recently that the interface anisotropy in Ta|CoFeB|MgO film
can be varied by changing the N-flow rate during Ta underlayer deposition [2]. Specifically
CoFeB|MgO films grown on optimally N-doped Ta underlayer has larger interface anisotropy than the
film deposited on Ta underlayer. In order to assess the technological potential of these
heterostructures it is important to understand the magnetic inhomogeneity which is an important
contributor to the damping coefficient. A powerful method to study the magnetic inhomogeneity is to
investigate the spin-wave linewidth. Brillouin Light Scattering (BLS) is a sensitive probe for detecting
spin-waves in magnetic thin films and multilayers [4,5,6]. The detailed magnetic properties
(saturation magnetization, magnetic dead layer thickness, and interface anisotropy) in
Ta(N)|CoFeB|MgO will be discussed. It will be further shown that the magnetic inhomogeneity can be
tuned in these heterostructures by doping N into the underlayer.
Acknowledgement: We acknowledge the financial assistance from Department of Science and
Technology Govt. of India under grant no. SR/NM/NS-09/2011 and S. N. Bose National Centre for
Basic Sciences under project no. SNB/AB/12-13/96.
Reference:
[1] S. Ikeda et al., Nature Materials 9, 721 (2010).
[2] J. Sinha et al., Appl. Phys. Lett. 102, 242505 (2013).
[3] L. Liu et al., Science 336, 555 (2012).
[4] B. Hillebrands, Phys. Rev. B, 41, 530 (1990).
[5] A. Haldar et al., J. Appl. Phys. 115, 133901 (2014).
[6] G. Gubbiotti et al., Phys. Rev. B, 86, 014401 (2012).
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Friday 10:15-10:45
Durham UK–India Workshop on Magnetisation Processes 2015
Spin Physics in Hybrid Metallo-Molecular Multilayers
O. Cespedes*1, M. Wheeler1, T. Moorsom1, F. Al Ma’Mari1, G. Burnell1, B.J. Hickey1, G. Teobaldi2,
F. Gonzalvez3, R. Stamps3
(1) School of Physics & Astronomy, University of Leeds, LS2 9JT, UK
(2) Department of Chemistry, University of Liverpool, L69 3BX, UK
(3) School of Physics & Astronomy, Kelvin Building, University Avenue, Glasgow, G12 8QQ, UK
*Email: o.cespedes@leeds.ac.uk
Carbon based materials are attractive for spintronic applications due to their long spin coherence time
and the possibility to implement low-dissipation electronics in eco-friendly devices. In the past, this
research has been mostly focused on reproducing the magnetoresistance (MR) of standard spin valves
and magnetic tunnel junctions but using organic spacers. These devices have proven successful, with
MR of up to 5-10% in spacers up to ~100 nm thick.1 The role of the interface and the generation of
proximity effects at the molecular material have been discussed extensively; orbital shifting and
hybridisation play an essential role when discussing the spin-dependent transmission probability, and
copper-molecular bilayers have been demonstrated to give rise to spin filtering.2
0
SiO2
1.4
1.5
1.6
1.7
Emission (eV)
1.8
Al 2 O 3
Magnetic
Al 2 O 3
10
Non-magnetic
Spin Polarised Effect in NPL
20
Al2O3
PY
Al 2 O 3
Non-magnetic
PY current
with / no MF
Magnetic
Al2O3
PY current
PY current (MF)
0.8
Au current
30
0.9
Au current (MF)
Intensity (counts/s)
Au
Al2O3
40
Negative luminescence (NPL)
Au / no current
no MF
1.0
0 current
V
I
Au / no current
with MF
1.1
0 current (MF)
50
Normalized emission
More recently, the research has shifted towards the possibility of using spin pumping into organic
materials.3 This method of spin injection would eliminate the problem of resistivity mismatch and
opens the doors for the propagation of pure spin currents without an applied voltage in low spin orbit
materials. Here, we will first show the effect of charge transfer in metallo-molecular multilayers,
demonstrating the appearance of an antiferromagnetic coupling4 and changes in the spectroscopic
properties of the molecules.5 We will then consider the effects of energy dissipation from a
ferromagnet into a fullerene film during ferromagnetic resonance.
Figure 1: Schematic of a device used to study the effects of spin polarization in photoluminescence
and changes measured as a function of the direction of the current and the applied magnetic field.
[1] X. Zhang et al., Nature Communications, 4, 2423 (2013).
[2] K.V. Raman et al., Nature, 493, 509 (2013)
[3] K. Ando et al., Nature Materials, 12, 633 (2013).
[4] T. Moorsom et al., Phys. Rev. B , 90, 125311 (2014).
[5] T. Moorsom et al., Appl. Phys. Lett., 105, 022408 (2014)
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Friday 10:45-11:15
Durham UK–India Workshop on Magnetisation Processes 2015
Spin-orbit torques in ferromagnets with broken inversion symmetry
Andrew Ferguson*
Cavendish Laboratory, JJ Thomson Avenue, Cambridge, CB3 0HE
*Email: ajf1006@cam.ac.uk
Passing electricity through a ferromagnetic conductor with uniform magnetisation and with broken
inversion symmetry may generate a torque [1]. This so-called spin-orbit torque can be used to switch
the magnetisation in ferromagnetic semiconductors at low temperature [2] and also in ferromagnetic
metals at room temperature [3], as might be useful in a memory device.
Here I will summarise the work of my group and collaborators on spin-orbit torque, using (Ga,Mn)As
as a model system. By employing current driven ferromagnetic resonance we are able to map out the
magnitude and direction of the field like spin-orbit torques [4]; observe an intrinsic anti-damping
spin-orbit torque originating in the Berry phase [5]; and measure the reciprocal effect to the spin-orbit
torque [6], whereby the precessing magnetisation pumps a charge current.
[1]
[2]
[3]
[4]
[5]
[6]
18
B. A. Bernevig and O. Vafek, Phys Rev B 72, 187601 (2005); A. Manchon and S. Zhang,
Phys Rev B 78, 187601 (2008); A. Manchon and S. Zhang, Phys Rev B 79, 187601 (2009).
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Nat Phys 5, 656 (2009).
I. M. Miron, K. Garello, G. Gaudin, P. J. Zermatten, M. V. Costache, S. Auffret, S. Bandiera,
B. Rodmacq, A. Schuhl, and P. Gambardella, Nature 476, 189 (2011).
D. Fang, H. Kurebayashi, J. Wunderlich, K. Vyborny, L. P. Zarbo, R. P. Campion, A.
Casiraghi, B. L. Gallagher, T. Jungwirth, and A. J. Ferguson, Nat Nanotechnol 6, 413 (2011).
H. Kurebayashi, J. Sinova, D. Fang, A. C. Irvine, J. Wunderlich, V. Novak, R. P. Campion,
B. L. Gallagher, E. K. Vehstedt, L. P. Zarbo, K. Vyborny, A. J. Ferguson, and T.
Jungwirth, Nat Nanotechnol 9, 211 (2014).
C. Ciccarelli, K. M. D. Hals, A. Irvine, V. Novak, Y. Tserkovnyak, H. Kurebayashi, A.
Brataas, and A. Ferguson, Nat Nanotechnol 10, 50 (2015).
Durham UK–India Workshop on Magnetisation Processes 2015
Friday 11:30-12:00
Magnetic Domain Walls Under Strain
Andrew Rushforth*1
(1) School of Physics and Astronomy, University of Nottingham, Nottingham NG7 2RD, UK.
*Email: andrew.rushforth@nottingham.ac.uk
Magnetic domain walls are the important constituents of many existing and proposed technologies.
These technologies include information storage devices, such as 3-terminal magnetic random access
memory (DW-MRAM)[1] and racetrack memory[2], information processing concepts using the
position[3] and chirality[4] of domain walls to represent the bit of information, and more diverse
applications such as in lab-on-a-chip[5] devices and motion sensors[6].
Traditional methods to control the motion of magnetic domain walls rely on external magnetic fields
or electrical currents. These methods place limits on the energy efficiency and miniaturisation of
devices. A promising alternative route to low energy control of magnetisation is to use electric fields.
In particular, the application of voltage-induced mechanical strain in hybrid
piezoelectric/ferromagnetic devices has received much attention recently[7,8]. The mechanical strain
induces a magnetic anisotropy in the ferromagnetic layer via inverse magnetostriction. This approach
has been used to demonstrate non-volatile switching of the magnetisation direction[9], control of the
efficiency of current induced domain wall motion[10,11], and predictions that domain wall
structure[12] and position[13] can be controlled by voltage induced strain alone.
In this talk I will review our recent work to study magnetic domain walls under the action of voltageinduced strain. Collaborative projects between researchers at the Universities of Nottingham,
Cambridge, Leeds, Sheffield, York, and at Diamond Light Source have investigated domain walls in
devices from macroscopic to sub-micrometre length scales, and under the action of magnetic fields,
electrical currents, and in nanostructured devices with intentionally designed pinning sites. In all of
these regimes, the action of mechanical strain is found to significantly modify the properties and
dynamics of domain walls.
[1] Fukami, S. et al., 2009 Symposium on VLSI Technology Digest of Technical Papers, 230–1
(2009).
[2] Parkin, Patent US 6834005; Science 320, 190 (2008).
[3] D.A. Allwood et al., Science 309, 1688 (2005).
[4] Omari, et al., Phys. Rev. Appl. 2, 044001 (2014).
[5] Rapoport et al., Lab Chip, 12, 4433–4440 (2012).
[6] Novotechnik, http://www.novotechnik.com/rsm
[7] Hu et al., Nature. Communications. 2, 553 (2011).
[8] Biswas et al., Sci. Rep. 4, 7553 (2014).
[9] Parkes et al., Appl. Phys. Lett 101, 072402 (2012).
[10] De Ranieri et al., Nature Materials 12, 808 (2013).
[11] Rushforth, App. Phys. Lett. 104, 162408 (2014).
[12] Bryan et al., J. Phys.: Condens. Matter 24, 024205 (2012).
[13] Dean et al., J. Appl. Phys. 109, 023915 (2011).
19
Friday 12:00-12:30
Durham UK–India Workshop on Magnetisation Processes 2015
Understanding and Controlling Stochastic Domain Wall Behaviour in
Magnetic Nanowire Devices
T.J. Hayward1, K. Omari1, M. Negiotia1, T.J. Broomhall1, M.P.P. Hodges1, P.W. Fry2, D.A.
Allwood1, M.T. Bryan3, M.-Y. Im4 and P. Fischer4
1
Department of Materials Science and Engineering, University of Sheffield, UK.
2
Nanoscience and Technology Centre, University of Sheffield, UK
3
Department of Cardiovascular Science, University of Sheffield, UK
4
Centre for X-ray Optics, Berkeley National Laboratory, Berkeley, CA, USA
Devices based on the controlled motion of domain walls (DWs) in planar magnetic nanowires have
great technological potential. However, the realisation of such technologies has long been hindered by
a number of fundamental problems. Some of the most serious of these relate to stochastic DW
pinning/depinning effects. For example, in nominally defect-free nanowires, DW transmission is
found to be probabilistic even for fields much greater than those required to initiate DW propagation
[1]. Furthermore, in nanowires containing artificial defect sites, different fields/currents are required
to depin DWs from one instance to the next, and DWs may pass dynamically through the defects
under applied fields that are not expected to cause depinning [2].
Here, we will use finite temperature micromagentic simulations to show that all of these
experimentally observed behaviours can be comprehensively explained by a complex, dynamical
interaction between thermal perturbations and Walker breakdown phenomena. Our results show that
stochastic phenomena are an intrinsic feature of DW behaviour at finite temperatures, and would not
be suppressed even in hypothetical systems where initial DW structures and external parameters were
perfectly defined.
Having explored the origins of stochastic DW pinning we will discuss a number of potential
solutions. These range from simple solutions, such as tuning defect sites and/or nanowire geometries
in order to simplify their interaction with dynamically propagating DWs, to more complex approaches
where DWs are carried directly by propagating 1D potential wells, created by either rotating magnetic
fields or by the interference of surface acoustic waves. Finally we will use micromagnetic simulations
to illustrate a potential material science-based solution, where doping Ni80Fe20 nanowires with rareearth elements creates systems where the complex magnetisation dynamics at the heart of stochastic
phenomena are almost entirely suppressed.
[1] M. Muñoz and J. Prieto, Nature Communications 2, 526 (2011), H. Tanigawa, T. Koyama, M.
Bartkowaik, S. Kasai, K. Kobayashi and T. Ono, Phys. Rev. Lett 101, 207203 (2008).
[2] U.-H. Pi, Y.-J. Cho, J.-Y. Bae, S.-C. Lee and S. Seo, Phys. Rev. B. 84, 024426 (2011), M.-Y. Im,
L. Bocklage, P. Fischer and G. Meier. Phys. Rev. Lett. 102, 147204 (2009).
Figure 1: Results of room-temperature micromagnetic
simulations in which vortex domain walls with
anticlockwise circulations were propagated to a notchshaped defect site at H = 35 Oe. The upper figure
illustrates the multitude of pinned domain wall
configurations formed at the notch. The lower plot
indicates the frequency of their formation and a derived
depinning field distribution.
20
Durham UK–India Workshop on Magnetisation Processes 2015
Friday 12:30-13:00
Imaging Magnetic Domains in Nano-Structured Thin Films for Data
Storage Applications
Dan Read1*
School of Physics & Astronomy, Cardiff University, Queen’s Buildings,
The Parade, Cardiff, CF24 3AA, UK
1
*
e-mail: ReadDE@Cardiff.ac.uk
In the current race for information storage media with ever increasing data densities the position or
state of magnetic domain walls, the region in a magnetic system where the local magnetization
continually rotates its direction between adjacent magnetic domains, is one of the most promising
routes for future storage media and devices.
Information storage requires ultrafast read-out and writing operations, but domain walls need to be
pinned so that the information is safely stored in the long term. Here we investigate the use of a
variety of pinning schemes and geometries to assess those that might be best for future device
technologies.
One promising candidate is to utilise remote magnetostatic charges to trap magnetic domain walls [1].
Over the years a great variety of imaging techniques such as, Magnetic Force Microscopy (MFM)
Scanning Magneto-Optic Kerr Effect Microscopy (MOKE) or Lorentz Electron Microscopy have
been used to image domain walls [2,3]. By using Scanning Transmission X-ray Microscopy (STXM)
and X-ray photoelectron emission microscopy (XPEEM) we have followed the position and structure
of domain walls of opposite charge being pinned or repelled by pinning potentials of increasing
strength.
Micromagnetic simulations have been performed and have shown excellent agreement with the
experimental results. We demonstrate the attractive or repulsive character of the interaction between
domain wall and trap depending upon the sign of their magnetic charges.
These quasi-static experiments are the antecedent to ultrafast time-resolved XMCD-PEEM
experiments where the spin-transfer torque effect will be studied dynamically by applying
picosecond-long current pulses across the magnetic nanowire.
[1] O’Brien et al., “Tunable Remote Pinning of Domain Walls in Magnetic Nanowires”, Physical
Review Letters, 106 087204, (2011).
[2] Ladak et al., “Direct observation of magnetic monopole defects in an artificial spin-ice system”,
Nature Physics, 6 359, (2010).
[3] Petit et al., “Magnetic imaging of the pinning mechanism of asymmetric transverse domain walls
in ferromagnetic nanowires”, Applied Physics Letters, 97 233102, (2010).
21
Friday 14:00-14:30
Durham UK–India Workshop on Magnetisation Processes 2015
Magnetization reversal study by magneto-optic Kerr microscopy
Subhankar Bedanta
National Institute of Science Education and Research (NISER), Institute of Physics Campus,
Po- Sainik School, Bhubaneswar, Odisha, India-751005
*sbedanta@niser.ac.in
Magneto-optic Kerr effect (MOKE) magnetometry has been widely performed to study and measure
magnetic hysteresis in ferromagnetic thin films. This technique is often preferred because it is cost
effective, fast measurement time and more importantly the capability of performing the vector
magnetometry. There are three configurations of MOKE magnetometry exists such as longitudinal,
transverse and polar, respectively. In past few decades Kerr microscopy based on the MOKE principle
has been often performed to image ferromagnetic domains.
In this talk I will give a brief overview of Kerr magnetometry and microscopy. In particular I will
highlight the significance of these techniques in studying magnetization reversal processes. In this
context I will show our recent results on four subjects which are listed below.
(i) Superferromagnetism (SFM): SFM domains in a non-percolated nanoparticle assembly are
expected to be similar to conventional ferromagnetic domains in a continuous film, with the decisive
difference that the atomic spins are replaced by the superspins of the single-domain nanoparticles. [1,2]
From the domain wall relaxation measurements we can calculate the domain wall velocity and plot it
as a function of external magnetic fields. The various domain wall dynamic modes such as creep, slide
and the depinning transition have been clearly observed. Angle dependent magnetization reversal study
has been performed which indicate that the size and relaxation dynamics can be controlled by changing
the angle between the easy axis and the magnetic field. [3]
(ii) Magnetic antidot arrays (MALs): MALs are defects in a continuous thin film. They introduce
perturbation in the thin film and hence their magnetization reversal mechanism is quite different from
that of a continuous thin film. MALs are receiving intense research interest because of their potential
advantages, such as lack of superparamagnetic limit to the bit size (as compared to dot arrays) [4]. We
will show how the magnetization reversal process occurs in a Co MAL system studied by Kerr
microscopy. [5]
(iii) Inter-layer coupling: The other topic of interest is competing inter-layer interaction effects in
dipolarly coupled ferromagnetic/non-magnetic multilayers. LMOKE microscopy has been performed
on [Co (t1)/Al2O3(t2)]N for various thicknesses of Co (t1) and Al2O3 (t2) and different number of bilayers,
respectively. We will show how the inter-layer interactions lead to layer-by-layer magnetization
reversal as evidenced by Kerr microscopy. [6-8]
iv) Interplay of uniaxial and cubic anisotropies in Fe/MgO(100) epitaxial thin film: I will present
a study on magnetization reversal process for Fe/MgO(001) thin films. Due to the oblique growth
configuration, a uniaxial anisotropy is found superimposed to the expected four-fold cubic anisotropy.
Domain wall motion images during magnetization reversal are captured by Kerr microscope which are
the clear evidence of two successive or separate 90° DW nucleation depending on the angle between
the applied field and easy axis i.e. <100> direction. Still now all systematic studies on magnetization
reversal mechanism of epitaxial Fe/MgO(001) film were explained on the basis of theoretical models.
But for the first time we are presenting the direct evidences of magnetization reversal mechanism in
this system. [9]
References:
[1] S. Bedanta and W. Kleemann, J. Phys. D : Appl. Phys. 42, 013001 (2009) [2] S. Bedanta et al. Phys.
Rev. Lett. 89, 176601 (2007); [3] N. Chowdhury et al. J. Appl. Phys. (under review); [4] N. G.
Deshpande et al, JAP 111, 013906 (2012); [5] Sougata Mallick and S. Bedanta, J. Magn. Magn. Mater.
352, 158 (2015); [6] S. Bedanta et al. Phys. Rev. B 74, 054426 (2006) ; [7] N. Chowdhury and S.
Bedanta, AIP Advances 4, 027104 (2014) ; [8] N. Chowdhury and S. Bedanta et al. (unpublished) ; [9]
Srijani Mallick, N. Chowdhury and S. Bedanta, AIP Advances 4, 097118 (2014)
22
Durham UK–India Workshop on Magnetisation Processes 2015
Friday 14:30-15:00
Collective Properties of Nanomagnet Arrays; Electric and Magnetic
Currents in Artificial Spin Ice
W. Branford*1,
(1) Blackett Laboratory, Dept of Physics, Imperial College London, SW72AZ
*Email: w.branford@imperial.ac.uk
I will discuss large-area arrays of single domain nanomagnets with frustrated interactions. The shape
of each nanomagnet controls the magnetic anisotropy and the elements are closely spaced so dipolar
interactions are important. Lattices are chosen such that the geometry prevents all dipole interactions
from being satisfied. Arrays of this type are generally called Artificial Spin Ice and I will describe
experiments on electrically continuous permalloy honeycombs structures. [1-2]
Here I report direct magnetic imaging studies of domain wall mediated magnetic charge flow in
artificial spin ice. [3-5]. The magnetic charge is carried by transverse domain walls and the chirality
of the domain wall is found to control the direction of propagation. Recently it has been shown that in
isolated Y-shaped junctions that support vortex domain walls, selectivity can be determined by
chirality (or topology), the suggestion being that vortex wall chirality is robust in the Walker
breakdown process.[6,7] Here I will show that in Y-shaped junctions, magnetic switching in the
important topologically protected regime exists only for a narrow window of field and bar geometry,
and that it will be challenging to access this regime in field-driven Artificial Spin Ice. This work has
implications for the wider field of magnetic charge manipulation for high density memory storage.
[1] S. Ladak, D. E. Read, G. K. Perkins, L. F. Cohen & W. R. Branford. Nature Physics 6, 359,
(2010).
[2] W. R. Branford, S. Ladak, D. E. Read, K. Zeissler & L. F. Cohen. Science 335, 1597, (2012).
[3] S. K. Walton, K. Zeissler, D. M. Burn, S. Ladak, D. E. Read, T. Tyliszczak, Cohen, L. F. &
Branford, W. R. New Journal of Physics 17, 013054, (2015).
[4] K. Zeissler, S. K. Walton, S. Ladak, D. E. Read et al. Sci. Rep. 3, 01252, (2013).
[5] S. Ladak, D. Read, T. Tyliszczak, W. R. Branford & L. F. Cohen. New Journal of Physics 13,
023023, (2011).
[6] T. Phung, A. Pushp, C. Rettner, B. P. Hughes, S. H. Yang & S. S. P. Parkin. Appl. Phys. Lett. 105,
222404, (2014).
[7] A. Pushp, T. Phung, C. Rettner, B. P. Hughes, S. H. Yang, L. Thomas & S. S. P. Parkin. Nature
Physics 9, 505-511, (2013).
23
Friday 15:00-15:30
Durham UK–India Workshop on Magnetisation Processes 2015
Strain Induced Vortex Core Switching in Planar Magnetostrictive
Nanostructures
T. A. Ostler1, R. Cuadrado1, R. W. Chantrell1, A. W. Rushforth2 and S. A. Cavill1,3*
1
2
Department of Physics, University of York, Heslington, York, YO10 5DD, United Kingdom
School of Physics and Astronomy, The University of Nottingham, Nottingham, NG7 2RD, United Kingdom
3
Diamond Light Source, Chilton, Didcot, Oxfordshire, OX11 0DE, United Kingdom
Magnetic vortex cores, often found in planar magnetic structures, arise from the complex interactions
between the magnetostatic and exchange energy. In recent years the magnetization dynamics of the core
have also been studied in great detail because the gyrotropic mode has applications in spin torque driven
magnetic microwave oscillators, and also provides a means to flip the direction of the core for use in
magnetic storage devices such as magnetic random access memory. The excitation of the core
gyrotropic mode can be achieved using various stimuli such as RF or pulsed magnetic fields or spinpolarized currents. Here we demonstrate a new means of stimulating magnetization reversal of the
vortex core by applying a time-varying strain to planar structures of the magnetostrictive material,
Fe81Ga19 (Galfenol), coupled to an underlying piezoelectric layer. Using micromagnetic simulations we
have shown that the vortex core state can be deterministically reversed by electric field control of the
time-dependent strain-induced anisotropy. These theoretical results can be used as a recipe for designing
experimental setups and could pave the way for low energy devices based on the magnetic vortex core.
24
Durham UK–India Workshop on Magnetisation Processes 2015
Friday 15:30-16:00
Nanometer resolution imaging of Helical and Skyrmion states in FeGe
D. McGrouther*1, S. McVitie1, R. L. Stamps1, T. Koyama2, Y. Nishimori2, Y. Togawa2
(1) University of Glasgow, Glasgow, G12 8QQ, United Kingdom
(2) Osaka Prefecture University, Osaka, Japan
*Email: damien.mcgrouther@glasgow.ac.uk
The behaviour of materials with B20 crystal structure is the focus of current attention due to a desire
to understand the varied and complex behaviour arising from the chiral Dzyaloshinskii-Moriya
interaction. In a phase diagram, depending on both temperature and magnetic field strength, ordered
helical and Skyrmion states have been observed and widely reported. Materials such as FeCoSi[1],
MnSi[2] and Cu2OSeO3[3] have received much attention but these exhibit magnetic ordering at
temperatures well below 100K. FeGe exhibits a much higher magnetic ordering temperature, in the
region 250-280K[4] and thus holds more potential for future application.
At Glasgow we have developed world-leading high spatial resolution imaging (resolution better than
1 nm) for magnetic materials. On an aberration corrected JEOL ARM200FCS Scanning
Transmission Electron Microscope (STEM) we have utilised the Differential Phase Contrast (DPC)
mode to study the magnetic behaviour of a <100nm thick, (110) oriented sheet of FeGe cut from a
bulk crystal. Using a specimen cooling holder we have imaged magnetic behaviour in various regimes
of the phase diagram, from 110-250K and by applying magnetic fields of strength 0-3kOe. Our
quantitative imaging capabilities, coupled with an applied spatial resolution of 3 nm for these
samples, have allowed us to investigate in detail the transition from helical to Skyrmion phase, the
evolution of the Skyrmion structure under applied fields and interesting behaviours that arise at phase
boundaries.
Figure 1. The Skyrmion lattice, period 74 nm,
occurring at 250K stabilised by an applied field of
strength 400 Oe.
[1] X. Z. Yu, et al., Nature 465, 09124 (2010)
[2] E. Karhu, et al., Physical Review B, 82, 184417 (2010)
[3] S. Seki, et al., Science 336, 198 (2012)
[4] X. Z. Yu, et al., Nature Materials 10, 106 (2011)
25
Durham UK–India Workshop on Magnetisation Processes 2015
26
Durham UK–India Workshop on Magnetisation Processes 2015
Thursday 19th, from 16:15
Posters
27
Durham UK–India Workshop on Magnetisation Processes 2015
28
Durham UK–India Workshop on Magnetisation Processes 2015
Poster P1
Feasibility of Spin Seebeck Based Thermoelectrics
A.J. Caruana*1, K. Morrison1
(1) Physics Department, Loughborough University, Loughborough, UK.
*Email: a.j.caruana@lboro.ac.uk
Thermoelectric generators (TEGs) are of increasing interest due to their potential use in energy
harvesting of waste heat. The efficiency of such devices is often characterised by the thermoelectric
figure of merit, zT[1], which is ultimately limited by the thermal and electric conductivities in
conventional TEGs. The ideal TEG material should have a high electrical conductivity (to reduce
resistive losses), and low thermal conductivity (so that a large temperature gradient can be setup
across the device) for the optimisation of zT. However, these properties are intrinsically linked to one
another, as best described by the Weidemann-Franz Law (κ=σL0T), thus providing a limit to the upper
value of zT.
The Spin Seebeck Effect (SSE) may provide a way in which to overcome this limit. Rather than the
generation of a charge current, Jc, in response to a thermal gradient, a spin polarized current, Js, arises
when a thermal gradient is applied to a magnetised layer. If a paramagnetic metallic contact is
deposited on top of the magnetic layer, this spin polarized current can be detected/harvested via the
inverse spin hall effect (ISHE) (see Figure 1)[2]. Due to the separation of the active material (magnetic
layer) and the electric circuit (paramagnetic layer) the magnetic layer can be chosen so that the
thermal conductivity is minimised without affecting the electrical conductivity of the contact layer
(and thus maximising device efficiency). We will present a broad overview of the current state of the
art with regards to thermoelectric materials, followed by a discussion of the merits of integrating the
spin Seebeck effect in TEGs.
[1] L. E. Bell, Science, 321, 1457 (2008)
[2] K. Uchida et al, J. Phys. Condens. Matter, 26, 343202 (2014)
Figure 1: Schematic diagram of the two Spin Seebeck effect configurations. In both cases the bottom
magnetic layer is magnetised as a thermal gradient is applied along (transverse), or through
(longitudinal) the device. This causes a spin accumulation in the device, which induces a charge
voltage in the top contact layer.
29
Poster P2
Durham UK–India Workshop on Magnetisation Processes 2015
Understanding the thickness dependence of Gilbert damping in
ferromagnetic thin films with non-magnetic capping layers
𝐒. 𝐀𝐳𝐳𝐚𝐰𝐢∗𝟏 , 𝐀. 𝐆𝐚𝐧𝐠𝐮𝐥𝐲 𝟐 , 𝐉. 𝐀. 𝐊𝐢𝐧𝐠 𝟏, 𝐉. 𝐒𝐢𝐧𝐡𝐚𝟐, 𝐀. 𝐓. 𝐇𝐢𝐧𝐝𝐦𝐚𝐫𝐜𝐡 𝟏 𝐀. 𝐁𝐚𝐫𝐦𝐚𝐧
𝐃. 𝐀𝐭𝐤𝐢𝐧𝐬𝐨𝐧 𝟏
1 Durham University
2 S. N. Bose National Centre for Basic Sciences
𝟐
&
Email: s.a.r.hammoodi-azzawi@durham.ac.uk
Magnetisation dynamics in thin-film magnetic multilayers may be significantly influenced by interfaces
with non-magnetic (NM) metal layers via effects such as spin-pumping or strong spin-orbit coupling
effects. Understanding these influences is of vital importance in realising low-energy spintronic and
magnonic devices utilising magnetisation precession and ultra-fast switching processes [1, 2].
Co10/Pt0

0.01
0.00
-0.01
-0.02
0.0
0.2
0.4
0.6
0.8
1.0
0.010
0.008
0.006
0.004
0.002
0.000
-0.002
-0.004
-0.006
-0.008
-0.010
1.2
Co10/Pt0.2

0.0
0.2
0.00
-0.01
0.2
0.4
0.6
Time (ns)
0.6
0.8
1.0
0.00
-0.01
1.2
0.0
0.8
1.0
1.2
Co10/Pt1.5

0.00
-0.01
0.0
0.2
0.4
0.6
Time (ns)
0.2
0.4
0.6
0.8
1.0
0.8
1.0
1.2
0.042
0.040
0.038
0.036
0.034
0.032
0.030
0.028
0.026
Co(10nm)/Pt(dPtnm)
0.0
0.5
1.0
1.5
dPt(nm)
2.0
Figure (1): Damping parameter 𝛼 as a function of capping layer thickness for Co(10 nm)/Pt (𝑡𝑃𝑡 )
bilayers, with precession frequency ~16 GHz.
1. Hillebrands, B. (2003). Spin dynamics in confined magnetic structures II. Springer.
2. Iihama, S., Mizukami, S., Naganuma, H., Oogane, M., Ando, Y., & Miyazaki, T. (2014). Gilbert
damping constants of Ta/CoFeB/MgO (Ta) thin films measured by optical detection of
precessional magnetization dynamics.Physical Review B, 89(17), 174416.
3. Barati, E., Cinal, M., Edwards, D. M., & Umerski, A. (2014). Gilbert damping in magnetic
layered systems. Physical Review B, 90(1), 014420.
30
1.2
Time (ns)
0.01

Co10/Pt1

0.0
0.4
Co10/Pt0.6

0.01
Time (ns)
Kerr Rotation (Arb. unit)
Kerr Rotation (Arb. unit)
Time (ns)
0.01
Kerr Rotation (Arb. unit)
0.02
Kerr Rotation (Arb. unit)
Kerr Rotation (Arb. unit)
Bilayer thin-films of Co/Pt, Co/Au, NiFe/Pt and NiFe/Au with varying thicknesses of the NM capping
layer were fabricated by magnetron sputtering. Magnetisation precession was studied using time
resolved magneto-optical Kerr effect (TR-MOKE) magnetomtery to detect ultra-fast magnetization
processes in the time-domain. Experimental results were fitted and interpreted within the framework of
the Landau-Lifshitz-Gilbert equation to extract the phenomenological Gilbert damping constant, α. The
dependence of the damping parameter on NM layer thicknesses was determined for layer thicknesses
ranging from 2 Å up to 20 Å. The figures show examples of the background corrected TR-MOKE
signals for a series of Co/Pt bilayers, and the NM thickness dependence of damping parameter for a Pt
capping layer. The xomplex non-monotonic thickness dependence of the damping parameter observed
is in good qualitative agreement with very recent theoretical predictions [3].
Durham UK–India Workshop on Magnetisation Processes 2015
Poster P3
Magnetisation dynamics of confined magnetic nanostructures controlled by
voltage-induced mechanical strain
S. Bowe*, R. Beardsly, D. Parkes, A. W. Rushforth and S. A. Cavill
(1) School of Physics and Astronomy, University of Nottingham, Nottingham NG7 2RD, UK.
(2) Diamond Light Source, Chilton, Didcot, Oxfordshire OX11 0DE, United Kingdom
(3) Department of Physics, University of York, Heslington, York YO10 5DD, United Kingdom
*Email: ppxsb3@nottingham.ac.uk
Magnetic nanostructures containing flux closure and vortex domain configurations have potential
applications including information storage technologies and spin torque oscillators. The magnetisation
dynamics of confined magnetic structures can be complex and consist of standing wave modes in
regions with uniform magnetisation, oscillations of the domain wall structure[1] and gyration of the
vortex core[2].
In our recent work we demonstrated how voltage induced strain can be used to significantly modify
the configuration of magnetic flux closure domains in structures fabricated using Fe81Ga19[2]. Here we
present investigations of the effects of a strain-induced uniaxial magnetic anisotropy on the
magnetisation dynamics of Fe81Ga19 square structures in the flux closure configuration. Using timeresolved XMCD PEEM and micromagnetic simulations we find that the induced anisotropy modifies
the precession frequency of the uniform magnetic regions, the oscillations of the domain wall
structure, and the gyration of the vortex core (Figure 1).
Our investigations show that inverse magnetostriction provides a promising route for tuning
significantly the complex magnetisation dynamics of magnetic nanostructures.
(b)
(a)
Figure 1. Spatial character of the approx. 5GHz mode of the x component of
magnetisation in a 500nm square with uniaxial anisotropy of (a) 0kJm-3 and (b) 10kJm-3
along x.
[1] Bailleul et al., Phys. Rev. B 76, 224401 (2007).
[2] Parkes et al., Appl. Phys. Lett. 105, 062405 (2014).
31
Poster P4
Durham UK–India Workshop on Magnetisation Processes 2015
Magnetic, Structural and Electrical Characterisation of CoFeTaB/Pt
Bilayer Films
Oto-obong Inyang*, Del Atkinson, and Aidan Hindmarch
Department of Physics, Durham University, Durham, DH1 3LE United Kingdom.
*Email:o.o.a.inyang@durham.ac.uk
Pure spin current, rather than charge current, is gaining importance in modern spintronics. In a bid to
produce and understand pure spin current, recent studies have demonstrated the generation and
detection of spin current by spin-Hall magnetoresistance (SHMR); a magnetoresistance arising due to
spin Hall effect and inverse spin Hall effect in ferromagnetic insulator-normal metal bilayers [1, 2].
Magnetic, structural, and electrical properties have been investigated in thin film bilayers of an
amorphous, highly resistive, ferromagnetic material (CoFeTaB) capped with paramagnetic materials
with strong spin orbit interaction, such as platinum. The aim of this study is to demonstrate SHMR in
this novel material system.
Thin films of CoFeTaB/Pt with different Pt thicknesses have been prepared using sputter deposition.
X-ray measurements were used to measure the sample layer structure and probe the roughness of the
CoFeTaB/Pt interface. Room temperature magneto-optical characterisation showed a uniaxial magnetic
anisotropy, with easy-axis coercivity of around 5 Oe for films capped with Pt, and 10 Oe for CoFeTaB
films without Pt; shown in the figure below.
Fig. 1. Magneto-optical Kerr effect hysteresis loops for CoFeTaB and CoFeTaB/Pt.
[1] H. Nakayama et al. PRL 110, 206601 (2013).
[2] N. Vlietstra et al. Phys. Rev. B 87, 184421 (2013).
32
Durham UK–India Workshop on Magnetisation Processes 2015
Poster P5
The POLREF Polarised Neutron Reflectometer: In-depth Structural and Magnetic Characterisation
of Magnetic Thin Films
C. J. Kinane, T. R Charlton, R. M. Dalgliesh and Sean Langridge
ISIS Facility, Rutherford Appleton Laboratory, Chilton, Oxfordshire, OX11 0QX, United Kingdom
POLREF is a polarised neutron reflectometer situated on the second target station 2 at the ISIS neutron source in
Oxfordshire, UK. It is designed for studying the inter and intra layer magnetic ordering of surfaces and thin film
systems. These magnetic systems lie at the heart of many of the technological devices that are now being
developed in areas such as computer storage media, field sensing, energy harvesting, spintronics,
superconducting devices, ferroelectrics, polymers and multiferroic materials to name a few. The proviso being
that if you can make a uniform thin film of reasonable area (8 x 8 mm or bigger) then the POLREF beamline
shown schematically in figure 1 a) can be used to study it. It does this via Polarised Neutron Reflectometry
(PNR) which is a technique well matched to the investigation of such systems, providing unique information in
both absolute depth and in-plane magnetometry, as well as imaging and magnetic/structural characterisation of
buried interfaces and layers. Due to the unique nature of the scattering length for neutrons across the periodic
table it can also provide excellent structural characterisation when dealing with light elements as compared to xray reflectometry.
POLREF is a next generation reflectometer its advantages over the 25year old CRISP reflectometer being
increased flux (x3), Q range (x2.5) and a low background (x10-1) as shown in figure 1 b) below. This coupled
with an innovative sample point design allows for a whole new range of sample environment, <1K fridges, High
temperature furnaces and high magnetic (+7.5T) and vector field geometries (3D 2T). This opens up new
research areas to exploration with polarised neutron scattering.
This poster hopes to give an over view of the capabilities of the POLREF machine and its new sample
environment, as well as explain what information can be obtained from its three primary operating modes,
neutron reflectivity/polarised neutron reflectivity and polarisation analysis, for magnetic and non-magnetic thin
films.
a)
b)
Figure 1: a) Schematic of the POLREF beamline based on Target Station 2 at the ISIS neutron spallation
source. B) Figure showing the increase in Flux/Q range and better background as compared to the older
CRISP machine based on TS1.
33
Poster P6
Durham UK–India Workshop on Magnetisation Processes 2015
Characterisation of Néel Transitions in Heusler Alloys
J.Sinclair*, T.Huminiuc, H.J. Wu, G.Vallejo-Fernandez and A.Hirohata
Department of Physics, University of York, Heslington, York, YO10 5DD, UK
*Email: js946@york.ac.uk
In the past few years there has been a large increase in demand for Iridium due to its applications in
magnetic memory and storage. This is due to its ability to form a sheet antiferromagnet with a
blocking temperature above 300K when combined with Manganese. Unfortunately as a consequence
of this increase in demand for Iridium, the price has soared making it necessary to explore other
options for creation of antiferromagnetic layers in spintronic devices.
The most promising group of materials for this application are Heusler alloys with a number predicted
to exist in an antiferromagnetic state [1]. To achieve this it will be necessary to characterise the
magnetic ordering temperatures of the alloys of interest, namely Ni2MnAl and Fe2VAl. Sheet
resistance measurements are achieved using 4 point measurement with Van der Pauw geometry in an
Oxford Instruments cryostat, to increase our testing capabilities much of the procedure has been
automated. This will allow measurement of the Néel temperature for the two alloys mentioned above
and also exploration of the dependence of the Néel temperature on annealing time and crystallinity.
These properties are controlled through the use of a vacuum annealing furnace and deposition
parameters on the HiTUS sputter deposition system used to produce the films.
m (emu x 10^-6)
6
4
2
0
-2
-4
-6
-1000 -500
0
500
H (Oe)
1000
Figure 1 - Temperature dependence of resistance and magnetisation data for a Ni2MnAl film, showing a clear transition to
the AF state at ~180K with little variation with temperature sweep speed and direction. AGFM measurement at 300K
showing ferromagnetic behaviour with a magnetisation of 7.20emu cm-3.
[1] Singh and Mazin, Phys. Rev. B 57, (2011)
34
Durham UK–India Workshop on Magnetisation Processes 2015
Poster P7
Control of the magnetic vortex chirality in Permalloy nanowires with
Asymmetric notches
J. Brandao*,a) R.L. Novak, H. Lozano, P. R. Soledade, A. Mello, F. Garcia, and L. C. Sampaio
Centro Brasileiro de Pesquisas Físicas, Xavier Sigaud, 150, Rio de Janeiro 22.290-180, Brazil
a) Present Address: Department of Physics, Durham University, Durham, DH1 3LE, United
Kingdom
*Email: jeobrandao@email.com
We have investigated the motion of vortex domain walls passing across non symmetric triangular
notches in single Permalloy nanowires. We have measured hysteresis cycles using the focused
magneto-optical Kerr effect before and beyond the notch, which allowed to probe beyond the notch
the occurrence probability of clockwise (CW) and counter – clockwise (CCW) walls in tail-to-tail
(TT) and head-to-head (HH) configurations. We present experimental evidence of chirality flipping
provided by the vortex-notch interaction. With a low exit angle, the probability of chirality flipping
increases and here with the lowest angle 15 (degrees), the probability of propagation of the
energetically favored domain wall configuration (CCW for TT or CW for HH walls) is ≈ 75 %.
Micromagnetic simulations reveal details of the chirality reversal dynamics.
[1] J. Brandao, R.L. Novak, H. Lozano, P. R. Soledade, A. Mello, F. Garcia, and L. C. Sampaio.
Journal of Applied Physics 116, 193902 (2014).
35
Poster P8
Durham UK–India Workshop on Magnetisation Processes 2015
Racetrack Memory Using Exchange Bias
I. Polenciuc1, A. J. Vick1, D. A. Allwood2, T. J. Hayward2, G. Vallejo-Fernandez1,
A. Hirohata 3,4 and K. O’Grady 1
1
Dept. of Physics, University of York, Heslington, York YO10 5DD.
Dept. of Materials Science and Engineering, University of Sheffield, Sheffield S1 3JD.
3
Dept. of Electronics, University of York, Heslington, York YO10 5DD.
4
PRESTO, Japan Science and Technology Agency, Kawaguchi 332-0012, Japan
2
The pinning of domain walls in ferromagnetic (F) wires is one possible technique for the
creation of a solid state magnetic memory [1]. Such a system has been under consideration for
some time but one of the main limitations is the control and non-uniformity of the domain wall
pinning. Techniques such as the lithographic definition of notches and steps in the substrate
have had some success in creating local pins but have the disadvantage of being expensive to
fabricate and the reproducibility of the domain wall pinning strength is limited. In this work
we report on an alternative strategy to create pins of reproducible strength using crossed
ferromagnetic and antiferromagnetic (AF) wires such that exchange bias can be introduced at
the crossing points [2]. Such a system has the advantage of ease of fabrication and creating
domain wall pins of controlled strength by varying the width of the AF wire. We have achieved
domain wall pinning field strengths of up to 37 Oe in a system where the AF wire is deposited
above the F wire which is comparable to the values achieved using notches.
[1]S.S.P. Parkin, M. Hayashi, L. Thomas, Science 320, 190 (2008).
[2]I. Polenciuc, A. J. Vick, D. A. Allwood, T. J. Hayward, G. Vallejo-Fernandez, A. Hirohata and K. O’Grady,
Appl. Phys. Lett. 105, 162406 (2014).
36
Poster P9
Durham UK–India Workshop on Magnetisation Processes 2015
Fluence study of Co2MnSi Thin Films for suitability in spin Seebeck
devices
C. Cox*, A. Caruana, K. Morrison
Physics Department, Loughborough University, Loughborough, UK
The Heusler alloy Co2MnSi (CMS) has been theorised to exhibit 100% spin polarisation at the
Fermi energy1 and as a result is of particular interest in the field of spintronics. More recently, the
observation of the spin Seebeck effect in CMS2 suggests potential energy harvesting applications that
could rival conventional thermoelectric technology.
In this study, CMS thin films were grown on glass substrates by pulsed laser deposition (PLD) as a
function of laser fluence, and the structural and magnetic properties were studied. The impact of the
deposition conditions on key parameters such as the coercive field (see Figure 1) and film structure
will be discussed with regards to the suitability of CMS in spin Seebeck devices.
1.5
Normalised Moment , M/MSAT (Arb. Units)
1
0.5
0
-0.5
-1
-1.5
-400
-300
-200
-100
0
100
200
300
400
Magnetic Field, H (Oe)
Low Laser Fluence (2 Loops)
High Laser Fluence Annealed at 673K (3 Loops)
Low Laser Fluence (3 Loops)
Medium Laser Fluence (3 Loops)
Low Laser Fluence (5 Loops)
High Laser Fluence (3 Loops)
Low Laser Fluence (6 Loops)
Figure 1: Normalised M(H) loops for thin films deposited on glass at 170°C using
different laser fluences and ablation loops.
[1 ]M. Jourdan et al., Nat. Commun. 5, 3974 (2014).
[2] S. Bosu et al., Phys. Rev. B 83, 224401 (2011).
37
Poster P10
Durham UK–India Workshop on Magnetisation Processes 2015
Interfacial Origin of Thickness Dependent In-Plane Anisotropic
Magnetoresistance
M. Tokac*1, M. Wang2, S. Jaiswal1, A. W. Rushforth2, B. L. Gallagher2, D. Atkinson1,
A. T. Hindmarch1
(1) Centre for Materials Physics, Durham University, Durham, DH1 3LE, UK
(2) School of Physics & Astronomy, University of Nottingham, Nottingham, NG7 2RD UK
We have demonstrated an interfacial contribution to the anisotropic scattering which produces the
AMR effect with structures containing an opaque Co/Ir interface. This contribution has scattering
anisotropy which is opposite in sign to the bulk scattering anisotropy. This provides a novel
explanation for the thickness dependence of ∆ρ and the AMR ratio [1].
We have studied in-plane AMR in cobalt films with overlayers having designed interface
transparency [2]. With an opaque interface, the AMR ratio is shown to vary in inverse proportion to the
cobalt film thickness. Interface scattering is found to have opposing anisotropy to volume scattering,
similar to the interfacial contribution to magnetic anisotropies.
Our study into ferromagnetic film-thickness dependence of the AMR in cobalt films uses layers
deposited onto Ta and Cu seed layers for all cobalt thicknesses. This allows us to isolate any
interfacial contribution to AMR from effects due to variations in the film microstructure with cobalt
thickness [3]. In order to isolate the contribution to AMR, we employed structures consisting of
Si/SiO/Ta[3nm]/Cu[3nm]/Co/overlayer[3nm]/Ta[3nm] with cobalt thickness ranging from 2nm to 55
nm and overlayers of either copper or iridium. Due to the similarity between the electronic structure
of copper and cobalt [4], structures with copper overlayers have electrically transparent interfaces, and,
due to the copper seed layers, preserve structural inversion symmetry. The different electronic
structure of iridium in comparison to cobalt means that structures with iridium overlayers have more
electrically opaque interfaces, in addition to broken structural inversion symmetry. Iridium also has
strong spin orbit interaction (larger atomic number), which should enhance any Rashba contribution
to AMR [5]. We show that these multilayered structures allow the isolation of the in-plane AMR
contribution due to the Co/Ir interface.
[1] T. McGuire and R. Potter, IEEE Trans. Mag. 11, 1018 (1975); I. A. Campbell and A. Fert,
“Ferromagnetic materials,” (North- Holland, Amsterdam, 1982)
[2] A. Kobs et al., Phys. Rev. Lett. 106, 217207 (2011)
[3] Th. G. S. M. Rijks et al., Phys. Rev. B 56, 362 (1997)
[4] E. Tysmbal and D. Pettifor, in Solid State Physics, Vol. 56 (Academic Press, 2001) pp. 113-237
[5] M. Trushin et al., Phys. Rev. B 80, 134405 (2009)
38
Durham UK–India Workshop on Magnetisation Processes 2015
Poster P11
Magnetisation reversal behaviour in interconnected artificial spin ice
structures
D.M. Burn*1, M. Chadha1, L.F. Cohen1 and W.R. Branford1
(1) Imperial College London, London, UK
*Email: d.burn@imperial.ac.uk
Magnetic meta-materials exhibit interesting and complex magnetisation behaviour which originates
from nanoscale patterning in addition to the intrinsic properties of the magnetic material. Artificial
spin ice is one such example where an array of magnetic nanowires are connected by vertices to form
a kagome structure. The nucleation and propagation of magnetic domain walls (DWs) is the
predominant magnetisation reversal process for magnetic nanowires. However, complexities in the
behaviour of artificial spin ice systems arise due to DW interactions at the vertices[1,2] and the flow
of magnetic charge throughout system[3].
In this work, spatially resolved magnetisation reversal behaviour in a kagome artificial spin ice
structure is investigated through focussed MOKE magnetometry. With an applied field the nucleation
and propagation of magnetic DWs is observed throughout the array. Varying the applied field
direction relative to symmetry axes in the patterning biases particular sub-lattice directions giving
physical insight into the DW propagation and vertex interactions taking place. Additional localised
pulsed-field injection techniques[4] allow the DW propagation behaviour to be explored at fields
below the intrinsic nucleation field of the system. This allows further characterisation of the DW –
vertex interaction and gives control over the DW nucleation location.
This research builds on our understanding of complex interconnected magnetic systems and opens
pathways to further explore the manipulation of magnetic charges[5] and their use in potential
technological applications.
[1] D. Burn et.al. Phys. Rev. B 90, 144414 (2014).
[2] S.K. Walton et.al. New J. Phys. 17, 013054 (2015).
[3] K. Zeissler et.al. Sci. Rep. 3, 1252 (2013).
[4] D. Burn et.al. Phys. Rev. B 88, 104422 (2013).
[5] E. Mengotti et.al. Nat. Phys. 7, 68 (2010).
We acknowledge Leverhulme Trust grant RPG_2012-692 and UK EPSRC grant EP/G004765/1 for
funding.
39
Poster P12
Durham UK–India Workshop on Magnetisation Processes 2015
Perpendicular Anisotropy in Ultrathin Co based Multilayers aiming for
Enhanced Spin Hall Effect
Kowsar Shahbazi, Thomas A. Moore, Christopher H. Marrows*
Condensed Matter Group, School of Physics and Astronomy, University of Leeds
*Email: C.H.Marrows@leeds.ac.uk
Spintronic devices need to make use of larger spin currents every day, and spin Hall effect is a major
source of these kind of currents. Spin Hall angle is the term which shows effectiveness of induced
spin current in such devices and increasing this term in a perpendicularly magnetized thin film stack is
favourable. Having an ultrathin ferromagnet sandwiched by dissimilar heavy metals with opposite
spin Hall angles would cause a substantial enhancement to the spin Hall effect. For example, growing
β-Ta in one side of the ferromagnetic layer and Pt on the other would give us a big SHA, as spin Hall
angle of β-Ta and Pt are both large, and opposite. Spin Hall Effect and other interactions such as DMI
and Rashba -which are very important in new logic and storage devices- believed to be stronger in
systems with perpendicular magnetic anisotropy. As the first step of working towards this goal, we
investigate different combinations of three layer structures (SiO2/HM1/FM/HM2) to get a
perpendicular anisotropy. Multilayer structures of SiO2/Ta/CoFeB/Pt using 3 different combinations
of Co, Fe and B were failed to have out-of-plane anisotropy (also tried Ta/Pt/CoFeB/Ta), but fill in Co
instead of CoFeB and inverting the stack, we had soft perpendicularly magnetized multilayers as
desired. Strangely, Ta/Co/Pt multilayers on SiO2 had in-Plane anisotropy which suggests probable
inter-diffusion of Co and Ta layers and needs more investigation.
1
SiO2/Ta(20)/Pt(21.8)/Co(x)/Ta(40)
0
Co Thickness
7.0 Å
7.8 Å
8.6 Å
9.5 Å
10.2 Å
11.0 Å
11.8 Å
12.5 Å
-1
-16
-14
-12
-10
-8
-6
-4
-2
0
2
4
6
8
10
12
Magnetic Field (mT)
Figure: Polar laser MOKE loops of SiO2/Ta(20Å)/Pt(20Å)/Co(x)/Ta(40Å) multilayers confirming
perpendicular magnetic anisotropy of the samples.
40
Poster P13
Durham UK–India Workshop on Magnetisation Processes 2015
Manipulation of magnetic damping by the focused ion-beam irradiation
induced intermixing of ferromagnetic/non-magnetic bilayers
J.A. King*1, A. Ganguly2, D. M. Burn1, S. Pal2, E.A. Sallabank1, T.P.A. Hase3, A.T. Hindmarch1, A.
Barman2 and D Atkinson1
(1) Department of Physics, Durham University, Durham, DH1 3LE, UK
(2) S.N. Bose National Centre for Basic Sciences, Salt Lake, Kolkata 700 098, India
(3) Department of Physics, University of Warwick, Coventry, C4 7AL, UK
*Email: jennifer.king@durham.ac.uk
The control and understanding of magnetic damping is technologically desirable. For spin-transfer
torque magnetic random access memory (STT-MRAM) and magnonic devices, lower damping allows
a lower writing current and longer propagation of spin waves, while increased damping increases
reversal rates and facilitates coherent reversal for fast switching in recording. In this work the
influence of interfacial intermixing on the picosecond magnetization dynamics of ferromagnetic/nonmagnetic thin-film bilayers was studied. Low-dose focused-ion beam (Ga+) irradiation was used to
induce intermixing across the interface between a 10 nm Ni81Fe19 layer and a 2-3 nm capping layer of
either Au or Cr. Time-resolved magneto-optical Kerr Effect magnetometry was used to study
magnetization dynamics as a function of ion-beam dose. With a Au cap the damping of the unirradiated bilayer was comparable with native Ni81Fe19 and increased with increasing ion dose. In
contrast, for Ni81Fe19/Cr the damping was higher than that for native Ni81Fe19 but the damping
subsequently decreased with increasing dose.
The high spatial resolution of the FIB technique combined with the capacity of very low irradiation
doses to cause intermixing offers the ability to locally modify the precessional magnetisation
behaviour of ferromagnetic materials on a micro- or nano-scale.
(a)
(b)
Figure 1. The damping coefficient, α, obtained from the TR-MOKE data as a function of FIB dose at
H = 1.5 kOe for (a) NiFe/Au bilayer (error bars are smaller than the data points), (b) NiFe/Cr bilayer.
41
Poster P14
Durham UK–India Workshop on Magnetisation Processes 2015
Understanding the proximity induced magnetism in Pt using interface
engineering through the addition of heavy metal interlayers
R.M. Rowan-Robinson1, M. Bjӧrck2, T.P. Hase3, A.T. Hindmarch1, D. Atkinson1
1
Department of Physics, Durham University, Durham DH1 3LE, United Kingdom
Department of Physics and Astronomy, Uppsala University, Box 516, SE-75120, Uppsala, Sweden
3
Department of Physics, University of Warwick, Coventry CV4 7AL, United Kingdom
2
Measurements by S. Parkin1 on Pt/ferromagnetic structures showed that domain wall velocities fell
rapidly as Au insertion layers were added at the interface. This hinted at the importance of proximity
induced magnetism for the Dzyaloshinkii-Moriya interaction.
Using X-ray resonant magnetic reflectivity (XRMR) on Pt/Co/Pt trilayer structures, we have measured
the proximity induced magnetization in the Pt for different Au and Ir spacer layer thicknesses. XRMR
was performed at the Pt L 3 edge and therefore only sensitive to the Pt magnetic moment. The technique
has depth sensitivity, and therefore direct comparison between the top and bottom Pt moments can be
made, combined with information on their respective structure.
Fits to the data show that even with no spacer, the induced moments at the Pt interfaces are asymmetric,
with a larger moment on the top Pt compared to the buffer Pt interface. Top Pt moment vanished rapidly
as spacer layer thickness is increased. The loss of moment is more rapid for Ir spacers, vanishing by
7Ȧ. This coincides with the thickness at which the sign of the DMI has been observed to reverse
entirely2. For the Au interlayers the moment persists longer, but decays on a length-scale consistent
with reduced current driven domain wall velocities observed by S. Parkin1.
Figure 1: Left: Scattering length density (SLD) profiles showing cross
sections through three sample, a) no spacer, b) Au(2.5Ȧ ), c) Au( 10Ȧ)
spacer layers. Black lines show the chemical SLD whereas the red lines
show the magnetic SLD, which is directly related to the induced moment
on the Pt. Above: ratio of areas under the magnetic SLD as spacer layer
thickness between the Co and top Pt layer is increased.
1. S. P. Parkin et al. Nat. Comms., 5, 3910 (2014)
2. A. Hrabec et al, Phys. Rev. B, 90, 020402(R) (2014)
42
Durham UK–India Workshop on Magnetisation Processes 2015
Poster P15
Spin Current Induced Modulation of Damping in Platinum-Permalloy
bilayer film using Time Resolved Kerr Microscopy
A. Ganguly1, R.M. Rowan-Robinson2, A. Haldar1, S. Jaiswal2, J. Sinha1, A. T. Hindmarch2,
D. A. Atkinson2, A. Barman1
1
Thematic Unit of Excellence on Nanodevice Technology, Department of Condensed Matter Physics
and Material Sciences, S. N. Bose National Centre for Basic Sciences, Kolkata 700098, India
2
Department of Physics, Durham University, South Road, Durham, DH1 3LE, UK
*Email: abarman@bose.res.in, del.atkinson@durham.ac.uk
Spin current can manipulate magnetization in Non-magnetic/ferromagnetic bi-layer film which can be
used in spintronics based devices. Spin Hall effect in large spin orbit coupling materials as a source of
pure spin current has been studied recently using spin torque ferromagnetic resonance. Here we use
time resolved Magneto-optical Kerr effect (TR-MOKE) technique to investigate the effect of spin
current generated due to spin Hall effect in Pt/Py bilayer stack via modulation of effective damping.
In our experiment, thin film stack of Pt (6.8 nm)/Py (12.7 nm)/MgO (2.4 nm) is sputter deposited on
Si substrate. A rectangular shaped sample of length 5mm and width 1.5mm is deposited through a
shadow mask along with Pt contact pads designed for applying current. The magnetization dynamics
is measured by using an all-optical TR-MOKE microscope [1] with 10 mJ/cm2 pump (λ = 400 nm,
pulsewidth = 100 fs) and 1.5 mJ/cm2 probe (λ = 800 nm, pulsewidth = 70 fs) and spot diameter of
~1μm.
In case of Pt/Py bi-layer stack the damping coefficient estimated in our experiment is ~0.021 which is
about two times larger than Py film of nearly same thickness. Enhanced value of damping is likely
due to the spin pumping effect [2]. Application of dc current along the length of the sample creates
spin current in Pt underlayer in a direction perpendicular to the flow of charge current due to spin Hall
effect. Injected spin current exerts spin torque on Py layer which modulates the effective value of
damping () [3]. With varying current density we observe linear variation of eff up to ~7% as shown
in Fig. 1 in case of θ= 90O, where θ is the angle between applied magnetic field and current. We
estimate the spin Hall angle for Pt to be 0.11±0.03 consistent with earlier reported values [4, 5]. We
also discuss the rate of modulation of damping as a function θ.
0.022

0.021
 90o
 45o
 0o
Fig.1: The variation of α with Jc for
magnetic fields oriented at angle θ= 0O,
45O and 90O with respect to the current
0.020
direction.
0.019
-1.2 -0.6 0.0 0.6
JC(1010A/m2)
1.2
[1] B. Rana et al, ACS Nano 5, 9559 (2011).
[2] Y. Tserkovnyak et al, Phys. Rev. Lett. 88, 117601 (2002).
[3] A. Ganguly et al, App. Phys. Lett. 104, 072405 (2014).
[4] L. Q. Liu et al, Phys. Rev. Lett. 106, 036601
[5] A. Ganguly et al, App. Phys. Lett. 105, 112409 (2014).
43
Poster P16
Durham UK–India Workshop on Magnetisation Processes 2015
Controlled Magnetization Dynamics in Ion Irradiated Ni81Fe19/Pt
A. Ganguly1, J. Sinha1, J.A. King2, R. Rowan-Robinson2, A.T. Hindmarch2,
D. Atkinson2 and A. Barman1
1
Thematic Unit of Excellence on Nanodevice Technology, Department of Condensed Matter Physics
and Material Sciences, S. N. Bose National Centre for Basic Sciences, Kolkata 700098, India
2
Department of Physics, Durham University, South Road, Durham, DH1 3LE, UK
*Email: abarman@bose.res.in, del.atkinson@durham.ac.uk
Study on magnetic multilayers reveal interesting phenomena like spin dependent scattering,
hybridization, spin injection, spin pumping where interface plays a crucial role in controlling
magnetic properties. In this work we present interface engineering of Ni 81Fe19(10 nm)/Pt(3 nm)
bilayer stack by low dose Ga+ ion irradiation using focused ion beam (FIB). Time resolved magnetooptical Kerr microscopy1 (TR-MOKE) is used to investigate the effective damping and precession
frequency in Ga+ ion irradiated films.
Figure 1(a) shows representative TR-MOKE data (open circles) obtained from Py/Pt with d = 0.3
pC/µm2 at H = 1.8 kOe where we observe a single mode oscillation decaying with time. An analytical
best fit (red curve) to the data is also shown in Fig. 1(a) and yields values for α ~ 0.042 and f ~ 13.28
GHz. Using the Kittel formula for uniform precession frequency, where γ = 1.76×1011 Hz/T, the
dependence of f on H was fitted and a value for the saturation magnetization was determined as MS ~
830 emu/cc. Fig. 1(b) shows the dependence of α on d where the top x-axis shows the number density
of incident Ga+ ions. A monotonic increase in the damping α was observed with dose up to a value of
dC=2.3 pC/µm2 (Region I). Above this dose α decreases with further increase in d (Region II). To
highlight detail, region I is expanded and the data is compared with a Py (10nm)/ Cu (3nm) in Fig.
1(c). Interestingly, in both cases α increases linearly at nearly same rate ~0.015 µm2/pC, but with a
constant shift of 0.019 to the higher side of α in case of the Py/Pt. Spin pumping due to strong spin
orbit coupling2 (SOC) of Pt at Py/Pt interface may explain the origin of this larger α. On the other
hand, Py/Cu approaches α = 0.015 which corresponds to single layer Py, suggesting negligible SOC at
the interface. However, SOC cannot explain the observed linear increase in α with d which is common
to both the samples. Due to ion irradiation, metal atoms may be dislocated into the Py interface giving
rise to an extrinsic two magnon type scattering3 which causes an enhancement in α. The effect
increases with increasing number of dislocated atoms, resulting in a linear variation of α with d. In
region II of Fig. 1(b), where the α decreases with d, moderately high value of d may result in an
interfacial intermixing and subsequent alloying over few nanometers of thickness at the interface.
This may effectively reduce the spin pumping efficiency significantly leading to a recovery of α. In
this region extrinsic effects are likely to be present and may probably saturate which is understood by
the enhancement of α with reduction of H. Concurrent with the change in α at dC a change in the
behavior of dependence of f on d will be discussed, as shown in Fig. 1(d).
1)A. Barman and A. Haldar, Solid State Physics (Academic Press, Burlington, 2014), Vol. 65, pp. 1–
108. 2) S. Mizukami et. al, J. Magn. Magn. Mater. 226, 1640 (2001). 3) J. A. King et. al, Appl. Phys.
Lett. 104, 242410 (2014).
0.0
0.2
0.060
  Ae  / t sin(2ft   )
f  Frequency
  1 / 2f  Damping
0.045
0.6
Time:t (ns)
0.8
1.0
Py(10nm)/Pt(3nm)
0.040
0
24.8
0.054
Region II
Region I
0.048
(b)
0.042
0.055
0.050
0.4
2
13.5
Py(10 nm)/Cu(3 nm)
Py(10 nm)/Pt(3 nm)
Py(10nm)/Pt(3nm)
13.0
(c)
0.036
2
3
2
d (pC/m )
Region II
0.024
11.5
0.018
1
dC
12.0 Region I
0.030
dC
(d)
12.5

 =0.042
(a)
0.065
+
f (GHz)
2
d =0.3 pC/m
f =13.28 GHz

Kerr Rotation: (arb. unit)
6
d (x10 Ga ion/m )
6.2
12.4
18.6
0.0
4
0.0
0.2 0.4 2 0.6
d (pC/m )
0.8
0
1
2
2 3
d (pC/m )
Fig. 1. (a) TR-MOKE spectrum of Py/Pt sample with dose 0.3 pC/µm2, (b) damping as function of
irradiation dose, (c) comparison of damping as function of irradiation dose at lower dose region and
(d) frequency as a function of irradiation dose in case of Py/Pt.
44
4
Poster P16
Durham UK–India Workshop on Magnetisation Processes 2015
Attendees
Del Atkinson
Sinan Azzawi
Anjan Barman
Durham University
Durham University
S.N. Bose National Center for Basic Sciences,
Kolkata, India
Subhankar Bedanta
National Institute of Science Education and Research,
Bhubaneswar, India
Stuart Bowe
University of Nottingham
Jeovani Brand˜ao
Durham University
Will Branford
Imperial College London
David Burn
Imperial College London
Andrew Caruana
Loughborough University
Stuart Cavill
University of York
Oscar C´espedes
University of Leeds
Chloe Cope
Durham University
Chris Cox
Loughborough University
Andrew Ferguson
University of Cambridge
Damian Hampshire
Durham University
Peter Hatton
Durham University
Tom Hayward
University of Sheffield
Aidan Hindmarch
Durham University
Oto-obong Inyang
Durham University
Olof Johansson
University of Edinburgh
Paul Keatley
University of Exeter
Christy Kinane
STFC ISIS neutron facility
Jenny King
Durham University
Tom Lancaster
Durham University
Josh Lay
Mantis Deposition Ltd
Damien McGrouther
University of Glasgow
Pranaba Kishor Muduli
Indian Institute of Technology, Delhi, India
Kevin O’Grady
University of York
Ioan Polenciuc
University of York
Dan Read
University of Cardiff
Alex Roper
Durham University
Richard Rowan-Robinson Durham University
Andrew Rushforth
University of Nottingham
Kowsar Shahbazi
University of Leeds
John Sinclair
University of York
Jaivardhan Sinha
S.N. Bose National Center for Basic Sciences,
Kolkata, India
Charles Spencer
University of Leeds
Brian Tanner
Durham University
Rowan Temple
University of Leeds
Mustafa Tokac¸
Durham University
Gonzalo Vallejo-Fernandez University of York
Mark Vaughan
Mantis Deposition Ltd
James Whicker
Durham University
del.atkinson@durham.ac.uk
s.a.r.hammoodi-azzawi@durham.ac.uk
abarman@bose.res.in
sbedanta@niser.ac.in
ppxsb3@nottingham.ac.uk
jeobrandao@gmail.com
w.branford@imperial.ac.uk
d.burn@imperial.ac.uk
a.j.caruana@lboro.ac.uk
stuart.cavill@york.ac.uk
o.cespedes@leeds.ac.uk
chloe.cope@durham.ac.uk
c.d.w.cox@lboro.ac.uk
ajf1006@cam.ac.uk
d.p.hampshire@durham.ac.uk
p.d.hatton@durham.ac.uk
t.hayward@sheffield.ac.uk
a.t.hindmarch@durham.ac.uk
o.o.a.inyang@durham.ac.uk
olof.johansson@ed.ac.uk
p.s.keatley@exeter.ac.uk
christy.kinane@stfc.ac.uk
jennifer.king@durham.ac.uk
tom.lancaster@durham.ac.uk
joshua.lay@mantisdeposition.com
damien.mcgrouther@glasgow.ac.uk
muduli@physics.iitd.ernet.in
kevin.ogrady@york.ac.uk
ip558@york.ac.uk
readde@cardiff.ac.uk
a.j.roper@durham.ac.uk
r.m.rowan-robinson@durham.ac.uk
andrew.rushforth@nottingham.ac.uk
pyks@leeds.ac.uk
js946@york.ac.uk
jaivardhan.sinha@gmail.com
pycs@leeds.ac.uk
b.k.tanner@durham.ac.uk
pyrct@leeds.ac.uk
mustafa.tokac@durham.ac.uk
gonzalo.vallejofernandez@york.ac.uk
mark.vaughan@mantisdeposition.com
j.j.whicker@durham.ac.uk
Schedule