Intern
ati
o
n
a
l
Jo
urn
a
l
o
f
Ad
va
nces
in Applied Sciences (IJ
A
AS)
Vol.
2, No. 4, Decem
ber
2013, pp. 205~
208
I
S
SN
: 225
2-8
8
1
4
2
05
Jo
urn
a
l
h
o
me
pa
ge
: h
ttp
://iaesjo
u
r
na
l.com/
o
n
lin
e/ind
e
x.ph
p
/
IJAAS
Martens
i
tic T
r
an
sformati
on Ch
aracteristi
c
of Ni-
M
n Bas
e
d
Ferromagnetic Shape Memory Alloys
Ajit
Beher
a
1
, Asit
Beh
era
2
, S
.
C.
M
i
sh
ra
3
1
Departem
ent
of
Metallurgi
c
al and Mater
i
als
En
gineer
ing, Indian Institut
e
of
T
e
chnolog
y
,
Kharagpur-721302
2
Departement of
Mechan
ical
Eng
i
neer
ing, Natio
n
a
l Institute of
Technolog
y
,
Rourk
e
la-769008
3
Departement of
Metallurgical and Mater
i
als
En
gineer
i
ng, Natio
nal Institute of
Technolog
y
,
Rour
kela-769008
Article Info
A
B
STRAC
T
Article histo
r
y:
Received Feb 6, 2013
Rev
i
sed
Au
g
23
, 20
13
Accepte
d
Se
p 3, 2013
Fe
rroma
gne
t
i
c
sha
p
e
me
mory
al
l
o
y
s
e
m
erge
as new func
ti
ona
l ma
t
e
ri
al
s
which have in
teresting magnetomechan
ic
al co
upling effe
cts
s
u
ch as
the
ferrom
a
gneti
c s
h
ape m
e
m
o
r
y
e
ffect
. Th
es
e t
y
p
e
s
of m
a
teri
als
s
i
gnific
a
nt
l
y
change
their sh
ape and dimensions under
the application of
ex
ternal fields
i.e. either b
y
using thermal en
er
g
y
or magnetic
energ
y
. Among them, some
are th
e m
a
gnet
o
s
t
rictiv
e a
llo
y
s
which in turn
can ch
ange th
ei
r s
h
ape
b
y
magnetic f
i
eld u
p
to 0.1 p
e
rcent
and b
y
m
echan
i
cal s
t
r
e
s
s
up to 1
0
perc
ent in
m
a
rtens
iti
c s
t
a
t
e
.
Up to 6 p
e
rc
e
n
t deform
at
ion
can b
e
obt
ained
in m
a
ter
i
als
under the
actio
n of the magnetic fiel
d which
undergo the
thermoelastic
transformation into ferromagnetic phase
. Due
to
higher processing cost and
costly
elements
for allo
y
i
ng, ferr
oma
gnetic shape memory
allo
y
h
a
ve not so
broadly
utilization and sa
tisfactorily
use. Among differ
e
nt ty
p
e
of Ni-Mn
based Heusler f
e
rromagnetic shape memo
r
y
allo
y
s
, Ni-Mn-Sn allo
y
hav
e
potential proper
ties and exhib
i
ts lowe
r cost. In this paper martensitic
transformation o
f
Ni
50
Mn
50-
y
Sn
y
(
y
= 5, 10, 12.5)
allo
y
s
wer
e
inv
e
stigated
.
B
y
differen
tia
l s
can
ning calorim
e
t
ri
c m
eas
urem
ent, it has
been obs
erved that
,
b
y
keeping on
e e
l
e
m
ent i.e
.
Ni
as c
onstant weigh
t
p
e
rcen
tag
e
, if
we
incre
a
se th
e
weight per
cent
of S
n
; then
m
a
rtens
iti
c s
t
art
i
ng tem
p
era
t
ure
as
well a
s
aus
t
enit
ic
s
t
art
i
n
g
tem
p
era
t
ure
gr
adual
l
y
de
cre
a
s
e
s
.
Keyword:
Au
sten
itic Tran
sfo
r
m
a
tio
n
Ferr
om
agnet
i
c
Sha
p
e M
e
m
o
ry
Allo
ys (FSMAs)
Marten
sitic Tran
sform
a
t
i
o
n
Ni-M
n
-
S
n
Copyright ©
201
3 Institut
e
o
f
Ad
vanced
Engin
eer
ing and S
c
i
e
nce.
All rights re
se
rve
d
.
Co
rresp
ond
i
ng
Autho
r
:
Aj
it Beh
e
ra,
Dep
a
rtem
en
t o
f
Metallu
rg
ical
and
Materials Engineeri
n
g,
Ind
i
an In
stitu
te of Tech
no
log
y
,
K
h
ar
ag
pu
r-7
213
02
.
Em
a
il: aj
it.b
e
hera88
@g
m
a
il.c
o
m
1.
INTRODUCTION
The cha
r
act
eri
s
t
i
c
behavi
or o
f
fer
r
om
agnet
i
c
shap
e m
e
m
o
ry allo
ys (FSMAs) is, b
y
co
m
b
in
ing
shap
e
m
e
m
o
ry
effect (SM
E
) an
d
the bul
k fer
r
om
agnetic
be
havi
or
. FSM
As ha
ve bee
n
use
d
as p
o
t
e
nt
i
a
l
microactuator
materials because they
show
a large
rec
ove
ry strain
upt
o
10
% a
n
d a
high
respondi
ng fre
que
ncy
(KHz)
[1]-[4]. New alloy syste
m
s are
investigated in this
decade
,
which exhibits
m
a
g
n
etic shape me
m
o
ry
related
p
h
e
nomen
a. Magn
et
ic sh
ap
e m
e
mo
ry effect i
n
th
ese m
a
terial
s inv
o
l
v
e
s th
e m
o
v
e
m
e
n
t
o
f
twin
bo
u
nda
ri
es
w
h
i
c
h re
sul
t
s
i
n
t
h
e
gr
o
w
t
h
o
f
o
n
e
of
t
h
e
t
w
i
n
vari
a
n
t
s
at
t
h
e
expe
nse
o
f
t
h
e
ot
her
i
n
res
p
o
n
se t
o
an
app
lied
m
a
g
n
e
tic field
belo
w th
e m
a
rte
n
sitic tran
sf
o
r
matio
n
te
m
p
eratu
r
e [5
]. Formatio
n
o
f
m
a
rten
site
varia
n
t is accom
p
anied by a
defi
ned s
h
a
p
e
strain; the m
i
crosc
opic s
h
ape
of t
h
e m
a
terial doe
s not change as a
whole be
fore or afte
r the transform
a
tion. T
h
is is becau
se of
self-accom
odation of
m
a
rtensite form
ation [6]
.
Sto
i
ch
io
m
e
tric Ni-M
n
-
Ga
h
e
u
s
ler allo
y i
nvo
lv
ing
co
m
p
le
te sub
s
titu
tio
n
o
f
Ga with Sn
, wh
ere cho
s
en
fro
m
a
num
ber of candidate alloys exhi
biting
m
a
rt
ensitic transformation as suggested
by
Wutting et al [4]. In recent
st
udy
Ni
-M
n
base
d He
usl
e
r
al
l
o
y
s
have b
een f
o
cu
s as one
of t
h
e t
y
pi
cal
m
a
gnet
o
cal
ori
c
effe
ct
m
a
t
e
ri
al
.
Am
ong t
h
em
, i
t
i
s
fou
nd t
h
at
Ni
-M
n
-
S
n
FS
M
A
i
s
a l
e
ss cost
m
a
t
e
ri
al
due t
o
l
e
sser c
o
st
of S
n
el
em
ent
.
B
y
Evaluation Warning : The document was created with Spire.PDF for Python.
I
S
SN
:
2
252
-88
14
IJAAS
Vol. 2, No.
4, Decem
ber :
205
–
208
20
6
co
nsid
eri
n
g
cost, th
e go
al o
f
th
is in
v
e
stig
atio
n
is to
find a
m
a
g
n
e
tic al
lo
y ex
h
i
b
itin
g a
m
a
rten
sitic
p
h
a
se
trans
f
orm
a
tion that woul
d provi
de
a
large cont
rollable displacem
ent
with
the a
pplication
of l
o
w m
a
gnetic
field at reas
onable operating te
m
p
erature
.
In m
a
ny
expe
r
i
m
e
nt
Ni
-M
n-
Ga al
l
o
y
s
are
widely exam
ined for
wh
ich
it serv
es as a
referen
c
e
allo
y. Bu
t th
e
h
u
s
ler
allo
ys t
h
e cho
i
ce of
Ni-Mn
-
Sn
allo
y is du
e to
:
(i)
Ni-Mn-Sn
n
o
t
ex
p
e
n
s
i
v
e
as galliu
m
,
(ii)
It do
es
no
t contain
to
x
i
c as that o
f
g
a
lliu
m
[7
],
(iii)
Ni-Mn-Sn
is less br
ittle th
an
Ni-Mn-Ga [8
],
(iv)
Low tra
n
sformation a
n
d Curi
e te
m
p
erature
of
stoichi
o
m
e
tr
ic Ni-M
n
-
Ga t
h
an
Ni
-M
n
-
S
n
,
(v
)
The aust
e
n
i
t
e
and m
a
rt
ensi
t
e
phase
of Ni
-
M
n-S
n
ha
ve the sa
m
e
crystal structure as the corre
spondi
ng
pha
ses
of
Ni
-
M
n-
Ga a
n
d
ha
ve t
h
e
sam
e
m
a
gnet
i
cal
l
y
easy
axi
s
[
5
]
,
(vi
)
Ni
-M
n
-
S
n
al
l
o
y
s
are kn
ow
n t
o
ha
ve com
p
ar
abl
y
hi
gh L
2
1
/ tetrag
on
al tran
sitio
n
te
m
p
erature as that of
Ni-M
n
-
Ga
,
(v
ii)
Sto
i
ch
io
m
e
tric o
f
Ni-M
n
-
Sn
allo
ys rev
e
als si
m
ilar
mag
n
e
t
o
strictiv
e b
e
h
a
v
i
o
r
wi
th
resp
ect to
te
m
p
erature
as
that of
Ni-M
n
-
Ga
alloy
s
[5]
,
(v
iii)
Ni-Mn-Ga alloys are insu
ffici
en
t fo
r FSM
A
actu
a
to
rs [9
].
2.
E
X
PERI
MEN
T
AL PR
O
C
EDU
R
E
A tern
ary in
termetall
i
c p
o
l
ycrystallin
e co
m
p
o
und
series
o
f
Ni
50
Mn
50-
y
Sn
y
(y
= 5,
10
, 1
2
.
5
) F
S
M
A
s
Heusl
e
r al
l
o
y
was pr
epa
r
ed
by
no
n-c
o
ns
u
m
abl
e
arc-m
e
l
t
i
ng. T
h
e com
m
e
rci
a
l
puri
t
y
of us
ed Ni
, M
n
, Sn a
r
e
99
.9
5%
,
99
.9
% an
d
9
9
.
9
9
%
res
p
ect
i
v
el
y
.
The
m
e
lt
i
ng
was ca
rri
e
d
o
u
t
un
der
hi
gh
p
u
r
i
t
y
atm
o
sp
he
re
(99
.
99
6
%
). For th
e
p
r
ep
arati
o
n
o
f
allo
y in
go
t, th
e m
e
lti
ng cham
ber was
evacuate
d
to a
press
u
re of
10-5 torr
an
d
t
h
en
w
a
s pu
rg
ed
w
ith pu
re ar
gon
. Th
e
pr
o
cess of
ev
acu
a
tio
n and
p
u
rg
ing
was r
e
p
e
ated
up
to
t
h
r
e
e
ti
m
e
s.
The m
e
lting was carried out in an
argon atm
o
sphere a
nd at a chamber
p
r
essur
e
of
n
ear
ly 10
-5
to
rr
.
Fo
r
co
m
p
lete h
o
m
o
g
e
n
i
zation
of th
e allo
y, th
e en
tire m
e
l
ti
ng proces
s was
repeated seve
ral times. Then t
h
e alloy
was cast in
to
a rod
fo
rm
sho
w
n
in
Figu
re 1
.
Th
is
co
m
p
o
s
ition
tran
sfo
r
m
s
Marten
site at ro
o
m
te
mp
erat
u
r
e
(Ms=
6
7
°C)
with
Marten
sitic Cu
rie tem
p
eratu
r
e, Tc cl
o
s
e t
o
roo
m
te
m
p
eratu
r
e
(1
4°C).
Th
e i
n
go
t
was
sealed
in
a q
u
a
rtz amp
o
u
l
e filled
wi
th
h
e
liu
m
g
a
s
an
d
so
lu
tion
i
zed
at 1
0
0
0
°C for 2
4
h
our for ho
m
o
g
e
n
i
zation. Th
e
Martensitic and auste
n
itic transform
a
t
i
ons in these alloys successfully
characterize
d
by usi
ng
Optical
M
i
crosc
opy
a
n
d
Di
ffe
re
nt
i
a
l
Scan
ni
n
g
C
a
l
o
ri
m
e
t
r
y
.
Fi
gu
re
1.
Pre
p
a
r
ed
sam
p
l
e
of
Ni
50
Mn
37
.5
Sn
12.5
Heusler
FS
M
A
3.
RESULTS
A
N
D
DI
SC
US
S
I
ON
3.
1.
Op
ti
cal
Mi
crosc
op
y
In
t
h
e Fi
g
u
re
2(a), d
i
fferen
t
marten
sitic lay
e
rs are
presen
t
with
d
i
fferen
t o
r
ie
n
t
atio
n
i
n
each
g
r
ai
n
o
f
the sam
p
le at room
te
m
p
erature.
T
h
e
phas
e
trans
f
o
r
m
a
tio
n
resu
lts
fro
m
a coo
p
e
rativ
e an
d co
llectiv
e
m
o
t
i
o
n
o
f
ato
m
s o
n
d
i
stan
ces sm
al
le
r th
an
th
e lattice p
a
ram
e
ters. Th
e ab
sen
ce o
f
d
i
ffu
s
ion
mak
e
s th
e m
a
rte
n
sitic
p
h
a
se tran
sfo
r
matio
n
al
m
o
st
in
stan
tan
e
ou
s.
Fig
u
re 2(b
)
sho
w
s m
a
g
n
i
fied i
m
ag
e o
f
m
a
rt
en
sitic layer with
20
X
magnification, prese
n
t at Ni
2
Mn
Sn
sam
p
le. Th
e crystal la
ttice o
f
th
e
m
a
rten
sitic p
h
a
se
h
a
s lo
wer symmetry
th
an
t
h
at of t
h
e p
a
ren
t
au
sten
itic p
h
a
se so
th
at sev
e
ral v
a
rian
ts
o
f
m
a
rten
site can b
e
form
ed
fro
m
th
e same
pare
nt
p
h
ase
cry
s
t
a
l
.
M
a
gn
et
i
c
shape m
e
m
o
ry
effect
i
n
t
h
ese m
a
t
e
ri
al
s i
nvol
ves t
h
e
m
ovem
e
nt
of t
w
i
n
bo
u
nda
ri
es
w
h
i
c
h re
sul
t
s
i
n
t
h
e
gr
o
w
t
h
o
f
o
n
e
of
t
h
e
t
w
i
n
vari
a
n
t
s
at
t
h
e
expe
nse
o
f
t
h
e
ot
her
i
n
res
p
o
n
se t
o
an
app
lied
m
a
g
n
e
tic field
b
e
lo
w th
e m
a
rtensitic tran
sformatio
n
tem
p
eratu
r
e. Th
e m
i
cro
s
tru
c
ture of Ni
2
Mn
Sn
sam
p
l
e
t
a
ken f
r
om
Opt
i
cal
M
i
crosc
ope
i
s
gi
ven
bel
o
w:
Fig
u
re
2
.
(a)
A nu
m
b
er of Marten
sitic layers
p
r
esen
t in Ni
50
Mn
45
Sn
5
, (b
) en
larg
ed m
a
rten
sitic layer at 2
0
X
m
a
gni
fi
cat
i
o
n
Evaluation Warning : The document was created with Spire.PDF for Python.
I
J
AA
S I
S
SN
:
225
2-8
8
1
4
Ma
rtensitic Tra
n
s
f
o
rma
tion
Ch
a
r
a
c
teristic o
f
Ni-M
n
Ba
sed
Ferromagn
et
ic S
hap
e Memo
ry (Ajit Beh
e
ra
)
20
7
3.2.
Di
fferential Sc
anning Cal
o
rimetr
y
Tran
sf
orm
a
t
i
on t
e
m
p
erat
ure
s
det
e
rm
i
n
ed
u
nde
r ze
ro
st
ress
by
u
s
i
ng
Di
f
f
ere
n
t
i
al
Scanni
ng
Calorim
e
ter.
To c
h
aracteriz
e the m
a
terial beha
vior
, it
is i
m
p
o
r
tan
t
to
id
en
tify th
e reg
i
o
n
s
wh
ere th
e
marten
site p
h
a
se ex
ists. Th
e mag
n
e
tic sh
ape
m
e
m
o
ry eff
ect
i
s
onl
y
pres
ent
i
n
re
gi
o
n
s
con
s
i
s
t
i
ng
of s
t
abl
e
marten
site. These reg
i
on
s
of stab
ility h
o
wev
e
r, are
tem
p
eratu
r
e
d
e
p
e
nden
t
. Tem
p
erat
u
r
es ov
er
wh
i
c
h
t
h
e
pha
se t
r
ans
f
o
r
m
a
t
i
on begi
n
s
and e
nds a
r
e cal
l
e
d t
r
ansf
or
m
a
t
i
on t
e
m
p
erat
ures. T
h
e al
l
o
y
abso
r
b
s, o
r
em
it
s,
heat over a s
m
all change i
n
the s
p
ecim
e
n te
m
p
erature
,
wh
en th
ere is a
p
h
a
se tran
sfo
r
matio
n
o
c
cu
rs
in
th
e
material. In
b
e
lo
w figures num
b
e
r-1
rep
r
esen
t as fo
rw
ard
marten
sitic tra
n
sfo
r
m
a
tio
n
and
nu
m
b
er-2
rep
r
esen
t
rev
e
rse m
a
rtensitic tran
sfo
r
m
a
tio
n
.
Marten
sitic start te
m
p
eratu
r
e, Marten
sitic fin
i
sh
tem
p
eratu
r
e, au
sten
itic
starte te
m
p
eratu
r
e and
au
stenitic fi
n
i
sh
temp
erat
u
r
e are
d
e
n
o
t
ed
as M
s
, M
f
, A
s
, A
f
re
s
p
ectively. In Figure 3,
t
h
e t
e
m
p
erat
ur
e was
rai
s
e
d
fr
om
300
°C
t
o
5
0
0
°
C
a
n
d
l
o
we
r f
r
o
m
500
°C
t
o
30
0°C
at
a
ra
t
e
of
5
°
C
/
m
i
n,
whi
l
e
th
e b
a
selin
e
h
e
at flo
w
rate v
s
. te
m
p
eratu
r
e
was record
ed
b
y
th
e d
a
ta acq
u
i
sition
co
m
p
u
t
er.
Here M
s
, M
f
, A
s
and A
f
ar
e 4
2
3
.
0
2
°C, 40
3.73
°C,
428
.3
6°C, 45
2.99
°C
r
e
sp
ectiv
ely.
I
n
Fi
g
u
re
4
,
t
h
e t
e
m
p
erat
ure
was rai
s
e
d
fr
o
m
100
oC
t
o
2
0
0oC
a
n
d l
o
wer
fr
om
200
oC
t
o
1
0
0oC
at
a
rat
e
of
5°C
/
m
i
n. M
s
, M
f
, A
s
and A
f
t
e
m
p
erat
ure o
b
t
a
i
n
e
d
are 16
9.
8
9
°
C
,
15
6.
5
9
°C
, 18
8.
9
4
°C
, 19
5
.
5
2
°C
respectively.
Fig
u
re
3
.
Mart
en
sitic tran
sfo
r
matio
n
fo
r
samp
le
Ni
50
Mn
45
Sn
5
Fig
u
re
4
.
Mart
en
sitic tran
sfo
r
matio
n
fo
r
samp
le
Ni
50
Mn
40
Sn
10
In
Fi
g
u
re
5, t
h
e t
e
m
p
erat
ure
was rai
s
e
d
fr
o
m
100
°C
t
o
20
0°C
a
nd l
o
we
r
fr
om
200
°C
t
o
1
0
0
°C
at
a
rat
e
of
5°C
/
m
i
n. M
s
, M
f
, A
s
and
A
f
t
e
m
p
erat
ure
o
b
t
a
i
n
ed are
16
9.
8
9
°
C
,
1
5
6
.
5
9
°C
,
18
8.
9
4
°C
,
19
5.
52
°C
respectively.
From
ab
ove
t
h
ree
fi
g
u
res
,
a
gra
p
h
dra
w
n i
n
Fi
g
u
re
6;
i
t
i
s
wel
l
kn
o
w
n
t
h
at
wi
t
h
c
o
n
s
t
a
nt
wei
ght
perce
n
t
of
Ni
,
by
i
n
c
r
easi
n
g
wei
g
ht
perce
n
t
o
f
S
n
i
n
a
n
all
o
y; there
is
de
crease i
n
all the val
u
e
of M
s
, M
f
, A
s
and A
f
. it is k
n
o
wn
th
at, th
e
m
a
rten
sitic st
artin
g
tem
p
eratu
r
e fo
r
Ni
50
Mn
37
Sn
13
allo
y h
a
v
e
17
°C [1
0] and
Ni
50
Mn
36
Sn
14
a
l
l
o
y
have
-
5
3°
C
[1
1]
.
Fig
u
re. 5. Mart
en
sitic tran
sfo
r
matio
n
fo
r
samp
le
Ni
50
Mn
37.5
Sn
12.5
Fi
gu
re 6.
C
o
m
p
ari
s
i
o
n o
f
M
s
, M
f
with
resp
ect
to
Sn
wei
g
ht
pe
rce
n
t
Evaluation Warning : The document was created with Spire.PDF for Python.
I
S
SN
:
2
252
-88
14
IJAAS
Vol. 2, No.
4, Decem
ber :
205
–
208
20
8
4.
CO
NCL
USI
O
N
In
Ni-Mn-Sn
allo
ys, if we in
crease th
e Sn
weig
h
t
pe
rcent
a
ge, t
h
e
n
M
s
,
M
f
, As a
nd
Af
t
e
m
p
erat
ure
sim
u
l
t
a
neousl
y
dec
r
eases.
REFERE
NC
ES
[1]
J. Pons,
et al.
"Structur
e
of the l
a
yer
e
d m
a
rten
sitic phases of Ni-Mn-Ga allo
y
s
”,
Materials Science and Engineering
A
, Pp. 438-440
,
93-934, 2006
.
[2]
Katsunari Oikawa,
et al
, "Mart
e
nsitic
Transfor
m
a
tion and Magneti
c Properties
of Cu-Ga-Mn
Allo
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”
,
Mate
rials
Transactions
, Vol/Issue: 45(8)
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S
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J
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u
rra
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a
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llen,
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a
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u
ttig
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[5]
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y
ung Sang Choi. “Thermal, Magnetic and
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e
n
t
Heusler allo
y
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X (X=Ga,In o
r
S
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)”,
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hik Bhat
tac
h
ar
ya.
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cc
ommodation in
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[7]
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.
Chatt
e
rj
ee,
et al.
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e
tic Investigations
on Ni-Mn-
S
n
Ferrom
a
gneti
c S
h
ape M
e
m
o
r
y
A
llo
y”
,
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rials Re
se
arc
h
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[8]
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.
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n
et
al
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.
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ens
.
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t
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, Vol. 18. Pp. 2249
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06.
[9]
Y. Sutou. “
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agneti
c and m
a
rt
en
sitic tr
ansform
a
ti
ons of NiMn
X
(
X
=In,Sn,Sb) ferr
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sha
p
e me
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l
l
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”,
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[10]
D. L. Schlagel,
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13
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i
ptamat.200
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a
ma,
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vation of f
i
eld-
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e
rse
tr
a
n
sforma
t
i
on in fe
rroma
gne
t
i
c sha
p
e
me
mory
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i
50
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36
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2189
916.
BIOGRAP
HI
ES OF
AUTH
ORS
Ajit Beher
a
was born in 1987. He received B.T
ech Degree in 2
009 from
Bijupatnaik univ
e
rsi
t
y
of technolog
y
,
Rourkela and M
.
Tech degrees
in 2012 from Na
tional Institute of Technolog
y
,
Rourkela, India. Currentl
y
he is
doctoral r
e
sear
ch scholar at In
dian Institu
te of
Technolog
y
,
Kharagpur, India. He published
some book
in
“M
aterials Engineering
”
.
He is working as a
Reviewer
/Edi
tor
in m
a
n
y
international journals.
Asit Beher
a
was born in 1991
. He received B
achlor
degr
ee (
M
echanical Eng
i
neer
ing) from
Bijupatn
aik University
of
Techn
o
log
y
, Rourk
e
la.
Currently
he
is doing
research in
Mechan
ical
Engine
ering, De
partm
e
nt in Nat
i
onal Institu
te of
Techno
log
y
, Ro
urkela
. His W
o
rking area
is on
M
echani
cal
M
a
t
e
ria
l
.
Prof. S.C Mishr
a
, One of the senior most prof
essor in the Departm
e
nt of Metallurg
ic
al and
Materi
al Engg
.,
Nationa
l Institut
e
of Techno
log
y
, Rourk
e
l
a
. He
has also com
posed a chap
ter in
a highl
y
acclai
m
e
d book in sc
ientif
ic circl
e
s:
"Advanced Plasm
a
Spray
Appli
cat
ions" titled
"Analy
sis of
ex
perimental
r
e
sults of plasma spray
co
atings
u
s
ing statistical
techniqu
es. In
addition
to all the awards and
r
ecognition, Th
e
International
Bi
ographic C
e
ntre of Cambridge,
England
has no
minated
the prof
essor
for th
e "Ol
y
m
p
ian
Achiev
e
r
" award.
Evaluation Warning : The document was created with Spire.PDF for Python.