elastic B-PRO
softening I-PRO
in O
single B-DSC
- I-DSC
crystalline I-DSC
la2-x B-MAT
Sr I-MAT
x I-MAT
CuO4 I-MAT
around I-MAT
x I-MAT
= I-MAT
⅛ I-MAT


ultrasound B-CMT
measurements I-CMT
have O
revealed O
a O
remarkable O
lattice B-PRO
softening I-PRO
of O
the O
transverse B-PRO
elastic I-PRO
modulus I-PRO
( I-PRO
C11 I-PRO
− I-PRO
C12 I-PRO
) I-PRO
/ I-PRO
<nUm> I-PRO
in O
single B-DSC
- I-DSC
crystalline I-DSC
la2 B-MAT
- I-MAT
xSrxCuO4 I-MAT
only I-MAT
around I-MAT
x I-MAT
= I-MAT
⅛ I-MAT
. O


analysis O
of O
the O
temperature O
dependence O
of O
the O
elastic B-PRO
modulus I-PRO
indicates O
that O
in O
the O
particular O
range O
of O
carrier B-PRO
concentration I-PRO
there O
exists O
a O
narrow O
electronic B-PRO
band I-PRO
in O
the O
vicinity O
of O
the O
fermi B-PRO
level I-PRO
which O
couples O
to O
the O
shearing B-PRO
strain I-PRO
exx I-PRO
− I-PRO
eyy I-PRO
. O


thermoelectric B-PRO
power I-PRO
of O
silver B-MAT
- O
containing O
glasses B-DSC


thermoelectric B-PRO
power I-PRO
measurements O
were O
made O
on O
both O
silver B-MAT
oxide I-MAT
- O
containing O
glasses B-DSC
and O
a O
silver B-MAT
iodide I-MAT
- O
containing O
glass B-DSC
. O


the O
latter O
is O
known O
to O
be O
a O
superionic O
conductor B-PRO
. O


the O
value O
of O
the O
heat B-PRO
of I-PRO
transport I-PRO
deduced O
from O
the O
temperature O
dependence O
of O
the O
thermoelectric B-PRO
power I-PRO
was O
zero O
for O
the O
former O
glasses B-DSC
while O
for O
the O
latter O
glass B-DSC
it O
was O
non-zero O
, O
<nUm> O
kcal O
/ O
mol O
, O
which O
is O
nearly O
equal O
to O
the O
activation B-PRO
energy I-PRO
for I-PRO
d.c. I-PRO
conduction I-PRO
, O
<nUm> O
kcal O
/ O
mol O
. O


these O
results O
were O
discussed O
in O
terms O
of O
the O
conduction B-PRO
mechanism I-PRO
. O


p B-PRO
- I-PRO
type I-PRO
conducting I-PRO
transparent I-PRO
characteristics I-PRO
of O
delafossite B-SPL
Mg B-MAT
- O
doped B-DSC
CrCuO2 B-MAT
thin B-DSC
films I-DSC
prepared O
by O
RF B-SMT
- I-SMT
sputtering I-SMT


the O
growth O
of O
technologically O
relevant O
compounds O
, O
Mg B-MAT
- O
doped B-DSC
CrCuO2 B-MAT
delafossite B-SPL
thin B-DSC
films I-DSC
, O
on O
a O
quartz B-MAT
substrate B-DSC
by O
radio-frequency B-SMT
sputtering I-SMT
is O
reported O
in O
this O
work O
. O


the O
deposition O
, O
performed O
at O
room O
temperature O
, O
leads O
to O
a O
nanocrystalline B-DSC
phase O
with O
extremely O
low O
roughness B-PRO
and O
high O
density B-PRO
. O


delafossite B-SPL
characteristic O
diffraction B-CMT
peaks O
were O
obtained O
as O
a O
function O
of O
the O
thermal B-SMT
treatment I-SMT
under O
primary O
vacuum O
. O


the O
electrical B-PRO
conductivity I-PRO
was O
optimized O
until O
<nUm> O
S O
cm-1 O
with O
an O
optical B-PRO
transmittance I-PRO
of O
<nUm> O
% O
in O
the O
visible O
range O
by O
a O
<nUm> O
° O
C O
annealing B-SMT
treatment I-SMT
under O
primary O
vacuum O
applied O
for O
<nUm> O
h O
. O


the O
transport B-PRO
properties I-PRO
were O
analyzed O
by O
seebeck B-CMT
and O
hall B-CMT
measurement I-CMT
, O
integrated B-CMT
spectrophotometry I-CMT
and O
optical B-CMT
simulation I-CMT
. O


these O
measurements O
highlighted O
degenerated B-PRO
semiconductor I-PRO
behavior I-PRO
using O
a O
hopping B-PRO
mechanism I-PRO
with O
a O
high O
hole B-PRO
concentration I-PRO
( O
<nUm> O
cm-3 O
) O
and O
a O
low O
mobility B-PRO
( O
<nUm> O
cm2 O
V-1 O
s-1 O
) O
. O


the O
direct B-PRO
optical I-PRO
bandgap I-PRO
of O
<nUm> O
eV O
has O
been O
measured O
according O
to O
tauc B-CMT
's I-CMT
relationship I-CMT
. O


A O
refractive B-PRO
index I-PRO
of O
<nUm> O
at O
a O
wavelength O
of O
<nUm> O
nm O
has O
been O
determined O
by O
spectroscopic B-CMT
ellipsometry I-CMT
and O
confirmed O
by O
two O
independent O
modellings O
of O
the O
optical B-PRO
transmittance I-PRO
and O
reflectance B-CMT
spectra I-CMT
. O


all O
these O
p B-PRO
- I-PRO
type I-PRO
TCO I-PRO
optoelectronic I-PRO
characteristics I-PRO
have O
led O
to O
the O
highest O
haacke B-PRO
's I-PRO
figure I-PRO
of I-PRO
merit I-PRO
( O
<nUm> O
× O
<nUm> O
− O
<nUm> O
O-1 O
) O
reported O
so O
far O
for O
such O
delafossite B-SPL
materials O
. O


high O
- O
temperature O
oxidation B-PRO
behavior I-PRO
of O
un-dense B-PRO
AlC2Ti3 B-MAT
material O
at O
<nUm> O
° O
C O
in O
air O


un-dense B-PRO
AlC2Ti3 B-MAT
material O
containing O
3wt O
% O
CTi B-MAT
was O
prepared O
by O
hot B-SMT
- I-SMT
pressing I-SMT
process O
using O
elemental O
powders B-DSC
of O
2TiC B-MAT
/ O
Ti B-MAT
/ O
Al B-MAT
. O


its O
oxidation B-PRO
behavior I-PRO
at O
<nUm> O
° O
C O
in O
static O
air O
was O
investigated O
. O


SEM B-CMT
analysis O
indicates O
that O
the O
as B-DSC
fabricated I-DSC
sample O
is O
un-dense B-PRO
and O
the O
AlC2Ti3 B-MAT
grains B-PRO
with O
plate O
- O
like O
shape O
exhibit O
two O
types O
of O
fracture B-PRO
surfaces I-PRO
of O
layered O
and O
flat O
features O
. O


the O
oxidation B-PRO
behavior I-PRO
of O
the O
product O
exposed O
at O
<nUm> O
° O
C O
for O
30h O
obeys O
a O
near O
- O
cubic O
law O
. O


the O
scale O
consists O
of O
rutile B-SPL
O2Ti B-MAT
and O
a-Al2O3 B-MAT
phases O
, O
and O
presents O
three O
layers B-DSC
, O
including O
an O
outer O
un-dense B-PRO
O2Ti B-MAT
layer B-DSC
adhering O
to O
a O
little O
Al2O3 B-MAT
, O
a O
thick O
intermediate O
TiO2+Al2O3 B-MAT
mixed O
layer B-DSC
and O
a O
thin O
inner O
Al2O3 B-MAT
layer B-DSC
with O
some O
pores O
. O


the O
thickness O
of O
the O
oxide B-MAT
layer B-DSC
was O
higher O
than O
<nUm> O
mm O
. O


In O
addition O
, O
the O
deleterious O
effects O
of O
CTi B-MAT
and O
innate O
- O
pores O
on O
the O
oxidation B-PRO
resistance I-PRO
of O
the O
product O
were O
also O
investigated O
. O


giant O
dielectric B-PRO
response I-PRO
and O
polaronic B-PRO
hopping I-PRO
in O
Al B-MAT
- O
substituted B-DSC
A5 B-MAT
/ I-MAT
3Sr1 I-MAT
/ I-MAT
3NiO4 I-MAT
( I-MAT
A I-MAT
= I-MAT
La I-MAT
, I-MAT
Nd I-MAT
) I-MAT
ceramics B-DSC


the O
structures B-PRO
and O
dielectric B-PRO
properties I-PRO
of O
A5 B-MAT
/ I-MAT
3Sr1 I-MAT
/ I-MAT
3Ni1-xAlxO4 I-MAT
( I-MAT
A I-MAT
= I-MAT
La I-MAT
, I-MAT
Nd I-MAT
; I-MAT
x I-MAT
= I-MAT
<nUm> I-MAT
, I-MAT
<nUm> I-MAT
) I-MAT
ceramics B-DSC
were O
investigated O
. O


the O
single O
tetragonal B-SPL
phases O
were O
found O
in O
all O
ceramics B-DSC
. O


giant O
dielectric B-PRO
responses I-PRO
were O
observed O
in O
these O
ceramics B-DSC
, O
and O
only O
one O
dielectric B-PRO
relaxation I-PRO
was O
found O
on O
the O
curve O
of O
the O
temperature O
dependence O
of O
dielectric B-PRO
constant I-PRO
. O


after O
comparing O
the O
activation O
energies O
of O
dielectric B-PRO
relaxation I-PRO
and O
electrical B-PRO
conduction I-PRO
, O
the O
giant O
dielectric B-PRO
response I-PRO
should O
be O
attributed O
to O
the O
adiabatic B-PRO
small I-PRO
polaronic I-PRO
hopping I-PRO
process O
in O
these O
ceramics B-DSC
. O


from O
order O
to O
disorder O
: O
the O
structure B-PRO
of O
lithium B-PRO
- I-PRO
conducting I-PRO
garnets B-SPL
Li7-xLa3TaxZr2-xO12 B-MAT
( I-MAT
x I-MAT
= I-MAT
<nUm> I-MAT
– I-MAT
<nUm> I-MAT
) I-MAT


structural B-PRO
properties I-PRO
of O
Li7-xLa3TaxZr2-xO12 B-MAT
garnets I-MAT
with I-MAT
x I-MAT
= I-MAT
<nUm> I-MAT
– I-MAT
<nUm> I-MAT
were O
clarified O
by O
means O
of O
rietveld B-CMT
analysis I-CMT
using O
results O
of O
x-ray B-CMT
diffraction I-CMT
and O
neutron B-CMT
diffraction I-CMT
at O
room O
temperature O
and O
at O
low O
temperature O
. O


In O
this O
work O
the O
controversy O
between O
awaka O
[1] O
and O
murugan O
[2] O
concerning O
the O
crystal B-PRO
structure I-PRO
of O
La3Li7O12Zr2 B-MAT
was O
solved O
. O


it O
was O
shown O
that O
the O
tetragonally B-SPL
derived O
garnet B-SPL
structure O
of O
space O
group O
I41 B-SPL
/ I-SPL
acd I-SPL
described O
by O
awaka O
[1] O
is O
the O
thermodynamically B-PRO
stable I-PRO
structure I-PRO
for O
La3Li7O12Zr2 B-MAT
. O


In O
the O
three O
- O
dimensional O
sub-network O
of O
this O
structure O
, O
lithium B-MAT
is O
ordered O
and O
occupies O
all O
octahedral O
sites O
as O
well O
as O
one O
third O
of O
the O
tetrahedral O
sites O
. O


Li7-xLa3TaxZr2-xO12 B-MAT
garnets B-SPL
with O
x O
= O
<nUm> O
– O
<nUm> O
crystallize O
in O
the O
garnet B-SPL
structure O
, O
space O
group O
ia B-SPL
<nUm> I-SPL
-d I-SPL
. O


As O
the O
tantalum B-PRO
content I-PRO
increases O
, O
the O
lattice B-PRO
parameter I-PRO
at O
room O
temperature O
decreases O
from O
a B-PRO
= O
<nUm> O
Å O
for O
La24Li55O96TaZr15 B-MAT
down O
to O
a B-PRO
= O
<nUm> O
Å O
for O
La3Li5O12Ta2 B-MAT
. O


In O
La6Li13O24TaZr3 B-MAT
garnet B-SPL
, O
lithium B-MAT
atoms O
are O
statistically O
partitioned O
among O
octahedral O
sites O
( O
occ. O
: O
<nUm> O
) O
and O
tetrahedral O
sites O
( O
occ. O
: O
<nUm> O
) O
. O


In O
the O
cases O
of O
ordered O
La3Li7O12Zr2 B-MAT
tetragonally B-SPL
derived O
garnet B-SPL
and O
statistically O
disordered O
La6Li13O24TaZr3 B-MAT
garnet B-SPL
, O
lithium B-MAT
partitioning O
remains O
unchanged O
as O
temperature O
decreases O
. O


atmospheric B-SMT
pressure I-SMT
MOCVD I-SMT
growth O
of O
high O
- O
quality O
OZn B-MAT
films B-DSC
on O
GaN B-MAT
/ O
Al2O3 B-MAT
templates B-DSC


In O
this O
paper O
, O
we O
present O
the O
epitaxial O
growth O
of O
high O
- O
quality O
OZn B-MAT
thin B-DSC
films I-DSC
on O
GaN B-MAT
/ O
c-Al2O3 B-MAT
templates B-DSC
by O
atmospheric B-SMT
pressure I-SMT
metal I-SMT
organic I-SMT
chemical I-SMT
vapor I-SMT
deposition I-SMT
( O
MOCVD B-SMT
) O
using O
deionized O
water O
( O
H2O O
) O
and O
diethyl O
zinc O
( O
DEZn O
) O
as O
the O
O O
and O
Zn B-MAT
sources O
, O
respectively O
. O


surface B-PRO
morphology I-PRO
of O
the O
films B-DSC
studied O
by O
metal B-CMT
- I-CMT
phase I-CMT
interference I-CMT
microscopy I-CMT
and O
AFM B-CMT
showed O
that O
the O
growth O
of O
the O
OZn B-MAT
films B-DSC
followed O
the O
regular O
hexagonal O
columnar O
structure O
with O
about O
<nUm> O
mm O
grain B-PRO
diameter I-PRO
. O


high B-CMT
- I-CMT
resolution I-CMT
x-ray I-CMT
double I-CMT
- I-CMT
crystal I-CMT
diffraction I-CMT
was O
used O
to O
investigate O
the O
structural B-PRO
properties I-PRO
of O
the O
as-grown B-DSC
films I-DSC
. O


the O
FWHMs O
of O
the O
( O
<nUm> O
) O
and O
( O
<nUm> O
<nUm> O
<nUm> O
¯ O
<nUm> O
) O
o-rocking B-CMT
curves I-CMT
were O
<nUm> O
and O
358arcsec O
, O
respectively O
, O
indicating O
the O
small O
mosaicity B-PRO
and O
low O
dislocation B-PRO
density I-PRO
of O
the O
films B-DSC
. O


the O
optical B-PRO
properties I-PRO
of O
the O
films B-DSC
were O
investigated O
by O
room O
temperature O
photoluminescence B-CMT
and O
temperature B-CMT
- I-CMT
dependent I-CMT
PL I-CMT
spectra O
. O


free B-PRO
excitons I-PRO
XA I-PRO
and O
the O
n O
= O
<nUm> O
state O
of O
FXA B-PRO
can O
be O
clearly O
observed O
at O
<nUm> O
and O
<nUm> O
eV O
at O
10K O
, O
respectively O
. O


the O
domination O
of O
the O
free B-PRO
exciton I-PRO
and O
the O
appearance O
of O
its O
four O
replicas O
strongly O
indicate O
the O
high O
quality O
of O
the O
film B-DSC
. O


effect O
of O
similar O
elements O
on O
improving O
glass B-PRO
- I-PRO
forming I-PRO
ability I-PRO
of O
La B-MAT
– I-MAT
Ce I-MAT
- O
based O
alloys B-DSC


to O
date O
the O
effect O
of O
unlike O
component O
elements O
on O
glass B-PRO
- I-PRO
forming I-PRO
ability I-PRO
( O
GFA B-PRO
) O
of O
alloys B-DSC
have O
been O
studied O
extensively O
, O
and O
it O
is O
generally O
recognized O
that O
the O
main O
consisting O
elements O
of O
the O
alloys B-DSC
with O
high O
GFA B-PRO
usually O
have O
large O
difference B-PRO
in I-PRO
atomic I-PRO
size I-PRO
and O
atomic B-PRO
interaction I-PRO
( O
large O
negative O
heat B-PRO
of I-PRO
mixing I-PRO
) O
among O
them O
. O


In O
our O
recent O
work O
, O
a O
series O
of O
rare O
earth O
metal O
- O
based O
alloy B-DSC
compositions B-PRO
with O
superior O
GFA B-PRO
were O
found O
through O
the O
approach O
of O
coexistence O
of O
similar O
constituent O
elements O
. O


the O
quinary O
Al4Ce13Co6Cu4La13 B-MAT
bulk B-PRO
metallic I-PRO
glass I-PRO
( O
BMG B-PRO
) O
in O
a O
rod B-DSC
form O
with O
a O
diameter O
up O
to O
<nUm> O
mm O
was O
synthesized O
by O
tilt B-SMT
- I-SMT
pour I-SMT
casting I-SMT
, O
for O
which O
the O
glass B-PRO
- I-PRO
forming I-PRO
ability I-PRO
is O
significantly O
higher O
than O
that O
for O
ternary O
ln B-MAT
– I-MAT
Al I-MAT
– I-MAT
TM I-MAT
alloys B-DSC
( O
ln O
= O
La B-MAT
or O
Ce B-MAT
; O
TM O
= O
Co B-MAT
or O
Cu B-MAT
) O
with O
critical B-PRO
diameters I-PRO
for I-PRO
glass I-PRO
- I-PRO
formation I-PRO
of O
several O
millimeters O
. O


we O
suggest O
that O
the O
strong O
frustration O
of O
crystallization O
by O
utilizing O
the O
coexistence O
of O
La B-MAT
– O
Ce B-MAT
and O
Co B-MAT
– O
Cu B-MAT
to O
complicate O
competing O
crystalline B-DSC
phases O
is O
helpful O
to O
construct O
BMG B-PRO
component O
with O
superior O
GFA B-PRO
. O


the O
results O
of O
our O
present O
work O
indicate O
that O
similar O
elements O
( O
elements O
with O
similar O
atomic B-PRO
size I-PRO
and O
chemical B-PRO
properties I-PRO
) O
have O
significant O
effect O
on O
GFA B-PRO
of O
alloys B-DSC
. O


synthesis O
and O
single B-DSC
- I-DSC
crystal I-DSC
growth O
of O
ca2-x B-MAT
Sr I-MAT
x I-MAT
O4Ru I-MAT


for O
the O
study O
of O
the O
quasi-two B-DSC
- I-DSC
dimensional I-DSC
mott B-PRO
transition I-PRO
system O
Ca2-xSrxRuO4 B-MAT
, O
we O
have O
succeeded O
in O
synthesizing O
polycrystalline B-DSC
samples O
and O
also O
growing O
single B-DSC
crystals I-DSC
by O
a O
floating B-SMT
- I-SMT
zone I-SMT
method I-SMT
. O


details O
of O
the O
preparations O
for O
the O
entire O
solution O
range O
are O
described O
. O


the O
structural B-PRO
, O
transport B-PRO
, O
and O
magnetic B-PRO
properties I-PRO
of O
both O
polycrystalline B-DSC
and O
single B-DSC
- I-DSC
crystal I-DSC
samples O
are O
fully O
in O
agreement O
. O


adhesion B-PRO
and O
wear B-PRO
properties I-PRO
of O
NTi B-MAT
films B-DSC
deposited O
on O
martensitic B-SPL
stainless B-MAT
steel I-MAT
and O
stellite B-MAT
by O
reactive B-SMT
magnetron I-SMT
sputter I-SMT
ion I-SMT
plating I-SMT


NTi B-MAT
films B-DSC
were O
deposited O
onto O
the O
turbine B-APL
blade I-APL
materials O
, O
AISI B-MAT
<nUm> I-MAT
martensitic B-SPL
stainless B-MAT
steel I-MAT
and O
stellite B-MAT
6B I-MAT
, O
using O
reactive B-SMT
magnetron I-SMT
sputter I-SMT
ion I-SMT
plating I-SMT
. O


the O
hardness B-PRO
of O
the O
NTi B-MAT
film B-DSC
increases O
with O
the O
residual O
compressive B-PRO
stress I-PRO
and O
has O
a O
maximum O
value O
of O
<nUm> O
kg O
/ O
mm2 O
at O
the O
substrate B-DSC
bias O
of O
about O
− O
<nUm> O
V O
. O


In O
the O
scratch B-CMT
adhesion I-CMT
test I-CMT
, O
the O
critical B-PRO
loads I-PRO
for O
cohesive B-PRO
failure I-PRO
and O
adhesive B-PRO
failure I-PRO
are O
sensitively O
governed O
by O
the O
film B-DSC
hardness B-PRO
. O


the O
wear B-PRO
rate I-PRO
decreases O
with O
increasing O
hardness B-PRO
and O
has O
a O
minimum O
value O
at O
about O
− O
<nUm> O
V O
. O


the O
ion B-SMT
plated I-SMT
NTi B-MAT
has O
a O
superior O
wear B-PRO
resistance I-PRO
than O
the O
bare O
stellite B-MAT
6B I-MAT
and O
AISI B-MAT
<nUm> I-MAT
martensitic B-SPL
stainless B-MAT
steel I-MAT
. O


synthesis O
and O
characterization O
of O
Cu B-MAT
- O
doped B-DSC
ceria B-MAT
nanopowders B-DSC


nanopowdered B-DSC
solid I-DSC
solution I-DSC
Ce1-xCuxO2-g B-MAT
samples O
( O
<nUm> O
≤ O
x O
≤ O
<nUm> O
) O
were O
synthesized O
by O
self B-SMT
- I-SMT
propagating I-SMT
room I-SMT
temperature I-SMT
synthesis I-SMT
( O
SPRT B-SMT
) O
. O


raman B-CMT
spectroscopy I-CMT
and O
XRD B-CMT
at O
room O
temperature O
were O
used O
to O
study O
the O
vibration B-PRO
properties I-PRO
of O
these O
materials O
as O
well O
as O
the O
Cu B-MAT
solubility O
in O
ceria B-MAT
lattice O
. O


the O
solubility O
limit O
of O
cu2+ O
in O
CeO2 B-MAT
lattice O
was O
found O
to O
be O
lower O
than O
published O
in O
the O
literature O
. O


results O
show O
that O
obtained O
powders B-DSC
with O
low O
dopant B-PRO
concentration I-PRO
are O
solid B-DSC
solutions I-DSC
with O
a O
fluorite B-SPL
- O
type O
crystal B-PRO
structure I-PRO
. O


however O
, O
with O
Cu B-PRO
content I-PRO
higher O
than O
<nUm> O
mass O
% O
, O
the O
phase O
separation O
was O
observed O
and O
two O
oxide B-MAT
phases O
, O
CeO2 B-MAT
and O
CuO B-MAT
, O
coexist O
. O


all O
powders B-DSC
were O
nanometric B-DSC
in O
size O
with O
high O
specific B-PRO
surface I-PRO
area I-PRO
. O


point B-PRO
defect I-PRO
parameters I-PRO
in O
b-PbF2 B-MAT
revisited O


the O
defect B-PRO
parameters I-PRO
in O
b-PbF2 B-MAT
that O
have O
been O
determined O
to O
date O
from O
the O
association O
and O
extrinsic O
regions O
of O
the O
isobaric B-PRO
conductivity I-PRO
plot O
as O
well O
as O
from O
conductivity B-PRO
measurements O
under O
various O
pressures O
, O
are O
studied O
. O


we O
find O
that O
, O
in O
the O
low O
temperature O
range O
where O
bulk B-DSC
elastic B-PRO
and O
expansivity B-PRO
data O
are O
available O
, O
the O
defect B-PRO
volumes I-PRO
scale O
linearly O
with O
the O
defect B-PRO
enthalpies I-PRO
with O
a O
slope O
which O
is O
governed O
by O
bulk B-DSC
qualities O
. O


A O
deviation O
from O
linearity O
is O
observed O
in O
the O
high O
temperature O
range O
from O
which O
the O
relevant O
parameters O
for O
the O
anion B-PRO
frenkel I-PRO
formation I-PRO
process I-PRO
are O
deduced O
. O


synthesis O
and O
characterization O
of O
BON B-MAT
thin B-DSC
films I-DSC
using O
low B-SMT
frequency I-SMT
RF I-SMT
plasma I-SMT
enhanced I-SMT
MOCVD I-SMT
: O
effect O
of O
deposition O
parameters O
on O
film B-DSC
hardness B-PRO


with O
the O
expectation O
of O
getting O
hard O
material O
, O
we O
have O
firstly O
grown O
the O
BON B-MAT
thin B-DSC
film I-DSC
by O
radio B-SMT
frequency I-SMT
plasma I-SMT
enhanced I-SMT
metal I-SMT
- I-SMT
organic I-SMT
chemical I-SMT
vapor I-SMT
deposition I-SMT
with O
<nUm> O
kHz O
frequency O
and O
trimethyl O
borate O
precursor O
. O


the O
plasma O
source O
gases O
used O
in O
this O
study O
were O
Ar O
and O
H O
, O
and O
two O
kinds O
of O
nitrogen O
source O
gases O
, O
N O
and O
H3N O
, O
were O
also O
employed O
. O


the O
as-grown B-DSC
films I-DSC
were O
characterized O
with O
XPS B-CMT
, O
IR B-CMT
, O
SEM B-CMT
and O
knoop B-CMT
microhardness I-CMT
tester I-CMT
. O


the O
film B-DSC
growth O
rate O
was O
influenced O
both O
by O
substrate B-DSC
temperature O
and O
by O
nitrogen O
source O
gas O
. O


it O
decreased O
with O
increasing O
the O
substrate B-DSC
temperature O
, O
and O
was O
higher O
by O
using O
H3N O
rather O
than O
by O
N O
. O


the O
hardness B-PRO
of O
the O
film B-DSC
was O
dependent O
on O
several O
factors O
such O
as O
nitrogen O
source O
gas O
, O
substrate B-DSC
temperature O
and O
film B-DSC
thickness O
due O
to O
the O
variation O
of O
the O
composition B-PRO
and O
the O
structure B-PRO
of O
the O
film B-DSC
. O


both O
nitrogen O
and O
carbon-content B-MAT
could O
raise O
the O
film B-DSC
hardness B-PRO
, O
on O
which O
nitrogen O
content O
had O
stronger O
effect O
than O
carbon B-MAT
. O


the O
smooth O
morphology B-PRO
and O
continuous O
structure B-PRO
yielded O
high O
hardness B-PRO
. O


the O
maximum O
hardness B-PRO
of O
BON B-MAT
film B-DSC
was O
approximately O
<nUm> O
GPa O
. O


investigation O
of O
the O
ground B-PRO
state I-PRO
in O
U B-MAT
x I-MAT
th1-x I-MAT
RuSi I-MAT


anomalous O
ln O
T O
- O
dependence O
of O
magnetic B-PRO
susceptibility I-PRO
, O
specific B-PRO
heat I-PRO
divided O
by O
temperature O
, O
and O
electrical B-PRO
resistivity I-PRO
have O
been O
reported O
for O
UxTh1-xRu2Si2 B-MAT
, I-MAT
x I-MAT
≤ I-MAT
<nUm> I-MAT
. O


we O
have O
attempted O
to O
elucidate O
the O
formation O
of O
the O
ground B-PRO
state I-PRO
in O
these O
alloys B-DSC
by O
systematic O
investigation O
of O
the O
trends O
in O
transport B-PRO
, O
thermodynamic B-PRO
, O
and O
magnetic B-PRO
properties I-PRO
for O
more O
concentrated O
u-alloys B-MAT
, I-MAT
<nUm> I-MAT
≤ I-MAT
x I-MAT
≤ I-MAT
<nUm> I-MAT
. O


In O
particular O
, O
we O
believe O
, O
our O
results O
reveal O
proximity O
of O
magnetism B-PRO
to O
a O
new O
ground B-PRO
state I-PRO
in O
these O
alloys B-DSC
. O


superplasticity B-PRO
in O
Al2O3-20vol B-MAT
% I-MAT
spinel B-SPL
( O
MgO B-MAT
· I-MAT
1.5Al2O3 I-MAT
) O
ceramics B-DSC


superplasticity B-PRO
in O
Al2O3-20 B-MAT
vol I-MAT
% I-MAT
spinel B-SPL
( O
MgO B-SPL
· I-SPL
1.5Al2O3 I-SPL
) O
is O
investigated O
by O
means O
of O
tensile B-CMT
testing I-CMT
in O
the O
temperature O
range O
<nUm> O
– O
<nUm> O
° O
C O
. O


the O
dispersion O
of O
spinel B-SPL
phase O
in O
Al2O3 B-MAT
slightly O
reduces O
the O
flow B-PRO
stress I-PRO
, O
and O
highly O
enhances O
the O
high O
- O
temperature O
ductility B-PRO
at O
the O
same O
stress B-PRO
level I-PRO
in O
comparison O
with O
<nUm> O
wt O
% O
MgO B-MAT
- O
doped B-DSC
single I-DSC
- I-DSC
phase I-DSC
Al2O3 B-MAT
. O


A O
maximum B-PRO
elongation I-PRO
of O
<nUm> O
% O
is O
obtained O
at O
<nUm> O
° O
C O
and O
a O
strain O
rate O
of O
<nUm> O
× O
<nUm> O
− O
<nUm> O
s-1 O
. O


the O
flow B-PRO
stress I-PRO
reduction O
is O
associated O
with O
a O
slight O
reduction O
in O
activation B-PRO
energy I-PRO
for O
superplastic B-PRO
flow O
. O


the O
extensive O
ductility B-PRO
in O
Al2O3-20 B-MAT
vol I-MAT
% I-MAT
spinel B-SPL
can O
not O
be O
explained O
only O
from O
the O
stress O
reduction O
. O


the O
Al2O3 B-MAT
/ O
spinel B-SPL
boundaries O
are O
expected O
to O
have O
much O
larger O
resistance B-PRO
to I-PRO
crack I-PRO
extension I-PRO
than O
Al2O3 B-MAT
grain B-PRO
boundaries I-PRO
. O


the O
influence O
of O
the O
focus O
position O
on O
laser B-SMT
machining I-SMT
and O
laser B-SMT
micro-structuring I-SMT
monocrystalline B-DSC
diamond B-MAT
surface B-DSC


micro-structured B-DSC
surface I-DSC
on O
diamond B-MAT
is O
widely O
used O
in O
microelectronics B-APL
, O
optical B-APL
elements I-APL
, O
MEMS B-APL
and O
NEMS B-APL
components I-APL
, O
ultra-precision B-APL
machining I-APL
tools I-APL
, O
etc O
. O


the O
efficient O
micro-structuring B-SMT
of O
diamond B-MAT
material O
is O
still O
a O
challenging O
task O
. O


In O
this O
article O
, O
the O
influence O
of O
the O
focus O
position O
on O
laser B-SMT
machining I-SMT
and O
laser B-SMT
micro-structuring I-SMT
monocrystalline B-DSC
diamond B-MAT
surface B-DSC
were O
researched O
. O


At O
the O
beginning O
, O
the O
ablation B-PRO
threshold I-PRO
and O
its O
incubation O
effect O
of O
monocrystalline B-DSC
diamond B-MAT
were O
determined O
and O
discussed O
. O


As O
the O
accumulated O
laser O
pulses O
ranged O
from O
<nUm> O
to O
<nUm> O
, O
the O
laser B-PRO
ablation I-PRO
threshold I-PRO
decreased O
from O
<nUm> O
J O
/ O
cm2 O
to O
<nUm> O
J O
/ O
cm2 O
. O


subsequently O
, O
the O
variation O
of O
the O
ablation O
width O
and O
ablation O
depth O
in O
laser B-SMT
machining I-SMT
were O
studied O
. O


with O
enough O
pulse O
energy O
, O
the O
ablation B-SMT
width O
mainly O
depended O
on O
the O
laser O
propagation O
attributes O
while O
the O
ablation B-SMT
depth O
was O
a O
complex O
function O
of O
the O
focus O
position O
. O


raman B-CMT
analysis I-CMT
was O
used O
to O
detect O
the O
variation O
of O
the O
laser B-SMT
machined I-SMT
diamond B-MAT
surface B-DSC
after O
the O
laser B-SMT
machining I-SMT
experiments O
. O


graphite B-MAT
formation O
was O
discovered O
on O
the O
machined B-SMT
diamond B-MAT
surface B-DSC
and O
graphitization B-SMT
was O
enhanced O
after O
the O
defocusing O
quantity O
exceeded O
<nUm> O
um O
. O


At O
last O
, O
several O
micro-structured B-DSC
surfaces I-DSC
were O
successfully O
fabricated O
on O
diamond B-MAT
surface B-DSC
with O
the O
defined O
micro-structure B-PRO
patterns I-PRO
and O
structuring B-PRO
ratios I-PRO
just O
by O
adjusting O
the O
defocusing O
quantity O
. O


the O
experimental O
structuring B-PRO
ratio I-PRO
was O
consistent O
with O
the O
theoretical O
analysis O
. O


thermal B-SMT
treatment I-SMT
effects O
on O
interfacial O
layer O
formation O
between O
O2Zr B-MAT
thin B-DSC
films I-DSC
and O
Si B-MAT
substrates B-DSC


this O
paper O
describes O
the O
growth O
condition O
of O
stoichiometric B-DSC
O2Zr B-MAT
thin B-DSC
films I-DSC
on O
Si B-MAT
substrates B-DSC
and O
the O
interfacial B-PRO
structure I-PRO
of O
O2Zr B-MAT
and O
Si B-MAT
substrates B-DSC
. O


the O
O2Zr B-MAT
thin B-DSC
films I-DSC
were O
prepared O
by O
rf B-SMT
- I-SMT
magnetron I-SMT
sputtering I-SMT
from O
Zr B-MAT
target O
with O
mixed O
gas O
of O
O O
and O
Ar O
at O
room O
temperature O
followed O
by O
post-annealing B-SMT
in O
O O
ambient O
. O


the O
stoichiometric B-DSC
O2Zr B-MAT
thin B-DSC
films I-DSC
with O
smooth O
surface B-DSC
were O
grown O
at O
high O
oxygen O
partial O
pressure O
. O


the O
thick O
Zr B-MAT
- O
free O
O2Si B-MAT
layer B-DSC
was O
formed O
with O
both O
Zr B-MAT
silicide I-MAT
and O
Zr B-MAT
silicate I-MAT
at O
the O
interface B-DSC
between O
O2Zr B-MAT
and O
Si B-MAT
substrate B-DSC
during O
the O
post-annealing B-SMT
process O
due O
to O
rapid O
diffusion O
of O
oxygen O
atoms O
through O
the O
O2Zr B-MAT
thin B-DSC
films I-DSC
. O


after O
post O
annealing B-SMT
at O
<nUm> O
– O
<nUm> O
° O
C O
, O
the O
multi-interfacial B-DSC
layer I-DSC
shows O
small O
leakage B-PRO
current I-PRO
of O
less O
than O
10-8 O
A O
/ O
cm2 O
that O
is O
corresponding O
to O
the O
high O
- O
temperature O
processed O
thermal B-SMT
oxidized I-SMT
O2Si B-MAT
. O


study O
on O
corrosion B-PRO
resistance I-PRO
and O
photocatalysis B-APL
of O
cobalt B-MAT
superhydrophobic B-PRO
coating B-APL
on O
aluminum B-MAT
substrate B-DSC


A O
textured O
flower B-DSC
- I-DSC
like I-DSC
cobalt B-MAT
superhydrophobic B-PRO
surface I-PRO
( O
SHS B-PRO
) O
with O
a O
water B-PRO
contact I-PRO
angle I-PRO
of O
<nUm> O
° O
and O
a O
sliding B-PRO
angle I-PRO
of O
less O
than O
<nUm> O
° O
was O
fabricated O
on O
aluminum B-MAT
substrate B-DSC
by O
immersing O
the O
processed O
aluminum B-MAT
sheets B-DSC
perpendicularly O
into O
cobalt O
( O
II O
) O
nitrate O
aqueous O
solution O
and O
followed O
by O
annealing B-SMT
treatment I-SMT
. O


the O
morphology B-PRO
and O
chemical B-PRO
composition I-PRO
of O
the O
SHS B-PRO
were O
characterized O
using O
scanning B-CMT
electron I-CMT
microscopy I-CMT
( O
SEM B-CMT
) O
, O
atomic B-CMT
force I-CMT
microscopy I-CMT
( O
AFM B-CMT
) O
, O
x-ray B-CMT
diffraction I-CMT
pattern I-CMT
( O
XRD B-CMT
) O
, O
energy B-CMT
- I-CMT
dispersive I-CMT
spectroscopy I-CMT
( O
EDS B-CMT
) O
and O
x-ray B-CMT
photoelectron I-CMT
spectroscopy I-CMT
( O
XPS B-CMT
) O
. O


the O
corrosion B-PRO
resistance I-PRO
of O
the O
samples O
was O
characterized O
via O
polarization B-PRO
, O
nyquist B-CMT
and I-CMT
bode I-CMT
modulus I-CMT
plots I-CMT
. O


the O
photocatalysis B-APL
of O
samples O
was O
also O
studied O
by O
catalytic O
degradation O
of O
methyl O
orange O
under O
a O
UV O
lamp O
( O
λ O
= O
<nUm> O
nm O
) O
with O
a O
light O
intensity O
of O
<nUm> O
W O
. O


the O
cobalt B-MAT
superhydrophobic B-PRO
sample O
not O
only O
exhibited O
excellent O
catalytic B-PRO
properties I-PRO
, O
but O
also O
substantially O
improved O
the O
corrosion B-PRO
resistance I-PRO
of O
aluminum B-MAT
substrate B-DSC
. O


effects O
of O
MgO B-MAT
and O
H2MgO2 B-MAT
on O
phase O
formation O
and O
properties O
of O
strontium B-MAT
– O
doped B-DSC
MgO3Ti B-MAT
microwave B-APL
dielectric I-APL
ceramics B-DSC


the O
effects O
of O
MgO B-MAT
and O
H2MgO2 B-MAT
on O
the O
phase O
formation O
and O
properties O
of O
0.97MgTiO3 B-MAT
– I-MAT
0.03SrTiO3 I-MAT
ceramics B-DSC
were O
investigated O
. O


MgO5Ti2 B-MAT
formed O
in O
pellets B-DSC
added O
with O
MgO B-MAT
( O
MST B-MAT
) O
and O
disappeared O
in O
pellets B-DSC
added O
with O
H2MgO2 B-MAT
( O
MHST B-MAT
) O
. O


abnormal O
grain O
growth O
was O
observed O
in O
MHST B-MAT
due O
to O
different O
reactions O
during O
the O
heating B-SMT
process O
. O


values O
of O
er B-PRO
= O
<nUm> O
− O
<nUm> O
, O
q B-PRO
× I-PRO
f I-PRO
= O
16,500-23,000 O
GHz O
and O
tf B-PRO
= O
− O
<nUm> O
to O
<nUm> O
ppm O
/ O
° O
C O
and O
of O
er B-PRO
= O
<nUm> O
− O
<nUm> O
, O
q B-PRO
× I-PRO
f I-PRO
= O
31,300-48,600 O
GHz O
and O
tf B-PRO
= O
− O
<nUm> O
to O
<nUm> O
ppm O
/ O
° O
C O
were O
measured O
for O
MST B-MAT
and O
MHST B-MAT
, O
respectively O
. O


lower O
er B-PRO
for O
MHST B-MAT
was O
caused O
by O
a O
lower O
density B-PRO
. O


q B-PRO
× I-PRO
f I-PRO
increased O
and O
tf B-PRO
shifted O
to O
more O
negative O
values O
when O
H2MgO2 B-MAT
was O
used O
instead O
of O
MgO B-MAT
. O


quantum B-PRO
- I-PRO
confined I-PRO
bandgap I-PRO
narrowing O
of O
O2Ti B-MAT
nanoparticles B-DSC
by O
graphene B-MAT
quantum B-DSC
dots I-DSC
for O
visible B-APL
- I-APL
light I-APL
- I-APL
driven I-APL
applications I-APL


we O
for O
the O
first O
time O
report O
a O
quantum B-PRO
- I-PRO
confined I-PRO
bandgap I-PRO
narrowing O
mechanism O
through O
which O
the O
absorption B-PRO
of O
two O
UV B-APL
absorbers I-APL
, O
namely O
the O
graphene B-MAT
quantum B-DSC
dots I-DSC
( O
GQDs B-MAT
) O
and O
O2Ti B-MAT
nanoparticles B-DSC
, O
can O
be O
easily O
extended O
into O
the O
visible O
light O
range O
in O
a O
controllable O
manner O
. O


such O
a O
mechanism O
may O
be O
of O
great O
importance O
for O
light B-APL
harvesting I-APL
, O
photocatalysis B-APL
and O
optoelectronics B-APL
. O


enhanced O
field B-PRO
emission I-PRO
properties I-PRO
from O
graphene-TiO2 B-MAT
/ O
DLC B-MAT
nanocomposite B-DSC
films I-DSC
prepared O
by O
ultraviolet B-SMT
- I-SMT
light I-SMT
assisted I-SMT
electrochemical I-SMT
deposition I-SMT


the O
graphene-TiO2 B-MAT
/ O
diamond B-MAT
- I-MAT
like I-MAT
carbon I-MAT
( O
G-TiO2 B-MAT
/ O
DLC B-MAT
) O
nanocomposite B-DSC
films I-DSC
were O
prepared O
on O
silicon B-MAT
substrates B-DSC
by O
a O
simple O
ultraviolet B-SMT
( I-SMT
UV I-SMT
) I-SMT
light I-SMT
assisted I-SMT
electrochemical I-SMT
deposition I-SMT
process I-SMT
using O
N O
, O
n-dimethylformamide O
( O
DMF O
) O
as O
carbon B-MAT
source O
and O
O2Ti B-MAT
nanoparticles B-DSC
/ O
graphene B-MAT
sheets B-DSC
as O
incorporated O
reagents O
. O


the O
results O
show O
that O
the O
O2Ti B-MAT
and O
graphene B-MAT
sheets B-DSC
are O
uniformly O
dispersed O
into O
the O
DLC B-MAT
matrix B-DSC
. O


the O
UV B-SMT
- I-SMT
light I-SMT
illumination I-SMT
not O
only O
affects O
the O
morphology B-PRO
of O
the O
films B-DSC
, O
but O
also O
promotes O
the O
field B-PRO
emission I-PRO
properties I-PRO
, O
probably O
due O
to O
the O
effect O
of O
photoinduced O
electron O
- O
hole O
pairs O
produced O
from O
O2Ti B-MAT
. O


the O
G-TiO2 B-MAT
/ O
DLC B-MAT
film B-DSC
exhibits O
the O
lowest O
turn-on B-PRO
field I-PRO
of O
<nUm> O
V O
/ O
mm O
and O
the O
highest O
current B-PRO
density I-PRO
of O
<nUm> O
mA O
/ O
cm2 O
at O
the O
electric O
field O
of O
<nUm> O
V O
/ O
mm O
. O


this O
enhancement O
of O
field B-PRO
emission I-PRO
properties I-PRO
are O
investigated O
based O
on O
the O
surface B-PRO
morphology I-PRO
of O
the O
self O
- O
assembled O
nanostructures B-DSC
, O
the O
improved O
conductivity B-PRO
, O
together O
with O
the O
reduced O
work B-PRO
function I-PRO
. O


effect O
of O
Nb B-MAT
addition O
on O
structure B-PRO
and O
mechanical B-PRO
properties I-PRO
of O
AlFe B-MAT
coating B-APL


mild B-MAT
steel I-MAT
was O
coated B-SMT
by O
hot B-SMT
- I-SMT
dipping I-SMT
in O
a O
molten O
aluminum B-MAT
bath O
. O


the O
Fe B-MAT
– I-MAT
Al I-MAT
– I-MAT
Nb I-MAT
alloyed B-SMT
coating B-APL
was O
prepared O
by O
implanting B-SMT
the O
Nb B-MAT
atoms O
into O
the O
Fe B-MAT
– I-MAT
Al I-MAT
coating B-APL
using O
a O
double B-SMT
- I-SMT
glow I-SMT
plasma I-SMT
surface I-SMT
metallurgy I-SMT
method O
. O


the O
morphology B-PRO
, O
element B-PRO
distribution I-PRO
and O
phase B-PRO
composition I-PRO
of O
the O
alloyed B-DSC
layer I-DSC
were O
characterized O
by O
OM B-CMT
, O
SEM B-CMT
/ O
EDX B-CMT
and O
XRD B-CMT
. O


meanwhile O
, O
the O
basic O
mechanical B-PRO
properties I-PRO
of O
these O
two O
coatings B-APL
were O
measured O
and O
compared O
. O


the O
results O
showed O
that O
the O
Nb B-MAT
element O
exhibited O
gradient O
distribution O
in O
the O
Fe B-MAT
– I-MAT
Al I-MAT
coating B-APL
. O


and O
the O
alloyed B-DSC
layer I-DSC
consisted O
of O
pure O
Nb B-MAT
, O
Al5Fe2 B-MAT
, O
AlFe3 B-MAT
, O
AlNb2 B-MAT
and O
Fe7Nb6 B-MAT
phases O
. O


after O
Nb B-MAT
addition O
, O
the O
microhardness B-PRO
of O
the O
Fe B-MAT
– I-MAT
Al I-MAT
coating B-APL
was O
improved O
for O
the O
diffusely B-PRO
distributed I-PRO
carbide B-MAT
phases O
. O


and O
the O
adhesion B-PRO
was O
enhanced O
with O
better O
plastic B-PRO
deformation I-PRO
. O


what O
's O
more O
, O
the O
nanoindentation B-CMT
tests I-CMT
indicated O
that O
the O
toughness B-PRO
of O
the O
Fe B-MAT
– I-MAT
Al I-MAT
coating B-APL
was O
improved O
with O
a O
stronger O
ability B-PRO
to I-PRO
resist I-PRO
plastic I-PRO
deformation I-PRO
and O
a O
greater O
plastic B-PRO
deformation I-PRO
work I-PRO
. O


effects O
of O
atomic B-PRO
ordering I-PRO
on O
the O
elastic B-PRO
properties I-PRO
of O
TiN- B-MAT
and O
VN B-MAT
- O
based O
ternary O
alloys B-DSC


improved O
toughness B-PRO
is O
one O
of O
the O
central O
goals O
in O
the O
development O
of O
wear B-APL
- I-APL
resistant I-APL
coatings I-APL
. O


previous O
studies O
of O
toughness B-PRO
in O
transition B-MAT
metal I-MAT
nitride I-MAT
alloys B-DSC
have O
addressed O
the O
effects O
of O
chemical B-PRO
composition I-PRO
in O
these O
compounds O
. O


herein O
, O
we O
use O
density B-CMT
functional I-CMT
theory I-CMT
to O
study O
the O
effects O
of O
various O
metal B-PRO
sublattice I-PRO
configurations I-PRO
, O
ranging O
from O
fully O
ordered O
to O
fully O
disordered O
, O
on O
the O
mechanical B-PRO
properties I-PRO
of O
VM2N B-MAT
and O
TiM2N B-MAT
( I-MAT
M2 I-MAT
= I-MAT
W I-MAT
, I-MAT
Mo I-MAT
) I-MAT
ternary O
alloys B-DSC
. O


results O
show O
that O
all O
alloys B-DSC
display O
high O
incompressibility B-PRO
, O
indicating O
strong O
me B-PRO
– I-PRO
N I-PRO
bonds I-PRO
. O


disordered B-PRO
atomic I-PRO
arrangements I-PRO
yield O
lower O
values O
of O
bulk B-PRO
moduli I-PRO
and O
C11 B-PRO
elastic I-PRO
constants I-PRO
, O
as O
well O
as O
higher O
values O
of O
C44 B-PRO
elastic I-PRO
constants I-PRO
, O
compared O
to O
ordered O
structures B-PRO
. O


we O
attribute O
the O
low O
C44 B-PRO
values O
of O
ordered B-PRO
structures I-PRO
to O
the O
formation O
of O
fully B-PRO
- I-PRO
bonding I-PRO
states I-PRO
perpendicular O
to O
the O
applied O
stress O
. O


we O
find O
that O
the O
ductility B-PRO
of O
these O
compounds O
is O
primarily O
an O
effect O
of O
the O
increased O
valence B-PRO
electron I-PRO
concentration I-PRO
induced O
upon O
alloying B-SMT
. O


ultra-efficient O
and O
durable O
photoelectrochemical B-APL
water I-APL
oxidation I-APL
using O
elaborately O
designed O
hematite B-MAT
nanorod B-DSC
arrays I-DSC


ultrahigh O
- O
efficiency O
photoelectrochemical B-APL
water I-APL
oxidation I-APL
using O
modified O
hematite B-MAT
( O
a-Fe2O3 B-MAT
) O
nanorod B-DSC
arrays I-DSC
is O
reported O
. O


the O
hematite B-MAT
nanorod B-DSC
arrays O
are O
synthesized O
using O
chemical B-SMT
bath I-SMT
deposition I-SMT
and O
further O
modified O
by O
hydrogen B-SMT
treatment I-SMT
, O
loading O
of O
a O
~ O
3.5-nm-thick O
O2Ti B-MAT
overlayer B-DSC
, O
and O
deposition O
of O
a O
cobalt B-MAT
phosphate I-MAT
( O
CoPi B-MAT
) O
catalyst B-APL
. O


although O
each O
modification O
method O
is O
well O
known O
, O
an O
elaborate O
optimization O
of O
the O
combined O
modification O
methods O
achieves O
a O
stable O
photocurrent B-PRO
density I-PRO
of O
~ O
<nUm> O
mAcm-2 O
at O
<nUm> O
V O
vs O
. O


RHE O
over O
100h O
under O
AM O
1.5G O
irradiation O
( O
100mWcm-2 O
) O
with O
the O
stoichiometric B-DSC
O O
and O
H O
evolutions O
at O
~ O
<nUm> O
% O
of O
faradaic B-PRO
efficiency I-PRO
. O


to O
the O
best O
of O
our O
knowledge O
, O
this O
is O
the O
highest O
photocurrent B-PRO
density I-PRO
obtained O
using O
a O
hematite B-MAT
- O
based O
photoanode B-APL
, O
and O
such O
long O
- O
term O
durability B-PRO
coupled O
with O
this O
level O
of O
efficiency B-PRO
has O
been O
rarely O
reported O
. O


the O
modified O
- O
hematite B-MAT
photoanodes B-APL
are O
thoroughly O
characterized O
using O
various O
spectroscopic B-CMT
and O
electrochemical B-CMT
techniques I-CMT
. O


while O
the O
hydrogen B-SMT
treatment I-SMT
enhances O
the O
electrical B-PRO
conductivity I-PRO
, O
the O
ultrathin O
O2Ti B-MAT
overlayer B-DSC
reduces O
the O
surface B-PRO
charge I-PRO
recombination I-PRO
and O
effectively O
preserved O
the O
integrity O
of O
the O
hydrogen B-SMT
- I-SMT
treated I-SMT
hematite B-MAT
electrode B-APL
. O


OZn B-MAT
and O
O2Ti B-MAT
1D B-DSC
nanostructures I-DSC
for O
photocatalytic B-APL
applications I-APL


OZn B-MAT
and O
O2Ti B-MAT
1D B-DSC
nanostructures I-DSC
( O
nanorods B-DSC
and O
nanotubes B-DSC
) O
were O
prepared O
by O
low B-SMT
- I-SMT
cost I-SMT
, I-SMT
low I-SMT
- I-SMT
temperature I-SMT
, I-SMT
solution I-SMT
- I-SMT
based I-SMT
methods I-SMT
and O
their O
properties O
and O
photocatalytic B-PRO
performance I-PRO
were O
studied O
. O


OZn B-MAT
nanorod B-DSC
samples O
with O
titania B-MAT
and O
alumina B-MAT
shells B-DSC
were O
also O
prepared O
by O
solution B-SMT
- I-SMT
based I-SMT
methods I-SMT
, O
and O
their O
properties O
and O
photocatalytic B-PRO
performance I-PRO
were O
compared O
to O
that O
of O
bare O
OZn B-MAT
nanorods B-DSC
. O


we O
found O
that O
OZn B-MAT
and O
O2Ti B-MAT
exhibited O
comparable O
photocatalytic B-PRO
performance I-PRO
. O


faster O
dye O
degradation O
under O
simulated O
solar O
illumination O
was O
observed O
for O
OZn B-MAT
, O
while O
under O
UV O
illumination O
faster O
degradation O
was O
observed O
for O
O2Ti B-MAT
. O


OZn B-MAT
nanorods B-DSC
with O
titania B-MAT
shells B-DSC
exhibited O
inferior O
photocatalytic B-PRO
performance I-PRO
, O
while O
for O
alumina B-MAT
shells B-DSC
the O
performance O
was O
similar O
to O
bare O
OZn B-MAT
. O


reasons O
for O
observed O
differences O
are O
discussed O
, O
and O
the O
effect O
of O
the O
shell O
on O
photocatalytic B-PRO
activity I-PRO
is O
attributed O
to O
the O
changes O
in O
native B-PRO
defects I-PRO
at O
the O
OZn B-MAT
surface B-DSC
/ I-DSC
shell I-DSC
interface I-DSC
. O


electric B-PRO
properties I-PRO
and O
structure B-PRO
of O
Ag B-MAT
x I-MAT
(As0.33S0.335Se0.335)100- I-MAT
x I-MAT
bulk B-DSC
glasses I-DSC


In O
this O
paper O
, O
results O
of O
investigation O
of O
the O
bulk B-DSC
glasses I-DSC
with O
composition B-PRO
of O
Agx(As0.33S0.335Se0.335)100-x B-MAT
( I-MAT
x I-MAT
= I-MAT
<nUm> I-MAT
– I-MAT
28at I-MAT
% I-MAT
) I-MAT
are O
revealed O
. O


the O
amorphous B-DSC
structure O
of O
samples O
was O
confirmed O
by O
the O
x-ray B-CMT
diffraction I-CMT
analysis O
. O


the O
structure B-PRO
was O
deduced O
from O
the O
raman B-CMT
spectra O
measured O
for O
all O
silver B-PRO
contents I-PRO
in O
As B-MAT
– I-MAT
S I-MAT
– I-MAT
Se I-MAT
matrix O
. O


from O
the O
point O
of O
their O
electrical B-PRO
properties I-PRO
, O
all O
glasses B-DSC
behave O
as O
ionic B-PRO
conductors I-PRO
. O


their O
ac B-PRO
conductivity I-PRO
increases O
with O
increasing O
content O
of O
silver B-MAT
. O


As O
determined O
from O
the O
comparison O
of O
ac B-PRO
and O
dc B-PRO
conductivities I-PRO
, O
the O
contribution O
of O
electronic B-PRO
conductivity I-PRO
to O
the O
overall O
conductivity B-PRO
is O
very O
low O
and O
decreases O
from O
about O
<nUm> O
% O
for O
the O
glass B-DSC
with O
12at O
% O
of O
Ag B-MAT
to O
about O
<nUm> O
% O
for O
the O
glass B-DSC
with O
22at O
% O
of O
Ag B-MAT
. O


influence O
of O
antimony B-MAT
doping B-SMT
on O
structure B-PRO
and O
conductivity B-PRO
of O
tin B-MAT
oxide I-MAT
whiskers B-DSC


tin B-MAT
dioxide I-MAT
whiskers B-DSC
doped I-DSC
with O
different O
concentrations O
of O
antimony B-MAT
( O
<nUm> O
– O
<nUm> O
at. O
% O
) O
have O
been O
grown O
from O
OSn B-MAT
and O
O3Sb2 B-MAT
mixture O
in O
a O
tube B-SMT
furnace I-SMT
in O
a O
flowing O
mixture O
of O
argon O
and O
oxygen O
at O
a O
constant O
source O
temperature O
. O


the O
whiskers B-DSC
possess O
high O
structural B-PRO
perfection I-PRO
. O


influence O
of O
Sb B-MAT
on O
crystal B-PRO
structure I-PRO
, O
morphology B-PRO
and O
conductivity B-PRO
of O
O2Sn B-MAT
whiskers B-DSC
is O
investigated O
. O


antimony B-MAT
doping O
allows O
a O
decrease O
in O
the O
resistance B-PRO
of O
O2Sn B-MAT
whiskers B-DSC
up O
to O
<nUm> O
times O
. O


preparation O
of O
and O
magnetic B-PRO
scattering I-PRO
in O
Nd2-xCexCuO4-d B-MAT


samples O
of O
Nd2-xCexCuO4-d B-MAT
were O
prepared O
by O
annealing B-SMT
under O
a O
high O
vacuum O
( O
<nUm> O
− O
<nUm> O
torr O
) O
. O


powder B-CMT
x-ray I-CMT
diffraction I-CMT
patterns O
indicated O
that O
the O
samples O
consisted O
of O
a O
single B-DSC
phase I-DSC
CuNd2O4 B-SPL
- O
type O
tetragonal B-SPL
structure O
with O
crystal B-PRO
symmetry I-PRO
I4 B-SPL
/ I-SPL
mmm I-SPL
. O


the O
normal B-PRO
state I-PRO
resistivity I-PRO
of O
the O
superconducting B-PRO
samples O
shows O
a O
logarithmic O
temperature O
dependence O
, O
which O
we O
show O
is O
a O
common O
feature O
in O
the O
electron O
cuprate O
superconductors B-PRO
. O


the O
absence O
of O
significant O
phonon O
- O
induced O
scattering O
by O
the O
lattice O
in O
the O
resistivity B-PRO
data O
indicates O
that O
the O
dominant O
contribution O
to O
the O
normal B-PRO
state I-PRO
resistivity I-PRO
in O
the O
electron O
cuprate O
superconductors B-PRO
comes O
from O
the O
magnetic B-PRO
scattering I-PRO
. O


refractory B-APL
oxynitride B-MAT
joints O
in O
silicon B-MAT
nitride I-MAT


sintered B-SMT
silicon B-MAT
nitride I-MAT
was O
joined O
to O
itself O
by O
heating B-SMT
interlayers B-DSC
of O
refractory B-APL
oxide B-MAT
compositions B-PRO
above O
their O
liquidus B-PRO
temperatures I-PRO
in O
flowing O
nitrogen O
. O


only O
enough O
pressure O
was O
used O
to O
maintain O
alignment O
of O
the O
parts O
in O
the O
fixture O
. O


the O
oxide B-MAT
compositions B-PRO
were O
in O
the O
Y2O3-Al2O3-SiO2 B-MAT
and O
SrO-Al2O3-SiO2 B-MAT
families O
and O
the O
silicon B-MAT
nitride I-MAT
was O
from O
two O
commercial O
sources O
. O


joined O
specimens O
were O
tested O
in O
four B-CMT
point I-CMT
flexure I-CMT
from O
room O
temperature O
to O
<nUm> O
° O
C O
. O


A O
maximum O
strength B-PRO
of O
<nUm> O
MPa O
was O
observed O
at O
<nUm> O
° O
C O
, O
which O
as O
far O
as O
we O
know O
is O
the O
highest O
<nUm> O
° O
C O
strength B-PRO
ever O
observed O
for O
silicon B-MAT
nitride I-MAT
joined O
without O
high O
applied O
pressure O
. O


quantitative O
measurements O
of O
composition B-PRO
profiles I-PRO
at O
the O
ceramic-oxide-ceramic B-DSC
interface I-DSC
revealed O
that O
interdiffusion O
of O
cations O
from O
the O
silicon B-MAT
nitride I-MAT
and O
the O
oxide B-MAT
joining O
material O
maintains O
local O
charge O
balance O
. O


synthesis O
of O
CoLiO2 B-MAT
cathodes B-APL
by O
an O
oxidation B-SMT
reaction I-SMT
in O
solution O
and O
their O
electrochemical B-PRO
properties I-PRO


layered B-DSC
CoLiO2 B-MAT
was O
synthesized O
by O
an O
oxidation B-SMT
of O
co2+ O
ions O
in O
aqueous O
solutions O
by O
lithium O
peroxide O
in O
the O
presence O
of O
excess O
lithium O
hydroxide O
, O
followed O
by O
firing B-SMT
at O
<nUm> O
– O
<nUm> O
° O
C O
. O


the O
samples O
were O
characterized O
by O
x-ray B-CMT
diffraction I-CMT
( O
XRD B-CMT
) O
and O
wet B-CMT
- I-CMT
chemical I-CMT
analysis I-CMT
. O


although O
single B-DSC
phase I-DSC
Li1+xCo1-xO2 B-MAT
samples O
with O
a O
Li B-PRO
/ I-PRO
Co I-PRO
ratio I-PRO
> O
<nUm> O
could O
be O
obtained O
at O
lower O
firing B-SMT
temperatures O
, O
they O
were O
metastable B-PRO
and O
transformed O
to O
the O
stoichiometric B-DSC
CoLiO2 B-MAT
with O
a O
Li B-PRO
/ I-PRO
Co I-PRO
ratio I-PRO
of O
<nUm> O
at O
higher O
firing B-SMT
temperatures O
( O
T O
≈ O
<nUm> O
° O
C O
) O
. O


the O
samples O
fired B-SMT
at O
low O
temperatures O
( O
T O
≤ O
<nUm> O
° O
C O
) O
exhibited O
lower O
capacity B-PRO
and O
poor O
electrochemical B-PRO
cyclability I-PRO
in O
the O
lithium B-APL
cells I-APL
, O
due O
to O
a O
disordering O
of O
the O
li+ O
and O
co3+ O
ions O
, O
and O
poor O
crystallinity B-PRO
. O


on O
the O
other O
hand O
, O
the O
samples O
fired B-SMT
at O
<nUm> O
° O
C O
exhibited O
a O
capacity B-PRO
as O
high O
as O
<nUm> O
mAh O
/ O
g O
in O
the O
voltage O
range O
<nUm> O
– O
<nUm> O
V O
, O
with O
excellent O
cyclability B-PRO
due O
to O
good O
cation B-PRO
ordering I-PRO
and O
crystallinity B-PRO
. O


surface B-SMT
roughening I-SMT
by O
anisotropic O
adatom B-PRO
kinetics I-PRO
in O
epitaxial O
growth O
of O
Ca33La67Mn100O300 B-MAT


the O
growth B-PRO
mechanisms I-PRO
and O
surface B-PRO
morphology I-PRO
of O
colossal B-PRO
magnetoresistance I-PRO
( O
CMR B-PRO
) O
Ca33La67Mn100O300 B-MAT
films B-DSC
deposited O
by O
rf B-SMT
magnetron I-SMT
sputtering I-SMT
on O
SrTiO3(001) B-MAT
substrates B-DSC
are O
investigated O
. O


the O
films B-DSC
are O
epitaxial O
, O
coherently B-PRO
strained I-PRO
and O
ferromagnetic B-PRO
. O


it O
is O
found O
that O
at O
early O
growth O
stages O
, O
in O
nanometric B-DSC
films I-DSC
, O
a O
layer O
- O
by O
- O
layer O
mechanism O
dominates O
, O
which O
results O
in O
step O
and O
terrace O
surface B-PRO
morphology I-PRO
. O


upon O
further O
growth O
, O
the O
flat O
surface B-DSC
becomes O
unstable O
when O
large O
two O
- O
dimensional O
( O
2D O
) O
islands O
form O
. O


the O
erlich B-PRO
- I-PRO
schwoebel I-PRO
step I-PRO
- I-PRO
edge I-PRO
energy I-PRO
barrier I-PRO
induces O
an O
anisotropic O
adatom B-PRO
kinetics I-PRO
that O
favors O
2D O
nucleation O
on O
top O
of O
the O
islands O
as O
it O
reduces O
downhill B-PRO
adatom I-PRO
current I-PRO
. O


As O
a O
result O
, O
there O
is O
an O
evolution O
with O
growth O
to O
mound O
- O
like O
structures O
of O
increasing O
height O
. O


critical B-PRO
thickness I-PRO
for I-PRO
mound I-PRO
formation I-PRO
and O
average O
mound B-PRO
separation I-PRO
can O
be O
tuned O
by O
substrate B-DSC
miscut B-PRO
angle I-PRO
and O
growth O
temperature O
. O


these O
results O
provide O
a O
detailed O
understanding O
of O
the O
roughening B-SMT
process O
in O
manganites B-MAT
and O
are O
relevant O
for O
the O
controlled O
fabrication O
of O
CMR B-PRO
films B-DSC
, O
in O
particular O
for O
its O
use O
in O
epitaxial O
heterostructures B-DSC
. O


effect O
of O
quasicrystal B-DSC
phase O
on O
mechanical B-PRO
properties I-PRO
and O
damping B-PRO
capacities I-PRO
of O
Mg B-MAT
– I-MAT
Zn I-MAT
– I-MAT
Y I-MAT
– I-MAT
Zr I-MAT
alloys B-DSC


four O
Mg B-MAT
– I-MAT
5x I-MAT
% I-MAT
Zn I-MAT
– I-MAT
x I-MAT
% I-MAT
Y I-MAT
– I-MAT
<nUm> I-MAT
% I-MAT
Zr I-MAT
alloys B-DSC
reinforced O
with O
the O
I-Mg3YZn6 B-MAT
quasicrystal B-DSC
phase O
were O
fabricated O
by O
introducing O
Zn B-MAT
and O
Y B-MAT
elements O
into O
Mg B-MAT
– I-MAT
<nUm> I-MAT
% I-MAT
Zr I-MAT
alloys B-DSC
under O
conventional O
solidification B-SMT
condition I-SMT
. O


due O
to O
the O
coherent O
lattice O
relationship O
between O
the O
I-Mg3YZn6 B-MAT
phase O
and O
the O
a-Mg B-MAT
matrix O
, O
the O
grain B-PRO
sizes I-PRO
of O
the O
Mg B-MAT
– I-MAT
Zn I-MAT
– I-MAT
Y I-MAT
– I-MAT
Zr I-MAT
alloys B-DSC
are O
obviously O
refined O
and O
the O
tensile B-PRO
strengths I-PRO
are O
largely O
improved O
to O
a O
maximum O
value O
of O
<nUm> O
MPa O
. O


the O
fracture B-PRO
mechanism I-PRO
transformed O
from O
cleavage O
fracture O
to O
quasi-cleavage O
fracture O
with O
increasing O
amount O
of O
I-Mg3YZn6 B-MAT
phase O
. O


the O
damping B-PRO
capacities I-PRO
of O
the O
Mg B-MAT
– I-MAT
Zn I-MAT
– I-MAT
Y I-MAT
– I-MAT
Zr I-MAT
alloys B-DSC
decrease O
with O
the O
increasing O
I-Mg3YZn6 B-MAT
phase O
and O
the O
damping B-PRO
behavior I-PRO
can O
be O
explained O
with O
the O
g B-CMT
– I-CMT
L I-CMT
dislocation I-CMT
model I-CMT
. O


the O
forming O
of O
the O
I-Mg3YZn6 B-MAT
phase O
makes O
more O
grain B-PRO
boundaries I-PRO
, O
phases O
and O
interfaces B-DSC
generate O
in O
the O
alloys B-DSC
. O


and O
the O
dislocation B-PRO
densities I-PRO
in O
the O
alloys B-DSC
hardly O
changes O
as O
little O
residual B-PRO
stress I-PRO
or O
entanglement O
of O
dislocation O
generates O
at O
the O
interface B-DSC
between O
the O
I-Mg3YZn6 B-MAT
phase O
and O
the O
a-Mg B-MAT
matrix O
. O


so O
the O
damping B-PRO
values I-PRO
are O
reduced O
accordingly O
with O
the O
strong O
pinning B-PRO
points I-PRO
on O
dislocations B-PRO
increasing O
tremendously O
. O


mechanical B-SMT
amorphization I-SMT
of O
B3Fe15Nb2 B-MAT
powder B-DSC
: O
microstructural B-PRO
and O
magnetic B-CMT
characterization I-CMT


the O
evolution O
of O
the O
amorphous B-DSC
fraction O
developed O
during O
the O
mechanical B-SMT
alloying I-SMT
of O
a O
mixture O
of O
pure O
75at. B-MAT
% I-MAT
Fe I-MAT
, I-MAT
10at. I-MAT
% I-MAT
Nb I-MAT
and I-MAT
15at. I-MAT
% I-MAT
B I-MAT
, O
XAm O
, O
has O
been O
followed O
by O
different O
techniques O
: O
x-ray B-CMT
diffraction I-CMT
, O
mossbauer B-CMT
spectroscopy I-CMT
and O
magnetic B-CMT
permeability I-CMT
measurements I-CMT
; O
in O
order O
to O
compare O
their O
sensitivity O
in O
the O
detection O
of O
small O
fractions O
. O


the O
values O
obtained O
for O
the O
amorphous B-DSC
fraction O
from O
the O
three O
techniques O
show O
a O
roughly O
linear O
correlation O
above O
∼ O
<nUm> O
% O
. O


the O
most O
sensitive O
technique O
was O
mossbauer B-CMT
spectroscopy I-CMT
( O
XAm O
obtained O
from O
the O
low O
hyperfine B-PRO
field I-PRO
contributions I-PRO
) O
and O
the O
less O
sensitive O
technique O
was O
x-ray B-CMT
diffraction I-CMT
. O


the O
curie B-PRO
temperature I-PRO
of O
the O
amorphous B-DSC
phase O
increases O
with O
the O
milling B-SMT
time O
due O
to O
a O
slow O
and O
progressive O
incorporation O
of O
boron B-MAT
into O
this O
phase O
and O
the O
nanocrystals B-DSC
from O
the O
boron B-PRO
inclusions I-PRO
. O


potential O
application O
of O
ceramic B-DSC
matrix I-DSC
composites I-DSC
to O
aero B-APL
- I-APL
engine I-APL
components I-APL


the O
present O
paper O
describes O
the O
potential O
application O
of O
ceramic B-DSC
matrix I-DSC
composites I-DSC
to O
aero B-APL
- I-APL
engine I-APL
components I-APL
by O
reviewing O
the O
related O
published O
papers O
and O
our O
experience O
in O
this O
field O
. O


it O
contains O
the O
material O
requirements O
for O
aero B-APL
- I-APL
engines I-APL
, O
trends O
in O
aero B-APL
- I-APL
engine I-APL
materials I-APL
use O
, O
japanese O
projects O
related O
to O
ceramic B-DSC
matrix I-DSC
composites I-DSC
( O
CMCs B-DSC
) O
and O
potential O
application O
of O
CMCs B-DSC
to O
aero B-APL
- I-APL
engines I-APL
, O
such O
as O
combustors B-APL
, O
nozzle B-APL
flaps I-APL
, O
bladed B-APL
disks I-APL
and O
others O
. O


from O
the O
point O
of O
application O
to O
aero B-APL
- I-APL
engines I-APL
, O
the O
remaining O
research O
and O
development O
issues O
are O
discussed O
to O
some O
extent O
. O


material O
developments O
, O
particularly O
of O
the O
interface B-DSC
and O
fibers B-DSC
for O
high O
temperature O
, O
are O
still O
required O
and O
stressed O
. O


thermal B-PRO
and O
electrical B-PRO
properties I-PRO
of O
AgI B-MAT
- O
based O
composites B-DSC


AgI B-MAT
- O
based O
composites B-DSC
with O
a O
general O
formula O
AgIMxOy B-MAT
( I-MAT
MxOy I-MAT
= I-MAT
O2Zr I-MAT
, I-MAT
CeO2 I-MAT
, I-MAT
Fe2O3 I-MAT
, I-MAT
O3Sm2 I-MAT
, I-MAT
MoO3 I-MAT
and I-MAT
O3W I-MAT
) I-MAT
have O
been O
studied O
in O
detail O
. O


the O
enhancement O
in O
the O
conductivity B-PRO
of O
AgI B-MAT
and O
its O
unusual O
thermal B-PRO
stability I-PRO
and O
amorphization O
are O
explained O
assuming O
a O
chemical B-PRO
interaction I-PRO
at O
the O
oxide B-MAT
- O
AgI B-MAT
interface B-DSC
. O


physical B-PRO
properties I-PRO
of O
the O
delafossite B-SPL
CuLaO2 B-MAT


high O
- O
quality O
CuLaO2 B-MAT
, O
elaborated O
by O
solid B-SMT
- I-SMT
state I-SMT
reaction I-SMT
in O
sealed O
tube O
, O
crystallizes O
in O
the O
delafossite B-SPL
structure O
. O


the O
thermal B-CMT
analysis I-CMT
under O
reducing O
atmosphere O
( O
H O
/ O
N O
: O
<nUm> O
/ O
<nUm> O
) O
revealed O
a O
stoichiometric B-PRO
composition I-PRO
CuLaO2 B-MAT
. O


the O
oxide B-MAT
is O
a O
direct B-PRO
band I-PRO
- I-PRO
gap I-PRO
semiconductor I-PRO
with O
a O
forbidden B-PRO
band I-PRO
of O
<nUm> O
eV O
. O


the O
magnetic B-PRO
susceptibility I-PRO
follows O
a O
curie B-CMT
– I-CMT
weiss I-CMT
law I-CMT
from O
which O
a O
cu2+ B-PRO
concentration I-PRO
of O
<nUm> O
% O
has O
been O
determined O
. O


the O
oxygen O
insertion O
in O
the O
layered B-DSC
crystal B-PRO
lattice I-PRO
induces O
p B-PRO
- I-PRO
type I-PRO
conductivity I-PRO
. O


the O
electrical B-PRO
conduction I-PRO
occurs O
predominantly O
by O
small O
polaron O
hopping O
between O
mixed O
valences O
cu+ O
/ O
2+ O
with O
an O
activation B-PRO
energy I-PRO
of O
<nUm> O
eV O
and O
a O
hole B-PRO
mobility I-PRO
( O
m300K B-PRO
= O
<nUm> O
× O
10-7 O
cm2V-1s-1 O
) O
, O
thermally O
activated O
. O


most O
holes O
are O
trapped O
in O
surface B-PRO
– I-PRO
polaron I-PRO
states I-PRO
upon O
gap O
excitation O
. O


the O
photoelectrochemical B-CMT
study I-CMT
, O
reported O
for O
the O
first O
time O
, O
confirms O
the O
p B-PRO
- I-PRO
type I-PRO
conduction I-PRO
. O


the O
flat B-PRO
band I-PRO
potential I-PRO
( O
vfb B-PRO
= O
<nUm> O
VSCE O
) O
and O
the O
hole B-PRO
density I-PRO
( O
NA B-PRO
= O
<nUm> O
× O
<nUm> O
cm-3 O
) O
were O
determined O
, O
respectively O
, O
by O
extrapolating O
the O
curve O
C-2 O
versus O
the O
potential O
to O
their O
intersection O
with O
C-2 O
= O
<nUm> O
and O
from O
the O
slope O
of O
the O
linear O
part O
in O
the O
mott B-CMT
– I-CMT
schottky I-CMT
plot I-CMT
. O


the O
valence B-PRO
band I-PRO
is O
made O
up O
of O
cu-3d O
orbital O
, O
positioned O
at O
4.9eV O
below O
vacuum O
. O


an O
energy B-PRO
band I-PRO
diagram I-PRO
has O
been O
established O
predicting O
the O
possibility O
of O
the O
oxide B-MAT
to O
be O
used O
as O
hydrogen B-APL
photocathode I-APL
. O


corrosion B-PRO
behavior I-PRO
of O
a O
CNZr B-MAT
coated B-SMT
Ti B-MAT
alloy B-DSC
with O
potential O
application O
as O
a O
bipolar B-APL
plate I-APL
for O
proton B-APL
exchange I-APL
membrane I-APL
fuel I-APL
cell I-APL


to O
improve O
the O
corrosion B-PRO
resistance I-PRO
, O
surface B-PRO
electrical I-PRO
conductivity I-PRO
and O
wettability B-PRO
of O
Ti B-MAT
– I-MAT
6Al I-MAT
– I-MAT
4V I-MAT
used O
in O
polymer B-APL
electrolyte I-APL
membrane I-APL
fuel I-APL
cell I-APL
( O
PEMFC B-APL
) O
, O
a O
CNZr B-MAT
nanocrystalline B-DSC
coating B-APL
was O
deposited O
on O
Ti B-MAT
– I-MAT
6Al I-MAT
– I-MAT
4V I-MAT
substrate B-DSC
using O
double B-SMT
cathode I-SMT
glow I-SMT
discharge I-SMT
technique I-SMT
. O


the O
new O
coating B-APL
exhibited O
a O
nanocomposite B-DSC
structure B-PRO
, O
consisting O
of O
amorphous B-DSC
C B-MAT
, O
CNx B-MAT
and O
nanocrystalline B-DSC
CNZr B-MAT
. O


the O
effect O
of O
the O
HF O
concentrations O
on O
the O
corrosion B-PRO
behavior I-PRO
of O
the O
coating B-APL
was O
investigated O
by O
potentiodynamic B-CMT
, O
potentiostatic B-CMT
polarizations I-CMT
and O
electrochemical B-CMT
impedance I-CMT
spectroscopy I-CMT
( O
EIS B-CMT
) O
in O
a O
simulated O
the O
operating O
conditions O
of O
a O
PEMFC B-APL
. O


with O
increasing O
HF O
concentrations O
, O
the O
corrosion B-PRO
potential I-PRO
( O
ecorr B-PRO
) O
decreased O
and O
the O
corrosion B-PRO
current I-PRO
density I-PRO
( O
icorr B-PRO
) O
of O
the O
CNZr B-MAT
coating B-APL
increased O
, O
indicating O
that O
corrosion B-PRO
resistance I-PRO
decreased O
with O
the O
increase O
of O
HF O
concentrations O
. O


however O
, O
at O
any O
given O
concentration O
of O
HF O
, O
the O
corrosion B-PRO
resistance I-PRO
of O
the O
CNZr B-MAT
coating B-APL
was O
significantly O
higher O
than O
that O
of O
uncoated O
Ti B-MAT
– I-MAT
6Al I-MAT
– I-MAT
4V I-MAT
. O


the O
results O
of O
EIS B-CMT
measurements O
showed O
that O
with O
increasing O
the O
concentration O
of O
HF O
, O
the O
resistance B-PRO
of O
the O
passive B-PRO
film B-DSC
( O
Rb B-MAT
) O
formed O
on O
the O
CNZr B-MAT
coating B-APL
decreased O
slightly O
, O
being O
of O
the O
order O
of O
magnitude O
of O
∼ O
<nUm> O
Ω O
cm2 O
, O
which O
was O
an O
improvement O
by O
four O
orders O
of O
magnitude O
compared O
to O
uncoated O
Ti-6A1-4V B-MAT
. O


At O
a O
compaction O
force O
of O
<nUm> O
N O
cm-2 O
, O
no O
perceptible O
difference O
in O
the O
interfacial B-PRO
contact I-PRO
resistance I-PRO
( O
ICR B-PRO
) O
of O
CNZr B-MAT
- O
coated B-DSC
Ti-6A1-4V B-MAT
was O
observed O
before O
and O
after O
potentiostatic O
polarization O
for O
<nUm> O
min O
, O
and O
its O
ICR B-PRO
values O
were O
reduced O
by O
one O
order O
of O
magnitude O
in O
comparison O
to O
that O
of O
uncoated O
Ti-6A1-4V B-MAT
. O


moreover O
, O
CNZr B-MAT
- O
coated B-SMT
Ti-6A1-4V B-MAT
exhibited O
a O
much O
low O
surface B-PRO
wettability I-PRO
than O
uncoated O
Ti B-MAT
– I-MAT
6Al I-MAT
– I-MAT
4V I-MAT
alloy B-DSC
, O
which O
was O
beneficial O
for O
both O
water O
management O
and O
improving O
corrosion B-PRO
resistance I-PRO
. O


hydrothermal B-SMT
synthesis I-SMT
and O
photoelectrochemical B-PRO
performance I-PRO
enhancement O
of O
O2Ti B-MAT
/ O
graphene B-MAT
composite B-DSC
in O
photo B-APL
- I-APL
generated I-APL
cathodic I-APL
protection I-APL


O2Ti B-MAT
/ O
graphene B-MAT
composites B-DSC
were O
synthesized O
through O
one B-SMT
- I-SMT
step I-SMT
hydrothermal I-SMT
method I-SMT
. O


the O
composites B-DSC
show O
an O
enhancement O
in O
photo B-PRO
- I-PRO
generated I-PRO
cathodic I-PRO
protection I-PRO
as O
the O
time O
- O
dependent O
profiles O
of O
photocurrent B-PRO
responses I-PRO
has O
confirmed O
. O


XRD B-CMT
data O
show O
that O
a O
bicrystalline B-DSC
framework O
of O
anatase B-SPL
and O
brookite B-SPL
formed O
as O
graphene B-MAT
provided O
donor O
groups O
in O
the O
hydrothermal B-SMT
process I-SMT
. O


the O
transfer O
of O
photoinduced O
electrons O
in O
the O
biphasic B-DSC
O2Ti B-MAT
results O
in O
effective O
electron O
- O
hole O
separation O
. O


moreover O
, O
graphene B-MAT
lead O
to O
a O
negative O
shift O
of O
the O
fermi B-PRO
level I-PRO
as O
evidenced O
by O
mott B-CMT
– I-CMT
schottky I-CMT
analysis I-CMT
, O
which O
decreases O
the O
schottky B-PRO
barrier I-PRO
formed O
in O
the O
O2Ti B-MAT
and O
<nUm> B-MAT
stainless I-MAT
steel I-MAT
interface B-DSC
and O
results O
in O
the O
enhancement O
of O
photo B-PRO
- I-PRO
generated I-PRO
cathodic I-PRO
protection I-PRO
. O


first B-CMT
principles I-CMT
study O
of O
the O
structural B-PRO
, O
electronic B-PRO
, O
mechanical B-PRO
and O
superconducting B-PRO
properties I-PRO
of O
WX B-MAT
( I-MAT
x I-MAT
= I-MAT
C I-MAT
, I-MAT
N I-MAT
) I-MAT


the O
structural B-PRO
, O
electronic B-PRO
, O
mechanical B-PRO
and O
superconducting B-PRO
properties I-PRO
of O
tungsten B-MAT
carbide I-MAT
( O
WC B-MAT
) O
and O
tungsten B-MAT
nitride I-MAT
( O
WN B-MAT
) O
are O
investigated O
using O
first B-CMT
principles I-CMT
calculations I-CMT
based O
on O
density B-CMT
functional I-CMT
theory I-CMT
( O
DFT B-CMT
) O
. O


the O
computed O
ground B-PRO
state I-PRO
properties I-PRO
, O
such O
as O
equilibrium B-PRO
lattice I-PRO
constant I-PRO
and O
cell B-PRO
volume I-PRO
, O
are O
in O
good O
agreement O
with O
the O
available O
experimental O
data O
. O


A O
pressure O
induced O
structural B-PRO
phase I-PRO
transition I-PRO
is O
observed O
in O
both O
tungsten B-MAT
carbide I-MAT
and O
nitride B-MAT
, O
from O
a O
tungsten B-MAT
carbide I-MAT
phase O
( O
WC B-SPL
) O
to O
a O
zinc B-SPL
blende I-SPL
phase O
( O
ZB B-SPL
) O
, O
and O
from O
a O
zinc B-SPL
blende I-SPL
phase O
( O
ZB B-SPL
) O
to O
a O
wurtzite B-SPL
phase O
( O
WZ B-SPL
) O
. O


the O
electronic B-PRO
structure I-PRO
reveals O
that O
these O
materials O
are O
metallic B-PRO
at O
ambient O
conditions O
. O


the O
calculated O
elastic B-PRO
constants I-PRO
obey O
the O
born B-CMT
- I-CMT
huang I-CMT
criteria I-CMT
, O
suggesting O
that O
they O
are O
mechanically B-PRO
stable I-PRO
at O
normal O
and O
high O
pressure O
. O


also O
, O
the O
superconducting B-PRO
transition I-PRO
temperature I-PRO
is O
estimated O
for O
the O
WC B-MAT
and O
WN B-MAT
in O
stable B-PRO
structures I-PRO
at O
atmospheric O
pressure O
. O


characterization O
of O
the O
free B-PRO
volume I-PRO
in O
a O
Ag87Al70Cu393Zr450 B-MAT
bulk B-DSC
metallic B-PRO
glass I-PRO
by O
reverse B-CMT
monte I-CMT
carlo I-CMT
simulation I-CMT
and O
density B-CMT
measurements I-CMT


the O
absolute O
contents O
of O
free B-PRO
volume I-PRO
in O
the O
as-cast B-DSC
and O
annealed B-SMT
Ag87Al70Cu393Zr450 B-MAT
bulk B-DSC
metallic B-PRO
glass I-PRO
( O
BMG B-PRO
) O
samples O
were O
quantified O
by O
density B-CMT
measurements I-CMT
and O
reverse B-CMT
monte I-CMT
carlo I-CMT
( O
RMC B-CMT
) O
simulation O
using O
the O
total O
structural B-PRO
factors I-PRO
F(Q) I-PRO
determined O
by O
x-ray B-CMT
diffraction I-CMT
( O
XRD B-CMT
) O
experiments O
as O
fitting O
constraints O
. O


the O
densities B-PRO
of O
the O
as-cast B-DSC
, O
annealed B-SMT
and O
crystallized B-DSC
samples O
measured O
by O
archimedes B-CMT
method I-CMT
are O
<nUm> O
, O
<nUm> O
and O
<nUm> O
g O
/ O
cm3 O
( O
precision O
± O
<nUm> O
g O
/ O
cm3 O
) O
, O
respectively O
. O


A O
new O
approach O
was O
used O
in O
the O
RMC B-CMT
simulation I-CMT
to O
define O
the O
free B-PRO
volume I-PRO
as O
the O
difference O
between O
the O
volume O
of O
the O
voronoi B-PRO
polyhedron I-PRO
and O
the O
volume O
of O
the O
wigner B-PRO
– I-PRO
seitz I-PRO
cell I-PRO
of O
the O
constituent O
atoms O
. O


two O
types O
of O
initial O
configurations O
were O
constructed O
: O
( O
<nUm> O
) O
in O
configuration O
A O
, O
all O
types O
of O
potential O
atomic O
pairs O
are O
allowed O
; O
( O
<nUm> O
) O
in O
configuration O
B O
, O
Al-Al B-MAT
and O
Ag-Ag B-MAT
atomic O
pairs O
are O
excluded O
. O


the O
contents O
of O
free B-PRO
volume I-PRO
in O
the O
as-cast B-DSC
and O
annealed B-SMT
samples O
were O
found O
to O
be O
<nUm> O
% O
and O
<nUm> O
% O
( O
configuration O
A O
) O
, O
<nUm> O
% O
and O
<nUm> O
% O
( O
configuration O
B O
) O
, O
respectively O
( O
precision O
± O
<nUm> O
% O
) O
. O


the O
probability O
distribution O
of O
the O
as-calculated O
free B-PRO
volume I-PRO
can O
be O
well O
- O
fitted O
by O
the O
equation O
proposed O
by O
turnbull O
and O
cohen O
. O


finally O
, O
it O
is O
shown O
that O
the O
contents O
of O
free B-PRO
volume I-PRO
determined O
by O
density B-CMT
measurements I-CMT
and O
RMC B-CMT
are O
comparable O
, O
while O
the O
discrepancy O
of O
the O
results O
is O
discussed O
. O


graphene B-MAT
based O
new O
energy B-APL
materials I-APL


graphene B-MAT
, O
a O
one O
- O
atom O
layer O
of O
graphite B-MAT
, O
possesses O
a O
unique O
two B-PRO
- I-PRO
dimensional I-PRO
( O
2D B-PRO
) O
structure B-PRO
, O
high O
conductivity B-PRO
and O
charge B-PRO
carrier I-PRO
mobility I-PRO
, O
huge O
specific B-PRO
surface I-PRO
area I-PRO
, O
high O
transparency B-PRO
and O
great O
mechanical B-PRO
strength I-PRO
. O


thus O
, O
it O
is O
expected O
to O
be O
an O
ideal O
material O
for O
energy B-APL
storage I-APL
and O
conversion B-APL
. O


during O
the O
past O
several O
years O
, O
a O
variety O
of O
graphene B-MAT
based O
materials O
( O
GBMs B-APL
) O
have O
been O
successfully O
prepared O
and O
applied O
in O
supercapacitors B-APL
, O
lithium B-APL
ion I-APL
batteries I-APL
, O
water B-APL
splitting I-APL
, O
electrocatalysts B-APL
for O
fuel B-APL
cells I-APL
, O
and O
solar B-APL
cells I-APL
. O


In O
this O
review O
, O
we O
will O
summarize O
the O
recent O
advances O
in O
the O
synthesis O
and O
applications O
of O
GBMs B-APL
in O
these O
energy O
related O
systems O
. O


the O
challenges O
and O
prospects O
of O
graphene B-MAT
based O
new O
energy B-APL
materials I-APL
are O
also O
discussed O
. O


synthesis O
of O
YAG B-MAT
: I-MAT
Ce I-MAT
phosphor B-APL
via O
different O
aluminum B-MAT
sources O
and O
precipitation B-SMT
processes I-SMT


ce3+ O
- O
doped B-DSC
yttrium B-MAT
aluminum I-MAT
garnet I-MAT
( O
YAG B-MAT
: I-MAT
Ce I-MAT
) O
phosphors B-APL
were O
synthesized O
by O
the O
four O
different O
precipitating B-SMT
processes I-SMT
, O
in O
which O
aluminum O
nitrate O
or O
aluminum O
ammonium O
sulfate O
was O
used O
as O
the O
aluminum B-MAT
source O
. O


pure O
YAG B-MAT
: I-MAT
Ce I-MAT
powder B-DSC
can O
be O
obtained O
by O
using O
aluminum O
nitrate O
combine O
normal O
strike B-SMT
precipitation I-SMT
method O
as O
calcined B-SMT
at O
<nUm> O
° O
C O
for O
2h O
. O


the O
property O
of O
YAG B-MAT
powder B-DSC
is O
affected O
by O
the O
cation B-PRO
homogeneity I-PRO
of O
precursor O
powder B-DSC
. O


the O
product O
formed O
by O
aluminum O
nitrate O
combine O
normal O
strike B-SMT
precipitation I-SMT
method O
has O
the O
highest O
emission O
peak O
at O
<nUm> O
nm O
after O
excitation O
at O
<nUm> O
nm O
. O


growth O
of O
large O
- O
sized O
Nd B-MAT
: I-MAT
NO8W2Y I-MAT
crystal B-DSC
and O
its O
spectral B-PRO
properties I-PRO


this O
paper O
reports O
the O
growth O
of O
nd3+ B-MAT
: I-MAT
NO8W2Y I-MAT
crystal B-DSC
with O
high O
optical B-PRO
quality I-PRO
and O
large O
size O
. O


nd3+ B-MAT
: I-MAT
NO8W2Y I-MAT
crystal B-DSC
with O
the O
dimension O
Ph30 O
× O
<nUm> O
mm2 O
and O
optical B-PRO
homogeneity I-PRO
<nUm> O
× O
<nUm> O
− O
<nUm> O
was O
grown O
by O
czhchoralski B-SMT
method I-SMT
: O
the O
seed O
used O
was O
[100] O
orientation O
, O
the O
pulling O
rate O
and O
rotating O
rate O
were O
<nUm> O
– O
<nUm> O
mm O
/ O
h O
and O
15rpm O
, O
respectively O
. O


the O
growing O
processes O
and O
characteristics O
of O
nd3+ B-MAT
: I-MAT
NO8W2Y I-MAT
crystal B-DSC
was O
discussed O
. O


its O
unpolarized O
absorption B-CMT
spectra O
and O
emission B-CMT
spectra O
were O
measured O
. O


the O
absorption B-PRO
cross-section I-PRO
and O
emission B-PRO
cross-section I-PRO
were O
presented O
. O


based O
on O
the O
judd B-CMT
– I-CMT
ofelt I-CMT
theory I-CMT
, O
we O
obtained O
the O
three O
intensity B-PRO
parameters I-PRO
: O
Ω B-PRO
<nUm> I-PRO
= O
<nUm> O
× O
<nUm> O
<nUm> O
- O
<nUm> O
, O
Ω B-PRO
<nUm> I-PRO
= O
<nUm> O
× O
<nUm> O
<nUm> O
- O
<nUm> O
, O
and O
Ω B-PRO
<nUm> I-PRO
= O
<nUm> O
× O
<nUm> O
<nUm> O
- O
<nUm> O
cm O
<nUm> O
. O


the O
radiative B-PRO
probabilities I-PRO
, O
radiative B-PRO
lifetimes I-PRO
, O
branch B-PRO
ratios I-PRO
and O
quantum B-PRO
efficiency I-PRO
of O
nd3+ B-MAT
: I-MAT
NO8W2Y I-MAT
were O
calculated O
too O
. O


influence O
of O
Fe B-MAT
and O
Al B-MAT
doping B-SMT
on O
the O
stabilization O
of O
the O
anatase B-SPL
phase O
in O
O2Ti B-MAT
nanoparticles B-DSC


anatase B-SPL
O2Ti B-MAT
nanoparticles B-DSC
doped I-DSC
with O
Al B-MAT
or O
Fe B-MAT
have O
been O
synthesized O
via O
a O
modified O
pechini B-SMT
method I-SMT
which O
allows O
us O
to O
reach O
high O
control O
in O
size O
and O
composition B-PRO
. O


microstructural B-CMT
analysis I-CMT
confirms O
the O
good O
crystallinity B-PRO
of O
the O
doped B-DSC
anatase B-SPL
nanoparticles B-DSC
with O
average O
sizes O
around O
<nUm> O
nm O
and O
dopant B-PRO
cationic I-PRO
concentrations I-PRO
up O
to O
<nUm> O
% O
. O


the O
anatase B-PRO
to I-PRO
rutile I-PRO
transition I-PRO
( O
ART B-PRO
) O
has O
been O
thermally O
driven O
and O
analyzed O
as O
a O
function O
of O
the O
doping B-SMT
. O


thermo B-CMT
- I-CMT
diffraction I-CMT
measurements I-CMT
indicate O
that O
the O
phase B-PRO
transition I-PRO
can O
be O
either O
promoted O
or O
inhibited O
by O
Fe B-MAT
or O
Al B-MAT
doping B-SMT
, O
respectively O
. O


the O
influence O
of O
Al B-MAT
and O
Fe B-MAT
doping B-SMT
on O
the O
phase B-PRO
transition I-PRO
has O
been O
discussed O
by O
means O
of O
raman B-CMT
spectroscopy I-CMT
, O
photoluminescence B-CMT
and O
x-ray B-CMT
photoelectron I-CMT
spectroscopy I-CMT
, O
with O
special O
attention O
paid O
to O
the O
role O
played O
by O
ti3+ O
at O
the O
surface B-DSC
. O


the O
anatase B-SPL
phase O
has O
been O
stabilized O
up O
to O
temperatures O
above O
<nUm> O
° O
C O
by O
appropriate O
Al B-MAT
doping B-SMT
. O


abrasive B-PRO
wear I-PRO
resistance I-PRO
of O
ti1- B-MAT
x I-MAT
Al I-MAT
x I-MAT
N I-MAT
hard B-APL
coatings I-APL
deposited O
by O
a O
vacuum B-SMT
arc I-SMT
system I-SMT
with O
lateral O
rotating O
cathodes B-APL


In O
this O
work O
, O
a O
series O
of O
Ti1-xAlxN B-MAT
( I-MAT
<nUm> I-MAT
≤ I-MAT
x I-MAT
≤ I-MAT
<nUm> I-MAT
) I-MAT
coatings B-APL
were O
deposited O
on O
high O
speed O
steel B-MAT
( O
HSS B-MAT
) O
substrates B-DSC
by O
a O
vacuum B-SMT
arc I-SMT
reactive I-SMT
evaporation I-SMT
process O
from O
two O
lateral O
rotating O
elemental O
titanium B-MAT
and O
aluminium B-MAT
cathodes B-APL
in O
a O
pure O
nitrogen O
atmosphere O
. O


the O
composition B-PRO
, O
crystalline B-PRO
structure I-PRO
and O
hardness B-PRO
of O
the O
as-deposited B-DSC
coatings B-APL
were O
analyzed O
by O
energy B-CMT
dispersive I-CMT
x-ray I-CMT
spectroscopy I-CMT
( O
EDX B-CMT
) O
, O
x-ray B-CMT
diffraction I-CMT
( O
XRD B-CMT
) O
, O
and O
nanoindentation B-CMT
experiments O
. O


the O
abrasion B-PRO
wear I-PRO
resistance I-PRO
of O
the O
AlNTi B-MAT
coatings B-APL
was O
measured O
by O
a O
micro-abrasion B-CMT
tester I-CMT
with O
the O
presence O
of O
CSi B-MAT
water B-DSC
- O
based O
slurry O
with O
a O
concentration O
of O
<nUm> O
g O
/ O
cm3 O
. O


it O
was O
found O
that O
with O
increasing O
the O
Al B-PRO
/ I-PRO
Ti I-PRO
atomic I-PRO
ratio I-PRO
the O
hardness B-PRO
of O
the O
as-deposited B-DSC
AlNTi B-MAT
coatings B-APL
initially O
increased O
up O
to O
a O
maximum O
value O
of O
about O
<nUm> O
GPa O
at O
around O
Al B-PRO
/ I-PRO
Ti I-PRO
= O
<nUm> O
, O
and O
then O
the O
coating B-APL
hardness B-PRO
decreased O
rapidly O
with O
increasing O
aluminium B-MAT
content O
further O
. O


the O
abrasion B-PRO
wear I-PRO
resistance I-PRO
of O
the O
AlNTi B-MAT
coatings B-APL
is O
evidently O
better O
, O
with O
one O
order O
of O
magnitude O
lower O
in O
the O
wear B-PRO
rate I-PRO
, O
than O
the O
bare O
HSS B-MAT
substrate B-DSC
. O


with O
increasing O
Al B-PRO
/ I-PRO
Ti I-PRO
atomic I-PRO
ratio I-PRO
, O
the O
variation O
trend O
of O
the O
abrasion B-PRO
wear I-PRO
rate I-PRO
of O
the O
AlNTi B-MAT
coatings B-APL
is O
generally O
opposite O
to O
that O
of O
coating B-APL
hardness B-PRO
. O


this O
means O
the O
abrasion B-PRO
wear I-PRO
resistance I-PRO
of O
the O
AlNTi B-MAT
PVD B-SMT
hard B-APL
coatings I-APL
is O
predominately O
determined O
by O
the O
hardness B-PRO
of O
the O
coating B-APL
materials O
. O


it O
was O
also O
noted O
that O
, O
besides O
the O
coating B-APL
hardness B-PRO
, O
the O
composition B-PRO
of O
the O
AlNTi B-MAT
coatings B-APL
also O
plays O
an O
important O
role O
in O
determining O
their O
abrasive B-PRO
wear I-PRO
resistance I-PRO
. O


the O
coatings B-APL
in O
the O
higher O
Al B-PRO
content I-PRO
range O
( O
Al B-PRO
/ I-PRO
Ti I-PRO
≥ O
<nUm> O
) O
exhibited O
an O
evident O
better O
abrasive B-PRO
wear I-PRO
resistance I-PRO
than O
those O
in O
the O
lower O
aluminium B-PRO
content I-PRO
range O
( O
Al B-PRO
/ I-PRO
Ti I-PRO
≤ O
<nUm> O
) O
when O
their O
hardness B-PRO
is O
similar O
. O


this O
fact O
could O
be O
related O
to O
the O
finer O
microstructure B-PRO
of O
the O
coatings B-APL
incorporated O
with O
higher O
aluminium B-MAT
content O
. O


graphene B-MAT
encapsulated B-DSC
Fe3O4 B-MAT
nanorods B-DSC
assembled O
into O
a O
mesoporous B-DSC
hybrid I-DSC
composite I-DSC
used O
as O
a O
high O
- O
performance O
lithium B-APL
- I-APL
ion I-APL
battery I-APL
anode I-APL
material O


the O
discovery O
of O
new O
anode B-APL
materials O
and O
engineering O
their O
fine B-PRO
structures I-PRO
are O
the O
core O
elements O
in O
the O
development O
of O
new O
- O
generation O
lithium B-APL
ion I-APL
batteries I-APL
( O
LIBs B-APL
) O
. O


to O
this O
end O
, O
we O
herein O
report O
a O
novel O
nanostructured B-DSC
composite I-DSC
consisting O
of O
approximately O
<nUm> O
% O
Fe3O4 B-MAT
nanorods B-DSC
and O
<nUm> O
% O
reduced B-MAT
graphene I-MAT
oxide I-MAT
( O
rGO B-MAT
) O
. O


microscopy B-CMT
and O
spectroscopy B-CMT
analyses I-CMT
have O
identified O
that O
the O
Fe3O4 B-MAT
nanorods B-DSC
are O
wrapped O
( O
or O
encapsulated O
) O
by O
the O
rGO B-MAT
nanosheets B-DSC
via O
covalent O
bonding O
, O
which O
further O
self O
- O
assemble O
into O
a O
mesoporous B-DSC
hybrid I-DSC
composite I-DSC
networked O
by O
the O
graphene B-MAT
matrix B-DSC
. O


the O
composite B-DSC
has O
an O
average O
pore B-PRO
size I-PRO
around O
<nUm> O
nm O
and O
exhibits O
a O
high O
surface B-PRO
area I-PRO
of O
<nUm> O
m2 O
g-1 O
, O
which O
is O
<nUm> O
times O
as O
high O
as O
that O
of O
conventional O
Fe3O4 B-MAT
powder B-DSC
. O


we O
have O
used O
the O
composite B-DSC
as O
an O
LIB B-APL
anode I-APL
material O
to O
fabricate O
coin B-APL
- I-APL
type I-APL
prototype I-APL
cells I-APL
with O
lithium B-MAT
as O
the O
cathode B-APL
. O


systematic O
half B-APL
- I-APL
cell I-APL
testing O
evaluations O
show O
that O
the O
electrochemical B-PRO
performance I-PRO
of O
the O
present O
composite B-DSC
material O
is O
amongst O
the O
best O
of O
the O
transition B-MAT
metal I-MAT
- I-MAT
oxide I-MAT
based O
LIB B-APL
anode I-APL
materials O
. O


the O
performances O
are O
characterized O
by O
a O
high O
reversible B-PRO
capacity I-PRO
of O
<nUm> O
mA O
h O
g-1 O
subjected O
to O
<nUm> O
charge O
– O
discharge O
cycles O
at O
<nUm> O
mA O
g-1 O
and O
an O
excellent O
rate B-PRO
capability I-PRO
with O
the O
deliverable B-PRO
energy I-PRO
of O
<nUm> O
– O
<nUm> O
mA O
h O
g-1 O
upon O
the O
application O
of O
high O
current O
densities O
of O
<nUm> O
– O
<nUm> O
mA O
g-1 O
. O


overall O
, O
we O
have O
demonstrated O
that O
Fe3O4 B-MAT
nanorod B-DSC
– O
rGO B-MAT
hybrid B-DSC
composite I-DSC
is O
an O
interesting O
and O
promising O
material O
for O
the O
fabrication O
of O
LIB B-APL
anodes I-APL
. O


delamination B-PRO
- I-PRO
resistant I-PRO
bi-layer B-DSC
electrolyte B-APL
for O
anode B-APL
- O
supported O
solid B-APL
oxide I-APL
fuel I-APL
cells I-APL


one O
of O
the O
critical O
fuel B-APL
cell I-APL
degradation O
phenomena O
is O
‘ O
cell O
imbalance O
’ O
in O
a O
series B-APL
- I-APL
connected I-APL
stack I-APL
, O
which O
can O
cause O
abnormal O
operation O
under O
a O
negative O
cell B-APL
voltage O
and O
consequently O
rapid O
degradation O
by O
anode B-APL
interface B-DSC
delamination O
. O


In O
a O
previous O
study O
, O
the O
effect O
of O
electrolyte B-APL
composition B-PRO
on O
the O
electrochemical B-PRO
degradation I-PRO
of O
solid B-APL
oxide I-APL
fuel I-APL
cell I-APL
( O
SOFC B-APL
) O
was O
investigated O
, O
and O
it O
was O
observed O
that O
a O
small O
amount O
of O
ceria B-MAT
( O
an O
electronic B-PRO
conducting I-PRO
material O
) O
prevents O
anode B-APL
delamination O
under O
abnormal O
( O
negative O
voltage O
) O
operation O
. O


however O
, O
the O
open B-PRO
circuit I-PRO
voltage I-PRO
( O
OCV B-PRO
) O
was O
lowered O
as O
a O
result O
of O
reduction O
of O
ceria B-MAT
. O


In O
the O
present O
study O
, O
bi-layer B-DSC
, O
YSZ B-MAT
( O
<nUm> O
mol O
% O
yttria B-MAT
doped B-DSC
zirconia B-MAT
, O
a O
predominantly O
ionic B-PRO
conductor I-PRO
) O
at O
the O
cathode B-APL
side O
and O
8CYSZ B-MAT
( O
<nUm> O
mol O
% O
ceria B-MAT
doped B-DSC
YSZ B-MAT
, O
a O
mixed B-PRO
ionic I-PRO
- I-PRO
electronic I-PRO
conductor I-PRO
) O
at O
the O
anode B-APL
side O
were O
fabricated O
for O
anode B-APL
- O
supported O
cells B-APL
with O
a O
Pt B-MAT
probe O
embedded O
in O
each O
layer B-DSC
to O
estimate O
the O
internal O
oxygen B-PRO
chemical I-PRO
potential I-PRO
and O
tested O
under O
a O
negative O
voltage O
. O


the O
results O
indicated O
that O
the O
OCV B-PRO
was O
close O
to O
the O
theoretical O
value O
( O
similar O
to O
that O
of O
a O
YSZ B-MAT
single B-DSC
layer I-DSC
cell B-APL
) O
and O
no O
delamination O
was O
observed O
under O
negative O
voltage O
operation O
( O
similar O
to O
the O
case O
of O
an O
8CYSZ B-MAT
single B-DSC
- I-DSC
layer I-DSC
cell B-APL
) O
. O


therefore O
, O
the O
bi-layer-structured B-DSC
electrolyte B-APL
( O
with O
locally O
increased O
electronic B-PRO
conduction I-PRO
at O
the O
anode B-APL
side O
) O
is O
effective O
in O
preventing O
anode B-APL
/ O
electrolyte B-APL
delamination O
as O
well O
as O
maintaining O
open B-PRO
circuit I-PRO
voltage I-PRO
. O


improving O
the O
uniformity O
in O
mechanical B-PRO
properties I-PRO
of O
a O
sintered B-SMT
Ti B-MAT
compact O
using O
a O
trace O
amount O
of O
internal O
lubricant B-APL


large O
sintered B-SMT
powder B-DSC
compacts O
are O
likely O
to O
be O
associated O
with O
variability O
in O
mechanical B-PRO
properties I-PRO
; O
an O
improvement O
of O
the O
uniformity O
of O
the O
mechanical B-PRO
properties I-PRO
of O
sintered B-SMT
powder B-DSC
compacts O
is O
important O
for O
powder B-APL
metallurgy I-APL
. O


In O
this O
work O
<nUm> O
– O
1wt. O
% O
stearic O
acid O
( O
SA O
) O
or O
magnesium O
stearate O
( O
MgSt O
) O
was O
added O
to O
a O
<nUm> O
mm O
diameter O
Ti B-MAT
powder B-DSC
compacts O
with O
height O
to O
depth O
( O
H O
/ O
d O
) O
ratio O
of O
unity O
to O
give O
a O
more O
uniform O
green B-PRO
density I-PRO
. O


tensile B-CMT
test I-CMT
pieces O
were O
cut O
from O
selected O
positions O
in O
each O
sintered B-SMT
compact O
to O
obtain O
the O
distribution O
of O
mechanical B-PRO
properties I-PRO
. O


results O
revealed O
that O
variations O
in O
mechanical B-PRO
properties I-PRO
are O
due O
to O
the O
pore B-PRO
morphology I-PRO
with O
respect O
to O
size O
, O
aspect O
ratio O
and O
preferred B-PRO
orientation I-PRO
. O


A O
trace O
amount O
of O
lubricant B-APL
significantly O
improves O
the O
uniformity O
in O
mechanical B-PRO
properties I-PRO
by O
optimizing O
the O
porosity B-PRO
distribution I-PRO
and O
minimizing O
the O
pore B-PRO
size I-PRO
and O
aspect B-PRO
ratio I-PRO
of I-PRO
pores I-PRO
after O
sintering B-SMT
. O


such O
an O
effect O
was O
achieved O
by O
reducing O
the O
initial O
green B-PRO
density I-PRO
inhomogeneity I-PRO
and O
the O
stress B-PRO
induced O
by O
the O
mismatch O
of O
sintering B-SMT
shrinkage O
. O


however O
a O
relatively O
high O
1wt. O
% O
SA O
addition O
with O
a O
large O
particle O
size O
created O
burnt O
- O
off O
pores O
in O
the O
top O
and O
bottom O
zones O
. O


MgSt O
is O
not O
recommended O
since O
it O
significantly O
increases O
the O
oxygen B-PRO
content I-PRO
. O


an O
addition O
of O
0.6wt. O
% O
SA O
is O
the O
best O
choice O
due O
to O
the O
even O
pore B-PRO
distribution I-PRO
, O
small O
pore B-PRO
size I-PRO
and O
acceptable O
level O
of O
oxygen B-PRO
pick I-PRO
up I-PRO
. O


microstructure B-PRO
refinement I-PRO
and O
magnetic B-PRO
property I-PRO
enhancement O
of O
nanocomposite B-DSC
BFe14Pr2 B-MAT
/ O
a-Fe B-MAT
magnets B-APL
by O
small O
substitution O
of O
m B-MAT
for I-MAT
Fe I-MAT
( I-MAT
m I-MAT
= I-MAT
Cr I-MAT
, I-MAT
Nb I-MAT
, I-MAT
Ti I-MAT
and I-MAT
Zr I-MAT
) I-MAT


A O
comprehensive O
study O
on O
the O
effect O
of O
various O
substitutions O
of O
m O
on O
the O
magnetic B-PRO
and O
structural B-PRO
properties I-PRO
of O
melt B-SMT
- I-SMT
spun I-SMT
nanocomposite B-DSC
Pr8Fe84M2B6 B-MAT
( I-MAT
m I-MAT
= I-MAT
Cr I-MAT
, I-MAT
Nb I-MAT
, I-MAT
Ti I-MAT
and I-MAT
Zr I-MAT
) I-MAT
magnets B-APL
has O
been O
performed O
with O
the O
aim O
of O
refining O
the O
microstructure B-PRO
and O
therefore O
enhancing O
the O
hard B-PRO
magnetic I-PRO
properties I-PRO
. O


it O
has O
been O
found O
that O
magnetic B-PRO
properties I-PRO
are O
improved O
by O
all O
the O
substitutions O
. O


the O
largest O
enhancement O
is O
obtained O
in O
Nb B-MAT
substituted O
B3Fe42NbPr4 B-MAT
magnets B-APL
where O
a O
coercivity B-PRO
of O
<nUm> O
kOe O
and O
a O
maximum O
energy B-PRO
product I-PRO
of O
<nUm> O
MGOe O
have O
been O
obtained O
, O
as O
compared O
to O
the O
coercivity B-PRO
of O
<nUm> O
kOe O
and O
the O
energy B-PRO
product I-PRO
of O
<nUm> O
MGOe O
in O
the O
B3Fe43Pr4 B-MAT
magnet B-APL
. O


microstructure B-CMT
studies I-CMT
revealed O
a O
finer O
and O
more O
uniform O
<nUm> O
: O
<nUm> O
: O
<nUm> O
/ O
a-Fe B-MAT
nanoscale O
microstructure B-PRO
with O
m O
substitutions O
. O


the O
most O
uniform O
microstructure B-PRO
with O
the O
smallest O
average O
grain B-PRO
size I-PRO
of O
<nUm> O
– O
<nUm> O
nm O
is O
developed O
in O
the O
Nb B-MAT
substituted O
magnets B-APL
. O


the O
enhancement O
of O
magnetic B-PRO
properties I-PRO
by O
m O
substitution O
is O
believed O
to O
be O
due O
to O
the O
microstructure B-PRO
refinement I-PRO
which O
leads O
to O
an O
enhanced O
exchange B-PRO
coupling I-PRO
between O
BFe14Pr2 B-MAT
and O
a-Fe B-MAT
. O


possible O
ferromagnetism B-PRO
in O
Cd B-MAT
- O
doped B-DSC
O2Ti B-MAT
: O
A O
first B-CMT
- I-CMT
principles I-CMT
study I-CMT


the O
magnetic B-PRO
properties I-PRO
of O
Cd B-MAT
- O
doped B-DSC
O2Ti B-MAT
have O
been O
investigated O
by O
first B-CMT
- I-CMT
principles I-CMT
calculations I-CMT
. O


it O
is O
found O
that O
the O
doped B-DSC
system O
favors O
the O
spin B-PRO
- I-PRO
polarized I-PRO
state I-PRO
and O
high O
curie B-PRO
- I-PRO
temperature I-PRO
ferromagnetism I-PRO
can O
be O
expected O
in O
it O
. O


the O
ferromagnetism B-PRO
can O
be O
attributed O
to O
the O
p-d B-PRO
hybridization I-PRO
between O
Cd B-MAT
and O
its O
surrounded O
oxygen O
atoms O
. O


Cd B-MAT
atoms O
do O
not O
tend O
to O
form O
clusters B-DSC
in O
O2Ti B-MAT
. O


the O
doped B-DSC
system O
can O
be O
favorably O
synthesized O
in O
oxygen O
- O
rich O
condition O
. O


moreover O
, O
Ti B-PRO
vacancies I-PRO
are O
much O
easier O
to O
form O
than O
oxygen B-PRO
vacancies I-PRO
in O
the O
doped B-DSC
system O
. O


we O
find O
that O
oxygen B-PRO
vacancies I-PRO
are O
harmful O
to O
the O
ferromagnetism B-PRO
of O
the O
doped B-DSC
system O
while O
Ti B-MAT
vacancies O
are O
beneficial O
to O
the O
stability B-PRO
of O
ferromagnetism B-PRO
. O


work B-SMT
hardening I-SMT
characteristics O
in O
Al B-MAT
base O
alloys B-DSC
with O
<nUm> O
and O
45wt. O
% O
Zn B-MAT


the O
stress B-PRO
– I-PRO
strain I-PRO
curves I-PRO
were O
obtained O
for O
Al B-MAT
– I-MAT
Zn I-MAT
alloys B-DSC
of O
12.6wt. O
% O
Zn B-MAT
( O
alloy B-DSC
I O
) O
and O
45wt. O
% O
Zn B-MAT
( O
alloy B-DSC
II O
) O
with O
elements O
of O
purity O
( O
<nUm> O
) O
. O


the O
monotonic O
shift O
of O
these O
curves O
towards O
lower O
flow B-PRO
stress I-PRO
and O
higher O
ductility B-PRO
was O
interrupted O
at O
the O
transformation B-PRO
temperatures I-PRO
<nUm> O
K O
( O
alloy B-DSC
I O
) O
and O
both O
<nUm> O
, O
<nUm> O
K O
( O
alloy B-DSC
II O
) O
. O


by O
increasing O
deformation B-PRO
temperature I-PRO
, O
young B-PRO
's I-PRO
modulus I-PRO
, O
Y B-PRO
, O
yield B-PRO
and O
fracture B-PRO
stresses I-PRO
, O
sy B-PRO
and O
sf B-PRO
, O
respectively O
, O
fracture B-PRO
time I-PRO
, O
tf B-PRO
, O
the O
coefficient B-PRO
of I-PRO
parabolic I-PRO
work I-PRO
hardening I-PRO
, O
χ B-PRO
, O
decreased O
while O
fracture B-PRO
strain I-PRO
, O
ef B-PRO
, O
and O
dislocation B-PRO
slip I-PRO
distance I-PRO
, O
L B-PRO
, O
increased O
. O


from O
the O
obtained O
x-rays B-CMT
diffraction I-CMT
patterns O
the O
lattice B-PRO
strain I-PRO
, O
ɛ B-PRO
, O
crystallite B-PRO
size I-PRO
, O
η B-PRO
, O
and O
dislocation B-PRO
density I-PRO
, O
ρ B-PRO
, O
were O
obtained O
at O
different O
deformation O
temperatures O
around O
transformation O
. O


fabrication O
of O
nanoporous B-DSC
copper B-MAT
surface B-DSC
by O
leaching B-SMT
of O
chill O
- O
zone O
Cu B-MAT
– I-MAT
Zr I-MAT
– I-MAT
Hf I-MAT
alloys B-DSC


In O
present O
work O
we O
report O
the O
synthesis O
of O
nanoporous B-DSC
surface I-DSC
using O
a O
copper B-MAT
- O
based O
alloy B-DSC
via O
leaching B-SMT
the O
less O
noble O
element O
- O
rich O
phase O
out O
of O
nanostructured B-DSC
ternary O
Cu B-MAT
– I-MAT
Hf I-MAT
– I-MAT
Zr I-MAT
alloys B-DSC
. O


the O
removal O
of O
Hf B-MAT
and O
Zr B-MAT
by O
mixed O
acid O
etchants O
in O
the O
chill O
- O
zone O
region O
of O
rapidly B-SMT
solidified I-SMT
ingots B-DSC
leads O
to O
the O
formation O
of O
a O
nano-roughened B-DSC
surface I-DSC
layer I-DSC
constituted O
of O
copper B-MAT
. O


the O
average O
pore B-PRO
and O
grain B-PRO
size I-PRO
of O
the O
obtained O
structure B-PRO
were O
shown O
to O
be O
less O
than O
<nUm> O
nm O
and O
<nUm> O
nm O
respectively O
. O


plasma B-SMT
- I-SMT
enhanced I-SMT
deposition I-SMT
of O
amorphous B-DSC
silicon B-MAT
at O
temperatures O
between O
<nUm> O
and O
<nUm> O
° O
C O


we O
have O
studied O
the O
influence O
of O
different O
deposition O
conditions O
on O
the O
mechanical B-PRO
and O
structural B-PRO
properties I-PRO
of O
amorphous B-DSC
silicon B-MAT
films B-DSC
prepared O
by O
plasma B-SMT
- I-SMT
enhanced I-SMT
deposition I-SMT
. O


the O
layers B-DSC
were O
deposited O
at O
temperatures O
between O
<nUm> O
and O
<nUm> O
° O
C O
, O
at O
total O
pressures O
between O
<nUm> O
and O
<nUm> O
Pa O
and O
r.f. O
frequencies O
between O
<nUm> O
and O
<nUm> O
MHz O
using O
SiH4Ar B-MAT
mixtures O
. O


the O
amounts O
of O
hydrogen O
and O
argon O
incorporated O
in O
the O
layers B-DSC
were O
measured O
by O
fourier B-CMT
transform I-CMT
IR I-CMT
( I-CMT
FTIR I-CMT
) I-CMT
spectroscopy I-CMT
and O
rutherford B-CMT
backscattering I-CMT
spectrometry I-CMT
respectively O
. O


furthermore O
, O
FTIR B-CMT
spectroscopy I-CMT
was O
used O
to O
measure O
the O
H2Si B-MAT
: O
HSi B-MAT
ratio O
in O
the O
films B-DSC
. O


the O
amount O
of O
argon O
and O
hydrogen O
, O
as O
well O
as O
the O
H2Si B-MAT
: O
HSi B-MAT
ratio O
, O
is O
highly O
dependent O
on O
the O
deposition O
conditions O
of O
the O
amorphous B-DSC
silicon B-MAT
layers B-DSC
. O


all O
three O
parameters O
decrease O
with O
increasing O
total O
gas O
pressures O
and O
r.f. O
frequencies O
. O


these O
reductions O
are O
attributed O
to O
a O
decrease O
in O
the O
number O
of O
energetic O
ions O
which O
reach O
the O
growing O
layer B-DSC
as O
a O
result O
of O
ion O
scattering O
in O
the O
dark O
space O
and O
the O
fact O
the O
ions O
can O
not O
respond O
to O
the O
r.f. O
field O
at O
frequencies O
above O
<nUm> O
– O
<nUm> O
MHz O
. O


the O
mechanical B-PRO
stress I-PRO
of O
the O
films B-DSC
depends O
on O
ion B-SMT
bombardment I-SMT
during O
deposition O
and O
stress O
relaxation O
during O
and O
/ O
or O
after O
deposition O
. O


layers B-DSC
deposited O
at O
temperatures O
above O
<nUm> O
° O
C O
do O
not O
show O
blistering O
after O
or O
during O
heat B-SMT
treatment I-SMT
at O
<nUm> O
° O
C O
. O


remarkable O
improvement O
of O
visible B-PRO
light I-PRO
photocatalytic I-PRO
activity I-PRO
of O
O2Ti B-MAT
nanotubes B-DSC
doped I-DSC
sequentially O
with O
noble O
metals O
for O
removing B-APL
of I-APL
organic I-APL
and I-APL
microbial I-APL
pollutants I-APL


the O
aim O
of O
this O
study O
was O
to O
show O
that O
Ag B-MAT
and O
Au B-MAT
nanoparticles B-DSC
( O
NPs B-DSC
) O
can O
have O
a O
synergistic O
effect O
on O
the O
photocatalytic B-PRO
and O
antibacterial B-PRO
activity I-PRO
of O
O2Ti B-MAT
nanotubes B-DSC
( O
NTs B-DSC
) O
under O
visible B-SMT
irradiation I-SMT
. O


O2Ti B-MAT
NTs B-DSC
were O
grown O
on O
Ti B-MAT
substrate B-DSC
by O
anodic B-SMT
oxidation I-SMT
and O
modified O
with O
Ag B-MAT
and O
Au B-MAT
NPs B-DSC
by O
dip B-SMT
coating I-SMT
and O
sputtering B-SMT
methods O
, O
respectively O
. O


the O
spherical O
<nUm> O
– O
<nUm> O
nm O
Ag B-MAT
and O
Au B-MAT
NPs B-DSC
were O
deposited O
on O
O2Ti B-MAT
NTs B-DSC
with O
diameter O
of O
<nUm> O
– O
<nUm> O
nm O
. O


In O
contrast O
to O
obtained O
results O
under O
UV B-SMT
irradiation I-SMT
, O
visible B-PRO
- I-PRO
light I-PRO
absorption I-PRO
range I-PRO
and O
visible B-PRO
photocatalytic I-PRO
activity I-PRO
of O
Ag B-MAT
and O
Au B-MAT
co-modified O
O2Ti B-MAT
NTs B-DSC
were O
much O
higher O
than O
O2Ti B-MAT
NTs B-DSC
without O
modification O
and O
O2Ti B-MAT
NTs B-DSC
modified O
with O
monometallic B-PRO
NPs B-DSC
. O


photocatalytic B-PRO
activity I-PRO
of O
modified O
O2Ti B-MAT
NTs B-DSC
increased O
with O
increasing O
annealing B-SMT
temperature O
and O
appearing O
rutile B-SPL
phase O
. O


antibacterial B-PRO
activity I-PRO
of O
Ag B-MAT
and O
Au B-MAT
- O
comodified O
O2Ti B-MAT
NTs B-DSC
against O
E. O
coli O
was O
noticeably O
more O
than O
that O
of O
O2Ti B-MAT
NTs B-DSC
modified O
with O
monometallic B-PRO
NPs B-DSC
. O


optoelectronic B-PRO
characteristics I-PRO
of O
single O
AlOZn B-MAT
nanotetrapod B-DSC


the O
AlOZn B-MAT
nanotetrapods B-DSC
were O
prepared O
by O
a O
simple O
thermal B-SMT
evaporation I-SMT
method I-SMT
. O


the O
typical O
characteristics O
of O
I B-PRO
– I-PRO
V I-PRO
curves I-PRO
for O
one O
of O
our O
devices O
illustrated O
that O
both O
the O
green O
light O
and O
the O
UV O
light O
could O
induce O
the O
increasing O
of O
conductance B-PRO
, O
but O
the O
conductance B-PRO
under O
the O
UV O
light O
is O
much O
larger O
than O
that O
under O
the O
illumination O
of O
green O
light O
. O


with O
the O
increasing O
of O
temperature O
, O
the O
conductance B-PRO
of O
the O
sample O
is O
also O
increased O
. O


furthermore O
, O
the O
change O
of O
current B-PRO
versus I-PRO
time I-PRO
as O
the O
UV O
light O
is O
switched O
on O
and O
off O
shows O
the O
sample O
has O
good O
switch B-PRO
characteristics I-PRO
. O


these O
findings O
illustrate O
the O
sample O
may O
be O
used O
in O
room B-APL
temperature I-APL
light I-APL
sensors I-APL
. O


A O
novel O
nanocomposite B-DSC
based O
on O
O2Ti B-MAT
/ O
Cu2O B-MAT
/ O
reduced B-MAT
graphene I-MAT
oxide I-MAT
with O
enhanced O
solar B-PRO
- I-PRO
light I-PRO
- I-PRO
driven I-PRO
photocatalytic I-PRO
activity I-PRO


A O
novel O
nanocomposite B-DSC
composed O
of O
O2Ti B-MAT
and O
Cu2O B-MAT
nanoparticles B-DSC
combined O
with O
reduced B-MAT
graphene I-MAT
oxide I-MAT
( O
RGO B-MAT
) O
was O
synthesized O
and O
characterized O
. O


x-ray B-CMT
diffraction I-CMT
( O
XRD B-CMT
) O
, O
scanning B-CMT
electron I-CMT
microscopy I-CMT
( O
SEM B-CMT
) O
, O
high B-CMT
- I-CMT
resolution I-CMT
transmission I-CMT
electron I-CMT
microscopy I-CMT
( O
HRTEM B-CMT
) O
, O
UV B-CMT
– I-CMT
vis I-CMT
diffuse I-CMT
reflectance I-CMT
spectroscopy I-CMT
( O
UV B-CMT
– I-CMT
vis I-CMT
DRS I-CMT
) O
, O
x-ray B-CMT
photoelectron I-CMT
spectroscopy I-CMT
( O
XPS B-CMT
) O
, O
thermogravimetry B-CMT
( O
TG B-CMT
) O
and O
elemental B-CMT
analysis I-CMT
were O
employed O
to O
investigate O
the O
structure B-PRO
, O
morphology B-PRO
, O
optical B-PRO
properties I-PRO
and O
composition B-PRO
of O
the O
nanocomposite B-DSC
and O
the O
intermediate O
materials O
. O


the O
photocatalytic B-PRO
activity I-PRO
of O
O2Ti B-MAT
/ O
Cu2O B-MAT
/ O
RGO B-MAT
and O
the O
individual O
materials O
were O
studied O
through O
the O
photodegradation O
of O
methylene O
blue O
under O
solar O
radiation O
. O


A O
considerable O
increase O
in O
the O
photodegradation B-PRO
activity I-PRO
using O
the O
nanocomposite B-DSC
was O
obtained O
after O
5h O
( O
∼ O
<nUm> O
% O
of O
MB O
degradation O
) O
. O


photoelectrochemical B-CMT
studies I-CMT
were O
carried O
out O
and O
confirmed O
the O
superiority O
of O
the O
novel O
nanocomposite B-DSC
in O
the O
photocurrent B-PRO
generation I-PRO
. O


the O
highest O
activity B-PRO
resulted O
from O
the O
synergy O
of O
this O
carbonaceous B-PRO
structure I-PRO
with O
O2Ti B-MAT
and O
Cu2O B-MAT
, O
which O
could O
absorb O
a O
wider O
portion O
of O
the O
solar O
spectrum O
, O
adsorb O
higher O
quantities O
of O
methylene O
blue O
on O
the O
surface B-DSC
and O
improve O
the O
effective O
separation O
of O
the O
generated O
electron B-PRO
– I-PRO
hole I-PRO
pairs I-PRO
. O


transparent B-PRO
conductive I-PRO
CrCuO2 B-MAT
thin B-DSC
films I-DSC
deposited O
by O
pulsed B-SMT
injection I-SMT
metal I-SMT
organic I-SMT
chemical I-SMT
vapor I-SMT
deposition I-SMT
: O
up O
- O
scalable O
process O
technology O
for O
an O
improved O
transparency B-PRO
/ O
conductivity B-PRO
trade O
- O
off O


metal B-SMT
organic I-SMT
chemical I-SMT
vapor I-SMT
deposition I-SMT
is O
carefully O
optimized O
for O
the O
growth O
of O
pure B-DSC
CrCuO2 B-MAT
delafossite B-SPL
coatings B-APL
on O
glass B-MAT
substrates B-DSC
. O


the O
pulsed O
direct O
liquid O
delivery O
is O
demonstrated O
to O
be O
an O
efficient O
process O
technology O
for O
the O
controlled O
supply O
of O
the O
precursor O
solution O
in O
the O
evaporation O
chamber O
, O
which O
is O
shown O
to O
be O
one O
of O
the O
main O
process O
parameters O
to O
tailor O
the O
thin B-DSC
- I-DSC
film I-DSC
properties O
. O


we O
investigated O
the O
influence O
of O
the O
precursor O
concentration O
ratio O
cu(thd)2 O
( O
bis[2,2,6,6-tetramethyl-3,5-heptanedionato]copper(II) O
) O
and O
cr(thd)3 O
( O
tris[2,2,6,6-tetramethyl-3,5-heptanedionato]chromium(III) O
) O
on O
the O
crystal B-PRO
structure I-PRO
, O
morphology B-PRO
and O
electrical B-PRO
conductivity I-PRO
, O
at O
a O
reduced O
temperature O
of O
<nUm> O
° O
C O
. O


we O
observe O
for O
a O
low O
ratio O
, O
a O
pure O
delafossite B-SPL
phase O
with O
a O
constant O
Cu B-MAT
- O
poor O
/ O
Cr B-MAT
- O
rich O
chemical B-PRO
composition I-PRO
, O
while O
at O
a O
high O
ratio O
a O
mixture O
of O
copper B-MAT
oxides I-MAT
and O
CrCuO2 B-MAT
was O
found O
. O


the O
as-grown B-DSC
<nUm> O
nm O
- O
thick O
pure O
delafossite B-SPL
films B-DSC
exhibit O
an O
exceptional O
high O
electrical B-PRO
conductivity I-PRO
for O
a O
non-intentionally B-DSC
doped I-DSC
CrCuO2 B-MAT
, O
<nUm> O
S O
cm-1 O
, O
and O
a O
near O
<nUm> O
% O
transparency B-PRO
in O
the O
visible O
spectral O
range O
. O


the O
role O
of O
iron B-MAT
in O
the O
formation O
of O
the O
magnetic B-PRO
structure I-PRO
and O
related O
properties O
of O
La0.8Sr0.2Co1- B-MAT
x I-MAT
Fe I-MAT
x I-MAT
O3 I-MAT
( I-MAT
x I-MAT
= I-MAT
<nUm> I-MAT
, I-MAT
<nUm> I-MAT
, I-MAT
<nUm> I-MAT
) I-MAT


La0.8Sr0.2Co1-xFexO3 B-MAT
( I-MAT
x I-MAT
= I-MAT
<nUm> I-MAT
, I-MAT
<nUm> I-MAT
, I-MAT
<nUm> I-MAT
) I-MAT
samples O
were O
studied O
by O
means O
of O
AC B-CMT
magnetic I-CMT
susceptibility I-CMT
, O
magnetization B-PRO
, O
magnetoresistance B-PRO
and O
57Fe B-CMT
mossbauer I-CMT
spectrometry I-CMT
. O


iron B-MAT
was O
found O
to O
take O
on O
a O
high B-PRO
spin I-PRO
3d5-a I-PRO
electronic I-PRO
state I-PRO
in O
each O
of O
the O
samples O
, O
where O
α O
refers O
to O
a O
partly O
delocalized O
3d O
electron O
. O


the O
compounds O
were O
found O
to O
exhibit O
a O
spin B-PRO
- I-PRO
cluster I-PRO
glass I-PRO
transition I-PRO
with O
a O
common O
transition B-PRO
temperature I-PRO
of O
∼ O
<nUm> O
K O
. O


the O
spin B-PRO
- I-PRO
cluster I-PRO
glass I-PRO
transition I-PRO
is O
visualized O
in O
the O
57Fe B-CMT
mossbauer I-CMT
spectra I-CMT
as O
the O
slowing O
down O
of O
magnetic B-PRO
relaxation I-PRO
below O
∼ O
70K O
, O
thereby O
showing O
that O
iron B-MAT
takes O
part O
in O
the O
formation O
of O
the O
glassy B-PRO
magnetic I-PRO
phase I-PRO
. O


the O
paramagnetic B-PRO
- O
like O
phase O
found O
at O
higher O
temperatures O
is O
identified O
below O
Tc B-PRO
≈ O
<nUm> O
K O
as O
being O
composed O
of O
weakly O
interacting O
, O
magnetically B-PRO
ordered I-PRO
nanosized B-DSC
clusters I-DSC
of O
magnetic B-PRO
ions O
in O
part O
with O
a O
magnetic B-PRO
moment I-PRO
oriented O
opposite O
to O
the O
net O
magnetic B-PRO
moment I-PRO
of O
the O
cluster B-DSC
. O


for O
each O
of O
the O
samples O
a O
considerable O
low O
- O
temperature O
negative B-PRO
magnetoresistance I-PRO
was O
found O
, O
whose O
magnitude O
in O
the O
studied O
range O
decreases O
with O
increasing O
iron B-MAT
concentration O
. O


the O
observed O
results O
obtained O
on O
the O
present O
compounds O
are O
qualitatively O
explained O
assuming O
that O
the O
absolute O
strengths O
of O
magnetic B-PRO
exchange I-PRO
interactions I-PRO
are O
subject O
to O
the O
relation O
|JCo B-PRO
– O
co| B-PRO
< O
|JFe B-PRO
– O
co| B-PRO
< O
|JFe B-PRO
– O
fe| B-PRO
. O


Cu2O B-MAT
/ O
O2Ti B-MAT
nanoporous B-DSC
thin I-DSC
- I-DSC
film I-DSC
heterojunctions B-APL
: O
fabrication O
and O
electrical B-CMT
characterization I-CMT


In O
this O
paper O
, O
cuprous B-MAT
oxide I-MAT
( O
Cu2O B-MAT
) O
/ O
titanium B-MAT
dioxide I-MAT
( O
O2Ti B-MAT
) O
diodes B-APL
have O
been O
fabricated O
by O
a O
facile O
and O
inexpensive O
method O
for O
possible O
use O
in O
solar B-APL
cells I-APL
. O


O2Ti B-MAT
nanoporous B-DSC
films I-DSC
were O
prepared O
through O
anodization B-SMT
of O
Ti B-MAT
foil B-DSC
and O
Cu2O B-MAT
films B-DSC
were O
deposited O
on O
it O
to O
make O
the O
diode B-APL
through O
electrodeposition B-SMT
. O


the O
structural B-PRO
and O
morphological B-CMT
characterization I-CMT
was O
studied O
by O
x-ray B-CMT
diffraction I-CMT
( O
XRD B-CMT
) O
and O
scanning B-CMT
electron I-CMT
microscope I-CMT
( O
SEM B-CMT
) O
. O


In O
electrical B-CMT
characterization I-CMT
the O
current B-PRO
– I-PRO
voltage I-PRO
( O
I B-PRO
– I-PRO
V I-PRO
) O
and O
capacitance B-PRO
– I-PRO
voltage I-PRO
( I-PRO
C I-PRO
– I-PRO
V I-PRO
) I-PRO
characteristics I-PRO
of O
the O
diodes B-APL
were O
measured O
at O
room O
temperature O
. O


the O
linear O
behavior O
of O
C B-CMT
– I-CMT
V I-CMT
curve I-CMT
indicated O
that O
the O
carrier B-PRO
concentration I-PRO
was O
homogeneous O
in O
the O
film B-DSC
region O
adjacent O
to O
the O
equilibrium O
space O
- O
charge O
region O
. O


the O
thickness O
of O
the O
depletion O
region O
o B-PRO
= O
<nUm> O
nm O
, O
carrier B-PRO
concentration I-PRO
N B-PRO
= O
8 O
× O
<nUm> O
m-3 O
and O
built B-PRO
in I-PRO
potential I-PRO
= O
0.80 O
V O
was O
estimated O
from O
C B-CMT
– I-CMT
V I-CMT
graph I-CMT
. O


the O
transport B-PRO
mechanism I-PRO
was O
due O
to O
the O
poole B-PRO
– I-PRO
frankel I-PRO
field I-PRO
effect I-PRO
because O
the O
experimentally O
obtained O
value O
of O
β B-PRO
was O
close O
to O
the O
theoretical O
value O
calculated O
for O
the O
poole O
– O
frenkel O
in O
logI O
against O
V1 O
/ O
<nUm> O
graph O
. O


the O
values O
of O
several O
electrical B-PRO
parameters I-PRO
such O
as O
ideality B-PRO
factor I-PRO
, O
barrier B-PRO
height I-PRO
, O
and O
series B-PRO
resistances I-PRO
were O
calculated O
from O
I B-PRO
– I-PRO
V I-PRO
, O
cheung B-CMT
's I-CMT
and I-CMT
norde I-CMT
's I-CMT
functions I-CMT
. O


microstructural B-PRO
evolution I-PRO
and O
tensile B-PRO
properties I-PRO
of O
Sn B-MAT
– I-MAT
5Sb I-MAT
solder B-APL
alloy B-DSC
containing O
small O
amount O
of O
Ag B-MAT
and O
Cu B-MAT


the O
near O
peritectic O
Sn B-MAT
– I-MAT
5Sb I-MAT
Pb I-MAT
- O
free O
solder B-APL
alloy B-DSC
has O
received O
considerable O
attention O
for O
high B-APL
temperature I-APL
electronic I-APL
applications I-APL
, O
especially O
on O
step B-APL
soldering I-APL
technology I-APL
, O
flip B-APL
- I-APL
chip I-APL
connection I-APL
. O


In O
the O
present O
study O
, O
a O
separate O
addition O
of O
the O
same O
amount O
of O
Ag B-MAT
and O
Cu B-MAT
are O
added O
with O
the O
near O
- O
peritectic O
Sn B-MAT
– I-MAT
5Sb I-MAT
solder B-APL
alloy B-DSC
to O
investigate O
the O
effect O
of O
a O
third O
element O
addition O
on O
the O
microstructural B-PRO
, O
thermal B-PRO
and O
mechanical B-PRO
properties I-PRO
of O
the O
newly O
developed O
ternary O
solder B-APL
alloys B-DSC
. O


the O
results O
indicate O
that O
the O
melting B-PRO
point I-PRO
of O
Sn B-MAT
– I-MAT
5Sb I-MAT
solder B-APL
is O
enhanced O
by O
Ag B-MAT
and O
Cu B-MAT
additions O
. O


besides O
, O
the O
Ag B-MAT
and O
Cu B-MAT
content O
refine O
the O
microstructure B-PRO
and O
form O
new O
intermetallic B-PRO
compounds O
( O
IMCs B-PRO
) O
with O
the O
near O
- O
peritectic O
Sn B-MAT
– I-MAT
5Sb I-MAT
solder B-APL
alloy B-DSC
. O


the O
tensile B-CMT
tests I-CMT
revealed O
that O
all O
alloys B-DSC
exhibit O
higher O
mechanical B-PRO
strength I-PRO
with O
increasing O
strain O
rate O
and O
/ O
or O
decreasing O
testing O
temperature O
, O
suggesting O
that O
the O
tensile B-PRO
behavior I-PRO
of O
the O
three O
alloys B-DSC
is O
strain O
rate O
and O
temperature O
dependence O
. O


the O
yield B-PRO
and O
ultimate O
tensile B-PRO
strength I-PRO
are O
higher O
for O
Sn B-MAT
– I-MAT
5Sb I-MAT
– I-MAT
0.7Cu I-MAT
alloy B-DSC
compared O
with O
Sn B-MAT
– I-MAT
5Sb I-MAT
and O
Sn B-MAT
– I-MAT
5Sb I-MAT
– I-MAT
0.7Ag I-MAT
alloys B-DSC
. O


good O
mechanical B-PRO
performance I-PRO
of O
Sn B-MAT
– I-MAT
5Sb I-MAT
– I-MAT
0.7Cu I-MAT
solder B-APL
is O
often O
correlated O
to O
a O
fine O
b-Sn B-MAT
grain B-PRO
size I-PRO
and O
more O
dispersed O
Cu-Sn B-MAT
IMC B-PRO
particles B-DSC
, O
which O
makes O
the O
solder B-APL
exhibit O
high O
strength B-PRO
and O
yield B-PRO
stress I-PRO
. O


microwave B-SMT
- I-SMT
assisted I-SMT
synthesis I-SMT
of O
the O
sandwich B-DSC
- I-DSC
like I-DSC
porous I-DSC
Al2O3 B-MAT
/ O
RGO B-MAT
nanosheets B-DSC
anchoring O
NiO B-MAT
nanocomposite B-DSC
as O
anode B-APL
materials O
for O
lithium B-APL
- I-APL
ion I-APL
batteries I-APL


hybridizing O
nanostructured B-DSC
metal B-MAT
oxides I-MAT
with O
reduced O
graphene B-MAT
oxide I-MAT
( O
RGO B-MAT
) O
is O
highly O
appropriate O
for O
the O
improvement O
of O
electrochemical B-PRO
performance I-PRO
of O
lithium B-APL
- I-APL
ion I-APL
batteries I-APL
( O
LIBs B-APL
) O
. O


herein O
, O
a O
AlNi B-MAT
- O
layered B-DSC
double B-MAT
hydroxide I-MAT
( O
LDH B-MAT
) O
is O
vertically O
grown O
on O
a O
RGO B-MAT
by O
the O
microwave B-SMT
- I-SMT
assisted I-SMT
method I-SMT
without O
any O
surfactant O
or O
template O
. O


the O
AlNi B-MAT
- O
LDH B-MAT
/ O
RGO B-MAT
is O
used O
as O
precursor O
to O
synthesize O
sandwich B-DSC
- I-DSC
like I-DSC
porous I-DSC
Al2O3 B-MAT
/ O
RGO B-MAT
anchoring O
NiO B-MAT
nanocomposite B-DSC
( O
NiO-Al2O3 B-MAT
/ O
RGO B-MAT
) O
by O
subsequent O
calcination B-SMT
and O
etching B-SMT
process O
. O


furthermore O
, O
doping O
Al2O3 B-MAT
can O
prevent O
active O
materials O
from O
agglomeration O
and O
generate O
porous B-DSC
structure O
in O
etching B-SMT
process O
. O


when O
used O
as O
anode B-APL
materials O
for O
LIBs B-APL
, O
the O
nanocomposite B-DSC
exhibits O
a O
high O
reversible B-PRO
capacity I-PRO
after O
<nUm> O
charge O
- O
discharge O
cycles O
at O
a O
current O
density O
of O
100mAg-1 O
. O


even O
at O
500mAg-1 O
, O
a O
stable O
capacity B-PRO
as O
high O
as O
<nUm> O
mAhg-1 O
could O
be O
obtained O
. O


the O
enhanced O
lithium B-PRO
storage I-PRO
performance I-PRO
is O
mainly O
ascribed O
to O
the O
presence O
of O
the O
conductive B-PRO
RGO B-MAT
and O
Al2O3 B-MAT
buffer B-DSC
phase O
, O
which O
can O
relieve O
structural B-PRO
collapse I-PRO
and O
offer O
high O
conductivity B-PRO
. O


A O
sensor B-APL
based O
on O
the O
planar B-APL
- I-APL
polarization I-APL
interferometer I-APL


we O
have O
successfully O
used O
a O
single B-APL
- I-APL
beam I-APL
planar I-APL
interferometer I-APL
based O
on O
the O
silicon B-MAT
- O
silicon B-MAT
dioxide I-MAT
- I-MAT
silicon I-MAT
nitride-phosphosilicate I-MAT
glass B-DSC
multilayer I-DSC
structure O
, O
s-and O
p-polarizations O
of O
the O
same O
light O
beam O
are O
used O
as O
its O
individual O
arms O
. O


the O
high O
sensitivity B-PRO
of O
the O
device O
when O
serving O
as O
a O
refractometer B-APL
and O
an O
immunosensor B-APL
is O
demonstrated O
. O


the O
experimental O
results O
are O
shown O
to O
be O
in O
a O
good O
agreement O
with O
those O
calculated O
within O
the O
framework O
of O
a O
transverse B-CMT
synchronism I-CMT
. O


do O
defects O
get O
ordered O
in O
Cu2S4SnZn B-MAT
? O


formation O
of O
ordered O
defect B-PRO
compounds O
and O
anomalous O
grain B-PRO
boundary I-PRO
physics I-PRO
are O
unique O
to O
Cu B-MAT
chalcogenides I-MAT
CuInX2 I-MAT
( I-MAT
S I-MAT
/ I-MAT
Se I-MAT
) I-MAT
and O
its O
alloys B-DSC
. O


x-ray B-CMT
photoelectron I-CMT
spectroscopy I-CMT
( O
XPS B-CMT
) O
studies O
were O
carried O
on O
Cu2-xZn1.3SnS4 B-MAT
( I-MAT
x I-MAT
= I-MAT
<nUm> I-MAT
, I-MAT
<nUm> I-MAT
, I-MAT
<nUm> I-MAT
and I-MAT
<nUm> I-MAT
) I-MAT
to O
determine O
the O
position O
of O
valence B-PRO
band I-PRO
edge I-PRO
and O
explore O
the O
formation O
of O
ordered O
vacancy B-PRO
compounds O
along O
with O
absorption B-CMT
studies I-CMT
. O


conductive B-CMT
atomic I-CMT
force I-CMT
microscopy I-CMT
( O
C-AFM B-CMT
) O
studies O
were O
carried O
out O
Cu2S4SnZn B-MAT
( O
CZTS B-MAT
) O
film B-DSC
deposited O
on O
Si B-MAT
and O
sodalime B-MAT
glass I-MAT
substrates B-DSC
to O
understand O
grain B-PRO
boundary I-PRO
physics I-PRO
. O


growth O
of O
high O
temperature O
superconducting B-PRO
single B-DSC
crystals I-DSC


YBa2-xSrxCu3O7-y B-MAT
and O
Ba2Cu3O7Y B-MAT
high-Tc B-PRO
superconducting I-PRO
single B-DSC
crystal I-DSC
up O
to O
<nUm> O
× O
<nUm> O
× O
<nUm> O
mm O
having O
orthorhombic B-SPL
lattices O
and O
transition B-PRO
temperatures I-PRO
of O
<nUm> O
and O
<nUm> O
K O
, O
respectively O
, O
have O
been O
grown O
. O


conductivity B-PRO
anisotropy I-PRO
has O
been O
confirmed O
. O


the O
grown O
single B-DSC
crystals I-DSC
exhibit O
superconducting B-PRO
properties I-PRO
even O
without O
additional O
thermal B-SMT
treatment I-SMT
. O


the O
Si(001) B-MAT
c(4 B-PRO
× I-PRO
<nUm> I-PRO
) I-PRO
surface I-PRO
reconstruction I-PRO
: O
a O
comprehensive O
experimental O
study O


we O
have O
carried O
out O
a O
comprehensive O
experimental O
study O
of O
the O
Si(001) B-MAT
c(4 B-PRO
× I-PRO
<nUm> I-PRO
) I-PRO
surface I-PRO
reconstruction I-PRO
by O
scanning B-CMT
tunneling I-CMT
microscopy I-CMT
( O
STM B-CMT
) O
( O
at O
room O
temperature O
and O
elevated O
temperatures O
) O
, O
auger B-CMT
electron I-CMT
spectroscopy I-CMT
( O
AES B-CMT
) O
, O
reflection B-CMT
high I-CMT
- I-CMT
energy I-CMT
electron I-CMT
diffraction I-CMT
( O
RHEED B-CMT
) O
and O
low B-CMT
- I-CMT
energy I-CMT
electron I-CMT
diffraction I-CMT
( O
LEED B-CMT
) O
. O


Si(001) B-MAT
samples O
were O
kept O
under O
ultra-high O
vacuum O
( O
UHV O
) O
at O
around O
<nUm> O
° O
C O
until O
the O
c(4 B-PRO
× I-PRO
<nUm> I-PRO
) I-PRO
reconstruction I-PRO
appeared O
. O


STM B-CMT
contrast O
of O
the O
c(4 B-PRO
× I-PRO
<nUm> I-PRO
) I-PRO
reconstruction I-PRO
is O
strongly O
influenced O
by O
electronic B-PRO
effects I-PRO
and O
changes O
considerably O
over O
a O
range O
of O
bias O
voltages O
. O


the O
c(4 B-PRO
× I-PRO
<nUm> I-PRO
) I-PRO
surface I-PRO
reconstruction I-PRO
is O
a O
result O
of O
stress O
which O
is O
caused O
by O
incorporation O
of O
impurities O
or O
adsorbates O
in O
sub-surface O
locations O
. O


the O
resulting O
c(4 B-PRO
× I-PRO
<nUm> I-PRO
) I-PRO
reconstruction I-PRO
in O
the O
top B-DSC
layer I-DSC
is O
a O
pure B-DSC
silicon B-MAT
structure O
. O


the O
main O
structural O
element O
is O
a O
one B-PRO
- I-PRO
dimer I-PRO
vacancy I-PRO
( O
1-DV B-PRO
) O
. O


At O
this O
vacancy B-PRO
, O
second O
layer O
Si B-MAT
- O
atoms O
rebond O
and O
cause O
the O
adjacent O
top O
Si B-MAT
- O
dimers O
to O
brighten O
up O
in O
the O
STM B-CMT
image O
at O
low O
bias O
voltages O
. O


At O
higher O
bias O
voltage O
the O
contrast O
is O
similar O
to O
Si B-MAT
- O
dimers O
on O
the O
( B-PRO
<nUm> I-PRO
× I-PRO
<nUm> I-PRO
) I-PRO
reconstructed I-PRO
Si(001) B-MAT
. O


therefore O
, O
besides O
the O
1-DV B-PRO
and O
the O
two O
adjacent O
Si B-MAT
- O
dimers O
, O
another O
Si B-MAT
- O
dimer O
under O
tensile B-PRO
stress I-PRO
may O
complete O
the O
<nUm> B-PRO
× I-PRO
unit I-PRO
cell I-PRO
. O


this O
is O
a O
refinement O
of O
the O
missing B-CMT
dimer I-CMT
model I-CMT
. O


additional O
polymorphism B-PRO
and O
non-stoichiometry B-PRO
in O
AgF B-MAT


A O
phase O
forming O
from O
B2 O
type O
AgF B-MAT
on O
decrease O
of O
pressure O
found O
recently O
by O
vaidya O
and O
kennedy O
has O
been O
studied O
by O
in O
situ O
x-ray B-CMT
diffraction I-CMT
. O


it O
is O
indexed O
as O
hexagonal B-SPL
with O
c B-PRO
= O
<nUm> O
± O
<nUm> O
Å O
and O
a B-PRO
= O
<nUm> O
± O
<nUm> O
Å O
, O
z B-PRO
= O
<nUm> O
. O


this O
structure B-PRO
is O
probably O
inverse O
AsNi B-MAT
. O


its O
pressure O
of O
formation O
is O
highly O
dependent O
on O
the O
samples O
history O
of O
pressure O
variation O
. O


all O
three O
phases O
, O
B1 O
, O
B2 O
and O
hexagonal B-SPL
have O
been O
made O
to O
give O
x-ray B-CMT
patterns I-CMT
with O
each O
line O
split O
into O
two O
lines O
of O
equal O
intensity O
. O


we O
interpret O
this O
as O
a O
decomposition O
into O
two O
non-stoichiometric B-DSC
phases O
, O
one O
Ag B-PRO
rich I-PRO
and O
the O
other O
F B-PRO
rich I-PRO
. O


the O
conditions O
for O
the O
formation O
of O
these O
split O
phases O
are O
not O
always O
reproducible O
which O
suggests O
that O
this O
is O
a O
metastable B-PRO
phenomenon O
possibly O
due O
to O
pressure B-PRO
gradients I-PRO
on O
the O
sample O
. O


the O
splitting O
could O
, O
however O
, O
also O
be O
explained O
by O
equilibrium B-PRO
behavior I-PRO
. O


investigation O
of O
the O
vibrational B-PRO
properties I-PRO
of O
cubic B-SPL
yttria B-MAT
- O
stabilized B-DSC
zirconia B-MAT
: O
A O
combined O
experimental O
and O
theoretical O
study O


A O
combined O
experimental O
and O
theoretical O
investigation O
into O
the O
vibrational B-PRO
properties I-PRO
of O
cubic B-SPL
<nUm> O
– O
<nUm> O
mol O
% O
yttria B-MAT
- O
stabilized B-DSC
zirconia B-MAT
( O
YSZ B-MAT
) O
is O
presented O
. O


measurements O
of O
acoustic B-PRO
phonon I-PRO
dispersion I-PRO
curves I-PRO
have O
been O
obtained O
from O
inelastic B-CMT
neutron I-CMT
scattering I-CMT
investigations O
using O
a O
triple B-CMT
axis I-CMT
spectrometer I-CMT
, O
as O
well O
as O
calculations O
of O
the O
vibrational B-PRO
density I-PRO
- I-PRO
of I-PRO
- I-PRO
states I-PRO
( O
vDOS B-PRO
) O
using O
density B-CMT
- I-CMT
functional I-CMT
theory I-CMT
. O


the O
present O
measurements O
agree O
closely O
with O
, O
and O
extend O
, O
previously O
published O
results O
. O


the O
phonons O
become O
broader O
and O
decrease O
in O
intensity O
as O
the O
brillouin B-PRO
zone I-PRO
boundary I-PRO
is O
approached O
, O
particularly O
in O
the O
γ O
– O
δ O
– O
x O
direction O
. O


interestingly O
, O
there O
is O
evidence O
of O
a O
previously O
unreported O
low O
energy O
phonon B-PRO
band I-PRO
( O
<nUm> O
– O
<nUm> O
meV O
) O
in O
the O
γ O
– O
σ O
– O
x O
direction O
, O
which O
could O
possibly O
be O
related O
to O
the O
stabilization O
( O
by O
yttria B-MAT
doping B-SMT
) O
of O
the O
imaginary O
mode O
of O
cubic B-SPL
O2Zr B-MAT
about O
the O
x-point O
. O


compared O
to O
pure O
cubic B-SPL
O2Zr B-MAT
, O
the O
vDOS B-PRO
of O
YSZ B-MAT
are O
broader O
and O
extend O
to O
higher O
frequency O
. O


furthermore O
, O
the O
prominent O
Zr B-MAT
- O
related O
feature O
in O
the O
vDOS B-PRO
of O
c-ZrO2 B-MAT
at O
≈ O
14meV O
is O
shifted O
to O
higher O
energy O
in O
the O
vDOS B-MAT
of O
YSZ B-MAT
. O


this O
behavior O
is O
consistent O
with O
the O
measured O
dispersion B-PRO
bands I-PRO
( O
first B-PRO
acoustic I-PRO
branch I-PRO
in O
the O
γ O
– O
x O
direction O
, O
about O
the O
x-point O
) O
of O
YSZ B-MAT
which O
is O
higher O
in O
energy O
by O
a O
similar O
amount O
relative O
to O
that O
of O
c-ZrO2 B-MAT
, O
thus O
providing O
support O
for O
the O
structural B-CMT
model I-CMT
considered O
. O


structural B-PRO
and O
optical B-PRO
properties I-PRO
of O
solvothermally B-SMT
synthesized I-SMT
SZn B-MAT
nano-materials B-DSC
using O
Na2S*9H2O B-MAT
and O
ZnSO4*7H2O B-MAT
precursors O


hexagonal B-SPL
wurtzite I-SPL
( O
HWZ B-SPL
) O
SZn B-MAT
nanorods B-DSC
were O
formed O
in O
specimens O
with O
a O
S B-PRO
/ I-PRO
Zn I-PRO
ratio I-PRO
of O
<nUm> O
, O
synthesized O
at O
temperatures O
≥ O
<nUm> O
° O
C O
in O
a O
solution O
containing O
80vol O
% O
water O
and O
20vol O
% O
of O
ethylenediamine O
( O
EN O
) O
. O


In O
contrast O
, O
HWZ B-SPL
SZn B-MAT
nanoparticles B-DSC
were O
formed O
in O
specimens O
synthesized O
at O
temperatures O
lower O
than O
<nUm> O
° O
C O
. O


also O
, O
cubic B-SPL
zinc I-SPL
blende I-SPL
( O
CZB B-SPL
) O
SZn B-MAT
nanoparticles B-DSC
were O
formed O
in O
specimen O
synthesized O
in O
water O
. O


the O
absorption B-CMT
peak O
for O
the O
HWZ B-SPL
nanorods B-DSC
and O
CZB B-SPL
SZn B-MAT
nanoparticles B-DSC
was O
at O
wavelength O
of O
<nUm> O
nm O
and O
<nUm> O
nm O
, O
respectively O
, O
indicating O
that O
the O
band B-PRO
gap I-PRO
energy I-PRO
of O
the O
former O
is O
larger O
than O
that O
of O
the O
latter O
. O


moreover O
, O
the O
HWZ B-SPL
SZn B-MAT
exhibited O
two O
emission B-CMT
peaks O
at O
<nUm> O
nm O
and O
<nUm> O
nm O
. O


the O
peak O
at O
<nUm> O
nm O
is O
attributed O
to O
Zn B-MAT
vacancies O
but O
the O
origin O
of O
the O
peak O
at O
<nUm> O
nm O
remains O
undetermined O
. O


since O
the O
intensity O
of O
the O
emission O
peak O
at O
<nUm> O
nm O
was O
significantly O
higher O
for O
the O
HWZ B-SPL
nanoparticles B-DSC
than O
for O
nanorods B-DSC
, O
this O
peak O
might O
be O
associated O
with O
defects O
in O
the O
HWZ B-SPL
SZn B-MAT
nanoparticles B-DSC
. O


low O
temperature O
phase B-PRO
transition I-PRO
and O
crystal B-PRO
structure I-PRO
of O
CsMgO4P B-MAT


CsMgO4P B-MAT
doped B-DSC
with O
radioisotopes O
is O
a O
promising O
compound O
for O
usage O
as O
a O
radioactive B-APL
medical I-APL
source I-APL
. O


however O
, O
a O
low O
temperature O
phase O
transition O
at O
temperatures O
close O
to O
ambient O
conditions O
( O
~ O
− O
<nUm> O
° O
C O
) O
was O
observed O
. O


information O
about O
such O
kind O
of O
structural O
changes O
is O
important O
in O
order O
to O
understand O
whether O
it O
can O
cause O
any O
problem O
for O
medical B-APL
use I-APL
of O
this O
compound O
. O


the O
phase B-PRO
transition I-PRO
has O
been O
investigated O
in O
detail O
using O
synchrotron B-CMT
powder I-CMT
diffraction I-CMT
, O
raman B-CMT
spectroscopy I-CMT
and O
DFT B-CMT
calculations O
. O


the O
structure O
undergoes O
a O
transformation O
from O
an O
orthorhombic B-SPL
modification O
, O
space O
group O
pnma B-SPL
( O
RT O
phase O
) O
to O
a O
monoclinic B-SPL
polymorph O
, O
space O
group O
P21 B-SPL
/ I-SPL
n I-SPL
( O
LT O
phase O
) O
. O


new O
LT O
modification O
adopts O
similar O
to O
RT O
but O
slightly O
distorted O
unit O
cell O
: O
a B-PRO
= O
<nUm> O
Å O
, O
b B-PRO
= O
<nUm> O
Å O
, O
c B-PRO
= O
<nUm> O
Å O
, O
β B-PRO
= O
<nUm> O
° O
, O
V B-PRO
= O
<nUm> O
A3 O
. O


CsMgO4P B-MAT
belongs O
to O
the O
group O
of O
framework O
compounds O
and O
is O
made O
up O
of O
strictly O
alternating O
MgO4- B-MAT
and O
PO4-tetrahedra O
sharing O
vertices O
. O


the O
cesium B-MAT
counter O
cations O
are O
located O
in O
the O
resulting O
channel O
- O
like O
cavities O
. O


upon O
the O
transformation O
a O
combined O
tilting O
of O
the O
tetrahedra O
is O
observed O
. O


A O
comparison O
with O
other O
phase B-PRO
transitions I-PRO
in O
ABW O
- O
type O
framework O
compounds O
is O
given O
. O


silicon B-MAT
carbide I-MAT
formation O
with O
pulsed B-SMT
laser I-SMT
and O
electron B-SMT
beams I-SMT


poly-crystalline B-DSC
silicon B-MAT
carbide I-MAT
layers B-DSC
were O
obtained O
through O
nanosecond B-SMT
pulse I-SMT
heating I-SMT
of O
thin O
carbon B-MAT
films B-DSC
deposited O
on O
silicon B-MAT
wafers B-DSC
. O


the O
samples O
were O
submitted O
to O
electron B-SMT
beam I-SMT
pulses I-SMT
( O
<nUm> O
kev O
, O
<nUm> O
ns O
) O
at O
various O
current O
densities O
in O
vacuum O
( O
~ O
<nUm> O
− O
<nUm> O
mbar O
) O
and O
to O
ClXe B-SMT
excimer I-SMT
laser I-SMT
pulses I-SMT
( O
<nUm> O
nm O
, O
<nUm> O
ns O
) O
in O
air O
. O


rutherford B-CMT
backscattering I-CMT
spectrometry I-CMT
( O
RBS B-CMT
) O
evidenced O
that O
in O
the O
electron B-SMT
beam I-SMT
annealed I-SMT
samples O
mixing O
of O
elements O
at O
the O
C B-MAT
Si I-MAT
interface B-DSC
starts O
at O
current O
densities O
of O
about O
<nUm> O
A O
/ O
cm2 O
. O


the O
mixed O
layer B-DSC
thickness O
increases O
almost O
linearly O
with O
current O
density O
. O


from O
the O
RBS B-CMT
spectra O
a O
composition B-PRO
of O
the O
intermixed O
layers B-DSC
close O
to O
the O
CSi B-MAT
compound O
was O
deduced O
. O


transmission B-CMT
electron I-CMT
microscopy I-CMT
( O
TEM B-CMT
) O
and O
electron B-CMT
diffraction I-CMT
studies O
clearly O
evidenced O
the O
formation O
of O
CSi B-MAT
poly-crystals B-DSC
. O


using O
the O
ClXe O
laser O
, O
intermixing O
of O
the O
deposited O
C B-MAT
film B-DSC
with O
the O
Si B-MAT
substrate B-DSC
was O
observed O
after O
a O
single O
<nUm> O
J O
/ O
cm2 O
pulse O
. O


further O
analysis O
evidenced O
the O
formation O
of O
CSi B-MAT
crystals B-DSC
, O
embedded O
in O
a O
diamond B-MAT
film B-DSC
. O


properties O
of O
B2Mg B-MAT
bulks B-DSC
after O
combined O
doping B-SMT
with O
Fe B-MAT
and O
C B-MAT
by O
adding O
Iron(II) O
lactate O
( O
C6FeH10O6 O
) O


bulk B-DSC
B2Mg B-MAT
doped B-DSC
with O
C B-MAT
and O
Fe B-MAT
was O
prepared O
by O
using O
the O
solid B-SMT
state I-SMT
sintering I-SMT
method O
with O
C6FeH10O6 O
as O
dopant O
. O


the O
phase B-PRO
composition I-PRO
, O
microstructure B-PRO
, O
and O
superconducting B-PRO
properties I-PRO
were O
studied O
. O


x-ray B-CMT
diffraction I-CMT
( O
XRD B-CMT
) O
shows O
the O
presence O
of O
iron B-MAT
after O
the O
doping B-SMT
. O


the O
addition O
of O
C6FeH10O6 O
increases O
the O
a- B-PRO
and O
c-axis B-PRO
parameters I-PRO
of O
B2Mg B-MAT
, O
as O
evidenced O
by O
the O
shifting O
of O
the O
( O
<nUm> O
) O
and O
( O
<nUm> O
) O
peaks O
to O
a O
lower O
angle O
on O
the O
XRD B-CMT
patterns O
. O


Fe B-MAT
atoms O
were O
distributed O
uniformly O
, O
as O
shown O
by O
the O
field B-CMT
emission I-CMT
scanning I-CMT
electron I-CMT
microscope I-CMT
images O
, O
while O
the O
magnetization B-PRO
of O
the O
sample O
was O
dominated O
by O
the O
signals O
from O
the O
B2Mg B-MAT
superconductor B-PRO
, O
although O
the O
iron B-MAT
- O
containing O
materials O
also O
contributed O
a O
minor O
amount O
of O
magnetization B-PRO
. O


the O
residual B-PRO
resistivity I-PRO
ratio I-PRO
was O
decreased O
as O
the O
C6FeH10O6 O
doping O
level O
increased O
. O


the O
critical B-PRO
temperature I-PRO
also O
decreased O
with O
increased O
doping B-SMT
level O
, O
as O
did O
the O
critical B-PRO
current I-PRO
density I-PRO
, O
jc B-PRO
. O


the O
doping B-SMT
also O
caused O
decreases O
in O
the O
irreversibility B-PRO
field I-PRO
, O
hirr B-PRO
, O
and O
the O
upper B-PRO
critical I-PRO
field I-PRO
, O
hc2 B-PRO
. O


the O
decrease O
in O
hc2 B-PRO
and O
hirr B-PRO
, O
together O
with O
the O
harmful O
effects O
from O
impurity O
phases O
such O
as O
MgO B-MAT
is O
the O
reason O
for O
the O
decrease O
in O
jc B-PRO
. O


optical B-CMT
characterization I-CMT
of O
CdS B-MAT
x I-MAT
se1-x I-MAT
films B-DSC
grown O
on O
quartz B-MAT
substrate B-DSC
by O
pulsed B-SMT
laser I-SMT
ablation I-SMT
technique O


CdSxSe1-xalloys B-MAT
have O
been O
deposited O
on O
quartz B-MAT
substrates B-DSC
by O
means O
of O
pulsed B-SMT
laser I-SMT
ablation I-SMT
, O
a O
relatively O
new O
technique O
for O
growing O
semiconductor B-PRO
films B-DSC
. O


we O
obtained O
high O
quality O
polycrystalline B-DSC
films I-DSC
which O
present O
photoluminescence B-CMT
efficiency O
up O
to O
at O
room O
temperature O
. O


the O
dependence O
of O
the O
band B-PRO
gap I-PRO
on O
the O
x O
composition B-PRO
, O
measured O
by O
absorption B-CMT
spectra O
at O
<nUm> O
K O
, O
shows O
an O
upwards O
band B-PRO
gap I-PRO
bowing I-PRO
. O


the O
real O
part O
of O
the O
refractive B-PRO
index I-PRO
in O
the O
transparent B-PRO
region O
at O
room O
temperature O
is O
well O
described O
by O
the O
sellmeier B-CMT
relation I-CMT
. O


optical B-PRO
effects I-PRO
of O
NiOx B-MAT
interlayer B-DSC
for O
OLEDs B-APL
with O
AZO B-MAT
embedded O
anodes B-APL


insertion O
of O
a O
nickel B-MAT
oxide I-MAT
( O
NiOx B-MAT
) O
in O
an O
aluminum B-MAT
zinc I-MAT
oxide I-MAT
( O
AZO B-MAT
) O
embedded O
organic B-APL
light I-APL
- I-APL
emitting I-APL
diode I-APL
( O
OLED B-APL
) O
has O
successfully O
obtained O
additional O
<nUm> O
% O
light B-PRO
extraction I-PRO
and O
led O
to O
an O
enhanced O
current B-PRO
efficiency I-PRO
up O
to O
<nUm> O
% O
. O


the O
introduced O
NiOx B-MAT
has O
a O
high O
reflective B-PRO
index I-PRO
of O
∼ O
<nUm> O
which O
allows O
more O
emitted O
light O
to O
travel O
through O
AZO B-MAT
/ O
ITO B-MAT
interfaces B-DSC
. O


the O
AZO B-MAT
/ O
ITO B-MAT
interfaces B-DSC
provide O
deflection O
and O
scattering O
effect O
to O
redirect O
light O
away O
from O
being O
totally O
reflected O
in O
the O
reflective-index-mismatched B-PRO
OLED B-APL
structures O
and O
thus O
are O
able O
to O
enhance O
external O
light O
out O
- O
coupling O
. O


results O
also O
showed O
that O
the O
coating B-APL
of O
NiOx B-MAT
layer B-DSC
increased O
the O
electrical B-PRO
resistance I-PRO
of O
AZO B-MAT
embedded O
ITO B-MAT
film B-DSC
which O
limited O
the O
current B-PRO
efficiency I-PRO
, O
and O
the O
introduced O
NiOx B-MAT
showed O
no O
benefit O
on O
carrier O
injection O
as O
expected O
. O


comparative O
properties O
of O
ternary O
oxides B-MAT
of O
O2Zr B-MAT
– O
O2Ti B-MAT
– O
O3Y2 B-MAT
obtained O
by O
laser B-SMT
ablation I-SMT
, O
magnetron B-SMT
sputtering I-SMT
and O
sol B-SMT
– I-SMT
gel I-SMT
techniques O


thin B-DSC
films I-DSC
of O
ternary O
oxides B-MAT
of O
zirconium B-MAT
( O
Zr B-MAT
) O
, O
yttrium B-MAT
( O
Y B-MAT
) O
and O
titanium B-MAT
( O
Ti B-MAT
) O
were O
obtained O
by O
the O
sol B-SMT
– I-SMT
gel I-SMT
, O
magnetron B-SMT
sputtering I-SMT
and O
laser B-SMT
ablation I-SMT
techniques O
. O


zirconium O
propoxide O
, O
titanium O
isopropoxide O
and O
yttrium O
nitrate O
hexahydrate O
reagents O
were O
used O
as O
precursors O
in O
the O
sol B-SMT
– I-SMT
gel I-SMT
process O
. O


the O
Zr B-MAT
/ O
Ti B-MAT
and O
Zr B-MAT
/ O
Y B-MAT
molar O
ratios O
have O
been O
controlled O
by O
varying O
the O
precursors O
and O
surfactant O
concentration O
. O


the O
obtained O
gels O
were O
supported O
by O
dip B-SMT
coating I-SMT
on O
a-alumina B-MAT
supports O
, O
dried B-SMT
at O
<nUm> O
K O
and O
calcinated B-SMT
at O
<nUm> O
K O
. O


the O
powders B-DSC
obtained O
after O
the O
removal O
of O
carbon B-MAT
residuals O
were O
subsequently O
pressed B-SMT
and O
calcinated B-SMT
for O
using O
as O
targets O
for O
the O
magnetron B-SMT
sputtering I-SMT
and O
pulsed B-SMT
laser I-SMT
deposition I-SMT
techniques O
. O


the O
chemical B-PRO
composition I-PRO
was O
determined O
by O
auger B-CMT
electron I-CMT
spectroscopy I-CMT
. O


the O
surface B-PRO
topography I-PRO
was O
investigated O
by O
atomic B-CMT
force I-CMT
microscopy I-CMT
, O
while O
the O
crystallinity B-PRO
was O
evaluated O
from O
x-ray B-CMT
diffraction I-CMT
. O


the O
electrical B-PRO
response I-PRO
of O
the O
deposits O
to O
nitrogen O
oxides O
( O
NOx O
) O
toxic O
gas O
is O
discussed O
according O
to O
the O
experimental O
conditions O
. O


enhanced O
effective B-PRO
mass I-PRO
in O
doped B-DSC
O3SrTi B-MAT
and O
related O
perovskites B-SPL


the O
effective B-PRO
mass I-PRO
is O
one O
of O
the O
main O
factors O
determining O
the O
seebeck B-PRO
coefficient I-PRO
and O
electrical B-PRO
conductivity I-PRO
of O
thermo B-PRO
- I-PRO
electrics I-PRO
. O


In O
this O
ab B-CMT
- I-CMT
initio I-CMT
LDA I-CMT
- I-CMT
GGA I-CMT
study O
the O
effective B-PRO
mass I-PRO
is O
estimated O
from O
the O
curvature B-PRO
of I-PRO
electronic I-PRO
bands I-PRO
by O
one-band-approximation B-CMT
and O
is O
in O
excellent O
agreement O
with O
experimental O
data O
of O
nb- B-MAT
and O
La B-MAT
- O
doped B-DSC
O3SrTi B-MAT
. O


it O
is O
clarified O
that O
the O
deformation O
of O
O3SrTi B-MAT
crystals B-DSC
has O
a O
significant O
influence O
on O
the O
bandgap B-PRO
, O
effective B-PRO
electronic I-PRO
DOS I-PRO
- I-PRO
mass I-PRO
and O
band B-PRO
- I-PRO
mass I-PRO
, O
but O
the O
electronic O
effect O
due O
to O
the O
eg B-PRO
- I-PRO
band I-PRO
flattening I-PRO
near O
the O
g-point O
due O
to O
Nb B-MAT
- O
doping B-SMT
up O
to O
0.2at O
% O
is O
the O
main O
factor O
for O
the O
effective B-PRO
mass I-PRO
increase O
. O


doping B-SMT
of O
La B-MAT
shows O
a O
linear O
decrease O
of O
the O
effective B-PRO
mass I-PRO
; O
this O
can O
be O
explained O
by O
the O
different O
surroundings O
of O
A- O
and O
b-sites O
in O
perovskite B-SPL
. O


substitution O
with O
other O
elements O
such O
as O
Ba B-MAT
on O
the O
a-site O
and O
V B-MAT
on O
the O
b-site O
in O
O3SrTi B-MAT
increases O
the O
effective B-PRO
mass I-PRO
as O
well O
. O


A O
study O
of O
defects B-PRO
in O
deformed B-DSC
FeSi B-MAT
alloys B-DSC
using O
positron B-CMT
annihilation I-CMT
techniques O


steels B-MAT
with O
high O
amounts O
of O
silicon B-MAT
are O
used O
in O
electrical B-APL
applications I-APL
due O
to O
their O
low O
magnetostriction B-PRO
, O
high O
electrical B-PRO
resistivity I-PRO
and O
reduced O
energy B-PRO
losses I-PRO
, O
but O
they O
exhibit O
poor O
formability B-PRO
. O


the O
slow O
positron O
beam O
of O
gent O
is O
used O
to O
investigate O
defects B-PRO
in O
different O
deformed B-DSC
FeSi B-MAT
alloys B-DSC
. O


it O
was O
found O
that O
the O
concentration O
of O
defects B-PRO
for O
the O
alloys B-DSC
deformed O
at O
high O
temperatures O
are O
different O
from O
the O
ones O
related O
to O
the O
alloys B-DSC
deformed B-SMT
at O
room O
temperature O
. O


these O
results O
are O
correlated O
to O
the O
results O
of O
positron B-CMT
annihilation I-CMT
lifetime I-CMT
spectroscopy I-CMT
( O
PALS B-CMT
) O
. O


an O
x-ray B-CMT
crystallographic I-CMT
study O
of O
superconducting B-PRO
bismuth B-MAT
- I-MAT
lead I-MAT
cuprates I-MAT
without O
superlattice B-DSC
modulation O


A O
single B-DSC
crystal I-DSC
x-ray B-CMT
crystallographic I-CMT
study O
of O
superconducting B-PRO
bismuth B-MAT
cuprate I-MAT
of O
the O
composition B-PRO
Bi2CaCu4O16Pb2Sr4Y B-MAT
without O
any O
superlattice B-DSC
modulation O
has O
been O
carried O
out O
. O


the O
cuprate B-MAT
has O
an O
orthorhombic B-SPL
symmetry O
with O
the O
space O
group O
pnan B-SPL
. O


rietveld B-CMT
profile I-CMT
analysis I-CMT
was O
carried O
out O
with O
high O
- O
resolution O
powder B-DSC
data O
for O
this O
composition B-PRO
along O
with O
BiCu2O8PbSr2Y B-MAT
. O


the O
structural B-PRO
parameters I-PRO
so O
obtained O
are O
discussed O
. O


sputter B-SMT
deposition I-SMT
and O
surface B-SMT
treatment I-SMT
of O
O2Ti B-MAT
films B-DSC
for O
dye B-APL
- I-APL
sensitized I-APL
solar I-APL
cells I-APL
using O
reactive B-SMT
RF I-SMT
plasma I-SMT


sputter B-SMT
deposition I-SMT
followed O
by O
surface B-SMT
treatment I-SMT
was O
studied O
using O
reactive B-SMT
RF I-SMT
plasma I-SMT
as O
a O
method O
for O
preparing O
titanium B-MAT
oxide I-MAT
( O
O2Ti B-MAT
) O
films B-DSC
on O
indium B-MAT
tin I-MAT
oxide I-MAT
( O
ITO B-MAT
) O
coated B-SMT
glass B-MAT
substrate B-DSC
for O
dye B-APL
- I-APL
sensitized I-APL
solar I-APL
cells I-APL
( O
DSCs B-APL
) O
. O


anatase B-SPL
structure O
O2Ti B-MAT
films B-DSC
deposited O
by O
reactive B-SMT
RF I-SMT
magnetron I-SMT
sputtering I-SMT
under O
the O
conditions O
of O
Ar O
/ O
O2(5 O
% O
) O
mixtures O
, O
RF O
power O
of O
<nUm> O
W O
and O
substrate B-DSC
temperature O
of O
<nUm> O
° O
C O
were O
surface B-SMT
- I-SMT
treated I-SMT
by O
inductive B-SMT
coupled I-SMT
plasma I-SMT
( O
ICP B-SMT
) O
with O
Ar O
/ O
O O
mixtures O
at O
substrate B-DSC
temperature O
of O
<nUm> O
° O
C O
, O
and O
thus O
the O
films B-DSC
were O
applied O
to O
the O
DSCs B-APL
. O


the O
O2Ti B-MAT
films B-DSC
made O
on O
these O
experimental O
bases O
exhibited O
the O
BET B-CMT
specific B-PRO
surface I-PRO
area I-PRO
of O
<nUm> O
m2 O
/ O
g O
, O
the O
pore B-PRO
volume I-PRO
of O
<nUm> O
cm2 O
/ O
g O
and O
the O
TEM B-CMT
particle O
size O
of O
∼ O
<nUm> O
nm O
. O


the O
DSCs B-APL
made O
of O
this O
O2Ti B-MAT
material O
exhibited O
an O
energy B-PRO
conversion I-PRO
efficiency I-PRO
of O
about O
<nUm> O
% O
at O
<nUm> O
mW O
/ O
cm2 O
light O
intensity O
. O


