characterization of vacancy-like defects in h 2 cycled mg and of ordered- nanochannels in si
DESCRIPTION
Characterization of vacancy-like defects in H 2 cycled Mg and of ordered- nanochannels in Si by combined PAS techniques . Roberto S. Brusa. Department of Physics , University of Trento, Italy. 5-9 September , Smolenice , Slovakia. Overview. - PowerPoint PPT PresentationTRANSCRIPT
Characterization of vacancy-like defects in H2 cycled Mg
and of ordered-nanochannels in Siby combined PAS techniques
Roberto S. BrusaDepartment of Physics, University of Trento, Italy
5-9 September, Smolenice, Slovakia
The underlying theme of this presentation is the combined use of different PAS Techniques for the characterization of “open spaces” with dimension in the 10-12 to 10-8 m range.
The Lecture will be divided into two parts:
1. PAS Techniques for the study of the role of vacancy-like defectsin the H2 sorption processes in Mg and Nb doped Mg materials
2 . Ps formation and cooling in oxidized ordered nanochannels specially made in Si. This system is allowing to retrieve fundamental information which will be useful for characterizing open porosities.
Overview
Study of nanostructured materials for hydrogen storage
vaulted ceiling at Sumela monastery (Trabzon-Turkey)
Some of the results were reviewed in a talk at thePPC8 in Coimbra (2005)
Phys. Rev. B 49, 7271 (1994)J. Appl. Phys. 85, 2390 (1999)J. Appl. Phys. 85,1401(1999)Phys Rev. B 61, 10154 (2000) Appl. Phys. Lett. 79, 1492 (2001)Phys. Rev. B 71, 245320 (2005) Appl. Phys. Lett. 88, 011920 (2006). Phys. Rev. B 74, 174120 (2006)
Background...Combined PALS, CDB, DBS for studying vacancy-like and cavities in He and H Implanted crystalline Si
Sample : ~10 μm Mg deposited by r.f. magnetron sputtering coated with a 10 nm thick Pd capping layer to prevent oxidation
Morphology:columnar structure. Lateral dimension of the columns : 0.5 μm.grain size : 100 ± 5 nm by the Scherrer eq. on the (0002) XRD reflection peak grain sizes do not change with H sorption cycles.
Mg
Mg hydride contains 7.6 wt. % of H H2 desorption requires phase transformation MgH2 Mg at T 573 - 673 K,and exhibits very slow kinetics.
residual O (< 10-4 at-1 )
Self supporting sample were activated and then subjected to sorption cycle
SORPTION CYCLE at 623 K:
i) At 1.5 Mpa H2 -20 h (ABSORPTION STEP)ii) Chamber evacuated (DESORPTION STEP)
Fig. (a) : Desorption rate Q(t)/(mMg + mH2) ( wt. % H2/ s)
Fig. b: H amount desorbed (wt. % H2)(time integral of the Desorption rate)
With Sievert’s type techniques H desorption flow Q (t) [mass hydrogen/s] from MgH2
was monitored .
4th
9th
H sorption cycles in pure Mg
Checchetto Brusa et al 2011 Phys. Rev. B 84 054115
4th
9th
Johnson-Mehl-Avramy eq. (t)=1-exp[-(kt)n
(t) the fraction of transformed material k rate constant n reaction order.The phase transformation is limited only by bulk processes.
analysis in stationary conditions at 583 K<T <623 K indicated that the desorptionobeys to a Nucleation and Growth mechanism with a reaction order n = 2 and an activation energy ~ 130 kJ/mol
Processes limiting desorption:a) Surface , H –H2 recombination, linear equation (t)=ktb) H diffusionc) Bulk – NG
H sorption cycles in pure Mg-analysis
PLEPS at NEPOMUC - FRMII
SURF-beam at TRENTO
e+ beams
BaF2 + PT detector
e+ pulsed beam START SIGNAL
STOP SIGNAL
n
i ii
i tItF
1exp)(
Lifetime spectroscopy
2° cycle , 16 keV
e+ beam 0.05-25 keV0.15 nm - 3 m
Ge detector
Ge detector
e+ beam 0.05-25 keV0.15 nm - 3 m
511 E keV
cEpL
2
Doppler broadening spectrosvopy: CDB -DBS
505 510 515 520 525 530 535 540
101
102
103
104
105 low-momentum electrons(conduction and valence bands)
high-momentum electrons(core electrons)
background in asingle-detector system
background ina coincidence system
Si coincidence Si non-coincidence
Cou
nts
Energy [keV]
0 10 20 30 40 50 60 70pL [10-3 m0c]
500 505 510 515 520 525100
101
102
103
104
coun
ts
energy ( keV )
500 505 510 515 520 525100
101
102
103
104
coun
ts
energy ( keV )
A
T
annihilation with low momentum electrons
areapeakareacentral
TAS
ii d
idMgOMgOMgMg SEfSEfSEfES )(
fMg= probability to annihilate in MgfMgO= probability to annihilate at MgO fd= probability to annihilate in a defect
SMg = characteristic S value of MgSMgO=characteristic S value of MgOSd =characteristic S value of the defect
Doppler broadening spectroscopy: DB
GMg () =characteristic G() spectrum of Mg
GMgO()=characteristic G ()spectrumof MgO
Gd ()=characteristic G() spectrumof the defect
Doppler broadening spectroscopy : CDB
Mg= 218±2 ps and GMg()
In Mg single crystal (99.99% purity)
In Mg single crystal (99.99% purity) cold worked at RT
v-Mg= 245±5 ps and Gv-Mg ()
Mg
Vacancy in Mg
In Mg single crystal (99.99% purity) at the surface
MgO
GMgO ()
Reference measurements for G() and
0 5 10 15 20 25 30
-0.5
0.0
0.5
1.0
1.5
re
lative
diffe
renc
e to
ann
ealed
M
g sin
gle cr
ysta
l
pL ( x 10-3 m0c )
vacancy vacancy cluster MgO pure Nb
GoMgO () Go
v-Mg ()
measurement of Gc-Mg ()
0,1 1 100,84
0,88
0,92
0,96
1,00
1,04
1 10 100 1000mean positron implantation depth ( nm )
Mg foil, polished
Mg foil, 10h @ 420oC
Mg foil, 1h @ 500oC
norm
aliz
ed S
par
amet
er
positron implantation energy ( keV )
ii d
idMgOMgOMgMg SEfSEfSEfES )(
Vacancys were introduced in Mg by polishing a Mg film
Annealing at 420°C produced vacancy clustering
Vacancy clusters were removed after annealing at 500 °C
0),(),()(),(2
2
EzPEznzCzEznD b
20
2)(
zz
eAzC
dzEznf bMg 0 ),(
Fractions f are related to the positron density n(z, E):
dzEznzCfdi 0 ),()(
0
),(
zMgO dz
EzdnDf
Guess defect profile
e+ implantation profile
1 10 100 1000
1E-4
1E-3
0.01E= 3 keV
E= 5 keV
E= 10 keV
E= 18 keV
P(z
)
depth z [nm]
E= 1keV
Analysis with the stationary positron diffusion equation
0,1 1 100,84
0,88
0,92
0,96
1,00
1,04
1 10 100 1000mean positron implantation depth ( nm )
Mg foil, polished
Mg foil, 10h @ 420oC
Mg foil, 1h @ 500oC
norm
aliz
ed S
par
amet
er
positron implantation energy ( keV )
0.1 1 10
0.0
0.2
0.4
0.6
0.8
1.0
1 10 100 1000mean positron implantation depth ( nm )
f
positron implantation energy ( keV )
surface defect #1 defect #2 bulk
Ef Mgv Ef Mgc
EfMg EfMgO
41 2 3
Coincidence DBS measurementsIn point 1, 2, 3, 4
EfEGEfEGEfEGEfEGEEG MgcMgcvvMgMgMgOMgO ,
with four measurements we construct a system, f are known, G are the unknown
0 5 10 15 20 25 30
-0.5
0.0
0.5
1.0
1.5
re
lative
diffe
renc
e to
ann
ealed
M
g sin
gle cr
ysta
l
pL ( x 10-3 m0c )
vacancy vacancy cluster MgO pure Nb
Goc-Mg ()
Samples[ps] [ps] [ps]
I1
%I2
%I3
%
#0 80±4 241±4 380 12 67 21#1 125±2 263±2 380 26 29 44#2 122±2 260±2 380 25 25 49#4 165±3 - 380 42 - 57#8 177±3 - 380 50 - 49
1 is the reduced bulk lifetime and increase with the number of cycles pointing out a decrease of intragranular defects
2 is due to trapping into mono- and di-vacancies, these defects disappear after the forth cycle. They are mainly intragranular
3 is due to trapping into vacancy clusters ( size of about 8 vacancies). Their number increases with cycling. They are inferred to form mainly at grain boudaries.
Measuerement in Mg bulk (16-18 keV , 1.5-2 m)
Lifetime results
The fraction are consistent with the lifetime intensities.
#0
#2
#4
#8
#1
CDB resultsSample CDB fractions fi (%)
fMg fc-Mg fv-Mg fo
Mg
#0 55 14 18 13
#1 42 23 17 18
#2 43 29 14 14
#4 45 41 - 14
#8 55 35 - 10
The phase transition (MgH2 Mg) is controlled by the nucleation and growth (NG) of Mg in the hydride phase. The NG mechanism progressive change and it is correlated to the change in difettology.
After 4° cyclepeak at 1800 s disappearance of V and saturation of I3 coming from e+ in clusters
4th cycle peak at 3103 s Mg nucleation at grain boundaries which act as nucleation centers
From 5th to 9th cyclesacceleration of the desorption kinetics and of the H2 desorbed amount faster grow of the Mg phase into the MgH2 matrix increase of the crystalline quality of the Mg nano-grains , ( increase of 1 and its intensity I1)
H kinetics and role of vacancy-like defects
In the free energy of formation of the critical Mg nucleus ΔG = ΔGvolume + ΔGinterface + ΔGstrain,ΔGvolume the volume free E ΔGinterface the interface free E ΔGstrain, strain E due to the volumetric misfit between the critical nucleus of Mg and the matrix.
It can be inferred that vacancy clusters at grain boundaries could assists the nucleation process counteracting the volume change of the crytical Mg nucleus by reducing the ΔGstrain term
e+ diffusion trapping model with a competitive e+ trapping at intragranular point defects and at grain boundaries in polycrystalline materials. (Analytical Model of B. Oberdorfer, R.
Würschum, PRB 79, 184103 (2009). α = specific positron trapping rate at grain
boundaries
lower limit value for the Cc
in the frame of the extreme diffusion-limited regime
Having about 2x1015 grains/cm3 and considering that there are 4x1022 Mg atoms/cm3, we estimated that about 40 vacancy clusters decorate the boundary of each Mg grain
Evaluation of vacancy-like defects Concentrationsamples Cv
at-1
α
m/s
Cc
at-1
As deposited 1.2x10-5 30 -
After 1st cycle 3.5x10-6 45 -
After 2nd cycle 3x10-6 55 -
After 4th and 8th 0 - 2x10-6
0 2 4 6 8 10
0.20.40.60.81.0
0.2
0.4
0.6
no Nb low Nb high Nb
I 2
number of cycles
I 3#0
#1
#4
#8
#2 Samples[ps] [ps] [ps]
I1
%I2
%I3
%#0HC - 296±1 - - 99.5 -#1HC - 263±2 415 - 57 42#2HC - 204±1 415 - 41 58#4HC - 207±5 415 - 48 51#8HC - 229±3 415 - 60 39
Nb ( 5 at %) doped Mg ̴
Mg+Nb (5%) CDB fractions fi
(%)
#0HC 25 34 28 13 - #1HC 30 40 19 11 - #2HC 39 57 - < 1 3 < f < 4 #4HC 43 40 - < 5 12 <f < 17 #8HC 33 39 13 < 2 13 < f < 15
Studying porous materials withPs
2 4 6 8 10 12 14
10-3
10-2
10-1
100
0GPa 2GPa 4GPa 6GPa 8GPa
Cou
nts
[arb
.uni
ts]
Time [ns] 0 2 4 6 80.00
0.05
0.10
0.15
0.20
0.25
0.30
0
20
40
60
80
100
Pore radius Pore radius at 8 GPaPo
re ra
dius
[nm
]
Intensity of o-Ps lifetime in pores
Pressure [GPa]
Intensity [%]
RRRn
nRRRP AAop
2sin2
11..With the Tao-Eldrup model R [nm] delta R=0.18 nm
Commercial grade Spectrosil (density 2.20g/cm3) was permanently densified applying at 500 °C a pressure and then realising the pressure and a rapidcooling down.
2GPa (2.21g/cm3), 4GPa (2.25g/cm3), 6GPa (2.41g/cm3), 8GPa (2.67g/cm
Shrinking of voids in silica Spectrosil (fused Quartz)
< 1nm
> 1nmPs
e+
Ps
Ps
Ps
e+
e+
Ps probes:1. Connected porosity (if not capped)-3-PAS, TOF2. Size of pores in a wide range- PALS, 3-PAS3. Distribution: DBS, PALS, 3-PAS
•size of pores
•shape of pores
•chemical environment of pores
•Ps thermalization and cooling
But annihilation and diffusion of Ps depend from:
Probing nano-pores
Searching for a porous materials with an high yield of Ps emitted in vacuum to be used as e+ Ps converter for anti hydrogen formation, we have synthesized nanochannel in silicon
AEGIS (Antimatter experiment: Gravity, Interferometry, Spectroscopy) experiement
Top view of the silicon samplewith nanochannels
Orderen nanochannels in Silicon
Ps
Positronium converter
Positron beam
Ps
Ps
Vacuum
Ps
Ps
QUANTUM CONFINEMENT
222 / amEg
gB EkT )3/2(
the minimum temperature is:
Mariazzi S, Salemi A and Brusa R S 2008 Phys. Rev. B 78 085428
#0 (4-7 nm) mini T is 180-60 K #1 (8-12 nm) min T is 45-20 K
160 K
Nano-size and Ps thermalization
Si p-type 0.15-0.21 Ohm/cmcurrent from 4-18 mA/cm2 , 15’
produced by electrochemical etching, as for porous silicon but adapting times and current for obtaining nano- structures
10 nm #0
#1
#2
#3
#4
100 nm
#5
Possibility of tuning: #0 = 4-7 nm #1=8-12 nm #2= 8-14 nm # 3= 10-16 nm #4= 14-20 nm #5= 80-120 nm Mariazzi S, Salemi A and Brusa R S 2008 Phys. Rev. B 78 085428
Tuning the size of nanochannels
470 480 490 500 510 520100
101
102
103
104
coun
ts
energy ( keV )
2γ rayspeak area
o-Ps 3γ raysvalley area
Annealed1h 300°C
Annealed2h 100°C#0
10 nm
a) b)
0.1 1 10
0.0
0.1
0.2
0.3
0.4
0.5
Mean positron implantation depth [nm]
not oxidized 0.5h 100°C 2h 100°C (#0) 4h 100°C 1h 300°C 1h 400°C
F 3 (o
-Ps
fract
ion)
Positron implantation energy [keV]
10 1000
Optimum oxidation for the Ps yield
0.1 1 10
0.1
0.2
0.3
0.4
0.5
Mean positron implantation depth [nm]
F 3 (o
-Ps
fract
ion)
Positron implantation energy [keV]
#3#4#5
0.1
0.2
0.3
0.4
0.5
#0#1#2
10 1000
0.1 1 100
50
100
150
200
250
300
350
400
450
420 440 460 480 500 520
#0 at 1 keV Silicon at 1 keV
coun
ts [a
rbitr
ary
units
]
Annihilation -ray energy (E)
Cou
nts
in P
eak+
Val
ley
(P+V
)
Positron implantation energy [keV]
Silicon #0
ENENPEP escapedSi 32
ENVEV Si
32
W
DetectorSample3cm
4cm
z
Ps yield with the size of the nano-channels
ENVEV Si
32
ENENPEP escapedSi 32
0.1 1 10
0.1
0.2
0.3
0.4
0.5
Mean positron implantation depth [nm]
F 3 (o
-Ps
fract
ion)
Positron implantation energy [keV]
#3#4#5
0.1
0.2
0.3
0.4
0.5
#0#1#2
10 1000
Corrected o-Ps fraction due to Detector solid angle
0.1 1 10
0.1
0.2
0.3
0.4
0.5
Mean positron implantation depth [nm]
F 3 (o
-Ps
fract
ion)
Positron implantation energy [keV]
#3#4#5
0.1
0.2
0.3
0.4
0.5
#0#1#2
10 1000
0.1 1 10
0.1
0.2
0.3
0.4
0.5
Mean positron implantation depth [nm]
F 3 (o
-Ps
fract
ion)
Positron implantation energy [keV]
#3#4#5
0.1
0.2
0.3
0.4
0.5
#0#1#2
10 1000
ECEBEAEF )(3
121
121EE
eFFFEA
6.1
0
1
1
EE
EB
2
2
21
1
C
EE
CCKEC
0 2 4 6 8 10 12 14 16 180
10
20
30
40
50
60
70
Inte
nsity
[%]
Positron implantation energy [keV]
I1 I2 I3
0.2
0.4
0.6
20
30405060
1
2
3
Life
time
[ns]
o-Ps formation o-Ps out diffusion probability o-Ps annihilation
via 3γ into pores
PALS in #1
Fitting with the diffusion equation
200
400
600
800
1000
1200
1400
1600
#0 #1 #2 #3 #4 #5
o-P
s di
ffusi
on le
ngth
[nm
]
Sample
The o-Ps fraction out-diffusing at 10 keV positron implantation energy is still 10 % in #0, 17 % in #1 23-25 % in #2, #3, #4 and #5.
Up to 42 % of implanted positrons at 1 keV emitted as o-Ps
LPs
0.1 1 10
0.1
0.2
0.3
0.4
0.5
Mean positron implantation depth [nm]
F 3 (o
-Ps
fract
ion)
Positron implantation energy [keV]
#3#4#5
0.1
0.2
0.3
0.4
0.5
#0#1#2
10 1000
2 channeltrons
target position
5 NaI scintillators
TOF ApparatusBEAMPrompt peak 16 ns
zo
zo
o-Ps Time of Flight measurements
where
tf
tp
z0
If tp ˂˂ tf tm tf
Mariazzi S, Brusa R S et al., Phys. Rev. Lett. 104 243401 (2010)
0 50 100 150 200 250
0.068 eV
coun
ts [a
rbitr
ary
units
]
o-Ps time of flight [ns]
7 keV, T = 150 K
2
0.076 eV
7 keV, T = 200 K
0 100 200 300 400
FWHM = 23 ns
coun
ts [a
rb. u
nits
]
Time of flight [ns]
Prompt
0.096 eV
7 keV, T = 300 K3
4
8
0.140 eV 4 keV, T = 300 K
After smoothing, subtraction of the background, and correction by multiplying by 142exp1 t
t
140 160 180 200 220 240 260 280 300 3200.065
0.070
0.075
0.080
0.085
0.090
0.095
0.100
aver
age
o-Ps
em
issio
n en
ergy
[eV]
Sample temperature [K]
Ps cooling - 5-8 nm channels
0.0 0.1 0.2 0.3
T=1515±15K
T=305±10K
T=1425±25K
T=195±10K
T=1260±15K
T=145±10K
7 KeV, T = 300 K 7 KeV, T = 200 K 7 KeV, T = 150 K
log(
dN/d
E) [a
rbitr
ary
units
]o-Ps kinetic energy [eV]
dEENdttN )()(
3)()( ttNEN
0 50 100 150 200 250
0.068 eV
coun
ts [a
rbitr
ary
units
]
o-Ps time of flight [ns]
7 keV, T = 150 K
2
0.076 eV
7 keV, T = 200 K
0 100 200 300 400
FWHM = 23 ns
coun
ts [a
rb. u
nits
]
Time of flight [ns]
Prompt
0.096 eV
7 keV, T = 300 K3
4
8
0.140 eV 4 keV, T = 300 K
The two lines in log-lin graph correspond to two beam-Maxwellian at two different T.
Thermalized Ps
1 100.0
0.1
0.2
0.3
0.4
Positron implantation depth [nm]
T = 300 K T = 200 K T = 150 K
F 3 o
-Ps
fract
ion/
impl
ante
d po
sitro
ns
Positron implantation energy [keV]
100 1000
0.0 0.1 0.2 0.3
T=1515±15K
T=305±10K
T=1425±25K
T=195±10K
T=1260±15K
T=145±10K
7 KeV, T = 300 K 7 KeV, T = 200 K 7 KeV, T = 150 K
log(
dN/d
E) [a
rbitr
ary
units
]
o-Ps kinetic energy [eV]
Fraction of o-Ps emitted thermalized : RT ~19 % 5% implanted e+ 200 K ~15 % 4 % implanted e+
150 K ~9 % 2.5 % implanted e+
Fraction of thermalized Ps
quantum confinement and thermalization
Crivelli et al., Phys. Rev. A 81, 052703 (2010)
Cassidy et al., Phys. Rev. A 81, 012715 (2010)
Similarsamples
42 meV in pores of 2.7 nm
Ps
Positronium converter
Ps
Ps
Vacuum
Ps
Ps
Permanence time of Ps in nano-channels before escaping into vacuum
tm= tp+tf
tf
tp
z0
At 7 keV e+ implantation energy a thermalized o-Ps fraction is foundMeasurements at three different distance z were done
t p thermal=19±9 ns tp cooled = 5±3 nsvthermal = 4.9x104±2x103 m/s
T=310±20 K
13.4± 0.9 meV
vcooled = 1.0x105±1x104 m/s
T=1370±300 K
59.4 ± 13.0 meV
The measured tp=tp thermal can be compared with the value obtained by a diffusion model (Cassidy et al. PRB A82, 052511 (2010))
the rate of the Ps emission from the sample is retrieved solving the diffusion equation
t theory = tp = 17 ns
Experimental Pick off lifetime of 44±4 ns is less than expectedby Tao-Eldrup RTE model at 300 K , ie. 77-97 ns for 5-8 nm nanochannels sizes.
Inferring that a Ps fraction annihilate hot and using as a first approximation the average T of thermal and cooled distributions (1100±300K ) we find 51±8 ns .
t exp = tp = 19 ns
Tunable nanochannels will allow to study:
Cooling and thermalization at tempertaure < 150 K
Cooling and thermalization in presence of decorated surfaces
Relations between diffusion and tortuosity
TOF apparatus will be set up at NEPOMUC
Concluding remarks Pas techniques can be improved
with new arrays and faster detectorsStrong need of friendly programs of analysis
based on diffusion equationStudy at low temperature can bring to a new
Ps tools for porosity characterization
THE WORK on Mg was DONE in COLLABORATION WITH:
THE WORK on Ps was DONE in COLLABORATION WITH:
S. MARIAZZI L. DI NOTOG. NEBBIA
positron Group, Università di Trentopositron Group, Università di TrentoINFN, Padova-Trento
S. MARIAZZI L. RAVELLI and W. EGGER C. MACCHI , A. SOMOZAR. CHECCHETTO, A. MIOTELLOUniversità di Trento
positron Group, Università di Trento
INFIMAT, Tandil, Buenos AiresUniversität der Bunderswehr