Fourth Network-wide GlaCERCo workshop Rennes –October 22 nd – 23 rd, 2014 Development of optical...
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Transcript of Fourth Network-wide GlaCERCo workshop Rennes –October 22 nd – 23 rd, 2014 Development of optical...
Fourth Network-wide GlaCERCo workshopRennes –October 22nd – 23rd, 2014
Development of optical sensors for early stage diagnosis of
pathologies
Fourth Network-wide GlaCERCo workshopRennes - October 22nd – 23rd, 2014
Yaroslav Shpotyuk
CNRS, Glasses and Ceramics Team, University of Rennes 1
Outline
o Introduction
o Description of work
o Results
o Conclusions
Fourth Network-wide GlaCERCo workshopRennes –October 22nd – 23rd, 2014
Introduction (I)Research and training activities
Role in GlaCERco Project: ESR 9
Start date : 01 October 2012 End date: 31 March 2014Work Package 3. Design, synthesis and characterisation of special glasses suitable for photonic devices.
Secondment: Phosphate glasses doped with a rare-earth for medical applications
Start date : October, 2013 Duration: 2 months
Work Package 3. Design, synthesis and characterisation of special glasses suitable for photonic devices.
Topic: Optical sensor characterization.
Main Objectives:• to fabricate Se\Te-based glasses with extended optical windows
towards far IR, which allows detect new vibration modes of targeted molecules as signatures of early stage pathologies;
• to develop rare-earth doped optical fibres pumped in visible or NIR and re-emitted in mid-IR as secondary remote sources for probing some biological liquids or tissues;
• Investigate the stability of this glasses against environment (oxidation etc.) and physical ageing;
• Improve the process of purification to avoid absorption in IR caused by H2O, CO2, O-based bonds, etc.
Introduction (I)Objectives: CNRS
Introduction (I)Objectives: Abo Academy
• Preparation of rare-earth doped glasses of B2O3-CaO/SrO-P2O5 systems using different CaO/SrO ratios.
• Investigation of the effect of the glass composition on the structural, optical and thermal properties of the glasses as well as on the glass bioactivity response when in contact with simulated body fluid (SBF).
• Preparation of preforms with good quality for further fiber drawing.
• Investigation of the effect of the drawing on the structural, optical and thermal properties of the glasses as well as on the glass bioactivity response when in contact with SBF.
Fourth Network-wide GlaCERCo workshopRennes –October 22nd – 23rd, 2014
Introduction (I)Still looking for Postdoc position…
Topic: Radiation induced effects on optical properties of As-Sb-S glasses.
Faculty of ElectronicsIvan Franko National University of LvivSupervisor: Ihor Polovynko
Topic: Development of optical sensors for early diagnosis of pathologies.
Institute of ChemistryUniversity of Rennes 1, CNRSSupervisors: Bruno Bureau and Catherine Boussard-Pledel
Joint-supervision PhD defense: 08.10.2014
Outline
o Introduction
o Description of work
o Results
o Conclusions
Fourth Network-wide GlaCERCo workshopRennes –October 22nd – 23rd, 2014
Description of workThe field of research
ChG – the unique disordered solids, being simultaneously:• inorganic polymers, in terms of their chemical nature,• semiconductors, in terms their electronic nature,• glasses, in terms of their thermodynamic nature.
Chalcogenide glass (ChG) – is a glass containing one or more chalcogen elements (S, Se or Te) with other elements from IV-th and V-th groups of the Periodic Table (typically As, Sb, Bi, Ge, etc.) obtained by conventional melt quenching.
Description of workChG preparation
Description of workThe aim of the activity
The spectral range of IR spectroscopy allows to probe the vibrational fingerprint of biomolecules.
Evanescent wave in optical fiber interacts with environment, allowing identification of molecules at the basis of spectrum analysis
To ensure high solubility of rare-earth ions, the ChVS matrix should contain Ga additions
Description of workThe aim of the activity
• transparent in IR up to 20 m;• good mechanical and thermodynamic properties (T=Tx–Tg > 100 oC);• well purified;
Main requirements to the glass properties to be used in FEWS:
• transparent in visible or NIR (up to 1.5 m );• glass with low phonon energy.• ability to introduce rare-earth ions;
Additional task: active fibers
As-Se based GaxTe20As30-xSe50; Gax(As0.4Se0.6)100-x-yTey;
Studied glasses:
Ge-Se-Te based Ga5Ge20Sb10Se65-xTex
Ga10Ge15Te75-xMx (M=Se, CsCl)
Dopands Pr3+
Tb3+
Description of workThe aim of the activity
400 600 800 1000 1200 1400 1600 1800 2000 2200 2400 26000
10
20
30
40
50
60
70
80
Te-basedSe-based
S-based
Tra
nsm
issi
on, %
Wavelength, nm4 6 8 10 12 14 16 18 20 22 24
0
10
20
30
40
50
60
70
80
Te-based
Se-based
Tra
nsm
issi
on, %
Wavelength, m
S-based
- Region of interest in the Vis/NIR for laser pumping (optical band gap more than 0.8 eV (less than 1500nm)
- Region of interest in the IR for biosensing(up to 20m)
Description of workThe aim of the activity
For the successful fiber drawingdifference between Tx and Tg should be at least 100 oC
Tx
Hea
t Flo
w, W
/g
Temperature, oC
Tg
Tx – Tg > 100 oC
Description of workThe aim of the activity
Why use RE?
• To have secondary remote sources of light in the IR region from 1 to 10 m.
• In case of Pr3+ the large numbers of bands in mid IR offers the promise of high-brightness sources for remote sensing.
To ensure solubility of rare-earth elements, the glassy matrix should contain some additions like Ga
Energy level diagrams of Pr3+ showing IR emission
Description of workThe aim of the activity
2 4 6 8 10 12 14 16 18 20 22 240
10
20
30
40
50
60
70
80
Tra
nsm
issi
on, %
Wavelength, m
As30Se
50Te
20
As30Se
50Te
20 + 500ppm Pr
2 4 6 8 10 12 14 16 18 20 22 240
10
20
30
40
50
60
70
80
Tra
nsm
issi
on, %
Wavelength, m
Ga1As
29Se
50Te
20
Ga1As
29Se
50Te
20 + 500ppm Pr
1%
of G
a
Effect of Ga-addition on solubility of RE
With
ou
t Ga
Outline
o Overview
o Description of work
o Results
o Conclusions
Fourth Network-wide GlaCERCo workshopRennes –October 22nd – 23rd, 2014
Results
Fourth Network-wide GlaCERCo workshopRennes –October 22nd – 23rd, 2014
xGa Sample Composition Density, g/cm3
Tg,C
Tx,C
T,C
0 G0 As40Se60 4.619 184 --- ---
1 G1 Ga1(As0.4Se0.6)99 4.629 182 --- ---
2 G2 Ga2(As0.4Se0.6)98 4.635 182 307 125
3 G3 Ga3(As0.4Se0.6)97 4.631 180 283 103
4 G4 Ga4(As0.4Se0.6)96 4.642 182 277 95
5 G5 Ga5(As0.4Se0.6)95 4.662 180 276 96
Gax(As0.4Se0.6)100-x system: Ga effects in glassy arsenic selenide
Restricted functionality at high Ga content is caused by spontaneous crystallization.
Ga2Se3 cubic phase, space group: mF 34
2 4 6 8 10 12 14 16 18 20 22 240
10
20
30
40
50
60
70
80
G0 G1 G2 G3 G4 G5
Tra
nsm
issi
on, %
Wavelength, m
10 20 30 40 50 60 70 80 90
G4
G3
G2G1
G0
* - Ga2Se
3 crystalline phase
* * * **
*
*
*
Inte
nsi
ty, a
.u.
2
*
G5
ResultsGa2(As0.4Se0.6)98-yTey system: Te effects in Ga-based arsenic selenide
Sample Composition Density, g/cm3
Tg,C
Tx,C
T,C
G2 Ga2(As0.4Se0.6)98 4.635 182 307 125
T10 Ga2(As0.4Se0.6)88Te10 4.791 151 267 116
T15 Ga2(As0.4Se0.6)83Te15 4.860 149 265 116
T20 Ga2(As0.4Se0.6)78Te20 4.940 132 239 107
T30 Ga2(As0.4Se0.6)68Te30 5.069 115 264 149
2 4 6 8 10 12 14 16 18 20 22 240
10
20
30
40
50
60
70
80
G2 T10 T15 T20 T30
Tra
nsm
issi
on, %
Wavelength, m
10 20 30 40 50 60 70 80 90
*
* * - Ga2Se
3 crystalline phase
Inte
nsi
ty, a
.u.
2
T30
T20
T15
T10
G2
Te effects: (1) decrease in the phonon energy of glassy matrix and stretching in the IR transmittance ;(2) covalent bonds delocalization – long-wave shift in the fundamental optical absorption edge (decrease in Eg).
The restricted functionality at high Te content is connected with spontaneous crystallization:
Ga2Se3 cubic phase, space group: mF 34
ResultsGa2(As0.4-zSbzSe0.6)98 system: AsSb effects in Ga-based arsenic selenide glass
600 800 1000 1200 1400 1600 1800 20000
10
20
30
40
50
60
70
80
G2 S1 S2 S3
Tra
nsm
issi
on, %
Wavelength, nm2 4 6 8 10 12 14 16 18 20 22 24
0
10
20
30
40
50
60
70
80
G2 S1 S2 S3
Tra
nsm
issi
on, %
Wavelength, m
Sample Composition Density, g/cm3
Tg,C
Tx,C
T,C
G2 Ga2(As0.4Se0.6)98 4.635 182 307 125
S1 Ga2(As0.36Sb0.04Se0.60)98 4.727 187 --- ---
S2 Ga2(As0.28Sb0.12Se0.60)98 4.900 191 --- ---
S3 Ga2(As0.20Sb0.20Se0.60)98 5.073 196 306 110
S4 Ga5(As0.28Sb0.12Se0.60)95 4.873 194 --- ---
10 20 30 40 50 60 70 80 90
Ga5(As
0.28Sb
0.12Se
0.60)95 (S4)
Ga5(As
0.40Se
0.60)95 (G5)
Inte
nsit
y, a
.u.
2Sb effects: (1) enhanced concentration limit (due to Ga) in phase separation and crystallization;(2) metallization of chemical bonds – small long-wave shift in optical absorption edge (decrease in Eg).
2 4 6 8 10 12 14 16 18 20 22 240
10
20
30
40
50
60
70
80
Ga5(As
0.28Sb
0.12Se
0.60)95 (S4)
Ga5(As
0.40Se
0.60)95 (G5)
Tra
nsm
issi
on, %
Wavelength, m
Partial substitution of As by Sb in As2Se3-based glass allows to introduce more Ga without crystallization
ResultsGaxTe20As30-xSe50 system (Ga-TAS-235): Ga effects in TAS-235
xGa Sample Composition Density, g/cm3
Tg,C
Tx,C
T,C
0 Ga0 As30Se50Te20 4.888 134 --- ---
1 Ga1 Ga1As29Se50Te20 4.912 131 --- ---
2 Ga2 Ga2As28Se50Te20 4.920 128 --- ---
5 Ga5 Ga5As25Se50Te20 4.940 126 223 97
10 Ga10 Ga10As20Se50Te20 4.899 118 231 113
2 4 6 8 10 12 14 16 18 20 22 240
10
20
30
40
50
60
70
80
Tra
nsm
issi
on, %
Wavelength, m
Ga0
Ga2
Ga1
Ga5
Restricted functionality at high Ga content is caused by spontaneous crystallization:Gа2 – the Rayleigh scattering on crystallites with character sizes of 200-300 nm;Gа5 – the Rayleigh scattering + the Mie scattering on intrinsic microscopic inhomogeneities.
Micrographs of Gа1 surface (homogeneous glass), Gа2 (droplets of homogeneous nano- inclusions of -Ga2Se3 cubic phase with 200–300 nm diameter) and Gа5 microcrystallites of - and - Ga2Se3 cubic phases with more than 10 m size).
Glass forming region:(a) glasses(b) tendency to phase separation
Ga2
Ga510 20 30 40 50 60 70 80 90
Ga10
Ga5
Ga2
Ga1
Ga0
Inte
nsi
ty, a
u
2
- dominant crystalline phase under small Ga content (3–5 %) is HT-modification of cubic -Ga2Se3. - additional extractions of cubic
-Ga2Se3 appear under higher Ga content (above 5 %).
ResultsGa5Ge20Sb10Se65-xTex system : Te effects
2 4 6 8 10 12 14 16 18 20 22 240
10
20
30
40
50
60
70
80
Tra
nsm
issi
on, %
Wavelength, m
Ga5Ge
20Sb
10Se
65
Ga5Ge
20Sb
10Se
60Te
5
Ga5Ge
20Sb
10Se
55Te
10
Ga5Ge
20Sb
10Se
45Te
20
Ga5Ge
20Sb
10Se
35Te
30
600 900 1200 1500 1800 2100 2400 2700 30000
10
20
30
40
50
60
70
80
Tra
nsm
issi
on, %
Wavelength, nm
Ga5Ge
20Sb
10Se
65
Ga5Ge
20Sb
10Se
60Te
5
Ga5Ge
20Sb
10Se
55Te
10
Ga5Ge
20Sb
10Se
45Te
20
Ga5Ge
20Sb
10Se
35Te
30
xTe Composition Density, g/cm3
Tg,C
Tx,C
T,C
0 Ga5Ge20Sb10Se65 4.629 279 --- ---
5 Ga5Ge20Sb10Se60Te5 4.724 267 --- ---
10 Ga5Ge20Sb10Se55Te10 4.824 253 408 155
20 Ga5Ge20Sb10Se45Te20 4.983 233 387 154
30 Ga5Ge20Sb10Se35Te30 5.129 221 335 114
40 Ga5Ge20Sb10Se25Te40 5.438 Crystallized
50 Ga5Ge20Sb10Se15Te50 5.733 Crystallized10 20 30 40 50 60 70 80 90
Counts
Position 2
Ga5Ge
20Sb
10Se
35Te
30
Ga5Ge
20Sb
10Se
25Te
40
ResultsRE doping and fiber drawing of Ga2(As0.4Se0.6)88Te10 glass
2 3 4 5 6 7 8 9 10 11 120
4
8
12
16
20
24
H2O
As-O
Se-H
Att
enua
tion
, dB
/m
Wavelength, m
Ga2(As
0.40Se
0.60)
88Te
10 (1-step distillation)
Ga2(As
0.40Se
0.60)
88Te
10 (3-step distillation)
Optical loss spectra in fiber drawn from glassy Ga2(As0.40Se0.60)88Te10 alloy,purified via single-step (black line) and three-step distillation (red line).
Optical transmission spectra of glassy samples RE1 and RE2 as compared with Ga2(As0.4Se0.6)88Te10.
Optical loss spectra in fiber drawn from glassy Ga2(As0.4Se0.6)88Te10
alloy, doped with 500 ppm Pr3+ (insert – micrograph of fiber cross section).
2 3 4 5 6 7 8 9 10 11 120
4
8
12
16
20
24
As-O
Pr3+: 3H4-3H
5Se-HSe-H
600 900 1200 1500 1800 2100 2400 27000
10
20
30
40
50
60
70
80
1200 1500 1800 2100 24000,00E+000
2,00E-020
4,00E-020
6,00E-020
8,00E-020
3F4
3H6
3F2
3F3
RE2
Abs
orpt
ion
cros
s se
ctio
n, c
m2
Wavelength, nm
T10 RE1 RE2
Tran
smis
sion
, %
Wavelength, nm
Sample CompositionDensity,
g/cm3
Tg,C
Tx,C
T,C
RE1Ga2(As0.4Se0.6)88Te10
+ 500ppm Pr4.778 160 273 113
RE2Ga2(As0.4Se0.6)88Te10
+ 1000ppm Pr4.787 160 279 119
Outline
o Overview
o Description of work
o Results
o Conclusions
Fourth Network-wide GlaCERCo workshopRennes –October 22nd – 23rd, 2014
• Glass forming ability of Ga-doped chalcogenides of ~100 compositions, such as
o GaxAs30-xSe50Te20
o Gax(As0.4Se0.6)100-x-yTey
o Ga5Ge25Se70-xTex
o Ga5Ge20Sb10Se65-xTex
o Ga10Ge15Te75-xSex
o Ga10Ge15Te75-CsCl
was studied;
• It was established that Ga2Se3 crystalline phase is destroying covalent-
bonding network arrangement of the most glassy systems which were studied;
• Selected compositions were successfully doped with rare-earth elements and drawn into fibers.
Conclusions (I)