Các hạt nano LaF3 pha tạp ion Eu3+ với các nồng độ khác nhau được chế tạo bằng phương
pháp thủy nhiệt. Các phép đo XRD, huỳnh quang và kích thích huỳnh quang được thực hiện tại
nhiệt độ phòng. Tỉ lệ giữa cường độ dải huỳnh quang 5D0→7F2 (dipole điện) và 5D0→7F1 (dipole
từ) (R) được sử dụng để đánh giá tính bất đối xứng của trường ligand xung quanh ion Eu3+. Các
thông số Judd – Ofelt được tính toán từ phổ huỳnh quang đã được sử dụng để dự đoán các tính
chất phát xạ của các chuyển dời 5D0→7FJ cũng như thời gian sống của mức 5D0. Giá trị nhỏ của
thông số Ω2 và tỉ số R liên quan đến tính đối xứng cao của trường ligand xung quanh ion Eu3+
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Journal of Science and Technology 54 (1A) (2016) 88-95
OPTICAL PROPERTIES OF Eu
3+
IONS IN LaF3 NANOCRYSTALS
Hoang Manh Ha
1,*
, Tran Thi Quynh Hoa
2
, Nguyen Ngoc Long
3
,
Le Van Vu
3
, Phan Van Do
4
1Hanoi Architectural University, Km 10 Nguyen Trai, Thanh Xuan, Hanoi
2National University of Civil Engineering, 55 Giai Phong, Hai Ba Trung, Hanoi
3Hanoi University of Science, 334 Nguyen Trai, Thanh Xuan, Hanoi
4Thuy Loi University, 175 Tay Son, Dong Da, Hanoi
*
Email: hahm1982@gmail.com
Received: 30 August 2015; Accepted for publication: 25 October 2015
ABSTRACT
LaF3 nanocrystals doped with different concentrations of Eu
3+
ions were synthesized by
hydrothermal method. The XRD, luminescence and excitation spectra have been studied at room
temperature. The ratio of the
5
D0→
7
F2 electric dipole transition intensity to the
5
D0→
7
F1
magnetic dipole transition intensity (R) was used to evaluate the asymmetry of Eu
3+
site. Judd-
Ofelt parameters were calculated from emission spectra and were used to predict the radiative
properties of
5
D0→
7
FJ transitions also the lifetime of
5
D0 level. The small values of Ω2 parameter
and R ratio relate to high degree of symmetry of ligand around Eu
3+
site in this material.
Keywords: LaF3:Eu
3+
nanocrystals, luminescence, Judd-Ofelt analysis.
1. INTRODUCTION
Rare earth (RE) doped crystals have attracted the attention of scientists due to their wide
applications in many optical devices like lasers, light converters, sensors, high-density memories
and optical amplifiers [1 - 5]. Compared to the oxide crystals, the fluoride crystals show more
featured advantages such as long lifetime, weak nephelauxetic effect and low phonon energy [6 -
8], so these crystals are promising candidates for producing the laser and upconversion devices
[4 - 6, 8]. Lanthanum fluoride nanocrystals (LaF3) are known with the maximal phonon mode
frequency about 380 cm
-1
[9], so they are an ideal material for RE dopant because they minimize
multiphonon decay processes between energy levels which are very close of the RE
3+
ions, this
increases the quantum efficiency of the fluorescent transitions. In practice, LaF3 nanocrystals
doped with RE
3+
have been used in fibre optics, electrodes, fluorescent lamps, optical amplifiers
and radiation applications [9 - 11].
Among the RE
3+
ions used to optically activate materials, the Eu
3+
ions are mostly chosen
due to Eu
3+
ions emit narrow-band, almost monochromatic light and have long lifetime of the
optically active states. Further, Eu
3+
ions have often been used as probes for estimation of local
Optical properties of Eu
3+
ions in LaF3 nanocrystals
89
environment around the Ln
3+
ions in different matrices [11 - 13]. In this paper, Eu
3+
ions are used
as probe to study the ligand field around RE
3+
in LaF3 nanocrystals. In addition, optical properties
of LaF3:Eu
3+
are analyzed using Judd–Ofelt theory.
2. EXPERIMENTAL
LaF3 nanocrystals doped with 0; 0.05; 0.1; 0.5 and 1.0 mol% of Eu
3+
ions were prepared by
hydrothermal method. All the chemicals used in our experiment, including lanthanum oxide
(La2O3), europium oxide (Eu2O3), ammonium fluoride (NH4F) and glycine (NH2CH2COOH) are
of analytic grade without further purification. Annealing process was carried out for 12 hours at
temperature of 425 K. The final product was dried in air at 330 K for 12 hours.
The synthesized samples were characterized for their structure by an X-ray diffractometer
(SIMENS D5005, Bruker, Germany) with Cu–Kα1 irradiation (λ = 1.54056 Å). The morphology
of the samples was observed by using a scanning electron microscopy (JEOL-JSM 5410 LV).
The optical absorption spectra were recorded in the range of wavelength from 200 to 3000 nm
using a spectrometer (Cary-5000). Room temperature photoluminescence (PL) and
photoluminescence excitation (PLE) of the samples were measured on a spectrofluorometer (FL
3-22 Jobin Yvon Spex) using 450 W Xe arc lamp as the excitation source.
3. RESULTS AND DISCUSSION
3.1. Structure characterization and morphology
X-ray diffraction patterns of pure LaF3 and LaF3:Eu
3+
(1 mol% of Eu
3+
ions) nanocrystals
are presented in Fig. 1.
First, quite strong diffraction lines in XRD
patterns indicate that LaF3 and LaF3:Eu
3+
nanoparticles have been crystallized well. Second,
all the XRD peaks are unambiguously indexed to
hexagonal phase with P3c1 space group of LaF3
structure (JCPDS card no. 32-0483 for LaF3) with
the following diffraction peaks: (002), (110),
(111), (112), (300), (113), (004), (302), (221),
(114), (222), (223), (304) and (410). The lattice
parameters were calculated to be a = 7.174 Å and
c = 7.344 Å.
Next, the obtained results showed that under
given experimental conditions no critical change
in XRD pattern of Eu
3+
ion doped (1 mol%) LaF3
was observed, compared to that of pure LaF3, indicating that there was no significant interfacial
interaction between Eu and LaF3. Thus, the fact that crystal structure of Eu doped LaF3 was
consistent with LaF3 for the investigated concentration range of Eu without presence of Eu own
phase or shift in d-spacing, this allows to conclude that metallic Eu ions are homogeneously
distributed in LaF3 matrix.
20 30 40 50 60 70
(0
0
4
)
2 theta (degrees)
In
te
n
s
it
y
(
a
.u
.)
LaF
3
:Eu
3+
LaF
3
(0
0
2
)
(1
1
0
)
(1
1
1
)
(1
1
2
)
(3
0
0
)
(1
1
3
)
(3
0
2
)
(2
2
1
)
(2
2
3
)
(4
1
0
)
(3
0
4
)
(2
2
2
)
(1
1
4
)
Figure 1. XRD patterns of LaF3 and LaF3:Eu
3+
samples.
Hoang Manh Ha, Tran ThiQuynhHoa, Nguyen Ngoc Long, Le Van Vu, Phan Van Do
90
The crystallite sizes of LaF3 and LaF3:Eu
3+
were estimated by using Scherrer’s formula [4]
depending on selected peaks. Average sizes of
LaF3 and LaF3:Eu
3+
nanocrystals are about 23
and 25 nm, respectively.
Figure 2 shows FE-SEM image at
efficiently high magnification which can provide
a rough evaluation about particle size and
morphology. From FE-SEM images it can be
seen that the average diameter of the particles is
approximately 50 nm that is larger than value
calculated from Scherrer’s formula. This
perhaps is because the crystallites have
aggregated, forming bigger particles.
3.2. Photoluminescence excitation spectrum and sideband phonon energy
The excitation spectrum of LaF3:Eu
3+
(1.0 mol %) nanocrystal was recorded in the spectral
region 330-560 nm by monitoring the emission at 617 nm (
5
D0-
7
F2 transition) and shown in Fig. 3.
The excitation spectrum consists of the
sharp bands due to the f-f transitions from
6
F0,1,2 of ions Eu
3+
to the excited levels. The
most intense excited band at wavelength of
397 nm corresponds to the
7
F0→
5
L6
transition, which is often used in
fluorescence excitation for Eu
3+
.
The shoulder appears at wavelength
around 458 nm can be related to the phonon
sideband (PSB), which is used to understand
the vibrational modes around the Eu
3+
[13,
14]. The PSB of Eu
3+
in LaF3 is associated
with the
7
F0 →
5
D2 transition and shown in
inset of Fig. 3, in which the
7
F0→
5
D2 excited
transition is the pure electronic transition
(PET). The PET is set as zero energy shift,
the sideband phonon energy in LaF3 can be calculated to be 290 cm
-1
.This phonon energy is
related to the Eg vibration group in LaF3 [9]. The electron phonon coupling constant (g) have been
calculated by [13]:
dI
dI
g
PET
PSB
)(
)(
(1)
where IPSB is the intensity of the phonon sideband and IPET is the intensity of the pure electric
transition. In LaF3:Eu
3+
(1.0 mol%), the g value is found to be 0.059. This value is equal to the
corresponding values in lead fluoroborate (LFB) glasses [13], but is much lower than that in
borotellurite glasses [14].
Figure 2. FE-SEM image of LaF3:Eu
3+
sample.
350 400 450 500 550
-200 -100 0 100 200 300 400
7
F
0
-5
D
2 x3
P
S
B
(
2
9
0
c
m
-1
)
P
E
T
In
te
n
s
it
y
Energy shift
7
F
0
-5
D
4
7
F
2
-5
G
6
7
F
1
-5
G
6
7
F
0
-5
G
6
7
F
2
-5
L
6
7
F
1
-5
L
6
7
F
0
-5
L
6
7
F
0
-5
D
2
7
F
1
-5
D
2
7
F
2
-5
D
2
7
F
0
-5
D
1
7
F
1
-5
D
1
7
F
2
-5
D
1
P
L
i
n
te
n
s
it
y
(
a
.u
)
Wavelength (nm)
Figure 3. The excitation spectrum of Eu
3+
in LaF3
nanocrystals.
Optical properties of Eu
3+
ions in LaF3 nanocrystals
91
This behavior shows that the electron-phonon coupling in LaF3 crystal and LFB glass is
weaker than that in borotellurite glasses. Thus, the ionic of Eu
3+
-F
-
bond in LaF3 nanocrystal is
higher than that Eu
3+
-O
2-
bond in borotellurite glasses [13].
3.3. Emission spectra
Figure 4 illustrates the emission spectra of LaF3:Eu
3+
nanocrystals using the 397 nm
excitation wavelength of xenon lamp source. The luminescence lines are interpreted according to
Carnall’s paper [15]. Owing to very low phonon energy, the multiphonon relaxation rates from
5
D2 and
5
D1 levels to
5
D0 level are very small, so luminescence from higher excited states of
5
D2
and
5
D1 were also observed. The emission spectra consist of 12 observed emission bands in Vis
and a band in NIR region. There are nine quite strong emission peaks at 488, 509, 525, 534, 553,
582, 590, 617 and 681 nm, which are attributed to
5
D2→
7
F2,
5
D2→
7
F3,
5
D1→
7
F0,
5
D1→
7
F1,
5
D1→
7
F2,
5
D0→
7
F0,
5
D0→
7
F1,
5
D0→
7
F2,
5
D0→
7
F4 transitions, respectively, and three weak
emission peaks at 648, 749 and 815 nm corresponding to
5
D0→
7
F3,
5
D0→
7
F5 and
5
D0→
7
F6
transitions, respectively. The
5
D0→
7
F0,3,5 transitions are forbidden under selection rules, so their
intensity are often very weak, however in our case the
5
D0→
7
F0 transition is quite strong. The
5
D0→
7
F2 transition is induced electric dipole (ED), so its intensity depends strongly on the local
symmetry around Eu
3+
ion, polarizability of ligand and energy separation between initial level
and final level. The
5
D0→
7
F1 transition is the most intense of all, this is allowed magnetic dipole
(MD), the intensity of this transition depends on the host but it is independent local symmetry and
reduced matrix elements. So this transition is often used as an internal standard to evaluate the
asymmetry of ligand and fluorescent efficiency of 5D0→
7
F2 transition.
The fluorescence intensity ratio (R) of
5
D0→
7
F2 to
5
D0→
7
F1 transitions of Eu
3+
ions
allows one to estimate the deviation from the
site symmetries of Eu
3+
ions. For LaF3 doped
with 0.05, 0.1, 0.5 and 1.0 mol % of Eu
3+
ions,
the R values are equivalent as shown in table 1.
The values of R are less than unity, i.e. the
fluorescent efficiency of 5D0→
7
F2 transition is
lower than those of 5D0→
7
F1 transition.
Moreover, these values are smaller than those
of many different hosts [13-15]. The lower R
values are attributed to the lower asymmetry
and covalency around the Eu
3+
ions in LaF3
than other hosts. In LaF3 crystal, Eu
3+
ion is
positioned in a La
3+
site with C2 point group
symmetry [9], with this symmetry the
5
D0→
7
F0,1,2 transitions split into 1, 3 and 5
components [12], respectively, like in Fig. 4. In
principle, the electricant magnetic dipoles are allowed in C2 symmetry, so both the
5
D0→
7
F1 and
5
D0→
7
F2 transitions have strong intensity [9]. However, the
5
D0→
7
F2 transition is only very
intense in the case of highly polarizable, whereas fluoride ligands have low polarizability. This
also is the reason for the reduction of R values in the fluoride compounds. Moreover, the
luminescence intensity of the
5
D0→
7
F1 transition is stronger than that of
5
D0→
7
F2 transition, this
suggests that Eu
3+
ions take a site with inversion symmetry in LaF3 crystal [13].
500 550 600 650 700 750 800
7
F
6
7
F
5
7
F
4
7
F
3
7
F
2
7
F
1
7
F
0
5
D
1
-7
F
0
5
D
2
-7
F
3
605 610 615 620 625 630 635
S
5
S
4
S
3
S
2
S
1
5
D
0
-
7
F
2
584 586 588 590 592 594
S
3
S
2S
1
5
D
0
-
7
F
1
d
c
b
a
5
D
2
-7
F
2
5
D
1
-7
F
1
5
D
1
-7
F
2
5
D
0
P
L
i
n
te
n
s
it
y
(
a
.u
)
Wavelength (nm)
Figure 4. The emission spectra of LaF3
nanocrystals doped with Eu
3+
: a) 0.05;b) 0.1;
c) 0.5 and d) 1.0 mol%..
Hoang Manh Ha, Tran ThiQuynhHoa, Nguyen Ngoc Long, Le Van Vu, Phan Van Do
92
3.4. Judd-Ofelt analysis
The Judd-Ofelt (JO) theory was shown to be useful to characterize radiative transitions for
RE
3+
-doped solids, as well as aqueous solutions, and to estimate the intensities of the transitions
for RE
3+
ions. This theory defines a set of three intensity parameters, Ωλ (λ = 2,4,6), that are
sensitive to the environment of the rare-earth ions. Commonly, JO intensity parameters are
usually derived from absorption spectrum. However, owing to the special energy level structure
of Eu
3+
ion, these JO parameters could be estimated from the emission spectra. Four main
emission peaks
5
D0→
7
F1,2,3,4 are used to calculate JO parameters. The
5
D0→
7
F1 is a MD
transition and its spontaneous emission probability Amd is given by [2,8,9]:
)12(3
64 334
Jh
Sn
A mdmd (2)
where h is the Planck constant, is the wave number of the transition in interest, J is the total
angular momentum of the excited state, and n is the refractive index. Smd is the MD line strength,
which is a constant and independent from the host material. The value of Amd can be estimated
using the reference value of A’md published somewhere, and using the relationship
Amd = (n/n’)
3
A’md [2], where A’md and n’ are spontaneous emission probability and refractive
index of the reference material, respectively.
The
5
D0 →
7
F2,4,6 transitions are an ED partially allowed. The spontaneous emission
probabilities Aed of ED transition is given using the following expression:
2
6,4,2
)(
2234
9
2
123
64
U
nn
Jh
A Jed (3)
where J is the wave number of transition
5
D0 →
7
FJ, e is the electron charge,
2
)(U are the
squared doubly reduced matrix elements of the unit tensor operator of the rank λ = 2, 4, 6, and
are calculated from intermediate coupling approximation for a transition ' 'J J .
These reduced matrix elements did not nearly depend on host matrix as noticed from earlier
studies. Thus the parameters could be evaluated simply by the ratio of the intensity of the
5
D0
7
FJ=2,4,6 transitions to the intensity of
5
D0
7
F1 transition as follows:
)(
)(
1
7
0
5
6,4,2
7
0
5
1
FDA
FDA
dI
dI J 2
6,4,2
)(
223
11
2
9
2
U
nn
S
e J
md
(4)
For
5
D0
7
F2 transition, U
(2)
= 0.033; U
(4)
= U
(6)
= 0,
5
D0
7
F2 transition, U
(2)
= 0; U
(4)
=
0.023; U
(6)
= 0 and
5
D0
7
F2 transition,U
(2)
= U
(4)
, U
(6)
= 0.003. Using equation (4) and the
reduced matrix elements, the JO parameters were calculated for different concentrations. The
results are shown in Table 1 in comparison with different matrix.
The Ωλ parameters are important to study the symmetry of local structure around RE
3+
ions
and nature of RE–X (X = F, O) bonding. The Ω4 and Ω6 are related to the bulk properties such as
viscosity and rigidity whereas the Ω2 is more sensitive to the local environment of the RE
3+
ions
and is often related with the asymmetry of the local crystal field. The Ω2 and Ω6 parameters in
LaF3 nanocrystal are smaller than those of other hosts. The smaller value of Ω2 can be attributed
to higher symmetry of the ligand field and lower covalency in Eu
3+
-F
-
bond than other hosts,
Optical properties of Eu
3+
ions in LaF3 nanocrystals
93
whereas the smaller of Ω6 parameter shows that the rigidity of the media in which rare earth ions
is put into is higher in other hosts. In addition, with the low concentration of Eu
3+
in LaF3
nanocrystal, the values of Ω2 and R are almost independent of the concentration of Eu
3+
. That is,
small changes in the concentration do not alter the asymmetry of the ligand as well as covalency
in Eu
3+
-F
-
bond.
Table 1. The Ωλ (×10
-20
cm
2
) JO parameters for Eu
3+
doped various hosts.
Host matrix R Ω2 Ω4 Ω6 Refs
LaF3 (0,05 mol%) 0.68 1.08 0.73 0.66 Present
LaF3 (0,10 mol%) 0.67 1.06 0.72 0.62 Present
LaF3 (0,50 mol%) 0.68 1.07 0.70 0.60 Present
LaF3 (1,0 mol%) 0.69 1.07 0.68 0.57 Present
K2YF10 (crystal) - 1.22 1.26 8.55 [17]
YAlO3 (crystal) - 2.66 6.33 0.80 [17]
PbFBE (glass) 2.09 2.55 0.36 0 [13]
L4BE (glass) 3.69 6.34 4.97 5.10 [16]
B0TN (glass) 2.86 3.29 0.21 0 [14]
B4TN (glass) 2.28 3.34 0.28 0 [14]
3.5. Radiative properties
The JO parameters have been used to estimate the radiative properties such as the radiative
transition rates (AR, s
-1
), branching ratios (βcal, %) and stimulated emission cross-section (σ(λP),
10
-22
cm
2
) for
5
D0→
7
FJ transitions and radiative lifetime (τR) of
5
D0 level of Eu
3+
in LaF3 by
using Eqs. in Ref. [18]. In addition, the gain band width (σ(λP)×Δλeff, 10
-28
cm
-3
) and optical gain
(σ(λP)×τR, 10
-25
cm
2
s
-1
) are also calculated for
5
D0→
7
FJ transitions. The results are presented in
Table 2.
Table 2. The radiative properties of Eu
3+
ions doped (1.0 mol %) in LaF3.
5
D0→
7
F0
7
F1
7
F2
7
F3
7
F4
7
F5
7
F6
AR 0 51 40 0 13.2 0 8.6
βcal 0 45.5 35.4 0 11.7 0 7.7
βmes 6.6 48.3 32 0.98 10.6 0.9 0.6
σ(λP) 0 5.6 4.2 0 2.0 0 1.6
σ(λP)×Δλeff 0 3.2 2.9 0 1.5 0 1.9
σ(λP)×τcal 0 49.7 35.5 0 17.7 0 14.2
The predicted branching ratio (βcal) of
5
D0 →
7
F1 transition get a maximum value and is
45.2 % whereas the measured ratio (βmes) is 48.3 %, thus there is a good agreement between
experimental and calculated branching ratios. The branching ratio, gain band width and optical
gain of this transition are larger than those of other transitions. These results suggest that the
5
D0
→ 7F1 transition of Eu
3+
ions in LaF3 nanocrystal is found to be suitable for developing the fibre
optics [19].
Hoang Manh Ha, Tran ThiQuynhHoa, Nguyen Ngoc Long, Le Van Vu, Phan Van Do
94
4. CONCLUSIONS
LaF3:Eu
3+
nanocrystals were prepared by hydrothermal method. The XRD patterns indicate
that LaF3 nanoparticles have been crystallized well. From the excitation spectrum, the PSB was
found with the energy phonon about 290 nm, which related to the Eg vibration group in LaF3.
The smaller value of g parameter than those in borotellurite glasses shows that the electron
phonon coupling in LaF3:Eu
3+
nanocrystal is weaker than that of borotellurite glasses.
The optical properties of Eu
3+
-doped LaF3 nanocrystals have been investigated. The small
value of R and Ω2 parameter shows that the coordination structure surrounding the Eu
3+
ions has
high symmetry and Eu
3+
-F
-
bond has low polarizability. The radiative parameters show that the
5
D5/2→
7
F1 transition of Eu
3+
ions in LaF3 nanocrystals is very useful fiber optic amplifier.
Acknowledgments. Authors of this paper would like to express their sincere gratitude to the Center for
Materials Science (CMS), Faculty of Physics, Hanoi University of Science, Vietnam National University
for permission to use equipment.
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TÓM TẮT
TÍNH CHẤT QUANG CỦA CÁC ION Eu3+ TRONG TINH THỂ NANO LaF3
Hoàng Mạnh Hà1, *, Trần Thị Quỳnh Hoa2, Lê Văn Vũ3, Nguyễn Ngọc Long3, Phan Văn Độ4
1 Đại học Kiến trúc Hà Nội, Km 10 Nguyễn Trãi, Thanh Xuân, Hà Nội
2 Đại học Xây dựng, 55 Giải Phóng, Hai Bà Trưng, Hà Nội
3
Đại học Khoa học Tự nhiên, 334 Nguyễn Trãi, Thanh Xuân, Hà Nội
4
Đại học Thủy lơi, 175 Tây Sơn, Đống Đa, Hà Nội
*
Email: hahm1982@gmail.com
Các hạt nano LaF3 pha tạp ion Eu
3+
với các nồng độ khác nhau được chế tạo bằng phương
pháp thủy nhiệt. Các phép đo XRD, huỳnh quang và kích thích huỳnh quang được thực hiện tại
nhiệt độ phòng. Tỉ lệ giữa cường độ dải huỳnh quang 5D0→
7
F2 (dipole điện) và
5
D0→
7
F1 (dipole
từ) (R) được sử dụng để đánh giá tính bất đối xứng của trường ligand xung quanh ion Eu3+. Các
thông số Judd – Ofelt được tính toán từ phổ huỳnh quang đã được sử dụng để dự đoán các tính
chất phát xạ của các chuyển dời 5D0→
7
FJ cũng như thời gian sống của mức
5
D0. Giá trị nhỏ của
thông số Ω2 và tỉ số R liên quan đến tính đối xứng cao của trường ligand xung quanh ion Eu
3+
trong vật liệu này.
Từ khóa: tinh thể nano LaF3:Eu
3+, huỳnh quang, phân tích Judd-Ofelt.
Các file đính kèm theo tài liệu này:
- 11810_103810382046_1_sm_669_2061460.pdf