- freely available
Materials 2014, 7(1), 496-507; doi:10.3390/ma7010496
Abstract: Tm3+:Li3Ba2Gd3(MoO4)8 crystal has been grown by the top seeded solution growth (TSSG) method from a Li2MoO4 flux. The room temperature polarized absorption spectra, fluorescence spectra, and fluorescence decay curves of the crystal were measured. Based on the Judd-Ofelt (J-O) theory, the main spectroscopic parameters of the crystal, including the spontaneous emission probabilities, fluorescence branching ratios, and radiative lifetimes were calculated and analyzed. The broad and strong absorption bands of the crystal show that it can be efficiently pumped by the diode laser, while the large emission cross-sections of the 3F4 → 3H6 transition indicate that the crystal is a promising candidate for tunable and short pulse lasers.
With the rapid progress of high power diode lasers, Tm3+-doped laser media has been intensively investigated because of their potential applications associated with emissions in the visible and infrared spectral regions, particularly at ~1.50 and ~2.0 μm wavelength. As we know, the 3F4 → 3H6 transition of Tm3+ ions is one of the most effective channels for the development of 2.0 μm lasers, which have many important applications in fields of medicine, gas detection, remote sensing, etc. On the other hand, the 3H4 → 3F4 transition of Tm3+ ions gives rise to an additional infrared emission band around 1.5 μm, where applications such as detection, ranging and optical communication have been found. Other important advantages of Tm3+ ions include strong absorption of AlGaAs diode laser radiation at ~800 nm, a long lifetime of the 3F4 state, a high quantum efficiency due to the cross-relaxation between 3H4 and 3F4 multiplets, as well as a wide emission band around in the range of 1800–2000 nm, which is definitely promising for the generation of tunable and ultrafast solid state lasers. To date, efficient laser operations around 2.0 μm have been realized in a number of Tm3+-doped crystals [1–10].
Among the reported crystals, the double tungstate and molybdate crystals with scheelite structure are characterized by their local disordered crystal structure [4–8]. The advantages of these crystals are high quantum efficiency, broad absorption and emission brands, as well as relatively low upper-level lifetime. Furthermore, such a combination of these merits is very promising for generations of tunable and ultra fast lasers. More recently, a new series of disordered molybdate compounds Li3Ba2Re3(MoO4)8 (Re = La-Lu, Y), which belong to the monoclinic system, with the space group C2/c, have emerged as new kinds of laser materials, especially in tunable and ultrafast laser domains [11–17]. The structure of Li3Ba2Re3(MoO4)8 can also be considered to be derived from the scheelite structure, in which the Ca2+ sites are occupied by a statistical mixture of 25% Ba2+, 37.5% Li+, and 37.5% Re3+ . Consequently, rare earth doped Li3Ba2Re3(MoO4)8 crystals usually exhibit very similar spectral properties to the typical disordered double molybdate crystals. Up to now, efficient laser operation has already been realized in Nd3+ and Yb3+-doped Li3Ba2Gd3(MoO4)8 crystals [11,13]. Not long ago, Zaldo et al.  have demonstrated the great potential of Tm3+:Li3Ba2Lu3(MoO4)8 crystal for tunable and ultrashort pulse lasers around 2 μm, i.e., a tunable laser in the range of 1853–2009 nm, with a slope efficiency up to 71%, higher than those obtained in disordered crystals so far, has been obtained with a Ti:laser as pump source. Furthermore, the large free running laser bandwidth indicated that the Tm3+:Li3Ba2Lu3(MoO4)8 crystal is definitely promising for generations of ultrafast laser pulses. In the present work, the studies are extended to Tm3+-doped Li3Ba2Gd3(MoO4)8 crystal with the objective of exploring new Tm3+-doped crystal for efficient laser operations near 2 μm, and the growth and spectral properties of Tm3+:Li3Ba2Gd3(MoO4)8 crystal are reported.
2. Experimental Section
2.1. Crystal Growth and Orientation
As Li3Ba2Gd3(MoO4)8 crystal melts incongruently , the crystal was grown by the top seeded solution growth (TSSG) method from a flux of Li2MoO4. The solubility curve of Li3Ba2Gd3(MoO4)8 crystal in the Li3Ba2Gd3(MoO4)8-Li2MoO4 solution can be found in Reference . The crystal growth was carried out in a vertical tubular muffle furnace with a nickel–chrome wire as the heating element. An AL-708 apparatus controlled the furnace temperature and the rate of cooling. The starting materials, 3 at% Tm3+-doped Li3Ba2Gd3(MoO4)8 and Li2MoO4 were weighed, with a molar ratio of TmLi3Ba2Gd3(MoO4)8:Li2MoO4 = 1:4. A single-crystalline bar cut along b-direction was used to introduce crystal nucleation. The growth temperature interval was 900–870 °C, with a cooling rate of 1 °C/d and a rotating rate of 12 rpm. Additional details on crystal growth can be found in Reference [14,15]. The as-grown Tm3+:Li3Ba2Gd3(MoO4)8 crystal with a prism shape is shown in Figure 1a. The initial dimension of the grown crystal is about 15 × 10 × 40 mm3 along the a, b, and c-directions, respectively. However, due to the cleavable nature of the crystal, the grown crystal has split along the middle along the cleavage plane (001) during the annealing process. As a result, only a small part of the obtained crystal is shown in Figure 1a. Figure 1b shows the morphological scheme of the grown crystal. The rectangular facets on the top and bottom of the crystal were established to be (010) and (0−10) faces, respectively, which are consistent with those of the Li3Ba2Lu3(MoO4)8 crystal . However, different from the Li3Ba2Lu3(MoO4)8 crystal, the facets along sides of the crystal were identified to be (110) and (−110) faces, respectively, rather than (100) and (−100) faces. As a consequence, the grown crystal possesses a trapezoid cross-section, as shown in Figure 1c. It can be found that the profile of the (00−1) face of the Tm3+:Li3Ba2Gd3(MoO4)8 crystal is in good accordance with that of the Yb3+:Li3Ba2Gd3(MoO4)8 and Er3+:Li3Ba2Y3(MoO4)8 crystal grown along the a-direction [12,15].
As the Li3Ba2Gd3(MoO4)8 crystal is biaxial, the three principal axes of the optical indicatrix should be determined before the polarized spectral measurement. In the monoclinic system, one of the principal axes is collinear with the crystallographic b-axis and the other two principal axes are perpendicular and positioned at certain angles with respect to crystallographic a and c-axes. Then, the other two principal axes can be easily determined when the sample is viewed along the b-axis direction under a polarized microscope. However, due to the restriction of the test conditions, the precise values of the refractive index for the three principal axes were not measured. As the cell parameters and the positions of the three principal axes relative to the crystallographic axes are very close to the Li3Ba2Lu3(MoO4)8 crystal, the three principal axes are temporarily named in the same way as the Li3Ba2Lu3(MoO4)8 crystal [16,17]. As shown in Figure 1a, the principal axis collinear with the crystallographic b axis is named as b′; a′ is rotated at 18° with respect to a axis in the clockwise direction as the crystals are viewed from the negative b axis, finally, c′ is perpendicular to a′ and b′.
The polarized absorption spectra were measured using a Perkin–Elmer UV-VIS-NIR spectrometer (Lambda-900) in a wavelength range of 300–2000 nm, the wavelength resolution of which is 0.08 nm. The polarized fluorescence spectra and the fluorescence decay curves were measured using an Edinburgh Instruments FLS920 spectrophotometer, the wavelength resolution of which is 0.2 nm. The concentration of Tm3+ ions in the Tm3+:Li3Ba2Gd3(MoO4)8 was measured to be 1.26 at% by the ICP atomic emission spectroscopy analysis method. Thus, the corresponding concentration and the segregation coefficient of Tm3+ ions in the grown crystal were 6.3 × 10−19 cm2 and 0.42, respectively. All the above measurements were carried out at room temperature.
3. Results and Discussion
3.1. Absorption Spectra and Judd-Ofelt Analysis
Figure 2 shows the polarized absorption spectra of Tm3+:Li3Ba2Gd3(MoO4)8 crystal measured at room temperature. For all polarizations, strong absorption bands occur around 475, 690, 800, 1200, and 1750 nm, corresponding to the transitions of Tm3+ ions from the ground state 3H6 to the excited states 1G4, 3F2,3 3H4, 3H5, and 3F4, respectively. The most attractive band of the absorption spectra is the one around 800 nm, which belongs to the 3H6 → 3H4 transition and is the main pumping channel for Tm3+ ions. The inset of Figure 2 shows the absorption cross-sections σabs of this band for clarity. As this band is composed of several overlapped peaks, a Lorentz fit was applied to it and three peaks, around 785, 796, and 805 nm, were found. For all polarizations, the peak absorption cross-sections are located at 796 nm and the values are 4.08, 2.59, and 3.55 × 10−20 cm2 for E//a′, E//b′, and E//c′, respectively. The full width at half the maximum (FWHM) of the 796 nm absorption peaks are 9, 11, and 8 nm for E//a′, E//b′, and E//c′, respectively, which are close to those of other disordered molybdate crystals, such as Tm3+:LiLa(MoO4)2 (8 nm for σ polarization) , Tm3+:LiGd(MoO4)2 (8 nm for σ polarization) , and Tm3+:Ba2Gd4(MoO4)4 (7 nm for E//X and 8 nm for E//Y) , but much larger than those of ordered Tm3+:YAG (4 nm) , Tm3+:YVO4 (5 nm for π polarization) , and Tm3+:KY(WO4)2 (5.4 nm for E//Nm) crystals . Such a broad bandwidth indicates an inhomogeneous broadening behavior of Tm3+:Li3Ba2Gd3(MoO4)8 crystal and make the crystal very suitable for diode pumping, as the thermal stabilization of pumping source is not so critical in this case. Furthermore, it can be found that both the profile and the intensity of the absorption bands of Tm3+:Li3Ba2Gd3(MoO4)8 are similar to those of the isostructural Tm3+:Li3Ba2Lu3(MoO4)8 crystal .
The Judd-Ofelt (J-O) theory has been widely used in the analysis of the spectroscopic properties of rare-earth ions in crystals and glasses [18,19] According the J-O theory, the Judd-Ofelt parameters Ωt (t = 2, 4, 6) for each polarization can be calculated by a least-square fitting between the theoretical and the experimental line strengths for the electric-dipole transitions. Then, the spontaneous emission probabilities of the electric-dipole Aed and magnetic-dipole Amd transitions, the fluorescence branching ratios β and the radiative lifetime τr can be estimated. In the present work, only the calculated results are presented, and the detailed calculation procedures are similar to those reported in Reference . The values of the refractive index, n, at different wavelengths were calculated using the Sellmeier Equations:
where the constants A, B, C, and D for the three polarizations were derived from Reference .
The values of Aed, Amd, β, and τr of some typical transitions are listed in Table 1.
3.2. Fluorescence Spectra and Emission Cross-Sections
Figure 3 shows the polarized emission spectra of Tm3+:Li3Ba2Gd3(MoO4)8 crystal in a range of 600–1600 nm, when the samples were excited into the 1G4 state with 475 nm radiation. There are four main emission bands around 650, 800, 1175, and 1450 nm for each polarization. The emission bands around 650, 1175, and 1450 nm can be assigned to the 1G4 → 3F4, 1G4 → 3H4, and 3H4 → 3F4 transitions, respectively. The emission band around 800 nm should be the superposition of two resonant transitions, namely 1G4 → 3H5 and 3H4 → 3H6, which were severely overlapped due to the very close barycentric wavelengths. To confirm the conclusion, the polarized emission spectra were also measured under 688 nm excitation, i.e., the Tm3+ ions were excited to the 3F2,3 states. In this case, the 3H4 state was populated through non-radiative relaxation from the 3F2,3 states and later on depopulated directly to the 3H6 ground state, giving rise the emissions at 800 nm as shown in Figure 3b. Then, it can be concluded that the weaker emission at 785 nm in Figure 3a belongs to the 1G4 → 3H5 transition.
The stimulated emission cross-sections of the 3H4 → 3F4 transition around 1.5 μm were calculated from the fluorescence spectra using the Füchtbauer-Ladenburg(F-L) formula :
where c is the speed of light in the vacuum; Iq(λ) is the relative fluorescence intensity at wavelength λ. Then, the emission cross-sections for three polarizations are shown in Figure 4. For E//b′, the peak emission cross-sections are 1.25 × 10−20 cm2 at 1452 nm. For E//a′ and E//c′, the peak emission cross-sections are located at 1495 nm and the values are 9.16 × 10−21 cm2 and 1.12 × 10−20 cm2, respectively. The 3H4 → 3F4 transition of the Tm3+ ions has provided a promising approach to achieve 1.5 μm lasers in a more efficient four-level laser operation scheme than the Er3+ ions. However, their practical applications at this wavelength are inevitably restricted by a detrimental bottlenecking effect because the lifetime of the 3F4 state is generally much longer than that of the 3H4 state. As a result, to achieve laser operation via 3H4 → 3F4 transition, some codopants, such as Ho3+, Yb3+, and Tb3+ should be introduced as deactivator to depopulate the 3F4 state .
Due to the restriction of the test conditions, only the uncalibrated emission spectra of the 3F4 → 3H6 transition, around 2 μm, were obtained, as shown in Figure 5. Thus, the emission cross-sections of this transition were calculated from the absorption spectra according to the reciprocity method :
where k is the Boltzmann’s constant; Zl and Zu are the partition functions of lower and upper states, respectively; Ezl is the zero-line energy defined as the energy separation between the lowest Stark levels of the upper and lower multiplets. However, the precise energy level diagram of Tm3+ ions in Li3Ba2Gd3(MoO4)8 crystal is not available now. Therefore the values of Zl/Zu and Ezl were roughly taken as Zl/Zu = 1.42 and Ezl = 5600 cm−1 (0.694 eV), respectively, in agreement with those of the isostructural Tm3+:Li3Ba2Lu3(MoO4)8 crystal . Then, the emission cross-sections are obtained and listed in Figure 5 combining with the corresponding absorption cross-sections. For all polarizations, the peak emission cross-sections are located at 1796 nm and the values are 2.38, 2.27, and 2.05 × 10−20 cm2 for E//a′, E//b′, and E//c′, respectively, which are larger than those of other disordered molybdate crystals (see Table 2). Furthermore, the FWHMs of the emission cross-sections are 133, 154 and 136 nm for E//a′, E//b′, and E//c′, respectively, which are similar to those of other disordered molybdate crystals in Table 2.
From the absorption and emission cross-sections calculated by the reciprocity method, the gain cross-section, σg, can be calculated according to the following equation:
where β is the ratio of the number of the excited Tm3+ ions to the total number of Tm3+ ions; σem and σabs are the emission and absorption cross-sections, respectively. The calculated gain cross-sections for several values of β are shown in Figure 6. According to Figure 6, a minimum inversion ratio of 0.1 is needed to achieve laser operations. For an inversion ratio of β = 0.3, a tunable range wider than 180 nm is possible for all polarizations.
The fluorescence decay curve of the 3H4 and 3F4 state was recorded by monitoring the emissions of the 3H4 → 3F4 and 3F4 → 3H6 transitions at 1500 and 1900 nm under excitation at 800 and 1730 nm, respectively. The decay curve of the 3H4 state exhibits a single exponential behavior as shown in Figure 7. The lifetime is obtained to be 153 μs by linear fitting, which is close to the radiative one. The high quantum efficiency η (τf/τr) of the 3H4 state means the cross-relaxation is inefficient in the crystal due to the low Tm3+ concentration. The lifetime of 3F4 state for the bulk crystal is measured to be 1.62 ms and much larger than the calculated radiative lifetime. Such a large discrepancy is mainly caused by the re-absorption effect, which has been widely observed in Tm3+-doped crystals [8,16]. To obtain the intrinsic lifetime of the 3F4 state, the powder method was adopted in this work . A piece of bulk crystal was grounded into fine particles and diluted to a lower concentration of 0.25 at% (1.25 × 10−19 cm2) with the powder of pure Li3Ba2Gd3(MoO4)8 crystal. Then, the powder was immersed into ethylene glycol (EG), which was used as refractive index matching fluid to reduce the internal reflection within the particles. The fluorescence lifetime of the powder sample was measured to be 0.92 ms, in reasonable agreement with the radiative one calculated by the J-O theory.
A Tm3+:Li3Ba2Gd3(MoO4)8 crystal has been successfully grown by the top seeded solution growth (TSSG) method, and the detailed spectral properties of the crystal were characterized and investigated on the basis of the J-O theory. The main spectral parameters of the crystal are listed in Table 2 and compared with other Tm3+-doped crystals. It can be found that Tm3+:Li3Ba2Gd3(MoO4)8 crystal possesses similar spectral characters to other disordered molybdate crystals, i.e., all of them exhibited broad optical bands, large absorption and emission cross-sections, as well as long lifetimes of 3F4 state. In summary, the main spectroscopic parameters of the Tm3+:Li3Ba2Gd3(MoO4)8 crystal are comparable to those of the Tm3+:Li3Ba2Lu3(MoO4)8 crystal. As a consequence, in view of the excellent laser performance of the Tm3+:Li3Ba2Lu3(MoO4)8 crystal , we may expect the Tm3+:Li3Ba2Gd3(MoO4)8 crystal to be a potential solid state laser material at ~2.0 μm.
This work was supported by the Natural Science Foundation of Shandong Province (ZR2010BL011) and the Science Foundation of Weifang University.
Conflicts of Interest
The authors declare no conflict of interest.
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|Transitions||λem (nm)||E//a′||E//b′||E//c′||β||τr (μs)|
|Aed + Amd (s−1)||Aed + Amd (s−1)||Aed + Amd (s−1)|
|1G4 → 3H6||477||5035.7||5474.1||4258.7||0.56||113|
|3F4||649||345.8 + 13.8||580.8 + 13.9||388.7 + 12.8||0.05|
|3H5||780||2031.8 + 207.2||2334.7 + 208.7||1936.4 + 192.4||0.26|
|3H4||1170||993.1 + 47.3||925.3 + 47.7||839.2 + 44.03||0.11|
|3F3||1485||93.2 + 3.8||173.7 + 3.9||113.2 + 3.6||0.02|
|3H4 → 3H6||785||5544.6||5597.5||4792.5||0.90||170|
|3F4||1430||469.8 + 26.8||497.8 + 27.1||407.2 + 25||0.08|
|3H5||2165||47.9 + 14||131.5 + 14.2||62.8 + 13||0.02|
|3H5 → 3H6||1225||676.0 + 117||969.5 + 118||671.6 + 108.9||0.99||1110|
|3F4||3825||12.8 + 0.16||15.2 + 0.16||10.9 + 0.14||0.01|
|3F4 → 3H6||1800||970.0||1040.0||791||1.00||1070|
|λabs (nm)||796||795 (σ)||795||798||797 (a′)|
|–||796 (π)||–||–||782 (b′)|
|σa (10−20 cm2)||4.08 (a′)||4.33 (σ)||4.04 (σ)||2.5 (X)||3.8 (a′)|
|2.59 (b′)||1.59 (π)||1.53 (π)||3.5 (Y)||2.7 (b′)|
|3.55 (c′)||–||–||2.1 (Z)||3.1 (c′)|
|FWHM (nm)||9 (a′)||8 (σ)||8 (σ)||7 (X)||8 (a′)|
|11 (b′)||37 (π)||36 (π)||8 (Y)||12 (b′)|
|8 (c′)||–||–||17 (Z)||8 (c′)|
|λe (nm)||–||1786 (σ)||1787 (σ)||1800 (X)||1800 (a′)|
|1796||1838 (π)||1837 (π)||1805 (Y)||1812 (b′)|
|–||–||–||1819 (Z)||1805 (c′)|
|σem (10−20 cm2)||2.38 (a′)||2.44 (σ)||1.48 (σ)||1.3 (X)||2.65 (a′)|
|2.27 (b′)||2.07 (π)||1.61 (π)||1.8 (Y)||2.30 (b′)|
|2.05 (c′)||–||–||1.3 (Z)||2.25 (c′)|
|FWHM (nm)||133 (a′)||175 (σ)||143 (σ)||110 (X)||90 (a′)|
|154 (b′)||160 (π)||164 (π)||84 (Y)||168 (b′)|
|136 (c′)||–||–||200 (Z)||137 (c′)|
|τf of 3F4 (ms)||0.92||0.93||1.29||–||0.97|
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