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Optical Spectra Properties and Continuous-Wave Laser Performance of Tm,Y:Ca[F.sub.2] Single Crystals.

1. Introduction

Calcium fluorides, as laser substrates, possess various advantages of large size, high thermal conductivity, well controlled crystal growth processes, and low nonlinear refractive coefficient. Trivalent rare-earth ions, like Tm, Nd, Pr, doped Ca[F.sub.2] crystals behave broad, smooth absorption and emission spectra due to heterovalent substitution of [Ca.sup.2+] within the structure without loss of structural integrity [1]. Various [RE.sup.3+] optical centers could be formed in this fluoride by substituting divalent cation ions, and the excessive charge of rare-earth ions is compensated by interstitial fluorine. The [Nd.sup.3+] doped Ca[F.sub.2] crystal as a laser-pumped-amplifier medium has been abandoned due to a very serious concentration quenching effect which results from the clustering of the neodymium ions and kinds of cross-relaxation type energy transfer processes, which weaken their emission quantum efficiency [2]. However, the [[Nd.sup.3+]-[Nd.sup.3+]] quenching pairs in clusters can be easily dissociated by codoping buffer ions such as [Y.sup.3+] ions [3-8], [La.sup.3+] ions [9], and [Sc.sup.3+] ions [10]. For example, [Nd,Y:CaF.sub.2] crystal, [Y.sup.3+] ions were codoped in [Nd:CaF.sub.2] crystal which substitute for [Ca.sup.2+] forming complicated local structure that performs an effect on spectroscopic properties [8].

As the solid-state lasers medium, the doped [Tm.sup.3+] calcium fluoride crystal proves the potential to achieve efficient compact diode-pumped lasers with an oscillation wavelength near 2 [micro]m which could be directly pumped around 790 nm ([sup.3][H.sub.6] [right arrow] [sup.3][H.sub.4] absorption transition) due to much lower nonradiative losses caused by multiphonon relaxation [11]. Tm ions act both as a sensitizer and activator in a single-doped sample, meaning that a higher concentration is necessary for effective absorption of 800 nm laser excitation. Compared to oxide crystals, pure Ca[F.sub.2] crystal has a thermal conductivity as high as 10 W/cm x K [12] and low phonon energy (maximum value of 495 [cm.sup.-1]) [13], making it very suitable for a laser host crystal and becoming one of the first laser hosts in the early 1960 nm. The predecessors have done some researches on [Tm.sup.3+] doped Ca[F.sub.2] single crystals and found that Tm:Ca[F.sub.2] crystals possessed broadband absorption and emission properties [11,14,15]. The spectroscopic investigation on [Tm.sup.3+] doped crystals indicates that [Tm.sup.3+] ions interactions occur (forming the cross relaxation) at relatively low dopant concentrations (nearly 1%), that is, two excited ions in the [sup.3][F.sub.4] upper ground level 7F6 for one absorbed pump photon. The distinction between isolated and clustered ions is observed in the emission spectra due to different doped concentration. Besides, nonradiative processes related to [sup.3][H.sub.5]-[sup.3][F.sub.4] induced by [Tm-Tm] clusters in the crystals could result in strong heat generation and distortions reducing quantum efficiency [16]. To achieve higher power laser at 2 [micro]m, one of the efficient ways is to prepare Tm:Ca[F.sub.2] with higher Tm deponent concentrations avoiding clustering. However, a spectral region around 1.45 [micro]m associated with a [sup.3][H.sub.4] [right arrow] [sup.3][F.sub.4] optical transition could be vanished when the [Tm.sup.3+] dopant concentration is beyond 1.34% due to [Tm-Tm] clusters [14], and the energy may be absorbed by the ground stated [sup.3][H.sub.6]. However, when the concentration of Tm becomes higher, some other possible ways of energy transfer would occur, such as [sup.1][G.sub.4] + [sup.3][H.sub.4] [right arrow] [sup.3][F.sub.4] + [sup.1][D.sub.2] [17], [sup.3][H.sub.5] [right arrow] [sup.3][H.sub.6] [18], and [sup.3][H.sub.5] + [photo.sub.800 nm] [right arrow] [sup.1][G.sub.4]. Therefore, we take the advantage of [Y.sup.3+] as buffer ions reported in [Nd,Y:CaF.sub.2] [3,8] crystals to prepare the Tm,Y:Ca[F.sub.2] crystals to break the [Tm-Tm] clusters and increase the [Tm.sup.3+] emission intensity as well as efficiency in higher concentration, and the laser performance and wide emission spectrum have been expected. Importantly, the incorporation of [Y.sup.3+] ions to the influences of spectroscopic properties in [Tm.sup.3+] doped Ca[F.sub.2] single crystals had not been investigated systematically.

In this paper, to improve high pump absorption efficiency and high gain per unit length, a series of 3 at.% Tm and x at.% Y:Ca[F.sub.2] crystals have been grown by the vertical Bridgman method, and spectroscopic properties were studied systematically. We have carried out laser experiments and obtained continuous-wave laser output.

2. Experimental

The single crystal samples, namely, 3 at.% Tm, x at.% Y:Ca[F.sub.2] (x = 0, 0.5,1, 2, 3) crystals (at.%, atom percent), were grown by the traditional vertical Bridgman method. High purity fluorides crystalline powders (4N), Ca[F.sub.2], [TmF.sub.3], [YF.sub.3], were used as starting materials, and 1 wt% [PbF.sub.2] was selected as an oxygen scavenger avoiding oxidation and volatilization additionally. These materials were completely mixed by molar ratios and filled into an assembled platinum crucible. The growth parameters are as follows: the temperature of the melt around 130[degrees]C, the pulling rate 0.8mm/h, the cooling rate 20[degrees]C/h. The samples (the same thickness of about 2 mm) were handled with cutting and double-face optically polishing for spectral measurement.

By recording absorption and emission spectra, we investigated the spectroscopic properties of the crystals. The absorption spectra were measured by using a Jasco V-570 UV/VIS/NIR spectrophotometer. The fluorescence spectra and lifetime were obtained with a FLS980 time-resolved fluorimeter with grating blazed at 1820 nm and detected using a Hamamatsu InSb. Measuring of fluorescence spectra was performed under pumping at 808 nm with a CW laser operation. All the measurements were conducted at room temperature.

3. Results and Discussion

3.1. Phase Identification and Crystal Structure. 3 at.% Tm, x at.% Y:Ca[F.sub.2] crystals (x = 0, 0.5,1,2,3) have been analyzed by powder XRD and behave the purity phase Ca[F.sub.2] without any impure peaks as shown in Figure 1(a). The XRD patterns of the crystals have matched well with the JCPDS standard card of Ca[F.sub.2] ICSD 00-075-0363 indicating that the fluorite cubic structure (Fm-3 m) has not been changed by the increasing concentration of yttrium. [Tm.sup.3+] and [Y.sup.3+] ions substitute for [Ca.sup.2+] ions in the Ca[F.sub.2] lattice, and smaller [F.sup.-] ions have taken placed in the interstitial positions of the empty cubes to compensate the charge and maintain electrical neutrality leading to the smaller Bragg's angels and larger lattice parameters which could be distinguished clearly on the enlarged view of (111) in Figure 1(a). The lattice parameters of series of 3 at.% Tm, x at.% Y:Ca[F.sub.2] (x = 0.5,1, 2, 3) single crystals are 5.46785 [Angstrom], 5.46947 [Angstrom], 5.47535 [Angstrom], 5.4763 [Angstrom], respectively, much larger than 5.4559 [Angstrom] of Tm:Ca[F.sub.2], and increase with the rising codoping [Y.sup.3+] ion concentration as shown in Figure 1(b). These observations confirm that [Tm.sup.3+] and [Y.sup.3+] ions had been effectively doped into the host lattice of Ca[F.sub.2].

3.2. Absorption and Emission Properties. The absorption spectra from 500 nm to 2000 nm at room temperature of 3 at.% Tm, x at.% Y are shown in Figure 2(a). Due to various splitting energy levels of [sup.3][H.sub.6] and [sup.3][F.sub.4], the absorption bands have been divided into several peaks. Several main absorption bands, [3.sup][H.sub.6]-[sup.3][F.sub.2] (652 nm), [sup.3][H.sub.6]-[sup.3][F.sub.3] (675 nm), [sup.3][H.sub.6]-[sup.3][H.sub.4] (667 nm, 792 nm), [sup.3][H.sub.6]-[sup.3][H.sub.5] (1135 nm, 1206 nm), [sup.3][H.sub.6]-[sup.3][F.sub.4] (1620 nm, 1668 nm), have been marked in the spectra. Clearly, all the absorption cross sections are increased with the Y ions. Additionally, the absorption [sup.3][H.sub.6]-[sup.3][H.sub.4], which is usually used for diode pumping, inset in the picture has been analyzed in detail at 767 nm and 792 nm in the same bands caused by different emission centers, defined as A-center and B-center.

The largest absorption cross section at 767 nm of 3 at.% Tm, 3 at.% Y:Ca[F.sub.2] improves to 0.45 x [10.sup.-20] [cm.sup.-2], much larger than that reported in [14]. On the other side, the absorption cross section at 792 nm decreases gradually from 0.22 x [10.sup.-20] [cm.sup.-2] to 0.12 x [10.sup.-20] [cm.sup.-2] with the increasing Y ions. Y ions play an important role in modulating spectral performance. The absorption spectra of [Tm.sup.3+] ions can be significantly altered by codoping with [Y.sup.3+] ions. The changeable absorption cross sections indicate that the local structure and symmetry of the calcium fluoride crystal have been modified by changing the amount of deponent codoping [Y.sup.3+] ions. The increasing phenomenon could be attributed to the stronger crystal field caused by interstitial [F.sup.-] ions in the lattice induced by the codoped [Y.sup.3+] separating the [Tm-Tm] clusters, caused by a considerable high doping concentration 3 at.% much larger than 1.34% [11,19], to an appropriate distance and forming A-centers instead of B-centers. By doping [Y.sup.3+] ions, B-center has been broken, forming more A-centers as a result. Anyway, it is clear that codoping Tm:Ca[F.sub.2] with [Y.sup.3+] ions slightly broadens the absorption bands [sup.3][H.sub.6]-[sup.3][H.sub.4], which should be profitable for LD pumping. The broad wavelength tunability indicated an efficient ground-state stark splitting with the introduction of [Y.sup.3+] ions in the as-grown Tm,Y:Ca[F.sub.2] crystal.

The fluorescence spectra of 3 at.% Tm, x at.% Y:Ca[F.sub.2] crystals, corresponding to [sup.3][F.sub.4]-[sup.3][H.sub.6] emission transition of [Tm.sup.3+] around 1.8 [micro]m, excited by 767 nm are reported in Figure 3. The emission spectra of the five crystals consist of four bands, peaking at 1611 nm (6207 [cm.sup.-1]), 1666 nm (6002 [cm.sup.-1]), 1820 nm (5494 [cm.sup.-1]), 1856 nm (5387 [cm.sup.-1]), respectively. The carves of Tm,Y:Ca[F.sub.2] demonstrate several intense separate local maxima compared to the one of the Tm:Ca[F.sub.2], indicating that the [Y.sup.3+] ions codoping modulate the emission spectral structure of [Tm.sub.3+] ions in Ca[F.sub.2] hosts. The emission intensity of 2873 a.u. at 1820 nm of the 3 at.% Tm, 3 at.% Y:Ca[F.sub.2] crystals is 3.4 times higher than that of the 3 at.% Tm:Ca[F.sub.2] crystal (842 a.u.), whose value is the largest above all the samples. As has been discussed in the absorption cross sections, [Y.sup.3+] codoping breaks the [Tm.sup.3+] ion clusters and increases the fluorescence quantum efficiency which could also be proved in Table 1. Additionally, the luminescence intensity of the 1.8 [micro]m band is improved by doping [Y.sup.3+].

Figure 4 shows the logarithm of the emission intensity at 1820 nm of [Tm.sup.3+] as a function of the decay time in 3 at.% Tm, x at.% Y:Ca[F.sub.2] crystals excited by 767 nm at room temperature. The straight lines indicated that the decay was consistent with a first-order exponential and the emission lifetimes were labelled as arrows. The emission lifetimes were fitted to be 6.16 ms, 7.25 ms, 6.53 ms, 7.55 ms, 8.15 ms for 3 at.% Tm, x at.% Y:Ca[F.sub.2](x = 0,0.5,1,2, 3), respectively, which is in the order of 5 ms [11] much shorter than the longer lifetime 15 ms [20]. Due to the higher concentration of [Tm.sup.3+], the emission lifetimes caused by the fluorescence of clustered thulium centers and the tetragonal optical centers are responsible for the longer lifetime 15 ms [11,20]. It also could be discussed that the emission centers with higher symmetry could extend the emission lifetime of the energy level [sup.3][F.sub.4] which could benefit the pump efficiency. The shorter emission lifetime means that in the 3 at.% Tm, x at.% Y:Ca[F.sub.2] crystals, [Tm-Tm] clusters take a dominant station affecting the lifetime of [sup.3][F.sub.4] compared to these tetragonal optical centers. The emission lifetimes of Tm,Y:Ca[F.sub.2] crystals were longer than that of the Tm:Ca[F.sub.2] crystal, indicating clearly that codoping [Y.sup.3+] ions as buffer ions increase the fluorescence lifetime of Tm ions.

3.3. Calculations for Spectral Parameters. In this session, some spectral parameters including the emission cross section [[sigma].sub.em], the radiation lifetimes [[tau].sub.rad], the quantum efficiency [eta], the quality factor [[sigma].sub.em] * [[tau].sub.em], the effective linewidth [DELTA][lambda] have been calculated to measure the quality of these crystals. The emission cross section [[sigma].sub.em] and the radiation lifetimes [[tau].sub.rad] have been calculated by the reciprocity method and the Fuchtbauer-Ladenburg (FL) equation, respectively, and the absorption cross sections [[sigma].sub.abs] could be obtained from the absorption spectra in Figure 2(a).

[[sigma].sub.em]([lambda]) = [[sigma].sub.abs]([lambda]) [Z.sub.l]/[Z.sub.u] exp[hc/[k.sub.B]T(1/[[lambda].sub.ZL] - 1/[lambda])], (1)

where [[lambda].sub.ZL] will be referred to as the "zero line" wavelength ([[lambda].sub.ZL] = 1666 nm wavelength associated with the transition between the lowest stark components of each multiplet [sup.3][H.sub.6] and [sup.3][F.sub.4]) and [Z.sub.l]/[Z.sub.u] represents the ratio of the partition functions of the lower and upper states and the value is 1.512 [14].

[[sigma].sub.em] = [[lambda].sup.4.sub.peak]/8[pi][n.sup.2][DELTA][lambda] x [[tau].sub.rad], (2)

where [[lambda].sub.peak] is the wavelength of the maximum emission intensity (here is 1820 nm) and n stands for the refractive index (the refractive index of calcium fluoride is 1.442 at 1820 nm). We can take advantage of (2) for the value of rrad. In theory, the product of [[sigma].sub.em] and [[tau].sub.rad] is inversely proportional to [DELTA][lambda]. It indicates that the result of the experiment is nearly in agreement with that of the theory. Equation (2) can also be expressed as

[[sigma].sub.em] x [[tau].sub.em] = [[lambda].sup.4.sub.peak]/8[pi][cn.sup.2] x 1/[DELTA][lambda] x [[tau].sub.em]/[[tau].sub.rad] = [[lambda].sup.4.sub.peak]/8[pi][cn.sup.2] x 1/[DELTA][lambda] x [eta], (3)

where [[lambda].sup.4.sub.peak]/8[pi][cn.sup.2] can be regarded as a constant and [eta] is the quantum efficiency. The calculated results have been shown in Table 1 and Figure 5.

The emission cross section [[sigma].sub.em] varies from 1.026 * [10.sup.-20]/[cm.sup.2] to 1.088 * [10.sup.-20]/[cm.sup.2]. The quantum efficiency of emission at 1820 nm is 58.2%, 63.4%, 63.7%, 69.8%, 80.3% for 3 at.% Tm, x at.% Y (x = 0,0.5,1,2,3), respectively. As discussed above, cooping Y ions as buffer ions actually benefit the quantum efficiency increasing the quantum efficiency effectively, indicating that the efficiency of the fluoresce is very sensitive to the cationic coordination [21], and the highest quantum efficiency has been increased to 80.3%.

We can see the difference of [DELTA][lambda] (where [DELTA][lambda] is the effective linewidth which can be obtained by measurement) from Figure 4. The change trend of the effective linewidth at 1820 nm is depicted in Figure 5, which is almost increasing with codoping [Y.sup.3+] ion concentration. [DELTA][lambda] at 1820 nm is 163.97 nm, 178.16 nm, 187.12 nm, 188.37 nm, 190.52 nm for 3 at.% Tm, v at.% Y:Ca[F.sub.2](v = 0, 0.5, 1, 2, 3), respectively, behaving the superiority for LD pumping. Compared with single-doped one, the effective linewidth of the codoping crystals increased rapidly, and the trend turns out to be saturated when the concentration of [Y.sup.3+] grows higher. It indicates that the effect of [Y.sup.3+] concentration on the effective linewidth causes saturation which is in favor of femtosecond laser output.

3.4. Laser Performance. Taking both emission intensity and lifetime into consideration, two samples, 3 at.% Tm:Ca[F.sub.2] and 3 at.% Tm, 3 at.% Y:Ca[F.sub.2], were applied in laser experiments as laser-pumped-amplifier mediums. The size of the crystal is 4 mm x 4 mm x 6 mm and the end faces were optically polished flat and parallel without being coated. The continuous-wave (CW) experiment with a fiber-coupled AlGaAs diode laser as the pump source emitting at 790 nm was carried out at room temperature, and the setup for testing was shown in Figure 6.

In this experiment, the output mirror transmission is 2%, and the folded cavity consisted of three mirrors: M1, M2, and M3, having the same radium of curvature of 10 cm. The pump light was focused into the crystal through a 1: 1 optical imaging module. The pump source was provided by a laser diode around 790 nm. The laser output powers of two samples were depicted in Figure 7, we obtained two different laser curves. To the sample, 3 at.% Tm, 3 at.% Y:Ca[F.sub.2] crystal, its laser slope efficiency and maximum output power of the crystal are 25.3% and 583 mW with the 2% transmission output coupler, while a lower slope efficiency of 15.9% and maximum output power 159 mW were obtained with 3 at.% Tm:Ca[F.sub.2] crystal. The maximum pump power was limited by the absorption capacity of the 3 at.% Tm:Ca[F.sub.2] crystal. We found its excited state absorption tended to be saturated when the absorbed pump power was over 1.6 W. To avoid damage, the absorbed pump power of 3 at.% Tm:Ca[F.sub.2] was set below 1.6 W corresponding to the incident pump power of 3 W, and the absorbed pump power of 3 at.% Tm, 3 at.% Y:Ca[F.sub.2] crystal was set below 2.5 W corresponding to the incident pump power of 4.5 W.

4. Conclusions

The codoping [Y.sup.3+] ions Tm:Ca[F.sub.2] crystals were successfully grown by vertical Bridgman method, and the properties of the series crystals were analyzed systematically. Absorption of [sup.3][H.sub.6]-[sup.3][H.sub.4] is caused by A-center at 767 nm and B-center at 792 nm, and the absorption cross section of A-center is increased while the absorption cross section of B-center is decrease by codoping [Y.sup.3+]. Emission intensity and effective linewidth of emission at 1820 nm are greatly improved when the concentration increased to 3 at.%. The quantum efficiency is enhanced to 80.3% by codoping [Y.sup.3+] ions compared to the undoped crystals. It demonstrates codoping [Y.sup.3+] ions have a positive effect on spectroscopic properties. In laser experiment, we finally obtained a maximum laser output power of 583 mW and slope efficiency of 25.3% in codoped sample.

https://doi.org/10.1155/2018/8592359

Conflicts of Interest

The authors declare that they have no conflicts of interest.

Acknowledgments

This work was financially supported by the National Natural Science Foundation of China (Grants nos. 61422511,61635012, and 61475089) and The National Key Research and Development Program of China (Grant no. 2016YFB0402101).

References

[1] C. R. A. Catlow, A. V. Chadwick, G. N. Greaves, and L. M. Moroney, "Direct observations of the dopant environment in fluorites using EXAFS," Nature, vol. 312, no. 5995, pp. 601-604, 1984.

[2] S. A. Payne, J. A. Caird, L. L. Chase, L. K. Smith, N. D. Nielsen, and W. F. Krupke, "Spectroscopy and gain measurements of [Nd.sup.3+] in Sr[F.sub.2] and other fluorite-structure hosts," Journal of the Optical Society of America B: Optical Physics, vol. 8, no. 4, pp. 726-740, 1991.

[3] T. P. J. Han, G. D. Jones, and R. W. G. Syme, "Site-selective spectroscopy of [Nd.sup.3+] centers in Ca[F.sub.2]:[Nd.sup.3+] and Sr[F.sub.2]:[Nd.sup.3+]," Physical Review B: Condensed Matter and Materials Physics, vol. 47, no. 22, pp. 14706-14723, 1993.

[4] N. E. Kask and L. S. Kornienko, "EPR of [Nd.sup.3+] ions in fluorite," Journal of Experimental and Theoretical Physics, vol. 26, pp. 331-335, 1968.

[5] A. A. Kaminskii, V. V. Osiko, A. M. Prochoro, and Y. K. Voronko, "Spectral investigation of stimulated radiation of [Nd.sup.3+] in Ca[F.sub.2]-[YF.sub.3]," Physics Letters, vol. 22, pp. 419-421, 1966.

[6] K. S. Bagdasarov, Y. K. Voronko, A. A. Kaminskii, L. V. Krotova, and V. V Osiko, "Modification of the optical properties of Ca[F.sub.2]-[TR.sup.3+] crystals by yttrium impurities," Physica Status Solidi, vol. 12, no. 2, pp. 905-912, 1965.

[7] T. T. Basiev, Y. K. Voronko, A. Y. Karasik, V V Osiko, and I. A. Shcherbakov, "Spectral migration of electronic excitation along [Nd.sup.3+] ions in Ca[F.sub.2]-[YF.sub.3] crystal on selective laser excitation," Journal of Experimental and Theoretical Physics, vol. 75, pp. 66-74, 1978.

[8] D. Jiang, Y. Zhan, Q. Zhang et al., "[Nd,Y:CaF.sub.2] laser crystals: novel spectral properties and laser performance from a controlled local structure," CrystEngComm, vol. 17, pp. 7398-7405, 2015.

[9] H. Wang, J. Zhu, Z. Gao et al., "Femtosecond mode-locked Nd,La:Ca[F.sub.2] disordered crystal laser," Optical Materials Express, vol. 6, no. 7, pp. 2184-2189, 2016.

[10] J. Zhang, J. Zhu, J. Wang, Z. Wei, L. Su, and J. Xu, "CW laser performance of Nd-La-Ca[F.sub.2] and Nd-Sc-Ca[F.sub.2] disordered crystals pumped by a laser diode," Acta Photonica Sinica, vol. 45, pp. 114001-1-114001-5, 2016.

[11] M. E. Doroshenko, O. K. Alimov, A. G. Papashvili et al., "Spectroscopic and laser properties of [Tm.sup.3+] optical centers in Ca[F.sub.2] crystal under 795 nm diode laser excitation," Laser Physics Letters, vol. 12, no. 12, Article ID 125701, 2015.

[12] P. J. D. Lindan and M. J. Gillan, "A molecular dynamics study of the thermal conductivity of Ca[F.sub.2] and U[O.sub.2]," Journal of Physics: Condensed Matter, vol. 3, no. 22, pp. 3929-3939, 1991.

[13] V Petit, L. Doualan, P. Camy, V Menard, and R. Moncorge, "CW and tunable laser operation of [Yb.sup.3+] doped Ca[F.sub.2]," Applied Physics B, vol. 78, p. 681, 2004.

[14] P. Camy, J. L. Doualan, S. Renard, A. Braud, V. Menard, and R. Moncorge, "[Tm.sup.3+]:Ca[F.sub.2] for 1.9 [micro]m laser operation," Optics Communications, vol. 236, no. 4-6, pp. 395-402, 2004.

[15] N. M. Strickland and G. D. Jones, "Site-selective spectroscopy of [Tm.sup.3+] centers in Ca[F.sub.2]:[Tm.sup.3+]," Physical Review B: Condensed Matter and Materials Physics, vol. 56, no. 17, pp. 10916-10929, 1997.

[16] J. Ganem and S. R. Bowman, "Use of thulium-sensitized rare earth-doped low phonon energy crystalline hosts for IR sources," Nanoscale Research Letters, vol. 8, p. 455, 2013.

[17] H. Zhang, Y. Li, Y. Lin, Y. Huang, and X. Duan, "Composition tuning the upconversion emission in NaY[F.sub.4]:Yb/Tm hexaplate nanocrystals," Nanoscale, vol. 3, no. 3, pp. 963-966, 2011.

[18] X. Bai, D. Li, Q. Liu, B. Dong, S. Xu, and H. Song, "Concentration-controlled emission in [LaF.sub.3]:[Yb.sup.3+]/[Tm.sup.3+] nanocrystals: switching from UV to NIR regions," Journal of Materials Chemistry, vol. 22, no. 47, pp. 24698-24704, 2012.

[19] P. J. Bendall, C. R. A. Catlow, J. Corish, and P. W. M. Jacobs, "Defect aggregation in anion-excess fluorites II. Clusters containing more than two impurity atoms," Journal of Solid State Chemistry, vol. 51, no. 2, pp. 159-169, 1984.

[20] M. E. Doroshenko, A. G. Papashvili, O. K. Alimov et al., "Specific spectroscopic and laser properties of [Tm.sup.3+] ions in hot-formed Ca[F.sub.2] laser ceramics," Laser Physics Letters, vol. 13, no. 1, Article ID 015701, 2016.

[21] G. Lakshminarayana, R. Yang, M. Mao, J. Qiu, and I. V. Kityk, "Photoluminescence of [Sm.sup.3+], [Dy.sup.3+], and [Tm.sup.3+]-doped transparent glass ceramics containing Ca[F.sub.2] nanocrystals," Journal of Non-Crystalline Solids, vol. 355, no. 52-54, pp. 2668-2673, 2009.

Jingxin Ding, (1,2) Beibei Zhao, (1) Weiwei Ma, (1) Hao Yu, (1) Xiaobo Qian, (1) Lingchen Kong, (3) Jingya Wang, (1) Guoqiang Xie [iD], (3) Anhua Wu, (1) Fanming Zeng, (2) and Liangbi Su [iD] (1,4)

(1) Synthetic Single Crystal Research Center, Key Laboratory of Transparent and Opto-Functional Inorganic Materials, Shanghai Institute of Ceramics, Chinese Academy of Sciences, Shanghai, China

(2) School of Materials Science and Engineering, Changchun University of Science and Technology, Changchun 130022, China

(3) Key Laboratory for Laser Plasmas (Ministry of Education), Collaborative Innovation Center of IFSA (CICIFSA), Department of Physics and Astronomy, Shanghai Jiao Tong University, Shanghai 200240, China

(4) State Key Laboratory of High Performance Ceramics and Superfine Microstructure, Shanghai Institute of Ceramics, Chinese Academy of Sciences, Shanghai, China

Correspondence should be addressed to Liangbi Su; suliangbi@mail.sic.ac.cn

Received 12 August 2017; Revised 19 November 2017; Accepted 13 December 2017; Published 23 January 2018

Academic Editor: Wonho Jhe

Caption: Figure 1: The XRD patterns (a) and lattice parameters (b) of 3 at.% Tm, % at.% Y:Ca[F.sub.2] crystals.

Caption: Figure 2: Absorption spectra (a) and energy level diagrams (b) of 3 at.% Tm, x at.% Y:Ca[F.sub.2] crystals at 300 K.

Caption: Figure 3: Fluorescence spectra for [sup.3][F.sub.4]-[sup.3][H.sub.6] transition of 3 at.% Tm, x at.% Y Ca[F.sub.2] crystals at 300 K.

Caption: Figure 4: Fluorescence lifetimes of energy level [sup.3][F.sub.4] of 3 at.% Tm, x at.% Y:Ca[F.sub.2] crystals.

Caption: Figure 5: [[tau].sub.rad] * [[sigma].sub.em] and AA obtained from 3 at.% Tm, % at.% Y:Ca[F.sub.2] crystals.

Caption: Figure 6: Schematic of the experimental setup for 1.8 [micro]m laser operation.

Caption: Figure 7: Laser output power versus absorbed pump power curve for 3 at.% Tm:Ca[F.sub.2] and 3 at.% Tm, 3 at.% Y:Ca[F.sub.2] crystals.
Table 1: The detailed values of [[sigma].sub.abs], [[sigma].sub.em],
[[tau].sub.rad], [[tau].sub.em], [eta] of 3 at.% Tm, a
at.% Y:Ca[F.sub.2] at 1820 nm.

Crystals             [[sigma].sub.abs]/    [[sigma].sub.em]/
                         [cm.sup.2]            [cm.sup.2]

3 at.%                     0.063          1.206 * [10.sup.-20]
Tm:Ca[F.sub.2]
3 at.% Tm, 0.5             0.054          1.026 * [10.sup.-20]
at.% Y:Ca[F.sub.2]
3 at.% Tm, 1               0.057          1.090 * [10.sup.-20]
at.% Y:Ca[F.sub.2]
3 at.% Tm, 2               0.054          1.026 * [10.sup.-20]
at.% Y:Ca[F.sub.2]
3 at.% Tm, 3               0.056          1.088 * [10.sup.-20]
at.% Y:Ca[F.sub.2]

Crystals             [[tau].sub.rad]/   [[tau].sub.em]/    [eta]/%
                            ms                 ms

3 at.%                    10.58               6.16          58.2
Tm:Ca[F.sub.2]
3 at.% Tm, 0.5            11.43               7.25          63.4
at.% Y:Ca[F.sub.2]
3 at.% Tm, 1              10.24               6.53          63.7
at.% Y:Ca[F.sub.2]
3 at.% Tm, 2              10.82               7.55          69.8
at.% Y:Ca[F.sub.2]
3 at.% Tm, 3              10.14               8.15          80.3
at.% Y:Ca[F.sub.2]
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Title Annotation:Research Article
Author:Ding, Jingxin; Zhao, Beibei; Ma, Weiwei; Yu, Hao; Qian, Xiaobo; Kong, Lingchen; Wang, Jingya; Xie, G
Publication:International Journal of Optics
Date:Jan 1, 2018
Words:4823
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