Abstract
We present a generally applicable theoretical model describing excited-state decay lifetime analysis of metal ions in a host crystal matrix. In contrast to common practice, we include multi-phonon non-radiative transitions competitively to the radiative one. We have applied our theory to Co2+ ions in a mixed AgCl0.5Br0.5 crystal, and as opposed to a previous analysis, find excellent agreement between theory and experiment over the entire measured temperature range. The fit predicts a zero absolute temperature radiative lifetime τrad(0) = 5.5 ms, more than three times longer than the measured effective low-temperature one τeff(0) = 1.48 ms. Furthermore, the fit configuration potential dissociation energy has been estimated as D = 2500 cm−1 and the lattice vibrational cutoff frequency as ħωco = 180 cm−1. We have experimentally verified the latter by optical reflection measurement in the far-IR.
© 2018 Optical Society of America under the terms of the OSA Open Access Publishing Agreement
1. Introduction
A very large part of laser science and technology involves the study of solid-state lasers. Generally, solid-state laser gain materials are composed of a host material doped with active metallic ions. Laser action stems from stimulated transitions between electronic states of the active ions. The host material holds the ions in their respective positions. However, the host itself, via interaction with the active ions, has an important impact on the lasing process. This includes gain shifting, splitting, broadening, and enabling of heat dissipation; in some cases also assisting in draining the lower laser state to the ground state. A considerable drawback is the host effect in shortening the effective excited state lifetime via non-radiative multi-phonon transitions. One expects these processes to turn more significant at longer transition wavelengths.
Recently, there was a significant resurgence of interest in transition metal ions for ultrafast lasers in the near and mid-IR [1, 2]. Thus, understanding the effect of host matrix on the active lasing ions in general, and its effective lifetime in particular, is of fundamental significance and of utmost importance for laser physics.
In this respect, a large number of studies, both theoretical and experimental, have been devoted to the non-radiative, multi-phonon transition subject. It has been rightfully assumed that low energy transitions are dominantly non-radiative. Many theoretical studies formulated the problem in “first principles” terms, yet the expressions obtained are cumbersome and agreement with experiment is rather poor (see [3,4] and the references cited therein). Researchers often resorted to gross simplifications and assumptions, and use of simplistic empiric expressions, to enable comparison with actual physical systems. In most treatments [5–9], empiric fit parameters assigned to the host material effects exhibit no specific relation with the matrix fundamental physical properties. In the limit of high energy transitions (e.g. in the short wavelength of the visible spectrum) it is reasonable to assume that the host vibrational effects are limited only to state broadening. However, hitherto the adequate theoretical foundation in the intermediate energy transition range (the mid- and far-infrared) is yet lacking. This important energy range still awaits a comprehensive treatment.
Generally, radiative and non-radiative transitions are simultaneously operative. In other words, any atom or ion in an excited state may “select” to decay by either of the above mechanisms according to its relative probability. In Burshtein’s paper [10], it has been pointed out that radiative and non-radiative transitions are both proportional to the transitions oscillator strength f. Therefore, for the same ion and matrix, states exhibiting a faster radiative transition, simultaneously exhibit a faster non-radiative one. Furthermore, a specific expression for the non-radiative multi-phonon transition rate has been developed [10]. It relates directly to the fundamental host material properties, specifically: mass density, unit-cell dimensions, vibrational cutoff frequency, and configuration potential dissociation energy.
In the present paper, we start by modeling a simple two level transition system. Next we generalize the treatment to more realistic scenarios, where the lower and/or upper levels consist of sub-level multiplets. We then apply the modeling to recently published experimental results on Co2+ ions in a mixed AgCl0.5Br0.5 crystal [11], and obtain an excellent fit over the entire temperature range. Consequently, we obtain a prediction for the radiative lifetime at zero absolute temperature, as well as the lattice cutoff vibrational frequency. We validate the latter experimentally by optical reflection measurements in the far-IR.
2. Theoretical background
2.1. A two-state system
In Fig. 1 we show a schematic view of a two-state system with an occupied excited-state |2〉, undergoing simultaneously competing radiative and a multi-phonon non-radiative decay to the lower |1〉 state. For a homogeneously broadened emission, the zero-temperature T = 0 limit of the radiative decay rate is given by [10, 12]:
where n is the ion host matrix refractive index, ν0 is the central radiative transition frequency, c is the vacuum speed of light constant, and σem is the frequency-dependent radiative transition cross section of the emission band (the fluorescence band). In the following we denote Eg = hν0 = E2 − E1, to be termed “the energy gap”. In principle, the radiative decay rate is temperature dependent, stimulated by thermal photons. We shall address this issue specifically later on, to see that under a broad range of physical conditions of interest, this contribution may be safely ignored.The transition oscillator strength is given by [10]:
where m is the electronic mass and e is the electron charge. One then gets Following [10], the zero-temperature multi-phonon non-radiative transition rate is given by where ωco is the cut-off angular frequency of the matrix vibrations (phonons), D is the characteristic dissociation energy of a Morse-type configuration potential [13] (related to the primitive unit cell vibrating at ωco), a3 is the primitive unit cell volume, ρM is the host material mass density, Nc is the number of atoms occupying the unit cell (correspondingly forming the ligand for each embedded ion). We now replace the expression by , where is the average unit cell atomic mass. For a unit cell containing a large number of atoms, this expression simply reduces to . The ratio υ ≡ Eg/ħωco represents the number of ħωco phonons involved in the non-radiative transition. The B(υ) function specified in Eq. (5) below is a υ-dependent numerical factor. Its presence in Eq. (4) stems from expansion to a Taylor series of the assumed lattice configuration potential, as well as from other model assumptions for the υ-order multi-phonon induced transitions [10]. It is shown graphically in Fig. 2 between υ = 1 and υ = 16:Note that υ is not necessarily an integer. It is a manifestation of the physical fact that lattice vibrations exhibit broad bands, practically covering the entire phonon energy scale up to ħωco. The ratio D/ħωco may be considered a measure of the deviation from harmonicity of the lattice vibrations, which allows phonon involvement in transitions between electronic states. In a perfectly harmonic potential, the D/ħωco ratio is infinite; mathematically, in that limit the non-radiative transition rate diminishes (Eq. (4)).
Setting Eq.’s (3) expression for f in (4), one gets
Hence, the combined upper state decay rate at the zero temperature limit is given by: where is the non-radiative contribution constant to the decay rate between the states. Note, that in the T → 0 limit, τrad(0)/τeff (0) = 1 + Cnr(Eg, ħωco, D).Notably, the non-radiative constant Cnr employs parameters related to the specific host material properties, and the actual transition in the ion. Particularly, it is inversely proportional to the squared energy gap . Naturally ħωco ≪ D; then Cnr reduces steeply as function of the number of phonons required for non-radiative decay (last factor in Eq. (8)).
For a finite absolute temperature T, the effective fluorescence decay rate becomes
The [exp (Eg/kBT) − 1]−1 addend inside the square brackets accounts for the thermal enhanced population effect of Eg-energy photons. The factor (recall that υ = Eg/ħωco), accounts for the thermal enhanced population effect of ħωco-energy phonons by the υ-phonon transition mechanism; see [14] equation (7) and [10] equation (70), and related text. For not too far-infrared energies, say Eg ≳ 2, 000 cm−1, and not too high temperatures, say T ≲ 900 K, the thermal photon population effect is negligibly small (in that particular limit it amounts to only ∼ 0.035 ≪ 1). For simplicity and brevity, we hereby ignore it. Equation (9) then reduces to
Apparently, for the two-state system of Fig. 1 under normal conditions, the major contribution capable of shortening the effective fluorescence lifetime τeff upon increased temperature T is non-radiative.
2.2. A single state to a multiplet decay system
In Fig. 3 we show a schematic view of a multi-state system with an occupied single excited-state, undergoing simultaneously competing radiative, and multi-phonon non-radiative decays to a lower states multiplet. Numbering of the latter states starts from ℓ = 0 for the lowest energy one. The analysis is based on the measured low-temperature limit of the fluorescence shape. Let gem(ν) be the fluorescence emission shape of a unity integral, which resolves into single-peak components (Gaussian, Lorentzian, or others) representing the different ℓ-state components, where . We then denote ; obviously, .
The effective fluorescence lifetime is determined by the weighted summation on all the transition lifetimes between the upper states and all the states of the lower multiplet. Hence, the expression for the effective fluorescence lifetime becomes
where υ(ℓ) ≡ Egℓ/ħωco, andNote, that in the T → 0 limit, . The fluorescence quantum efficiency would correspondingly be
The dominant non-radiative contribution to the effective decay rate is usually the largest ℓ transition (smallest energy gap). If gaps among the multiplet states are large, the effective system reduces to a two-state case, per section 2.1.
2.3. A higher to a lower multiplet decay system
In Fig. 4 we show a schematic view of a multi-state system with an occupied excited upper states multiplet, undergoing simultaneously competing radiative and multi-phonon non-radiative decays to a lower states multiplet. Numbering of the lower multiplet states starts upwards in energy from ℓ = 0 of the lowest energy one. Numbering of the upper multiplet states starts upward in energy from u = 0∗ for the lowest energy one. The occupation statistics of the upper multiplet is assumed to follow a quasi-thermal equilibrium distribution (effected by very fast, mostly non-radiative transitions among those states). du indicates the degeneracy of an upper multiplet u-state, and Eu its energy relative to E0∗. The figure describes decay transitions from both lowest and first thermally occupied state of the upper multiplet.
The analysis is based on the measured low-temperature limit of the absorption cross section and fluorescence shapes spectra, as follows:
- Let σabs(ν) be the absorption cross-section spectrum from the ground (ℓ = 0) lower multiplet state to the entire upper multiplet. The spectral shape resolves into single-peak components (Gaussian, Lorentzian, or others), representing the different u-state components, such that . We denote ; obviously, . An underlying assumption in the following analysis is that the radiative decay rate from any u-state to the lower multiplet ones is proportional to the u-state “absorption strength” S0,u.
- The lower multiplet states characteristics are identical with those of Fig. 3. The actual radiative decay rate from any u-state to the entire lower multiplet is now also temperature dependent, related to the relative thermal occupation of the u-state. Under quasi thermal equilibrium conditions, it would be given by
Notably, increased temperature also affects the fluorescence spectral shape by added emission of higher energy photons [10]. Analysis of this important spectral effect, however, is beyond the scope of our present paper.
The dominant, both radiative and non-radiative contributions to the effective decay rate is usually the smallest u transition (smallest set of energy gaps). If energy gaps among the higher multiplet states are large, the effective system reduces to a single state to a multiplet decay case, per section 2.2.
3. Experimental methods
Single crystals of Co2+:AgCl0.5Br0.5 were grown from the melt by the Bridgman-Stockbarger method [15]. Parallel plates approximately 3 mm thick and 10 mm in diameter were cut and polished to near optical quality [16]. A room temperature reflection spectrum of a 3.03 mm thick sample was measured in the frame of our present work between 50 and 600 cm−1, using a Nicolet 6700, with DTGS/PE detector at a resolution of 0.5 cm−1 (Fig. 9 below). The beam incidence angle was 10°. Since sample thickness was only 3.03 mm, correction for rear surface reflectance was needed, assumed as about 35% of the front surface one. The equation used for the said correction is specified in Appendix A.
Analysis of the above reflectance spectral shape results was worked out by fitting to the classical independent oscillator model, see [17] chapter IV. For completeness of presentation, the expressions used are summarized in Appendix B.
4. Fluorescence transitions in Co2+:AgCl0.5Br0.5 crystals
4.1. Background
In this section we provide a revised analysis of the photo-excited fluorescence lifetime of Co2+ ions embedded in the mixed silver halide crystal AgCl0.5Br0.5 [11]. The 4.2 µm centered fluorescence was excited by 1.92 µm wavelength, 9 ns long laser pulses. The decay lifetime was measured between 20 and 280 K. The authors attempted to match the lifetime vs. temperature dependence to a single configuration-coordinate model, assuming a strong coupling between the ion states and the ligand vibrations of the form (Eq. 1 in [11])
where is the high-temperature limit non-radiative decay rate, and Eact is the energy required for non-radiative activation back to the ground state. A fit was obtained only for the low temperature range between 40 and 150 K, yet failed to fit a further shortening of the lifetime at higher temperatures by over an order of magnitude till 280 K.4.2. Revised analysis
Our revised analysis involves the single state to a multiplet decay system model of section 2.2 (Fig. 3 above) particularly, Eqs. (11), (12). The absorption and fluorescence spectra were re-plotted and resolved each into Gaussian single-peak components, with their relevant parameters inset in the figures’ frames (Figs. 5 and 6, respectively).
The resultant energy scheme is plotted in Fig. 7. The Co2+ ions are described to reside in two different sites, with some overlap. Excitation into the O-symmetry T2(4F) multiplet results in a fast non-radiative intersystem crossing into the Td-symmetry T2(4F) multiplet. The measured radiative fluorescence relates to the T2(4F) → T1(4F) allowed transition of the Co2+ ions residing in the Td-symmetry sites.
A fit of the effective fluorescence lifetime τeff as function of the absolute temperature T to Eq.(11) was obtained, and shown in Fig. 8 using the following known material parameters: ; Nc = 8; n = 2.1. Other process parameters deducted via Figs. 4–7 are listed in Table 1, along with adjustable parameters obtained by the fit to Eq. (11). The latter are emphasized by bold-type lettering.
5. Results and discussion
Correction of the experimental reflectance results for rear surface reflection were performed in such a manner that the fit reflectance at the zero frequency limit agrees with the theoretically calculated static dielectric constant ε(0) = 13.4 [18] (equivalent to 32.6% single surface reflection); see Appendices A and B. The ε(∞) parameter was chosen as 4.41, to be consistent with the ≈2.1 optical refractive index in the near-IR [19].
A notable result of the fit summarized in Table 1 is the value of the vibrational cutoff frequency ħωco = 180 cm−1. To verify consistency of this parameter with other methods of estimating the cutoff frequency of this particular material, we have carried out a reflection spectral measurement of the crystal surface in the far-IR region (50 − 600 cm−1). The results are shown in Fig. 9. The reflectance is moderate in the high frequency region with very little structure, but exhibits a steep rise at approximately 180 cm−1, up to about 45 − 50% towards the low frequencies. At about 75 cm−1 it appears to reduce towards about 35%, although with a considerable experimental noise level. A fit of the steep rise was obtained according to the Eq. (28) using the parameters appearing in Fig. 9. The vibrational ħω01 = 97 cm−1 and ħω02 = 75 cm−1 are quite close to the transverse optical (TO) frequencies measured at the Brillouin zone Γ point for pure AgCl (117.5 cm−1) and pure AgBr (89.1 cm−1) crystals quoted by Fujii et al ([20], Table. 2). Their corresponding longitudinal optical (LO) frequencies are 194.5 cm−1 and 139.3 cm−1. Particularly, the LO frequencies of the mixed crystals are somewhat lower than the quoted LO frequency of AgCl.
In Table 2 we summarize the parameters used in the theoretical to experimental fit of Fig. 9. The related LO frequency of each TO one is given by
where Q0j is j’s band strength parameter (see Appendix B).The effective oscillator strength feff that simulates the behavior of the molecular dipole as an electronic one, is given by
where Vc is the unit cell volume given by Vc = a3 for the crystalline period a = 5.66 Å [21].The highest obtained LO frequency, 162.5 cm−1 is only slightly lower than the ħωco = 180 cm−1 obtained for the τeff temperature dependence fit of Fig. 8. This, quite impressive correlation between the two entirely different methods for obtaining physical quantities, lends support to the theory of non-radiative transitions, and its application to analysis of fluorescence decay lifetime presented in section 2 above.
The enhanced reflectance between 350 and 600 cm−1 has been overlooked in the fit (Fig. 9). The origin of this effect is not yet clear. We suspect that it emanates from bulk imperfections due to the polishing process that contributes a broad spectrum of higher vibrational frequencies. This particular effect certainly requires further studies; however, it has no bearing on the ħωco estimate which is relevant to the non-radiative contribution to the decay process.
The radiative lifetime quantity is important for laser gain estimation: it appears in the denominator of the well known gain expression; see [22] Eq. (5.6-1). For the free-space wavelength λ as the variable, the gain expression reads
where γ is the crossing light intensity gain, ∆N is the population inversion, n is the material refractive index, and g(λ) is the fluorescence decay intensity spectral shape.The effective upper state lifetime at the absolute zero temperature limit has been often considered as a fair estimate of τrad [11, 23]. Our analysis suggests that the actual τrad might be substantially longer than τeff, and hence the gain significantly smaller. Thus, a proper estimate of τrad requires the measurements of τeff over a broad range of temperatures (starting from near zero); that, in conjunction with spectral measurements of both absorption and fluorescence.
A side conclusion of the energy-level scheme of Fig. 7, is estimation of the spin-orbit coupling that forms the energy separations among the different multiplet components. The spin-orbit coupling energy splitting ΓSLJ is given by
where ξLS is the spin-orbit coupling coefficient, and L, S and J are the orbital, spin, and total angular momentum quantum numbers, respectively; see [24] equation (4.25). Accepting that the first four lower peak positions indicate the four A1(4F9/2) → T2(4F) absorption transitions of the Co2+ in the Td symmetry, then ξLS = −90 cm−1. That parameter has been estimated as −150 cm−1 for Co2+ of a Td symmetry residing in ceramic Co2+:MgAl2O4 (Co2+:spinel) [25]. For the T2(4F) states in the O-symmetry (higher energy four transitions), one obtains ξLS = −100 cm−1. For the T1(4F) states in the Td symmetry (four transitions), one obtains ξLS = −80 cm−1.It should be emphasized that the transitions between the excited Co2+ manifold states belonging to the octahedral and tetrahedral sites, as indicated in Fig. 7, exhibit no bearing on the present excited state lifetime analysis. The analysis involves only the lower excited state component in the Td spectrum.
6. Conclusions and summary
In the present paper we have introduced the competing non-radiative multi-phonon decay transitions into the modeling of effective fluorescence lifetime of the rare-earth ions embedded in host dielectric matrices. Our theory, when applied to the Co2+:AgCl0.5Br0.5 crystal, is consistent with recently published experimental results [11] over the full measured temperature range. The original authors attempt to match the lifetime vs. temperature dependence to a single configuration-coordinate model, assuming a strong coupling between the ion states and the ligand vibrations, provided a fit only for the low temperature range. It however failed to account for a steep shortening of the lifetime at higher temperatures by over an order of magnitude.
In addition, our analysis predicts a zero absolute temperature radiative lifetime τrad(0) = 5.5 ms, and a lattice cutoff vibrational frequency ħωco = 180 cm−1. The latter estimate shows good agreement with experimentally measured value of ħωco = 162.5 cm−1 [20]. The configuration potential dissociation energy was estimated to be D ≅ 2500 cm−1. This parameter describes the dissociation energy in the attractive configuration potential that bonds the atoms to their equilibrium positions. It should thus correspond to the host material melting characteristics, see [26] section 121. This particular aspect requires further experimental and theoretical considerations.
An interesting application of the role of multi-phohon non-radiative transition would be the design and use of fast saturable absorbers where the excited state lifetime is very short compared to the photon back-and-forth transit time between the end resonator cavity mirrors. A host of pico-second and sub-picosecond mode-locked pulsed lasers have been designed on the basis of fast saturable absorption in the laser cavity; for example semiconductor saturable absorber mirrors (SESAM), see [27] section 9.2.4.
Notably, the bulk medium parameters responsible for the non-radiative transitions are independent of its periodic nature. Therefore, the expression obtained maybe be adopted to metal ions embedded in glasses and even to electronic-vibronic internal conversion in free large molecules. The latter two issues deserve further analysis and experimental study.
Appendix A: Front surface reflectance correction for a thin slab
Relating to incoherent two-surface reflections, the expression used for the corrected front surface reflection is
where Rex is the experimentally measured intensity reflectance, R1 is the front surface reflectance and R2 is the rear surface “effective” reflectance. The rear surface effective reflectance is reduced compared to the front surface one due to geometric stopping as well as some surface wedging. These effects are lumped by setting R2 = βR1, where β < 1 is an empiric correction factor. Solving for R1 yields the desired front surface reflectance (only physical solution in presented):Appendix B: Classical independent oscillators expressions
The reflection of a flat dielectric surface involving several bulk oscillators; see [17] chapter IV, is related to the bulk dielectric function by [28]
where ε′(ω) and ε″(ω) are the real and imaginary parts of the dielectric function, respectively, at a frequency (energy) ω, ω0j is the transverse optical (TO) frequency, Q0j is a strength parameter, and γj is a damping parameter, all of the j-th oscillator. ε(∞) is the dielectric function at frequencies considerably greater than the longitudinal optical (LO) cutoff frequency of the lattice vibrations, but considerably smaller than the lowest electronic frequency. The related real n and imaginary κ parts of the refractive index are given by The surface reflection spectrum is then given byFunding
Israel Ministry of Science and Technology (grant No. MOST 1-14459).
Acknowledgments
We are indebted to Dr. S. Kolusheva of the Ilse Katz Institute for Nano-Science and Technology (IKI), Ben Gurion University of the Negev, Israel, for her skillful technical assistance in performing the optical reflectance measurements.
References and links
1. S. B. Mirov, V. V. Fedorov, D. Martyshkin, I. S. Moskalev, M. Mirov, and S. Vasilyev, “Progress in mid-IR lasers based on Cr and Fe-doped II-VI chalcogenides,” IEEE J. Sel. Top. Quantum Electron , 21, 1601719 (2015). [CrossRef]
2. I. T. Sorokina and E. Sorokin, “Femtosecond Cr2+- based lasers”, IEEE J. Sel. Top. Quantum Electron. 21, 1601519 (2015). [CrossRef]
3. Y. Kalisky, The Physics and Engineering of Solid State Lasers(SPIE, Bellingham, WA, 2006). [CrossRef]
4. Y. V. Orlovskii, K. K. Pukhov, T. T. Basiev, and T. Tsuboi, “Nonlinear mechanism of multiphonon relaxation of the energy of electronic excitation in optical crystals doped with rare-earth ions,” Opt. Mater. 4, 583–595 (1995). [CrossRef]
5. Y. V. Orlovskii, R. J. Reeves, R. C. Powell, T. T. Basiev, and K. K. Pukhov, “Multiple-phonon nonradiative relaxation: Experimental rates in fluoride crystals doped with Er3+ and Nd3+ ions and a theoretical model,” Phys. Rev. B 49, 3821–3830 (1994). [CrossRef]
6. Y. V. Orlovskii, T. T. Basiev, I. N. Vorobiev, E. O. Orlovskaya, N. P. Barnes, and S. B. Mirov, “Temperature dependencies of excited states lifetimes and relaxation rates of 3–5 phonon (4–6 µm) transitions in the YAG, LuAG and YLF crystals doped with trivalent holmium, thulium, and erbium,” Opt. Mater. 18, 355–365 (2002). [CrossRef]
7. L. A. Riseberg and H. W. Moos, “Multiphonon orbit-lattice relaxation of excited states of rare-earth ions in crystals,” Phys. Rev. 174, 429–438 (1968). [CrossRef]
8. M. J. Weber, “Multiphonon relaxation of rare-earth ions in yttrium orthoaluminate,” Phys. Rev. B 8, 54–64 (1973). [CrossRef]
9. C. B. Layne, W. H. Lowdermilk, and M. J. Weber, “Multiphonon relaxation of rare-earth ions in oxide glasses,” Phys. Rev. B 16, 10–20 (1977). [CrossRef]
10. Z. Burshtein, “Radiative, nonradiative, and mixed-decay transitions of rare-earth ions in dielectric media,” Opt. Eng. 49, 091005 (2010). [CrossRef]
11. Y. Tsur, S. Goldring, E. Galun, and A. Katzir, “Ground state depletion - a step towards mid-IR lasing of doped silver halides,” J. Luminescence 175, 113–116 (2016). [CrossRef]
12. V. B. Fowler and D. L. Dexter, “Relation between absorption and emission probabilities in luminescent centers in ionic solids,” Phys. Rev. 128, 2154–2165 (1962). [CrossRef]
13. P. M. Morse, “Diatomic molecules according to the wave mechanics. II. Vibrational levels,” Phys. Rev. 34, 57–64 (1929). [CrossRef]
14. C. Layne, W. Lowdermilk, and M. Weber, “Multiphonon relaxation of Rare-Earth ions in oxide glasses,” Phys. Rev. B 16, 10–20 (1977). [CrossRef]
15. I. Zakosky-Neuberger, I. Shafir, L. Nagli, and A. Katzir, “Optical and luminescence properties of Co2+:AgCl0.2Br0.8 crystals and their potential applications as gain media for middle-infrared lasers,” Appl. Phys. Lett. 99, 201111 (2011). [CrossRef]
16. H. Hecht, Z. Burshtein, A. Katzir, S. Noach, M. Sokol, E. Frumker, E. Galun, and A. A. Ishaaya, “Passive Q-switching of a Tm:YLF laser with a Co2+-doped silver halide saturable absorber,” Opt. Mater. 64, 64–69 (2017). [CrossRef]
17. A. Hadni, Essentials of Modern Physics Applied to the Study of the Infrared(Pergamon, 1967).
18. D. Bunimovich and A. Katzir, “Dielectric properties of silver halide and potassium halide crystals,” Appl. Opt. 32, 2045–2048 (1993). [CrossRef] [PubMed]
19. A. S. Korsakov, D. S. Vrublevsky, A. E. Lvov, and L. V. Zhukova, “Refractive index dispersion of AgCl1−xBrx (0<x<1) and Ag1−xTlxBr1−xlx(0<x<0.05),” Opt. Mater. 64, 40–46 (2017). [CrossRef]
20. A. Fujii, H. Stolz, and W. von der Osten, “Excitons and phonons in mixed silver halides studied by resonant Raman scattering,” J. Phys. C 16, 1713–1728 (1983). [CrossRef]
21. C. R. Berry, “Physical defects in silver halides,” Phys. Rev. 97, 677–679 (1955). [CrossRef]
22. A. Yariv, Introduction to Optical Electronics, (Holt-Reinhart-Winston, 1971).
23. L. D. DeLoach, R. H. Page, G. D. Wilke, S. A. Payne, and W. F. Krupke, “Transition metal-doped zinc chalcogenides: spectroscopy and laser demonstration of a new class of gain media,” IEEE J. Quantum Electron , 32, 885–895 (1996). [CrossRef]
24. B. Henderson and R. H. Bartran, Crystal-Field Engineering of Solid-State Laser Materials(Cambridge University, 2000). [CrossRef]
25. A. Goldstein, P. Loiko, Z. Burshtein, N. Skoptsov, I. Glazunov, E. Galun, N. Kuleshov, and K. Yumashev, “Development of saturable absorbers for laser passive Q-switching near 1.5 µm based on transparent ceramic Co2+:MgAl2O4,” J. Am. Ceram. Soc. 99, 1324–1330 (2016). [CrossRef]
26. F. Seitz, The Modern Theory of Solids (McGraw-Hill, New York, 1940).
27. W. Koechner, Solid-State Laser Engineering(Springer, 2006).
28. S. Perets, R. Z. Shneck, R. Gajic, A. Golubovic, and Z. Burshtein, “Vibrational spectra of sodium gadolinium tungstate NaGd(WO4)2 single crystals: Observation od spatial dispersion,” Vib. Spectrosc. 49, 110–117 (2009). [CrossRef]