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Abstract
We report the generation of mid-infrared (~2 µm) high repetition rate (MHz) sub-100 ns pulses in buried thulium-doped monoclinic double tungstate crystalline waveguide lasers using two-dimensional saturable absorber materials, graphene and MoS2. The waveguide (propagation losses of ~1 dB/cm) was micro-fabricated by means of ultrafast femtosecond laser writing. In the continuous-wave regime, the waveguide laser generated 247 mW at 1849.6 nm with a slope efficiency of 48.7%. The laser operated at the fundamental transverse mode with a linearly polarized output. With graphene as a saturable absorber, the pulse characteristics were 88 ns / 18 nJ (duration / energy) at a repetition rate of 1.39 MHz. Even shorter pulses of 66 ns were achieved with MoS2. Graphene and MoS2 are therefore promising for high repetition rate nanosecond Q-switched infrared waveguide lasers.
© 2019 Optical Society of America under the terms of the OSA Open Access Publishing Agreement
1. Introduction
Waveguide (WG) lasers emitting in the spectral range of ~2 μm are of interest for spectroscopy, telecom and environmental sensing applications [1]. This is because their emission is eye-safe and matches the absorption lines of various atmospheric and bio-molecules. The laser operation at ~2 μm is achieved using such trivalent rare-earth ions as Thulium (Tm3+) or Holmium (Ho3+). In the former case, the transition of interest is 3F4 → 3H6. Due to the large Stark splitting of the Tm3+ ground-state, its emission is wavelength-tunable. The Tm3+ ions feature strong absorption at ~0.8 μm (3H6 → 3H4 transition) allowing for their efficient pumping by AlGaAs laser diodes and Ti:Sapphire lasers. Moreover, the cross-relaxation for adjacent Tm3+ ions, 3H4 + 3H6 → 3F4 + 3F4, can potentially raise the pump quantum efficiency up to 2.
Efficient continuous-wave (CW) thulium WG lasers are known [2,3]. Several methods have been used to fabricate WGs based on Tm3+-doped materials, e.g., liquid phase epitaxy (LPE) in combination with ion beam etching [2], optical bonding [4], ion diffusion [5], reactive co-sputtering [6] and femtosecond direct laser writing (fs-DLW) also referred as ultrafast laser inscription (ULI) [7]. In the latter approach, the output of an ultrafast (fs) amplifier is tightly focused in a transparent laser material causing a permanent variation of its refractive index. An inscription of a three-dimensional structure may thus lead to the waveguiding behaviour. Fs-DLW is attractive because it allows one to fabricate a variety of photonic microstructures [8,9] in different materials (from glasses to crystals and ceramics).
Less attention has been paid to pulsed (Q-switched and mode-locked) thulium WG lasers. In particular, passive Q-switching is realized by insertion into the laser cavity of a nonlinear optical element – saturable absorber (SA) – showing increasing (bleachable) transmission for high laser fluence / intensity.
For the spectral range of ~2 μm, there exist two types of SAs. The first type (“slow” SAs) includes transition-metal -doped crystals, e.g., Cr2+:ZnS or Cr2+:ZnSe [10]. The second one (“fast” SAs) includes semiconductor saturable absorber mirrors (SESAMs) and nanostructures based on two-dimensional (2D) few-atomic layer materials, e.g., graphene [11], single-walled carbon nanotubes (SWCNTs) [12] and transition metal dichalcogenides (TMDs) [13]. When employed in a passively Q-switched (PQS) laser, “fast” SAs provide the generation of nanosecond (ns) pulses at high repetition rates in the range of hundreds of kHz – few MHz.
Graphene is the most prominent example of 2D materials. It consists of a single layer of carbon atoms arranged in a honeycomb lattice. Graphene features hollow cone valence and conduction bands meeting each other at the Dirac point. Such a zero band gap electronic structure leads to wavelength-independent small-signal absorption of graphene (πα ≈2.3%, α = e2/ħc ≈1/137 is the fine structure constant) [14]. Moreover, graphene exhibits broadband (0.8 – 3 µm) saturable absorption due to the finite number of electron and hole states according to the Pauli blocking principle [11,15]. The low-signal absorption is almost independent of the photon energy hν, but the saturation intensity of graphene Isat increases with hν due to the band structure [16]. Thus, the application of graphene as a saturable absorber (SA) in lasers emitting at ~2 µm is of particular interest [17]. As a SA, graphene offers relatively low Isat, ultrafast recovery time and sufficiently high laser-induced damage threshold.
The success of graphene SAs stimulated the study of other 2D materials containing few atomic layers and exhibiting broadband linear and nonlinear absorption such as, e.g., TMDs, MX2 where M = Mo or W and X = S, Se or Te. For TMDs, one layer of M atoms is sandwiched between two layers of X atoms and the adjacent layers are bound by weak Van-der-Waals forces. Molybdenum disulfide (MoS2) is one of the most studied TMDs [13,18]. TMDs offer a higher fraction of the saturable absorption as compared to graphene [19]. Both graphene and MoS2 can be used in transmission-type and evanescent-field-based SAs.
An overview of PQS thulium WG lasers reported to date is presented in Table 1. Regarding planar WG lasers produced by LPE, a “slow” SA (Cr2+:ZnS) was employed in a Tm:KY(WO4)2 laser yielding 1.2 μs / 0.12 μJ (duration / energy) pulses at a low repetition rate of 10 kHz [24]. The use of a “fast” SWCNT-based SA in a similar laser lead to much shorter pulses of 83 ns / 33 nJ at 1.39 MHz [25]. However, both these lasers generated spatially multimode output.
Table 1. Laser Performance* of PQS Thulium Waveguide Lasers Reported So Far
As for channel WGs produced by fs-DLW, solely “fast” SAs have been used, incl. graphene, topological insulator (Bi2Te3) and SWCNTs [20–23]. Typically, these lasers generated μs-long pulses with a low average output power. In [20], a fs-DLW Tm:ZBLAN glass WG laser was passively Q-switched by a graphene-SA yielding 2.76 μs / 0.24 μJ pulses at a repetition rate of 25 kHz. The output power of this laser was 6 mW at ~1.9 μm with a slope efficiency of only 5%. MoS2 has never been used in Tm WG lasers yet, to the best of our knowledge.
In the present work, we employ few-atomic-layer graphene and MoS2 as saturable absorbers in fs-DLW Thulium channel WG lasers based on a monoclinic crystal, for the first time, to the best of our knowledge. We demonstrate the generation of sub-100 ns pulses from such lasers at MHz repetition rates.
2. Experimental
2.1. Femtosecond-laser-written waveguide
A depressed-index channel WG with a circular cladding was fabricated by fs-DLW in a bulk monoclinic crystal of Tm:KLu(WO4)2 (shortly KLuW) [23]. The crystal itself was grown by the Top-Seeded Solution Growth (TSSG) Slow-Cooling method using potassium ditungstate (K2W2O7) as a flux and a [010]-oriented seed [26]. It was doped with 3 at.% Tm3+ (NTm = 2.15 × 1020 at/cm3). The crystal was oriented along the Ng axis of the optical indicatrix (length: 3.0 mm, aperture: 3.10(Nm) × 2.85(Np) mm2). For the inscription, a Ti:Sapphire regenerative amplifier emitting 120 fs pulses at 795 nm at a repetition rate of 1 kHz was used. The laser beam was focused into the crystal using a 40 × microscope objective (N.A. = 0.65). The incident pulse energy was 57 nJ. The crystal was scanned at 400 μm/s along its Ng-axis producing damage tracks. The WG consisted of a 40 μm diameter core and a ring of damage tracks forming a cladding. The axis of the WG was located at 120 μm below the crystal surface. The separation between adjacent tracks was 2 μm. The estimated variation of the refractive index in the cladding was ~6 × 10−4 [27].
To characterize the WG, we employed confocal laser microscopy (LSM 710, Carl Zeiss). First, one of the polished WG end-faces was studied. In transmission mode with polarized light, a dark ring of damage tracks below the crystal surface representing the cladding was observed, Fig. 1(a). No cracks surrounding the cladding are visible for the selected pulse energy. The cladding exhibits a blue emission related to color centers, Fig. 1(b), confirming the modification of the material in this region.
Fig. 1 Confocal laser microscope images of the laser-grade-polished end-face of the Tm:KLuW WG: (a) transmission mode, polarized light (P || Np), λ = 405 nm; (b) back-propagating luminescence, unpolarized light, natural color, λexc = 405 nm; (c) transmission mode, crossed polarizers (P || Np, A || Nm), λ = 488 nm.
With the help of crossed polarizers, the birefringence of the laser-written tracks forming the cladding was revealed. Fs-DLW induces a spatially localized modification of the material compromising its crystallinity and therefore its index of refraction, as well as inducing anisotropic stress fields surrounding each laser-written track [28]. The latter will result in a local variation of the optical indicatrix due to the photo-elastic effect leading to an additional phase shift for rays propagating through such a structure. KLuW is optically biaxial so that with a crossed polarizer (P) and an analyzer (A) oriented along the optical indicatrix axes, Fig. 1(c), no transmitted light is expected. One can see a bright ring of damage tracks and weaker distributed “flows” in the core and in the surrounding area induced by the stress fields. They are symmetric with respect to the vertical direction (direction of propagation of the writing laser).
Similarly, observing the WG from the top crystal surface, in Fig. 2(a), a dark barrel-shaped cladding is visible in the unmodified bulk material. The cladding has a periodic net-like surface, Fig. 2(b), that may be related to defects in the motion of the micro-positioning stage during fabrication. Both these measurements were done in transmission mode with polarized light. With crossed polarizers, a bright cladding is visible in a dark crystal, Fig. 2(c), indicating a notable birefringence.
Fig. 2 Confocal laser microscope images (top view) of the central part of the circular cladding WG in Tm:KLuW: (a,b) transmission mode, polarized light (P || Ng), λ = 405 nm; (c) transmission mode, crossed polarizers (P || Ng, A || Nm), λ = 488 nm.
2.2. Laser set-up
The laser experiments were performed under pumping by a Ti:Sapphire laser (Coherent, model Mira 900) tuned to 802 nm (3H6 → 3H4 Tm3+ transition). The pump beam was linearly polarized (polarization in the crystal: E || Nm). The pump radiation was coupled into the WG using a microscope objective (Mitutoyo M Plan NIR 10 × , numerical aperture, N.A.: 0.28, focal length, f = 20 mm, working distance: 30.5 mm). The pump spot size 2wP on the input facet of the WG was 40 ± 5 μm. The measured pump coupling efficiency ηcoupl was 81 ± 2% (as determined from pump-transmission measurements performed at ~0.83 μm, out of Tm3+ absorption) including the Fresnel losses at the uncoated WG facet and the measured pump absorption under lasing conditions ηabs,L was 75 ± 2%. The incident pump power was varied with a gradient neutral density (ND) filter (Thorlabs, NDC-50C-4M) placed before the objective (Fig. 3).
Fig. 3 Laser set-up: ND – gradient neutral-density filter, PM – pump mirror, SA – saturable absorber, OC – output coupler, F – cut-off filter.
External (bulk) cavity mirrors were used. The laser cavity consisted of a flat pump mirror (PM) that was anti-reflection (AR) coated for 0.7–1.0 μm and highly-reflective (HR) coated for 1.8–2.1 μm and a flat output coupler (OC) having a transmission TOC of 20% or 30% at 1.8–2.1 μm. The crystal was passively-cooled and mounted on a BK7 glass substrate. Its input face was placed close to the PM. Between the crystal and the OC, a transmission-type SA was inserted for PQS operation (at normal incidence). All optical elements were separated by minimum air gaps. No index-matching liquid was used to avoid damage of optical elements. The geometrical cavity length was 4.0 mm.
The laser output was filtered from the residual pump with a long-pass filter (FEL1000, Thorlabs). The spectrum of the laser emission was measured using an optical spectrum analyser (OSA, Yokogawa, AQ6375B) and the near-field beam profile was captured using a plano-convex lens (f = 40 mm) and a FIND-R-SCOPE near-IR camera. The crystal was replaced by a 1951 USAF resolution test target (R1DS1, Thorlabs) to determine the mode size at the OC.
2.3. Saturable absorbers
Two transmission-type SAs were studied. Both of them were deposited on a laser-grade-polished quartz substrate (thickness: 1.0 mm). The first SA was based on a commercial large-area multi-layer chemical vapor deposition (CVD) graphene. Its small-signal transmission TSA measured at the laser wavelength of ~1.85 µm was 94.3% (the initial (non-saturated) absorption α'SA = 1 – TSA was 5.7%). For a single-layer graphene deposited at the same conditions, α'SA ≈2.3%, in good agreement with the theoretical value. Thus, the sample contained between 2 and 3 carbon layers (n) deposited layer-by-layer. The saturable absorption α'S = 0.24% (at ~1.85 µm) and the saturation intensity Isat = 0.6 MW/cm2 (at ~2 µm). We describe the saturation of the graphene-SA by the “fast” SA model [19]:
Here, α'(I) is the actual absorption and I is the light intensity. Multi-carbon-layer graphene-SA was selected in order to increase the saturable absorption (α'S) which is raising with the number of graphene layers [16]. As a competing detrimental process, with the increase of n, the fraction of the saturable loss to the small-signal absorption (α'S/α'SA) is decreasing due to enhanced scattering at the layer-to-layer interfaces. In [29], a graphene-SA containing three carbon layers shown the best PQS performance at ~2 μm.The second SA was based on a MoS2 film prepared by pulsed laser deposition (PLD) using polycrystalline MoS2 [19]. Its characteristics were as follows: TSA = 95.5%, α'S = 0.33% and Isat ~0.5 MW/cm2. The measured MoS2 film thickness was 20 nm, thus containing about 30 MoS2 layers if considering an individual layer thickness of ~0.65 nm and their bonding by Van der Waals interaction.
The small-signal internal transmission (T(SA + substrate)/T(substrate)) spectra as well as the Raman spectra of both SAs are shown in Fig. 4.
Fig. 4 Graphene- and MoS2-SAs: (a) small-signal transmission spectra, (b) Raman spectra, λexc = 514 nm. The arrow in (a) corresponds to the laser wavelength.
Raman spectroscopy is a sensitive method to characterize few-atomic layer materials. In the Raman spectrum of graphene-SA, two intense bands centered at 1587 cm−1 (G) and 2688 cm−1 (2D) are observed. The increase of the number of carbon layers affects the Raman spectra, i.e., it modifies the spectral shape of the 2D band and the intensity ratio of the 2D and G ones [30,31]. In our case, I(2D)/I(G) = 1.73 which is lower than for the single-layer graphene (I(2D)/I(G) = 2.2). The position of the 2D band corresponds to n between 2 and 3. In the Raman spectrum of the MoS2-SA, two characteristic bands at 382 cm−1 (E12g) and 408 cm−1 (A1g) [32] are observed. The former one is assigned to the motion of the Mo + S atoms in the x-y layered plane of the unit cell.
3. Results and discussion
3.1. Continuous-wave laser
Without the SA in the cavity, we studied the laser performance in the continuous-wave (CW) mode, see Fig. 5. The maximum output power reached 247 mW at 1849.6 nm corresponding to a slope efficiency η of 48.7% vs. the absorbed pump power Pabs (for 30% OC). The optical-to-optical efficiency vs. the incident pump power ηopt was 38.4%. For 20% OC, the laser generated 184.3 mW at 1851.4 nm with lower η = 35.9% and ηopt = 28.8%. The laser thresholds were at Pabs = 41 mW and 45 mW for 20% and 30% OCs, respectively. The input-output dependences were clearly linear representing no detrimental thermal effects; no thermal fracture nor damage of the WG facets were observed.
Fig. 5 CW Tm:KLuW channel WG laser: (a) input-output dependences, η – slope efficiency; (b) typical laser emission spectra (measured at Pabs = 0.52 W).
The WG propagation (passive) loss δloss was estimated using the Caird analysis [33] (taking into account the laser performance at low output coupling [23]) as ~1.0 ± 0.3 dB/cm.
The laser emission was linearly polarized, E || Nm, the polarization was naturally-selected by the anisotropy of the gain. The typical laser emission spectra are presented in Fig. 5(b). The full width at half maximum (FWHM, 3 dB bandwidth) of the spectra is 1.4 nm and 2.4 nm for TOC = 20% and 30%, respectively.
In Table 2, we compared the CW performance of fs-DLW thulium WGs lasers reported to date (the best results were selected from multiple publications on the same material). Fs-DLW was employed for microstructuring of Tm3+-doped fluoride glasses (ZBLAN, GPNG), oxide ceramics (based on cubic YAG and Lu2O3) and crystals (YAG). All these materials are optically isotropic. Using a WG written in monoclinic (anisotropic) Tm:KLuW crystal, we have achieved the highest output power, the lowest laser threshold and the highest slope efficiency for any ceramic / crystalline material.
Table 2. CW Laser Performance* of Fs-Laser-Written Thulium Waveguides Reported So Far
3.2. Passively Q-switched laser
Passive Q-switching of the Tm WG laser was studied using graphene and MoS2 SAs. The laser operated in the range of Pabs = 0.14...0.35 W because it was not very stable near the laser threshold and at higher absorbed pump powers due to the SA heating [39]. The emission of the PQS laser was linearly polarized, E || Nm.
The input-output dependences and typical laser emission spectra of the graphene and MoS2 PQS Tm:KLuW WG lasers are shown in Fig. 6. In terms of average output power and slope efficiency, the 30% OC provided the best performance: The laser generated 24.9 mW at 1844.8 nm with η = 9.3% (for graphene SA) and 22.1 mW at a shorter wavelength of 1843.4 nm with slightly lower η of 8.5% (for MoS2 SA). Considering the output power achieved in the CW mode at Pabs = 0.35 W, the Q-switching conversion efficiency ηconv was 16.6% and 14.7% for graphene and MoS2 SAs, respectively. The reduction of η for the PQS WG laser as compared to the CW operation mode is due to the insertion loss of the SA (including the non-saturable losses for the graphene and MoS2 films and Fresnel losses at the uncoated substrate). It is estimated as 11.9% and 10.7% for the graphene and MoS2 SAs, respectively.
Fig. 6 Graphene and MoS2 PQS Tm:KLuW channel WG lasers: (a) input-output dependences, η – slope efficiency, (b) typical laser emission spectra measured at maximum Pabs, (c) calibrated 1D intensity profiles of the laser mode at the output face of the WG along the Nm and Np axes: symbols – experimental data, curves – Gaussian fits, inset – 2D mode profile, the white circle indicates the cladding (graphene SA, TOC = 30%, Pabs = 0.35 W). The laser polarization is E || Nm.
Regarding the laser emission spectra, see Fig. 6(b), higher output coupling corresponded to a slightly shorter emission wavelength in agreement with the quasi-three-level nature of the Tm3+ ion.
The 1D intensity profiles of the laser mode along the horizontal (|| Nm-axis) and vertical (|| Np-axis) directions are shown in Fig. 6(c). They are well fitted with a Gaussian distribution (quality of the fit R2 >0.99) yielding the diameters of the laser mode 2wL of 38.2 μm and 40.2 μm, respectively. Thus, the laser mode is well confined within the WG cladding indicated by a white circle at the inset of Fig. 6(c) showing a 2D mode profile. The M2 (beam quality) parameter of the laser mode was determined by analysing its divergence as 1.20 ± 0.05 (for both horizontal and vertical directions).
According to the determined M2 being close to unity and nearly-Gaussian 1D intensity profiles of the laser mode, Fig. 6(c), we conclude that the laser operated at the fundamental mode (LP01). Within the step-index approximation, we calculated the normalized frequency V = 2πaN.A./λL = 2.4 ± 0.1 (N.A. = 0.035 is the numerical aperture of the WG, a = 20 μm is the WG core radius, λL is the laser wavelength). The cut-off V parameters for the LPlm = LP01 and LP11 (doubly degenerated) modes are 0 and 2.405, respectively. In our case, the generation of the LP11 modes is not observed probably to an additional effect of gain-guiding.
The pulse duration (determined as full width at half maximum, FWHM) Δτ and the pulse repetition frequency (PRF) were measured directly. The pulse energy, Eout = Pout/PRF, was calculated. In Fig. 7, we summarized the results regarding Δτ, PRF and Eout for graphene and MoS2 PQS Tm:KLuW WG lasers (for 30% OC).
Fig. 7 Graphene and MoS2 PQS Tm:KLuW channel WG laser: (a) pulse duration (FWHM), (b) pulse repetition frequency (PRF) and (c) pulse energy. Symbols: experimental data; curves – numerical calculation using the model from [17] for graphene-SA.
The pulse characteristics were dependent on Pabs. This behaviour is typical for “fast” SAs contrary to the “slow” ones (e.g., Cr2+:ZnS) and it is related to their dynamic bleaching [17]. “Fast” SAs such as graphene or MoS2 are saturated by the laser intensity. With an increase of the pump power, the intracavity intensity on the SA (Iin = X·(2Eout/(πwL2Δτ*)), where X = (2 – TOC)/TOC is the output-coupling factor and Δτ* ≈1.06Δτ is the effective pulse duration assuming both Gaussian laser mode and temporal pulse profile) increases thus leading to larger modulation depth asymptotically approaching the α'S value. This, in turn, will lead to an increase of the pulse energy and shortening of the pulse duration with the pump power. For TOC = 30%, the maximum intracavity laser intensity Iin on both SAs is ~0.19 MW/cm2 being smaller than Isat. Thus, the SA bleaching is indeed partial.
For TOC = 30% and graphene SA, the pulse duration shortened from 208 to 88 ns, the PRF increased from 0.78 to 1.39 MHz and the pulse energy – from 5.7 to 18.0 nJ. The maximum peak power Ppeak = Eout/Δτ thus reached 0.21 W. For the MoS2-SA, Δτ shortened from 199 to 73 ns, the PRF increased from 0.85 to 1.58 MHz and Eout – from 4.9 to 14.0 nJ. The peak power was similar to that for the graphene-SA, Ppeak = 0.19 W. A “saturation” of the dependence of the pulse energy on the pump power, Fig. 7(c), is an indication of the SA heating by the residual pump leading to a decreased α'S.
The pulse characteristics of the PQS WG laser were also calculated numerically using the model of a quasi-three-level laser medium and a “fast” SA described in [17,40]. The results for graphene-SA are shown in Fig. 7 as curves. The model reasonably describes the observed PQS behaviour. For the maximum Pabs = 0.35 W, it predicts the generation of 94 ns / 19.6 nJ pulses at a repetition rate of 1.49 MHz. The uncertainty in the calculated pulse characteristics is about 20%. The calculated results for the MoS2-based SA were similar to those of graphene (within the indicated uncertainty) and thus they are not shown in Fig. 7.
The use of 20% OC resulted in a shorter pulse duration for both graphene- and MoS2-SAs (due to the higher intracavity intensity on the SA Iin reaching ~0.27 MW/cm2) albeit at lower pulse energy.
The oscilloscope traces of the shortest Q-switched pulses and the corresponding pulse trains from the graphene and MoS2 PQS Tm:KLuW WG lasers are shown in Fig. 8. The Q-switching intensity instabilities were below 20% (measured over a time span of 1 ms) and they are attributed to the heating of the SA due to the non-absorbed pump radiation [39].
Fig. 8 Oscilloscope traces of (a) the typical pulse trains and (b) the shortest Q-switched pulses from the graphene and MoS2 PQS Tm:KLuW channel WG lasers.
The output characteristics of the fs-DLW channel WG lasers PQS by graphene- and MoS2-SAs are summarized in Table 3. The possibility to achieve shorter pulses with MoS2 SA is explained by a larger fraction of the saturable loss to the small-signal absorption for this material (α'S/α'SA = 0.074) as compared to graphene (α'S/α'SA = 0.042) [19].
Table 3. Output Characteristics of the PQS Tm:KLuW Channel WG Lasers.
4. Conclusion
Two-dimensional materials (graphene and few-layer MoS2) are promising SAs for WG lasers emitting at ~2 µm. They enable the generation of sub-100 ns pulses with nJ-level energies at high repetition rates (MHz-range). A fs-DLW circular cladding channel WG laser based on monoclinic Tm:KLu(WO4)2 crystal is PQS by graphene and MoS2 SAs. For graphene-SA, the best pulse characteristics are 88 ns / 18 nJ at a PRF of 1.39 MHz corresponding to an average output power of ~25 mW and a slope efficiency of ~9%. Using MoS2 SAs, shorter pulses (down to 66 ns) are achieved.
The achieved results represent a significant improvement of the laser performance as compared to the previously reported Tm WG lasers PQS by 2D materials such as graphene or topological insulator [20–22] (cf. Table 1). In particular, we report on the highest output power and slope efficiency while maintaining sub-100 ns pulse duration.
Graphene and MoS2 are interesting for PQS fs-DLW Tm surface waveguide lasers relying on evanescent field interaction [41]. In such a way, the limitation due to the heating of the SA by the residual pump will be diminished and the Q-switching conversion efficiency with respect to the CW regime will be enhanced. Pulsed operation with durations of few tens of ns is expected from such lasers. Such laser sources are potentially interesting for bio and environmental sensing applications.
Regarding the CW laser performance, we have achieved the highest output power for any fs-DLW Tm WG laser based on crystalline, ceramic or glassy material (cf. Table 2). Further power scaling was limited by the available pump power. Note that for most of the previously studied fs-DLW Tm WG lasers [34–38], Ti:Sapphire was used as a pump source. For further power scaling and for potential applications, it is desirable to fabricate WGs suitable for diode-pumping (e.g., by fiber-coupled AlGaAs laser diodes). In the case of high-power diodes with multimode fibers, a larger diameter of the WG cladding is necessary. According to the procedure described in Section 2.1, we have fabricated circular cladding WGs with a diameter of 100 μm. Such WGs are expected to provide spatially multimode laser output. Diodes with a single-mode fiber (whilst with a limited pump power) can be used for pumping the existing WGs. We plan to perform such studies in the future.
Funding
Ministerio de Economía y Competitividad (MAT2016-75716-C2-1-R (AEI/FEDER,UE), TEC 2014-55948-R, FIS2017-87970); Consejería de Educación, Junta de Castilla y León (UIC016, SA046U16); Agència de Gestió d’Ajuts Universitaris i de Recerca (2017SGR755); Horizon 2020 Framework Programme (747055).
Acknowledgments
E. K. acknowledges financial support from the Generalitat de Catalunya under grants 2016FI_B00844, 2017FI_B100158 and and 2018FI_B200123. F. D. acknowledges additional support through the ICREA academia award 2010ICREA-02 for excellence in research. A. R. acknowledges funding from the European Union’s Horizon 2020 research and innovation programme under the Marie Skłodowska-Curie Individual Fellowship Grant Agreement No. 747055. P. L. acknowledges financial support from the Government of the Russian Federation (Grant 074-U01) through ITMO Post-Doctoral Fellowship scheme.
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