Waveguide (WG) lasers emitting in the spectral range of ∼2μm are of interest for bio- and environmental sensing applications. This is because such a radiation matches spectrally with the absorption of some relevant molecules, such as H2O or CO2. Typically, laser emission at ∼2μm is achieved using thulium (Tm3+) or holmium (Ho3+) ions. In the former case, the emission is due to the F43→H63 transition ^[1]. Tm3+ ions are attractive because of a strong absorption at ∼0.8μm (H63→H43 transition), efficient cross-relaxation (CR) enhancing the pump quantum efficiency up to 2 ^[2], low-threshold behavior, and typically large Stark splitting of the ground state leading to a broadband tuning feature.

Highly efficient laser operation was achieved with continuous-wave (CW) Tm WG lasers. In Ref. ^[3], a “mixed” Tm:K(Y,Lu,Gd)(WO4)2 crystalline channel WG laser generated 1.6 W at 1.84 μm with a record slope efficiency η of 80%, promoted by an efficient CR at a high Tm3+ doping level. The active layer was fabricated by liquid phase epitaxy (LPE) ^[4]. The WG propagation loss δ was ∼0.1dB/cm ^[5]. The refractive index contrast with respect to the undoped KY(WO4)2 substrate Δn was ∼1×10−3. Note that the active material belongs to the crystal family of monoclinic double tungstates (DTs), which are well-known for Tm3+ ion doping due to their advantageous spectroscopic properties for polarized light ^[6].

Another method of fabricating photonic microstructures in transparent dielectric materials has attracted a lot of attention, namely femtosecond direct laser writing (fs-DLW) ^[7–10]. This method is easier than LPE or pulsed laser deposition ^[11] and it allows for three-dimensional (3D) WG geometries. It can be applied to a variety of glass and crystalline materials. To date, several studies have been dedicated to CW fs-DLW Tm WG lasers ^[12–17]. One can note the results achieved in Ref. ^[16] with an fs-DLW Tm:ZBLAN glass channel WG laser, which generated 205 mW at 1.89 μm with η=67% (corresponding to δ∼0.4dB/cm).

Recently, we employed fs-DLW for the fabrication of depressed-index buried channel WGs in Tm3+-doped monoclinic DTs. In Ref. ^[18], proof of the concept was demonstrated using a bulk Tm:KLu(WO4)2 (shortly Tm:KLuW) crystal, and circular-cladding channel WGs were prepared. Power scaling of such lasers was shown in Ref. ^[19] using a hexagonal lattice-like cladding WG. The output power reached 136 mW at 1.844 μm with η=34.2%, and the WG propagation loss was estimated to be 1.2 dB/cm. The spatially averaged variation of the negative refractive index change across the microstructured cladding Δn was ∼0.6×10−3.

Passive Q-switching is a commonly used method to produce nanosecond (ns) pulses in solid-state lasers. It is typically realized by the insertion into the cavity of a nonlinear optical element—a saturable absorber (SA) whose linear absorption spectrally matches the laser wavelength.

Recently, multiple studies were dedicated to novel nanostructured SAs featuring a broadband linear and saturable absorption due to the special band structure. The most prominent example is carbon nanostructures, such as graphene ^[20,21], representing a 2D layer of carbon atoms arranged in a honeycomb lattice, and single-walled carbon nanotubes (SWCNTs) ^[22], representing rolled sheets of graphene. Other materials, such as few-layer transition metal dichalcogenides ^[23,24] (e.g., MoS2, MoSe2, or WS2), topological insulators, and related nanomaterials (e.g., Bi2Te3, Bi2Se3, or Sb2Te3) ^[25–27], black phosphorus ^[28], graphene oxide ^[29], and graphite nanoparticles ^[30], were also studied.

SWCNTs are promising SAs for passively Q-switched (PQS) solid-state lasers at 2 μm as they offer low saturation intensity, high fraction of saturable losses, and ultrafast recovery time of initial absorption. The fabrication of a SWCNT-SA is relatively easy. SWCNTs provide compatible pulse characteristics as compared to, for instance, commercial semiconductor SAs for 2 μm ^[31]. SWCNTs have been employed in PQS compact microchip-type (thermally guided) Tm lasers. In Ref. ^[32], an SWCNT PQS Tm:KLuW laser generated 25 ns/1.1 μJ pulses at a repetition rate of 0.64 MHz.

To date, only a few studies have been dedicated to PQS Tm WG lasers leading either to long (few μs) pulses or low average output power (few mW) ^[33–37]. Such SAs as Cr2+:ZnS, graphene, topological insulator (Bi2Te3), and SWCNTs were studied. For instance, in Ref. ^[36], an fs-DLW Tm:ZBLAN glass WG laser PQS by graphene generated 2.8 μs/240 nJ pulses at an output power of only 6 mW. Very recently, we employed SWCNTs in an fs-DLW Tm:KLuW WG laser providing much shorter pulses (50 ns/7 nJ) while the output power was still low, 10.3 mW ^[18].

The feature of the previously studied PQS Tm WG lasers was the use of transmission-type SAs. It is known that in such a geometry the SA suffers from heating due to the residual pump, causing Q-switching intensity instabilities and even laser-induced damage ^[21]. The interaction length (modulation depth) is limited by the SA thickness. On the other hand, an increase of the thickness will lead to higher insertion loss and lower laser efficiency. An alternative method is the deposition of the SA on top of a surface WG laser, so that the saturation of the SA is provided by an indirect interaction with the exponentially decaying evanescent field extending into the cladding along the propagation length. This method allows one to increase the interaction length with the SA, avoid its heating, and reduce the insertion losses. It is well known and has been extensively studied at ∼1μm in WG lasers based on Yb3+ and Nd3+ ions ^[38–42]. SWCNTs have also been employed in this WG laser geometry. In Ref. ^[38], a Yb:KY(WO4)2 planar WG laser generated 433 ns/110 nJ pulses at a repetition rate of 0.23 MHz. Note that particularly surface channel WG lasers are of interest for evanescent-field-interaction SA Q-switching as their top surface can be easily functionalized. Evanescent-field-interaction SAs have also been successfully implemented in mode-locked fiber lasers ^[43,44].

In the present work, we aimed to demonstrate passive Q-switching of a Tm surface waveguide laser based on evanescent field coupling operating in the 2 μm spectral range. We used a Tm3+-doped monoclinic DT crystal as a gain material, fs-DLW for the preparation of the WGs, and SWCNTs as an SA. The proposed geometry allowed us to achieve a record output power for any PQS Tm WG laser.

Depressed-index surface channel WGs were fabricated in a bulk Tm:KLuW crystal by fs-DLW. The active crystal was grown by the top-seeded-solution growth slow-cooling method using K2W2O7 as a solvent ^[6]. It was doped with 3 at. % Tm3+ (NTm=2.15×1020cm−3). Tm:KLuW is monoclinic (sp. gr. C2h6−C2/c) and optically biaxial. A rectangular sample was cut for light propagation along the Ng optical indicatrix axis, because it gives access to the high-gain E||Nm polarization and corresponds to athermally compensated thermo-optic properties ^[45]. The sample thickness t was 3.4 mm. Its aperture was 10.0mm(Nm)×1.7mm(Np), and both Nm×Np faces were polished to laser-grade quality and remained uncoated. Before the DLW and deposition of the SA, the two Ng×Nm faces were also polished to a laser-grade quality using a Logitech PM5 polishing machine and alumina powders in the range of 9–0.3 μm in diameter. When inspecting such surfaces with atomic force microscopy (Pico SPM II), we observed no defects, and the root-mean-square (rms) surface roughness was about 1.02±0.12nm.

The DLW was performed using 120 fs, 795 nm pulses from a Ti:sapphire regenerative amplifier (Spitfire, Spectra Physics) employing a small amount of the pulse energy at 1 kHz repetition rate. The laser beam was focused into the crystal with a 40× microscope objective (numerical aperture, N.A.=0.65). The fraction of the pulse energy incident on the crystal was 65 nJ. The crystal was scanned at a speed of 500 μm/s along its Ng-axis, producing the damage tracks. The polarization of the fs laser was perpendicular to the writing direction (E||Nm). The line scan procedure was repeated at different depths and lateral positions of the crystal to make half-ring-shaped cladding structures. Two surface channel WGs with core diameters of 50 and 60 μm were fabricated. Each cladding consisted of a total of 31 and 45 damage tracks, respectively. The separation between adjacent tracks along the horizontal direction was 2 μm. The axes of the waveguides were located at 25 μm beneath the crystal surface. Typical cross-section sizes of inscribed tracks were of 600 nm in width and 6 μm in height as previously observed in crystalline cladding waveguides fabricated in the same experimental conditions ^[46].

The selection of 50 and 60 μm diameter WGs is due to low propagation losses (below 1 dB/cm) expected for such structures according to our previous experiments.

The commercially available SWCNTs (Meijo Nano Carbon Co., Ltd.) were synthesized by the arc-discharge method. They had diameters varying from 1.5 to 2.2 nm. The SWCNTs were dissolved in 1,2-dichlorobenzene (o-DCB) at concentrations of 0.1–0.35 mg/mL and agitated in an ultrasonic bath. The SWCNT solution was centrifuged for about 20 min to induce sedimentation of large bundles and metal impurities. The well-dispersed SWCNT solution was then mixed with a separately prepared polymethyl methacrylate (PMMA, Polymer Source, Inc.) solution (100 mg/mL in o-DCB) at a volume ratio of 1:1 and stirred. The final concentration of SWCNTs in PMMA was 0.1–0.35 wt. %.

To fabricate the evanescent-field coupled SA, the 0.35 wt. % SWCNT/PMMA film was spin-coated on the top surface of the Tm:KLuW crystal containing the WGs. The whole length of the WGs was covered with the film. The WG faces were protected during the spin-coating. For the measurements of transmission spectra, films with different SWCNT concentrations were spin-coated on uncoated quartz substrates. The coated samples were placed on a hot plate in a vacuum oven to dry the SWCNT/PMMA film. The individual nanotubes were randomly oriented in the films (spaghetti-like); see Ref. ^[32] for scanning electron microscopy images of SWCNTs. The spin-coating speed was 1500 r/min. All deposited films had a thickness of 300 nm. More details can be found elsewhere ^[22,32]. Note that in Ref. ^[22], high-pressure carbon monoxide (Technique) SWCNTs were used, but the fabrication procedure was similar.

The deposited films were clear and uniform and contained no particles as examined by optical microscopy. The small-signal transmission (T0) spectra of the SWCNT/PMMA films deposited on quartz substrates are shown in Fig. 1(a) (the Fresnel losses are subtracted). For the same film thickness, it was possible to vary the absorption by changing the concentration of SWCNTs. The films feature a broadband absorption at 1.6–2.2 μm due to the first fundamental transition of the semiconducting nanotubes (E11). For the 0.35 wt. % SWCNT/PMMA film, T0=97.5% at 1.85 μm (small-signal absorption αSA′=1−T0=2.5%). Note that the film thickness can be changed by varying the spin-coating speed (1500–200 r/min) and the number of coating runs (1–3).

Raman spectra were measured for the 0.35 wt. % SWCNT/PMMA film spin-coated on the Tm:KLuW WGs; see Fig. 1(b). The excitation wavelength λexc was 514 nm (Ar+-ion laser). The most intense G-band is the optical phonon mode of graphite materials. This band is split, which is a distinctive feature of cylindrically rolled graphene sheets, that is, SWCNTs. The high-frequency peak (G+,1590cm−1) corresponds to vibrations of C atoms along the nanotube axis, and the low-frequency one (G−,1567cm−1) arises from vibrations along the circumferential direction. The other bands are assigned as D(1366cm−1) and D′(2684cm−1). The radial beating mode (160–190 cm⁻¹, as determined using films coated on quartz substrates) was not resolved because it overlaps with strong Raman bands of KLuW crystal.

The absorption saturation property of SWCNT/PMMA films was proved by pump-probe experiments at 1.92 μm, revealing two characteristic recovery times τrec, “fast” (0.25 ps) and “slow” (1.16 ps) ^[47]. The saturation intensity Isat of a similar SWCNT-based transmission-type SA was estimated as 7±1MW/cm2 and the fraction of the saturable losses αS′/αSA′ as 0.21 at ∼2μm ^[32].

Optical microscope images of the SWCNT/PMMA film and the top surface of the Tm:KLuW crystal coated with this film are shown in Fig. 2.

First, we studied the WGs by confocal laser microscopy using an LSM 710 microscope (Carl Zeiss) equipped with a polarizer (P), an analyzer (A), a blue GaN laser (405 nm), and an Ar+ ion laser (488 nm). The characterization started with one of the laser-grade-polished end-faces of the WGs; see Fig. 3. The measurements were done in transmission mode with polarized light (P||Np,λ=405nm).

A clear dark half-ring of damage tracks having a length of 6 μm is observed. The surrounding bulk crystal does not contain any cracks. The inner part of the WG is darker because part of the light is coupled and is not detected.

Then the polished top-surface of the WGs (before the SWCNT coating) was also examined using the transmission mode. With polarized light (P||Ng,λ=405nm), a dark half-barrel-shaped cladding is surrounded by the bright unmodified bulk material; see Figs. 4(a) and 4(b). The cladding has a periodic net-like surface. With crossed polarizers (P||Ng,A||Nm,λ=488nm), a bright cladding is seen in the dark crystal, Figs. 4(c) and 4(d). For crossed polarizers oriented along the optical indicatrix axes of KLuW, no transmitted light is expected for the stress-free bulk crystal. A modification of the cladding may provide an additional phase shift due to the stress-optic effect, leading to transmission of light through the crossed P and A. Figures 4(c) and 4(d) indicate such a birefringence of the cladding.

The modification of the crystal structure in the WG core and cladding regions was further studied with μ-Raman mapping spectroscopy. A Renishaw inVia Reflex microscope with a 514 nm Ar+ ion laser and a 50× Leica microscope objective was used. The excitation laser was linearly polarized with E||Nm in the crystal. The measurement geometry was g(mm)g. We monitored the most intense internal Raman mode at ∼907cm−1 related to the W–O stretching vibrations in the distorted WO6 octahedra of KLuW ^[6]. Its peak intensity and position were studied over the cross section of the WG faces with a spatial resolution of 0.4 μm.

The results are shown in Fig. 5. Both the Raman peak intensity and the peak frequency (in cm−1) are similar in the WG core volume and in the pristine bulk crystal surrounding the WG. Thus, the crystalline quality of the material in the core region is preserved. A reduction of the Raman peak intensity and a phonon energy shift of ∼0.8cm−1 to higher frequencies are observed in the cladding region. These changes indicate a reduced crystallinity of the damaged material within the cladding, as well as the presence of microstress-induced lattice compaction leading to higher phonon energy, both agreeing well with the presence of depressed index changes at tracks as well as collateral induced stress fields.

The scheme of the laser setup is shown in Fig. 6. The fs-DLW waveguide laser was pumped by a CW Ti:sapphire laser (MIRA 900, Coherent) tuned to ∼802nm. The polarization of the pump beam corresponded to E||Nm in the WG. It was coupled into the waveguides with a 10× microscope objective (N.A.=0.28, focal length f=20mm) resulting in a spot radius wp of 20 μm at the focus located at the front end-face of the WG. The incident pump power was varied with a gradient neutral density (ND) filter. Under 802 nm pumping, the WGs exhibited blue (480 nm) upconversion luminescence (G41→H63 transition of Tm3+).

The Tm:KLuW sample containing the fs-DLW WGs was placed on a passively cooled Al support. The laser cavity consisted of a flat pump mirror which was antireflection coated for 0.7–1.0 μm and high-reflection coated for 1.8–2.1 μm and a flat output coupler (OC) having a transmission TOC of 1.5%, 3%, 5%, 9%, 20%, and 30% at 1.8–2.1 μm. The PM and the OC were placed close to the WG endfaces with minimum air gaps. No index-matching liquid was used. The physical cavity length was then 3.4 mm.

The pump absorption under lasing conditions, ηabs=Pabs/Pcoupl, and the coupling efficiency, ηcoupl=Pcoupl/Pinc, were determined from a combination of pump-transmission studies at 802 and at 830 nm (out of the Tm3+ absorption) and a rate-equation modelling accounting for the bleaching of the Tm3+ ground-state (H63) and CR for the Tm3+ ions ^[48]. ηcoupl was 83%±2% for both WGs, and ηabs amounted to (69%–72%)±1%, depending on the OC. Note that the small-signal pump absorption calculated from the spectroscopic data is ∼98% (σabs=6.2×10−20cm2 is the corresponding absorption cross-section of Tm3+ ions in KLuW for E||Nm) ^[6].

The laser output was collimated using an uncoated lens with f=15mm. The nonabsorbed pump was blocked using a long-pass filter (FEL 1000, Thorlabs). The output power was measured with an Ophir Nova P/N 1Z01500 power meter. The real output was corrected for the optical losses at the lens and filter. The emission spectrum was measured using an optical spectrum analyzer (AQ6375B, Yokogawa). Imaging of the waveguide laser near-field output mode at 1850 nm wavelength was performed using a FIND-R-SCOPE near-IR camera (model 85726). The laser mode size at the output face of the WG was calibrated using a 1951 USAF resolution test target (R1DS1, Thorlabs). The oscilloscope traces were detected using a fast InGaAs photodiode and a 2 GHz Tektronix DPO5204B digital oscilloscope.

Before the SWCNT/PMMA coating of the WGs, we studied their CW performance. The corresponding input–output dependences are shown in Fig. 7. The laser emission was linearly polarized, E||Nm (horizontal). The polarization was naturally selected by the anisotropy of the gain. The output dependences were linear for all OCs up to at least ∼0.5W of absorbed pump power (Pabs), indicating the lack of detrimental thermal effects. No damage of the WGs was observed.

The 60 μm WG exhibited the best laser performance, Fig. 7(a). For the optimum 30% OC, the maximum CW output power was 171.1 mW at 1847.4 nm corresponding to a slope efficiency η of 37.8% (with respect to Pabs). The laser threshold was as low as 52 mW. For the 50 μm WG, a lower output power of 150.6 mW at 1847.2 nm and lower η of 34.5% were achieved, Fig. 7(b). The laser threshold increased to 59 mW (for the same TOC=30%). For both WGs, the laser performance improved with TOC indicating a minor effect of upconversion that is known to affect the laser performance of Tm3+-doped materials at high inversion rates β associated with high output coupling.

The achieved CW output power and the slope efficiency exceed the values reported previously for the hexagonal-cladding fs-DLW buried Tm:KLuW WG ^[19].

The typical laser emission spectra for both CW WG lasers are shown in Fig. 8 (measured at maximum Pabs). With the increase of output coupling from 1.5% to 30%, the emission shifted to shorter wavelengths. This behavior is due to the quasi-three-level nature of Tm3+ ions, and it is related to an increase of β (in other words, a decrease of reabsorption) with TOC. For the 60 μm WG, the laser wavelength blueshifted from 1947.4 to 1847.4 nm and for the 50 μm WG, from 1916.4 to 1847.2 nm.

For the two studied WGs, the laser oscillations occurred around two narrow spectral ranges. For the 60 μm WG, the laser emitted at ∼1.94μm for small TOC≤5% and at ∼1.85μm for higher output coupling. For the 50 μm WG, the emission was at ∼1.91μm for small TOC<3%, in two spectral ranges for intermediate 3%–5% output coupling, and finally for TOC≥9% it was solely at ∼1.85μm. This is related to the presence of three narrow local peaks in the gain spectra of Tm3+ ions in KLuW for E||Nm ^[6]. The prevalence of these peaks is changing with β.

The WG propagation loss was estimated from a Caird analysis modified for high output coupling ^[17], 1/η=(1/η0)(1+2γ/γOC), where γ=−ln(1−L) and γOC=−ln(1−TOC), L is an internal loss per pass, and η0 is an intrinsic slope efficiency. Figure 9 shows a plot of the inverse of the slope efficiency versus the inverse of the outcoupling loss γOC for both WGs. The least-square fit of the experimental data yields η0=43±2%, δ=4.34L/t=0.7±0.3dB/cm for the 60 μm WG and η0=36±2%, δ=0.9±0.3dB/cm for the 50 μm one. These values of the WG propagation loss are lower than those reported for an fs-DLW Tm:KLuW WG with a hexagonal cladding (1.2 dB/cm) ^[19] and for an fs-DLW Yb:KGd(WO4)2 WG based on a pair of damage tracks (1.9 dB/cm) ^[49] and indicate the good potential of the designed structures for further PQS experiments.

A higher propagation loss for the 50 μm WG explains its worse laser performance—see Fig. 7(b)—namely, lower η and higher laser threshold, as well as shorter laser wavelengths achieved even with smaller TOC, Fig. 8(b), as compared with the 60 μm WG.

The measured intensity spatial profiles of the output laser mode for CW fs-DLW Tm:KLuW surface WG lasers are shown in Figs. 10(a) and 10(b). The laser mode was confined by the half-ring-shaped cladding from below and the air–sample interface from above. Because of this, the mode profiles were slightly asymmetric, and they were extended in the vertical direction (||Np-axis). For both directions, ||Nm and ||Np, the intensity profiles were well fitted with a Gaussian function; see Figs. 10(c) and 10(d). No notable change of the beam profiles with Pabs was observed.

Using the calibration target, we determined the actual size of the laser mode at the output end-face of both WGs. For the 60 μm one, the 1/e2 mode diameters 2wL were 58.3 μm (horizontal, ||Nm) and 62.8 μm (vertical, ||Np). For the 50 μm WG, 2wL was smaller, 48.1 μm (horizontal), and 52.3 μm (vertical). Thus, the measured mode was mostly confined inside the WG cladding and the size of the mode follows the spatial shape and size of the cladding structures.

Finite element method numerical simulations of the waveguides incorporating various index change processes (damage and stress-optic index changes) have also been performed. Such simulations allow us to predict local index change values at submicrometer volumes within the cladding region at the near-IR range. The simulations of the waveguides, following our previous simulation model (see Ref. ^[46] for further results), deliver fundamental modes for both waveguides very similar to those measured, Fig. 11. The obtained refractive index change at submicrometer tracks is of −0.01+0.0017i, which are values very similar to those previously obtained for fs-DLW channel WGs fabricated under the same laser conditions but on LiNbO3 crystals ^[46].

After the CW laser experiments, the WGs were spin-coated with the SWCNT/PMMA film. The coated Tm:KLuW sample was tested in the same laser setup. Two OCs with transmission of 20% and 30% were used. Stable passive Q-switching was achieved with both WGs and OCs. In all cases, the laser output was linearly polarized, E||Nm. No damage of the sample or SA was observed after a long-term, about an hour, operation. No special laser alignment was needed to observe Q-switching.

The input–output dependences are shown in Fig. 12(a). They were linear for both OCs up to at least Pabs=0.5W. The 60 μm WG laser provided the best output performance. For TOC=30%, it generated a maximum average output power of 150 mW at 1846.8 nm with η=34.6%. Considering the output power achieved in the CW mode, the Q-switching conversion efficiency ηconv was as high as 87.6%. Note that a small blueshift of the emission wavelength with respect to the CW laser, Fig. 8(a), and a very high ηconv indicate low insertion loss for the SWCNT-SA. For the same OC, the 50 μm WG laser emitted a lower average output power of 115 mW at a slightly shorter wavelength of 1844.0 nm with η=24.6% and ηconv=76.3%.

The typical emission spectra of the PQS WG lasers are shown in Fig. 12(b). With increasing TOC, the spectra experienced a slight blue shift, e.g., from 1847.9 to 1846.8 nm for the 60 μm WG. For all studied WGs and OCs, the laser oscillations were around 1.85 μm.

The pulse characteristics, such as the pulse repetition frequency (PRF) and pulse duration (determined as full width at half-maximum, FWHM) Δτ were measured directly. The pulse energy Eout was calculated from the average output power as Pout/PRF, and the peak power Ppeak as Eout/Δτ. The results on the pulse characteristics obtained with the optimum TOC=30% are shown in Fig. 13. All of them were dependent on Pabs. This effect is known for “fast” SAs such as graphene and SWCNTs, and it is related to the dynamic bleaching of the SA ^[50].

For the 60 μm WG laser with the increase of Pabs from 0.1 to 0.5 W, the pulse duration shortened from 237 to 98 ns, the pulse energy increased from 24 to 105.6 nJ, and the PRF increased from 0.86 to 1.42 MHz. The maximum peak power reached 1.07 W. For the 50 μm WG laser, the best pulse characteristics were 52.2 nJ/90 ns at a PRF of 2.20 MHz. The maximum Ppeak value was 0.58 W.

The oscilloscope traces of the shortest single Q-switched pulses and the corresponding pulse trains recorded at the maximum Pabs of 0.5 W (for both studied WG lasers) are shown in Fig. 14. The single Q-switched pulses have a nearly Gaussian temporal shape. The intensity instabilities in the pulse trains are <15%, and the root mean square (rms) pulse-to-pulse timing jitter is <10% (for both WGs).

The output characteristics of the fs-DLW Tm:KLuW surface channel WG lasers PQS by SWCNTs are listed in Table 1.

The results achieved in the present work represent the highest average output power (150 mW) and slope efficiency (34.6%) ever achieved in any PQS Tm waveguide laser. We refer this to the use of a surface-deposited SA, thus minimizing the insertion losses, as indicated by the high achieved Q-switching conversion efficiency of 87.6%. The shortest pulses (50 ns) from a PQS Tm waveguide laser were obtained in Ref. ^[18] using a buried fs-DLW Tm:KLuW WG and a transmission-type SWCNT-SA with higher modulation depth than in the present work.

In conclusion, we have demonstrated the first Tm waveguide laser PQS by evanescent field interaction with a surface-deposited SA. We selected a monoclinic Tm:KLu(WO4)2 crystal as a gain material where 50 and 60 μm diameter half-ring surface channel WGs were fabricated by fs-DLW. A thin film containing randomly oriented SWCNTs served as an SA. This laser design featured low WG propagation losses, <1dB/cm, low insertion losses for the SA, and a weak sensitivity of the SA to the non-absorbed pump. This configuration enabled a relatively high laser output (150 mW at 1846.8 nm), laser slope efficiency (34.6%), low laser threshold, high Q-switching conversion efficiency (approaching 90%), and low intensity instabilities in the PQS pulse trains (<15%). The designed WG laser operated at medium repetition rates, in the MHz-range.

For the studied WG lasers, the power scaling was limited by the available pump. Further scaling is possible when using, for instance, fiber-coupled AlGaAs laser diodes. The slope efficiency of the laser can be improved by using higher Tm3+ doping levels (5–10 at. %), which will lead to an enhanced CR. In the present work, this was limited by the fact that Tm3+ ions absorb at the wavelength used for fs-DLW (795 nm), and thus the quality of the WGs written in highly doped Tm:KLuW crystals was lower. The solution to this problem can be the use of an fs-laser wavelength tuned out of the Tm3+ absorption.

Further shortening of the Q-switching pulses from the surface WG laser can be achieved by a higher concentration of SWCNTs in the film, thus resulting in an increased modulation depth of the SA. The geometry of the waveguide (e.g., the depth of its axis beneath the crystal surface) should be optimized to ensure the maximum interaction of the laser mode with the surface-deposited SA while simultaneously keeping the Q-switching conversion efficiency high.

The designed PQS waveguide lasers are promising for bio- and environmental sensing ^[51].

Acknowledgment. E. Kifle acknowledges financial support from the Generalitat de Catalunya. F. Díaz acknowledges additional support through the ICREA academia for excellence in research. A. Ródenas acknowledges funding from the European Union’s Horizon 2020 Research and Innovation Programme under the Marie Skłodowska-Curie Individual Fellowship (747055). P. Loiko acknowledges financial support from the Government of the Russian Federation through ITMO Post-Doctoral Fellowship scheme (074-U01).