Enhanced 1.5 μm emission from Yb³⁺/Er³⁺ codoped tungsten tellurite glasses for broadband near-infrared optical fiber amplifiers and tunable fiber lasers

Abstract

Strong 1.5 μm emission with full width at half maximum (FWHM) of 64 nm has been obtained in 3 mol% Yb₂O₃ and 1 mol% Er₂O₃ codoped tungsten tellurite glass under the excitation of a 980 nm laser diode. Spectroscopic properties of Yb³⁺/Er³⁺ codoped tungsten tellurite glasses as a function of Yb³⁺ and Er³⁺ contents are systematically investigated by absorption spectra, emission spectra and lifetime measurement. The structure of tungsten tellurite glass is characterized by Raman spectrum. In addition, emission cross section and gain coefficient of Er³⁺ ions near 1.5 μm are determined and respective maximum values attain 1.06 × 10⁻²⁰ cm² and 4.07 cm⁻¹. Moreover, gain bandwidth and figure of merit associated with gain properties in tungsten tellurite glass are calculated and compared with other reported glasses. These results indicate that Yb³⁺/Er³⁺ codoped tungsten tellurite glasses with better gain properties are promising candidates in constructing broadband optical fiber amplifiers and tunable fiber lasers in the optical telecommunication window.

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1. Introduction

In the past few decades, wavelength-division-multiplexing (WDM) technology has been extensively used in optical communication systems to meet the rapid increase in demand for information transmission capacity of networks.^1–3 Optical fiber amplifiers with broadband gain bandwidth and high gain are the key devices for WDM network systems.⁴ Since the Er³⁺:⁴I_13/2 → ⁴I_15/2 radiative transition emits fluorescence at around 1.5 μm that lies in the third optical telecommunication window and Er³⁺ ions can be excited by high power and low cost 980 nm laser diode (LD), Er³⁺ doped fiber amplifiers (EDFA) were initially developed and have been widely used in WDM network systems.⁵ At present, most of the commercial EDFA adopted in WDM network systems are made of silica glass. However, silica glass has relatively narrow emission bandwidth at 1.5 μm (∼35 nm) and lower doping concentration of Er³⁺ ions resulting in narrow and low gain profile, which limits data transmission capacity of WDM systems.^2,6

In order to overcome these shortcomings and achieve broad gain bandwidth and high gain, a lot of works have been dedicated to the exploitation for new glass host materials such as silicate, phosphate, germanate and tellurite glasses.^7–10 Among these glass hosts, tellurite glasses own relatively low phonon energy (650–800 cm⁻¹), broad infrared transmission region (up to 5 μm), high rare-earth solubility and refractive index (∼2).¹¹ It is very attractive that tellurite glasses possess a variety of structural units such as TeO₄ trigonal bipyramid, TeO_3+δ polyhedron and TeO₃ trigonal pyramid, which creates a range of electro-static fields around rare earth ions and thus results in inhomogeneous broadening of the spectrum.¹² Broad gain amplification of more than 20 dB in the wavelength range from 1530 to 1610 nm has been demonstrated in EDFA based on tellurite glass.¹⁰ In addition, WO₃ not only improves the thermal stability of tellurite glasses but also creates new structural units such as WO₄ tetrahedra and WO₆ octahedra.^13–15 Therefore, further inhomogeneous broadening can be expected in tungsten tellurite glasses. On the other hand, co-doping Yb³⁺ ions play a role of sensitization for Er³⁺ ions because Yb³⁺ ions with larger absorption cross section at 980 nm than Er³⁺ ions can enhance the pump efficiency of 980 nm LD and then transfer the energy to Er³⁺:⁴I_11/2 energy level via resonant energy transfer process (Yb³⁺:²F_5/2 + Er³⁺:⁴I_15/2 → Yb³⁺:²F_7/2 + Er³⁺:⁴I_11/2).⁵ To further enhance 1.5 μm emission from Er³⁺ through Yb³⁺ → Er³⁺, the optimization of Yb³⁺ and Er³⁺ doping concentrations are very essential.

In the present work, we systematically study spectroscopic properties of Yb³⁺/Er³⁺ codoped tungsten tellurite glasses as a function of Yb³⁺ and Er³⁺ concentrations by absorption spectra, emission spectra and lifetime measurement. The structure of tungsten tellurite glass is characterized by Raman spectrum. Furthermore, Judd–Ofelt (J–O) intensity parameters, emission cross section and gain coefficient of Er³⁺:⁴I_13/2 → ⁴I_15/2 transition are evaluated based on absorption and emission spectra. Besides, gain bandwidth and figure of merit associated with gain properties in tungsten tellurite glass are calculated and compared with other reported glasses.

2. Experimental methods

Tungsten tellurite glasses with different nominal compositions (in mol%) of 60TeO₂–30WO₃–3ZnO–7La₂O₃, 60TeO₂–30WO₃–3ZnO–(6 − x)La₂O₃–1Er₂O₃–xYb₂O₃ (x = 0, 1, 2, 3 and 4) and 60TeO₂–30WO₃–3ZnO–(4 − y)La₂O₃–3Yb₂O₃–yEr₂O₃ (y = 0, 0.5, 1, 1.5, 2 and 3) which are henceforth labeled as TW, TWEY-x and TWYE-y, respectively, were synthesized by standard melt-quenching method. Since La, Er and Yb belong to lanthanide family, La³⁺ is easily replaced by Er³⁺ and Yb³⁺, which is beneficial to the enhancement of doping concentrations of Er³⁺ and Yb³⁺ in the host glass. La₂O₃ may act as glass network modifier. In addition, the addition of ZnO can decrease the melting temperature of the host glass and increase the glass formation ability. All high-purity reagents (99.99% minimum) were weighed and mixed thoroughly before batches of 15 g mixtures were melted in alumina crucibles in an electric furnace at ∼850 °C for 30 min. These melts were cast into preheated cylindrical graphite molds and annealed at 450 °C for 2 h to relax the internal stresses, followed by slow cooling to room temperature. Finally, the annealed samples were optically polished to the disks with the size of Φ 15 mm × 1.5 mm for optical measurements.

Glass density (ρ) was calculated by Archimedes' principle using distilled water as an immersed liquid. After obtaining glass density, the total population of Er³⁺ or Yb³⁺ ions (N) was determined by the equation:

where N's unit is cm⁻³, x stands for the doping concentration of Er³⁺ or Yb³⁺ ions (mol%), M represents the average molecular mass of glass and N_A is Avogadro's number.

The refractive indices at 632.8, 1309 and 1533 nm were obtained by the prism coupling method (Metricon model 2010/M, Metricon Corp., America). Raman spectrum was measured by Raman spectrometer (Renishaw inVia, Gloucestershire, UK) and 532 nm laser as the excitation source. Absorption spectra of samples were recorded by Perkin-Elmer Lambda 900 UV/VIS/NIR double beam spectrophotometer (Waltham, MA, America) in the wavelength range from 400 to 2000 nm. The fluorescence spectra were recorded with a computer-controlled iHR 320 spectrofluorometer (Jobin-Yvon Corp., Horiba Scientific, France) under the excitation of a 980 nm LD. The fluorescence signal was collected by InGaAs detector. In addition, the luminescence decay curves of Er³⁺ were measured by a digital oscilloscope (TDS3012C, Tektronix Inc., America) and a function generator (TFG3051C, Tektronix Inc., America) connected to the iHR 320 spectrofluorometer. All of the measurements were carried out at room temperature.

3. Results and discussion

3.1 Raman and absorption spectra

Fig. 1 represents Raman spectrum of undoped tungsten tellurite glass (TW) in the wavenumber range of 200–1200 cm⁻¹. It is observed that five main bands appear in tungsten tellurite glass. The peak A at ∼360 cm⁻¹ and sharp peak E at ∼930 cm⁻¹ are attributed to the bending vibrations of corner-shared WO₆ octahedra and the vibrations of W–O⁻ and W=O bonds in WO₄ tetrahedra, respectively.^13–15 In addition, the peak B, C and D at ∼450, 678 and 750 cm⁻¹ are assigned to the symmetrical stretching or bending vibrations of Te–O–Te linkages at corner sharing sites, the anti-symmetric stretching vibrations of Te–O–Te linkages constructed by two un-equivalent Te–O bonds containing bridging oxygens (BO) in TeO₄ trigonal bipyramid and the symmetrical stretching vibrations of Te–O⁻ and Te=O bonds with non-bridging oxygens (NBO) in TeO₃ trigonal pyramid and TeO₃₊₁ polyhedra, respectively.^15,16 Therefore, very diverse types of structural units in the present glass can provide various local ligand field environments for Er³⁺ ions in favor of inhomogeneous broadening of 1.5 μm emission band.

Fig. 1 Raman spectrum of TW glass.

Fig. 2 depicts the absorption spectra of Yb³⁺ singly doped, Er³⁺ singly doped and Yb³⁺/Er³⁺ codoped tungsten tellurite glasses in the wavelength range from 400 to 2000 nm. Different characteristic absorption bands from Yb³⁺ and Er³⁺ ions are labeled in the figure. For Er³⁺ singly doped glass, eight absorption bands are located at 1532, 978, 798, 654, 544, 522, 490 and 452 nm, which are assigned to respective transitions from the ⁴I_15/2 ground state to the higher excited states ⁴I_13/2, ⁴I_11/2, ⁴I_9/2, ⁴F_9/2, ⁴S_3/2, ²H_11/2, ⁴F_7/2 and ⁴F_5/2. Energy levels above ⁴F_5/2 energy level are not clearly distinguished due to strong intrinsic bandgap absorption in the host glass. It is worth mentioning that absorption bands centered at 978 and 798 nm well match with the laser wavelength of commercial high power 980 and 800 nm LD. Based on the Beer–Lambert equation,¹⁷ absorption cross section at 978 nm (3.45 × 10⁻²¹ cm²) is 2.6 times as high as that at 798 nm (1.32 × 10⁻²¹ cm²), indicating that more efficient pump absorption can be achieved under the excitation of 980 nm LD. In addition, absorption intensity at 978 nm is greatly enhanced by the addition of Yb³⁺ ions due to Yb³⁺:²F_7/2 → ²F_5/2 transition. Therefore, Yb³⁺/Er³⁺ codoped tungsten tellurite glasses can be efficiently pumped by 980 nm LD. The inset of Fig. 2 presents the integral absorption intensity at 654 nm as a function of Er₂O₃ concentration. Good linear fitting implies that Er³⁺ ions are uniformly distributed without phase separation and agglomeration in the present tungsten tellurite glasses.¹⁸

Fig. 2 Absorption spectra of TWEY-0, TWYE-0 and TWYE-1 glasses. The inset shows the integral absorption intensity at 654 nm as a function of Er₂O₃ concentration.

It is well known that J–O theory^19,20 is a common tool to analyze spectroscopic properties of rare-earth (RE) ions doped crystals and glasses. With the help of this theory, three J–O intensity parameters Ω_t (t = 2, 4, 6) of Er³⁺ ions in TWEY-0 glass are determined using Fig. 2 and the procedure introduced elsewhere.²¹ Three J–O intensity parameters of Er³⁺ doped TWEY-0 glass are compared with that in other typical glass hosts in Table 1. The root mean square deviation for the best-fitted oscillator strengths is only 2.2 × 10⁻⁷ for TWEY-0 glass, indicating that calculated J–O intensity parameters are dependable. Higher Ω₂ implies that the degree of asymmetry of coordination environment for RE ions is higher and the covalency between RE ions and ligand is stronger.²¹ It is found that Ω₂ of Er³⁺ doped TWEY-0 glass is higher than that of other glass hosts in Table 1, resulted from the co-existence of various structural units as shown in Fig. 1, indicating that Er–O bond in the present glass possesses stronger covalency and coordination environment for Er³⁺ ions is of low symmetry.

Table 1 J–O intensity parameters in Er³⁺ doped TWEY-0 glass and other glass hosts

Glasses	J–O intensity parameters (10^−20 cm^2)			References
	Ω2	Ω4	Ω6
Oxyfluoroborosilicate	6.69	3.08	3.28	22
Phosphate	3.50	0.78	0.57	23
Fluoride	3.74	1.78	1.50	24
TeO2–GeO2–Na2O–Nb2O5	6.23	1.66	1.25	25
TWEY-0	6.89	1.85	1.14	This work

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3.2 Fluorescence spectra, lifetime and energy transfer mechanism

To investigate the effect of Yb³⁺ concentration on spectra properties of TWEY-x glasses, near-infrared and upconversion fluorescence spectra are recorded upon 980 nm excitation, as shown in Fig. 3. It is noted from Fig. 3(a) that a strong and broad emission band is located at 1536 nm, attributed to Er³⁺:⁴I_13/2 → ⁴I_15/2 transition. Furthermore, with increasing Yb₂O₃ concentration from 0 to 3 mol%, this emission intensity is enhanced by about 3 times, which is due to the reduction of the distance between Yb³⁺ and Er³⁺ ions and thus increases the energy transfer probability from Yb³⁺:²F_5/2 to Er³⁺:⁴I_11/2 energy level. But the emission intensity begins to reduce with further increasing the concentration, which may be ascribed to concentration quenching phenomenon and the enhancement of upconversion processes, as presented in Fig. 3(b). Three visible fluorescence peaks around 524, 546 and 658 nm appear, corresponding to Er³⁺:²H_11/2 → ⁴I_15/2, ⁴S_3/2 → ⁴I_15/2 and ⁴F_9/2 → ⁴I_15/2 transitions, respectively. Moreover, with the increment of Yb³⁺ content, three visible fluorescence intensities monotonously increase due to the enhancement of energy transfer process from Yb³⁺:²F_5/2 to Er³⁺:⁴I_11/2 energy level. Consequently, the optimum concentration of Yb₂O₃ is 3 mol% in view of 1.5 μm emission intensity.

Fig. 3 (a) Near-infrared and (b) upconversion spectra of TWEY-x glasses upon 980 nm excitation.

In the case where Yb₂O₃ concentration is fixed at 3 mol%, near-infrared emission spectra in TWYE-y glasses with different Er₂O₃ concentration are measured and depicted in Fig. 4 to further discuss energy transfer from Yb³⁺ to Er³⁺ ions. It is found from Fig. 4(a) that with increasing Er₂O₃ concentration from 0 to 3 mol%, 1018 nm emission intensity from Yb³⁺:²F_5/2 → ²F_7/2 transition decreases monotonously, which provides evidence for energy transfer process from Yb³⁺:²F_5/2 to Er³⁺:⁴I_11/2 energy level again. It should be mentioned that the emission band centered at 1018 nm can't be completely recorded upon 980 nm excitation because of getting close to the pump wavelength.

Fig. 4 Near-infrared spectra of TWYE-y glasses in the wavelength range of (a) 1000–1150 nm and (b) 1400–1700 nm pumped by 980 nm LD. The inset shows Er₂O₃ concentration dependence of FWHM.

The influence of Er₂O₃ content on 1.5 μm emission intensity and full width at half maximum (FWHM) is presented in Fig. 4(b). With the argument of Er₂O₃ concentration, this intensity heightens gradually due to enhanced energy transfer probability from Yb³⁺ to Er³⁺ before it reaches the maximum value of 1 mol%. And then the intensity decreases gradually with further enhancing the concentration owing to diffusion towards OH⁻ and other impurities present in the starting materials.²⁶ The broadening related to 1.5 μm emission band is very important for EDFA, which is usually evaluated by FWHM. Large FWHM is beneficial for wavelength tuning laser and WDM system.²⁷ The inset of Fig. 4(b) shows that FWHM of ⁴I_13/2 → ⁴I_15/2 emission band increases gradually from 59 to 74 nm when Er₂O₃ concentration varies from 0.5 to 3 mol%. These values are larger than that in other glass hosts used for optical fiber amplifiers, such as 38 nm in lead borosilicate glasses,²⁸ 47 nm in lead phosphate glasses,²⁹ 46 nm in niobium germanate glasses³⁰ and 48 nm in fluorotellurite glasses.⁵ The larger FWHM is ascribed to not only high refractive index (∼2.1) which strengthens the ligand fields around Er³⁺ but also to the existence of multiple structural units such as TeO₄ trigonal bipyramid, TeO₃ trigonal pyramid, TeO₃₊₁ polyhedra, WO₆ octahedra and WO₄ tetrahedra, which creates diverse coordination environments. Therefore, it is in favor of covering the optical communication C (1530–1565 nm) and L (1565–1625 nm) bands and the achievement of tunable fiber lasers.

Fig. 5 shows the fluorescence decay curve of Er³⁺:⁴I_13/2 energy level monitored at 1536 nm in TWYE-1 glass along with the lifetime values in TWYE-y glass. It is found that the lifetime of Er³⁺:⁴I_13/2 energy level monotonously reduces from 3.96 to 2.44 ms as Er₂O₃ concentration increases from 0.5 to 3 mol%. It is worth noting that the lifetime value slightly changes and is still relatively long (3.83 ms) in TWYE-1 glass.

Fig. 5 Fluorescence decay curves of Er³⁺:⁴I_13/2 energy level monitored at 1536 nm in TWYE-1 glass. The inset shows Er₂O₃ concentration dependence of the lifetime.

Based on above-mentioned results, the related energy transfer (ET) mechanism in Er³⁺/Yb³⁺ codoped tungsten tellurite glasses is illustrated in Fig. 6 with the help of the simplified energy level diagram of Er³⁺ and Yb³⁺. When samples are excited by 980 nm LD, both Yb³⁺ and Er³⁺ ions are initially motivated from the ground states ²F_7/2 and ⁴I_15/2 to the excited states ²F_5/2 and ⁴I_11/2, respectively. Since absorption cross section of Yb³⁺ ions at this wavelength is much larger than that of Er³⁺ ions and Yb³⁺:²F_5/2 and Er³⁺:⁴I_11/2 energy levels are closely in resonance, a majority of Yb³⁺ ions transfer their energy to nearby Er³⁺ ions through energy transfer process (ET1): Yb³⁺:²F_5/2 + Er³⁺:⁴I_15/2 → Yb³⁺:²F_7/2 + Er³⁺:⁴I_11/2, except that a small part of ions de-excite radiatively to ²F_7/2 energy level and emits fluorescence at 1018 nm. Thereafter, a part of Er³⁺ ions on this energy level relax radiatively and non-radiatively (NR) to Er³⁺:⁴I_13/2 and then return radiatively to the ground state producing fluorescence at 1.5 μm while the remainder is excited to ⁴F_7/2 energy level via excited state absorption (ESA), ET2: Yb³⁺:²F_5/2 + Er³⁺:⁴I_11/2 → Yb³⁺:²F_7/2 + Er³⁺:⁴F_7/2 and energy transfer upconversion process (ETU1): Er³⁺:⁴I_11/2 + Er³⁺:⁴I_11/2 → Er³⁺:⁴I_15/2 + Er³⁺:⁴F_7/2. Hence, the green emitting energy levels of ²H_11/2 and ⁴S_3/2 can be populated by relaxing NR from the upper ⁴F_7/2 energy level, followed by radiative transitions of ²H_11/2 → ⁴I_15/2 and ⁴S_3/2 → ⁴I_15/2 emitting fluorescence at 524 and 546 nm. On the other hand, the red emitting energy level of ⁴F_9/2 can be populated by ESA, ET3: Yb³⁺:²F_5/2 + Er³⁺:⁴I_13/2 → Yb³⁺:²F_7/2 + Er³⁺:⁴F_9/2 and relaxing NR from ²H_11/2 and ⁴S_3/2 energy levels. Then radiative transition of ⁴F_9/2 → ⁴I_15/2 produces fluorescence at 658 nm. It is worth noting that both ESA from Er³⁺:⁴I_13/2 and ETU2: Er³⁺:⁴I_13/2 + Er³⁺:⁴I_13/2 → Er³⁺:⁴I_15/2 + Er³⁺:⁴I_9/2 depopulate ⁴I_13/2 energy level and thus lead to decreased emission intensity at 1.5 μm.

Fig. 6 Simplified energy level diagram and energy transfer mechanism for Yb³⁺/Er³⁺ codoped tungsten tellurite glasses.

3.3 Gain properties of Er³⁺/Yb³⁺ codoped tungsten tellurite glasses

Emission cross section of Er³⁺:⁴I_13/2 → ⁴I_15/2 transition is very crucial parameter to evaluate the suitability for broadband EDFA. The emission cross section (σ_e) can be estimated by the following McCumber formula:³¹where σ_a is absorption cross section, Z_l and Z_u represent the partition function of the lower and upper state for ⁴I_13/2 → ⁴I_15/2 transition, respectively, k_B is the Boltzmann constant, T is the temperature and E_ZL is the zero-line energy, defined as the energy difference between the lowest stark of the upper and lower manifolds. The absorption cross section can be estimated by the Beer–Lambert equation:¹⁷where I₀ and I represent the intensities of incident and transmitted light, respectively, N is the total population of Er³⁺ ions and l is the thickness of the sample. According to eqn (1), the total population of Er³⁺ ions in TWYE-1 glass reaches 3.84 × 10²⁰ cm⁻³ (2 mol%). Fig. 7(a) presents the absorption and emission cross section as a function of wavelength in TWYE-1 glass. It is found that the maximum σ_e of Er³⁺ reaches 1.06 × 10⁻²⁰ cm² near 1.5 μm which is larger than those values reported in oxyfluorosilicate glass (4.88 × 10⁻²¹ cm²),³² lead phosphate glass (4.9 × 10⁻²¹ cm²),²⁹ bismuthate glass (8.2 × 10⁻²¹ cm²)³³ and gallogermanate glass (7.6 × 10⁻²¹ cm²),² indicating that high gain coefficient and low pump threshold can be excepted in the present glass.³⁴ Large emission cross section of Er³⁺ in TWYE-1 glass is due to high refractive index. The measured refractive indices at 632.8, 1309 and 1533 nm in TWYE-1 glass reach 2.0673, 2.0186 and 2.0152, respectively.

Fig. 7 (a) Absorption and emission cross sections of Er³⁺:⁴I_13/2 ↔ ⁴I_15/2 transitions (b) the effect of ⁴I_13/2 → ⁴I_15/2 transition wavelength on the gain coefficient in TWYE-1 glass.

Assuming that Er³⁺ ions are only in either ⁴I_15/2 ground state or ⁴I_13/2 first excited state, the gain coefficient G(λ) near 1.5 μm associated with the absorption and emission cross section is evaluated by the expression to estimate the gain properties qualitatively:³⁵

G(λ) = N[pσ_e − (1 − p)σ_a] (4)

where N stands for the total population of Er³⁺ ions and p represents the population inversion defined as the ratio between the population at ⁴I_13/2 energy level and the total population. Fig. 7(b) depicts the gain coefficient of Er³⁺:⁴I_13/2 → ⁴I_15/2 transition as a function of the wavelength in TWYE-1 glass while p increases from 0 to 1 in step of 0.2. It is noticed that respective wavelength of the maximum gain shifts toward shorter wavelength side as p raises, revealing a typical characteristic of the quasi-three-level system. Moreover, positive gain coefficient is obtained when p is higher than 0.2, indicating a lower pump threshold. It is worth noting that the maximum gain coefficient of TWYE-1 glass is 4.07 cm⁻¹ at 1534 nm, which is larger than those values reported in borosilicate glass (1.01 cm⁻¹),²² phosphate glasses (1.02 cm⁻¹),³⁶ bismuthate glass (3.51 cm⁻¹)³³ and niobium germanate glass (0.28 cm⁻¹).³⁰

Gain bandwidth is a key parameter for optical fiber amplifiers and is usually defined as the product of FWHM and emission cross section (FWHM × σ_e).³⁷ The larger FWHM × σ_e implies the better properties of amplifier. FWHM × σ_e in TWYE-1 glass reaches 6.78 × 10⁻²⁶ cm,³ which is larger than those values reported in silicate glass (2.2 × 10⁻²⁶ cm³),³⁸ zincfluorophosphate glass (1.61 × 10⁻²⁶ cm³),²⁷ gallogermanate glass (4.02 × 10⁻²⁶ cm³)² and zinctellurite glass (4.91 × 10⁻²⁶ cm³).³⁷ On the other hand, the figure of merit (FOM) is another vital parameter for optical fiber amplifiers to achieve high gain amplification, which is usually defined as the product of emission cross section and measured lifetime.³⁹ The larger FOM indicates a lower pump threshold. FOM in TWYE-1 glass reaches 4.06 × 10⁻²³ cm² s, which is higher than that in silicate glass (2.09 × 10⁻²³ cm² s),³⁸ zincfluorophosphate glass (1.26 × 10⁻²³ cm² s),²⁷ germanate glass (2.89 × 10⁻²³ cm² s)⁴⁰ and fluorotellurite glass (1.84 × 10⁻²³ cm² s).³⁸ As a consequence, Yb³⁺/Er³⁺ codoped tungsten tellurite glasses with larger emission cross section and better gain properties are potential candidates for broadband optical fiber amplifiers and tunable fiber lasers.

4. Conclusions

In conclusion, Yb³⁺/Er³⁺ codoped tungsten tellurite glasses with a series of doping concentration were prepared and their spectroscopic characteristics dependence of Yb³⁺ and Er³⁺ concentrations under 980 nm excitation were measured and studied in detail. Strong 1.5 μm emission with FWHM of 64 nm has been achieved in tungsten tellurite glass codoped with 3 mol% Yb₂O₃ and 1 mol% Er₂O₃, profiting from enormous absorption coefficient of Yb³⁺ ions at the pump wavelength and efficient resonance energy transfer process from Yb³⁺:²F_5/2 to Er³⁺:²I_11/2 energy level. Furthermore, the present glass owns multiple structural units and shows long lifetime of Er³⁺:⁴I_13/2 energy level (3.96 ms), high emission cross section (1.06 × 10⁻²⁰ cm²) and gain coefficient (4.07 cm⁻¹) near 1.5 μm, resulting in larger gain bandwidth (6.78 × 10⁻²⁶ cm³) and figure of merit (4.06 × 10⁻²³ cm² s) than those values reported in other glasses. In consequence, these results indicate that Yb³⁺/Er³⁺ codoped tungsten tellurite glasses with better gain properties are promising candidates in constructing broadband optical fiber amplifiers and tunable fiber lasers in the optical telecommunication window.

Author contributions

Jian Yuan conceived the idea and supervised the experimental work and paper writing. Guodong Zheng and Yingyi Ye performed the sample preparation. Yongbin Chen and Yichen Ye performed the optical measurements. Tingting Deng, Peng Xiao and Weichao Wang contributed to data analysis and secured funding. All authors reviewed the manuscript.

Conflicts of interest

There are no conflicts to declare.

Acknowledgements

The authors gratefully acknowledge the financial support from the National Natural Science Foundation of China (Grant No. 51902053, 61804029), Natural Science Foundation of Guangdong Province (Grant No. 2019A1515011988), Guangdong Basic and Applied Basic Research Foundation (Grant No. 2019A1515110002), the Foundation for Distinguished Young Talents in Higher Education of Guangdong (Grant No. 2019KQNCX172), the Project of Foshan Education Bureau (Grant No. 2019XJZZ02), Research Fund of Guangdong-Hong Kong-Macao Joint Laboratory for Intelligent Micro-Nano Optoelectronic Technology (Grant No. 2020B1212030010), the Open Fund of the State Key Laboratory of Luminescent Materials and Devices (South China University of Technology, Grant No. 2020-skllmd-13) and the Open Fund of the Guangdong Provincial Key Laboratory of Fiber Laser Materials and Applied Techniques (South China University of Technology, Grant No. 2021-07).

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