Limit to the erbium ions emission in silicon-rich oxide films by erbium ion clustering

1. Introduction

Erbium (Er³⁺)-doped silicon-rich oxide (SRO) films are studied as active material to a silicon-integrated optical amplifier or laser [1,2]. By using the sensitization action of silicon nanoclusters (Si-ncl) [3], limitations of the Er³⁺ excitation process are avoided (small absorption cross-section, spectrally narrow absorption lines [2]), and the overall material emission performance is improved [3–5]. At the same time, complementary-metal-oxide-semiconductor (CMOS) process compatibility is maintained, and emission in the third telecom window (1.53 µm) is achieved [1]. This allows for direct compatibility with the mainstream semiconductor technology, which yields mass manufacturing and heavy integration density of photonic devices [1]. Additional attractiveness is given by the possibility of electrical injection through electrical transport in the Si-ncl [6].

Despite these premises, optical gain achievement is still eluding. There is consensus in the literature that the principal reason obstructing the optical gain achievement in this material is a low fraction of sensitized erbium ions [7–10]. Recently, we have demonstrated that this is followed by the loss of light emission capability of Er³⁺ when embedded in SRO material [11]. While the main fraction of embedded erbium ions does not participate in the process of light emission, absorption properties of non-emitting ions remain unaltered [12]. Evidently, this becomes a major obstacle toward population inversion in this material. At this point, elucidating the origin of this phenomenon becomes of paramount significance for further material optimization and device development. In this work, we address this issue in a conclusive way and report on the mechanism responsible for it, i.e., erbium ion clustering.

2. Experiment

The samples used in this work are thin Er³⁺-doped (by ion implantation) films of alternating SRO and SiO₂ layers deposited on a crystalline silicon wafer by low-pressure chemical vapor deposition (LPCVD) in a standard CMOS line. Thin films (d ~50 nm) have the advantage that can be studied by electrical [6], optical [13] and optoelectronic means [14]. Deposition starts with a d = 2 nm thin SiO₂ layer deposited on p-type crystalline silicon wafer on top of which is deposited a d = 3 nm thick SRO layer with nominal silicon excess of 20 at. %. The procedure is repeated 10 times in order to reach the desired thickness of d ~50 nm for optimum performance in slot waveguide amplifier [15]. Finally, a d = 2 nm thin layer of SiO₂ is deposited on top. After deposition, samples are thermally treated in order to induce phase separation and amorphous silicon nanoparticles growth and formation (T_annealing = 900°C for t = 1 h) [16,17]. Subsequently, the samples were implanted with erbium ions (dose: 1 × 10¹⁵ at./cm² and energy: 20 keV) and thermally treated for a second time (T_{post-annealing} = 800°C for t = 6 h) to recover implantation damage.

Photoluminescence (PL) measurements were done by employing the three different lines of an argon ion laser: λ_exc = 488 nm (resonant, excitation wavelength coincides with absorption line of Er³⁺), λ_exc = 476 nm (non-resonant, Er³⁺ are excited by energy transfer from Si-ncl) and an additional line in UV λ_exc = 361 nm for the continuous wave (CW) visible PL measurements. In addition, a laser diode (λ_exc = 974 nm, resonant) was used as well. Time-resolved (TR) PL measurements in the infrared were performed by modulating the laser beam with a mechanical chopper in the case of excitation with the argon ion laser, or by modulating the diode driving current by an external function generator in the case of excitation with the laser diode. For detection in the visible, a GaAs photomultiplier tube (PMT) for CW PL is used, and an InGaAs PMT is used for the IR (both CW and TR PL measurements). In the case of TR PL measurements in IR, the InGaAs PMT was interfaced with a multichannel scalar averager. In all cases before detection, the optical signal was spectrally filtered with a monochromator.

Electroluminescence (EL) spectra are collected using a fiber bundle and analyzed with a Spectra-Pro 2300i monochromator coupled with a nitrogen-cooled charge-coupled device (CCD) cameras (one in visible and one in IR). Emitted optical power and external quantum efficiency (EQE) are measured using either a calibrated LED or a Ge photodiode. The acceptance angle of the photodiode is taken into account.

For transmission electron microscopy (TEM), a JEOL 2010-FEG (200kV) scanning transmission electron microscope was used, equipped with a GIF spectrometer for STEM-EELS and EFTEM imaging mode. Samples for TEM observations were prepared through conventional mechanical polishing with a final Ar⁺ bombardment using a PIPS Gatan system. Erbium concentrations were determined by secondary ion mass spectrometry (SIMS) calibrated with a sample of known erbium concentration. The silicon excess was calculated with the formula (1 − x/2)/(1 + x), with x = [O]/[Si] as measured by x-ray photon spectroscopy (XPS).

3. Results and discussion

The erbium concentration profile in our thin films has been determined by SIMS, and it is reported in Fig. 1(a) . The peak concentration n_peak = 5.2 × 10²⁰ at./cm³ is located in the center of the active layer, at approximately d ~20 nm below the sample surface. The average erbium concentration is n_average = 2.9 × 10²⁰ at./cm³. A silicon excess of 9 at. % was determined by XPS. The thickness of the active material d ~44 nm was found by TEM (see Appendix A). Note that this Er³⁺ concentration was chosen based on previous reports that indicate long lifetimes and high emission intensities, i.e., no cooperative photoluminescence quenching effects [18].

 

Fig. 1 (a) Semi-log plot of erbium concentration profile in the studied samples obtained by SIMS. Thick vertical dashed lines indicate interfaces between air/SRO and SRO/silicon substrate. Vertical red dotted line corresponds to the peak Er³⁺ concentration, and the horizontal red dotted line to an average Er³⁺ concentration in the active layer. The shaded area corresponds to the layer where erbium clusters are visible in TEM images. (b) Bright field scanning TEM (STEM) image of the sample.

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Surprisingly, erbium clusters are visible as a dark spotted layer in TEM image (Fig. 1(b)). This erbium cluster layer is located at d ~20 nm below the sample surface, and it is approximately 15 nm wide (see Fig. 1(b)). It contains 55 ± 5% of the total number of erbium ions (shaded area in Fig. 1(a)). This is a first insight on what could limit the Er³⁺ emission capability as the clustered erbium ions emit light very inefficiently [19]. However, not all of the Er³⁺ in this layer may be clustered and, on the other hand, owing to the finite resolution of TEM, the erbium clustered region could be wider, as small erbium clusters (formed by a few atoms only) may escape detection. Thus, we correlate these findings with the results of a spectroscopic analysis.

It is worth mentioning that similar local inhomogeneity in erbium ions spatial distribution and the tendency to clusterize in silicon rich oxide films have been reported previously in thin films prepared with very different deposition techniques [20–24]. Thus, this type of behavior is not inherent to LPCVD but is quite general for Er³⁺ concentrations larger than 10²⁰ at./cm³ [20–24].

Er³⁺ emission can be observed in our samples both by non-resonant (Fig. 2(a) - λ_exc = 476 nm with an excitation photon flux Φ_exc = 3 × 10²⁰ ph./cm²) and resonant optical excitation, as well as by electrical excitation (see Appendix B). In Fig. 2(b), a visible PL spectrum under CW UV optical excitation (λ_exc = 364 nm, Φ_exc = 3 × 10¹⁸ ph./cm²) is also reported. The broad PL band in Fig. 2(b) situated at λ = 750 nm is attributed to residual Si-ncl PL. The additional peak at 550 nm, which is observable only under UV optical excitation or electrical bias, could be associated with direct excited state emission (⁴S_3/2 – ⁴I_15/2 radiative Er³⁺ transition) visible owing to its high emission cross section. Moreover, the presence of cooperative upconversion (CUC) processes are observed by the shortening of the lifetimes of the 1.535 µm Er³⁺ emission with increased excitation photon flux (Fig. 3(a) - λ_exc = 476 nm, excitation photon flux varies from Φ_exc = 2.8 × 10¹⁸ ph./cm² to 2.7 × 10²⁰ ph./cm²).

 

Fig. 2 (a) PL spectrum of the ⁴I_13/2 – ⁴I_15/2 radiative erbium transition in the studied sample under non-resonant optical excitation. (b) Normalized visible PL spectrum under CW UV optical excitation.

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Fig. 3 (a) The best fit (red line) of experimental data (black spheres) obtained using non-resonant optical excitation by Eq. (1). Dashed horizontal line represents the time decay in absence of cooperative upconversion. (b) The best fit (red line) of experimental data (black spheres) obtained using resonant optical excitation by Eq. (2).

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In order to evaluate the fraction of Er³⁺ that emits light efficiently, n_active, CUC has been quantified with the method of [16]. The PL measurements were carried out by resonant (λ_exc = 974 nm) and non-resonant (λ_exc = 476 nm) optical excitation. The experimental data were fitted by Eq. (1) [16]:

An example of the fit of experimental data by Eq. (1) is reported in Fig. 3(a) (λ_exc = 476 nm). The fit yields C_up = 2.1 ± 0.3 × 10⁻¹⁵ cm³/s, and τ₀ = 2.13 ± 0.05 ms. This is a long lifetime considering the estimated radiative lifetimes in these samples (7 ms, see Appendix C). It is worth noticing that this same material shows a very high EQE under electrical bias (~0.4%) [25].

C_up is significantly higher than the previously reported value for similar Er³⁺ concentrations [9], although it is in agreement with the large erbium clustering observed in TEM images. Note that C_up represents an average value, and the local C_up can vary significantly across the active layer owing to the Er³⁺ concentration profile (see Fig. 1(a)).

Knowing C_up and σ_abs, the direct Er³⁺ absorption cross-section (measured value agrees with those reported in [11] within the experimental errors), n_active can be estimated by fitting the experimental data obtained using resonant optical excitation (λ_exc = 974 nm) with the following Eq. (2) (Fig. 3(b)) [11]:

This number is significantly lower than the non-clustered fraction estimated from TEM (~45%). However, in the TEM images only clusters of certain size can be seen (few nm of size). Thus, if erbium clusters consist of only few erbium ions they will not be observed by TEM, although they will heavily influence the optical properties of the active material. This explains the observations of previous reports, even though higher fractions of active erbium ions were reported [11,26,27]. Therefore, Er³⁺ clustering is the main phenomenon that limits n_active.

While different fabrication protocols could lead to different matrix quality [28] and consequently, a different local Er³⁺ environment [29], loss of emission capability of erbium ions is a frequently reported issue [11,20,21], indicating a similar quenching mechanism. This is here studied on samples made by LPCVD. Furthermore, variations in silicon excess (0 at.% - 10 at.%) and thermal treatment do confirm the data presented here. We studied variation in annealing temperatures (900°C – 1100°C), duration (5 – 60 min.) and methods (furnace or rapid thermal processing)

Although we observe a certain variations in n_active and CUC’s coefficient among different samples, the degree of these variations (n_active being always ≤ 1% of total Er³⁺ content) is not sufficient to provide an amplifier material (which requires n_active > 50%) or to change the overall picture. For sake of completeness, we have not found appreciable difference in SIMS profiles and TEM images between different samples.

It is important to emphasize that in these samples, a significant fraction of erbium ions is situated in the silica layers that prevent the suggested silicon excess induced Er³⁺ ion de-excitation [30]. Moreover, n_active is determined by using a sub-bandgap (for Si-ncl) resonant (for Er³⁺) optical excitation, avoiding the possibility of energy back-transfer toward the Si-ncl [7]. Furthermore, we would like to stress the fact that no optical gain was reported in this material (silicon-rich oxide) with high Er³⁺ concentration (> 1 x 10²⁰ at./cm³) regardless of the particular deposition technique used. Thus, we conclude that the erbium ion clustering is the main mechanism responsible for the low optical activity of Er³⁺ ions in this material at the used erbium concentration (~10²⁰ at./cm³).

Therefore, to achieve full Er³⁺ inversion (i.e. net optical gain), the Er³⁺ concentration should be decreased significantly with respect to the usually considered optimum value of n_Er3+ ~10²⁰ at./cm³ [18]. This will reduce the maximum gain value achievable.

4. Conclusions

In summary, thin erbium-doped films of alternating layers of SRO and silica were fabricated and characterized in a configuration that mitigates previously proposed mechanisms for loss of light emission capability of erbium ions [7,8,30]. Even though promising results in terms of erbium PL lifetime (~2 ms) and EQE under electrical bias have been obtained, the main fraction of erbium ions does not contribute efficiently to the light emission owing to erbium ion clustering. The only possibility left to achieve net gain in this material system is to decrease the Er³⁺ concentration to level where clustering no longer occurs.

Appendix A: Structural analysis of the samples

Energy filtered (EFTEM) TEM image of the sample obtained by filtering at 15 eV (c-Si plasmon peak) is reported in Fig. 4(a) . An active layer, approximately 44 nm thin, can be clearly seen, with the SRO (bright lines) and oxide layer (darker lines) visible. Erbium clusters can be seen close to the center of the active layer (dark spots in Fig. 4(a)) their chemical nature confirmed by HAADF (Fig. 4(b) - bright line in the center of the layer corresponds to a high concentration of erbium (Z = 68) clusters), EFTEM and EELS (not shown). These clusters lay at d ≈ 20 nm and extend in a region 15 nm thick.

 

Fig. 4 (a) EFTEM image of the sample. (b) High angle annular dark field STEM image of the sample.

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Appendix B: Electroluminescence (EL) spectrum of the samples

EL spectrum of the samples in the IR obtained with an injected current of I = 100 µA and a forward bias of U = 45.1 V is reported in Fig. 5 . This spectrum, owing to the ⁴I_13/2 – ⁴I_15/2 erbium radiative transition, resembles the one obtained under optical excitation (Fig. 2(a)).

 

Fig. 5 EL spectrum of the ⁴I_13/2 – ⁴I_15/2 radiative erbium transition in the studied samples.

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Appendix C: Erbium radiative lifetime estimate

To estimate the CUC’s coefficient [16] and the fraction of Er³⁺, which can emit efficiently [11], we estimate the Er³⁺ radiative lifetime. In the literature, it is reported that Er³⁺ in a bulk silica has a radiative lifetime τ_rad = 18 ms [31]. However, since in SRO films refractive index is different than in SiO₂ [32], the radiative lifetime of Er³⁺ changes. Considering the silicon excess (9 at.%) and literature reports [6,16,27,32,33], a radiative lifetime of τ_rad ~ 10 ms can be estimated in our films.

This value is also what is expected for bulk samples when accounting for the near-field enhancement of radiative rate in vicinity of silicon nanoparticles (τ_rad = 10 ms [34] - τ_rad = 7 ms [35]). Finally, since we are using thin films deposited on a high refractive index material (silicon substrate), a certain enhancement of the radiative rate is expected [36–39], and therefore we assumed a value of τ_rad = 7 ms.

Acknowledgments

This work was supported by EC through the project ICT-FP7-224312 HELIOS and by Italy-Spain integrated actions. D. N.-U. thanks the financial support of AGAUR through the Beatriu de Pino`s program and J.-M. R. thanks the CSIC for a JAE predoc grant. Authors would like to acknowledge the Laboratory of Electron NanoScopy, MIND-IN2UB, Dept. Electrònica, and the Scientific and Technological Centers (Universitat de Barcelona). A. Ruiz-Caridad, F. Peiró, Y. Berencén and O. Jambois are acknowledged for electron microscopy analysis and fruitful discussion. We acknowledge the contributions from N. Daldosso and A. Marconi at an early stage of the work.

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