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Nanoscale Res Lett. 2013; 8(1): 43.
Published online Jan 21, 2013. doi:  10.1186/1556-276X-8-43
PMCID: PMC3562245

Microstructure and optical properties of Pr3+-doped hafnium silicate films

Abstract

In this study, we report on the evolution of the microstructure and photoluminescence properties of Pr3+-doped hafnium silicate thin films as a function of annealing temperature (TA). The composition and microstructure of the films were characterized by means of Rutherford backscattering spectrometry, spectroscopic ellipsometry, Fourier transform infrared absorption, and X-ray diffraction, while the emission properties have been studied by means of photoluminescence (PL) and PL excitation (PLE) spectroscopies. It was observed that a post-annealing treatment favors the phase separation in hafnium silicate matrix being more evident at 950°C. The HfO2 phase demonstrates a pronounced crystallization in tetragonal phase upon 950°C annealing. Pr3+ emission appeared at TA = 950°C, and the highest efficiency of Pr3+ ion emission was detected upon a thermal treatment at 1,000°C. Analysis of the PLE spectra reveals an efficient energy transfer from matrix defects towards Pr3+ ions. It is considered that oxygen vacancies act as effective Pr3+ sensitizer. Finally, a PL study of undoped HfO2 and HfSiOx matrices is performed to evidence the energy transfer.

Keywords: Praseodymium, Hafnium silicate, Oxygen vacancies, Photoluminescence, Energy transfer

Background

Rare-earth elements are important optical activators for luminescent devices. Among various rare-earth luminescent centers, trivalent praseodymium (Pr3+) offers simultaneously a strong emission in the blue, green, orange, and red spectral range, satisfying the complementary color relationship [1,2]. Consequently, Pr3+-doped glass/crystals are often used as phosphor materials [2,3]. SiO2-(Ca, Zn)TiO3:Pr3+ phosphors prepared with nanosized silica particles exhibit an intense red photoluminescence (PL) [3]. The Pr3+ emission was achieved for Si-rich SiO2 (SRSO) implanted with Pr3+ ions, but its intensity was lower [4].

Hafnium dioxide (HfO2) and hafnium silicates (HfSiOx) are currently considered as the predominant high-k dielectric candidates to replace the conventional SiO2 due to the rapid downscaling of the complementary metal-oxide semiconductor (CMOS) transistors [5,6]. It is ascribable to their good thermal stability in contact with Si, large electronic bandgaps, reasonable conduction band offset in regard to Si, and their compatibility with the current CMOS technology. Our group has first explored the structural and thermal stability of HfO2-based layers fabricated by radio frequency (RF) magnetron sputtering [7,8] and their nonvolatile memory application [9,10].

It is worth to note that both HfO2 and HfSiOx matrices have lower phonon frequencies compared to those of SiO2, and as a consequence, both are expected to be suitable hosts for rare-earth activators. Thus, PL properties have been investigated for the HfO2 matrix doped with Tb3+[11], Eu3+[11,12], or Er3+[12,13] and have been explained by the interaction of rare-earth ions with host defects. Recently, our group has demonstrated that an enhancement of Er3+ PL emission can be achieved for the Er-doped HfSiOx matrix in comparison with that of the Er-doped HfO2[14]. It was also observed that an energy transfer from the HfO2 host defects towards Er3+ ions, whereas the existence of Si clusters allowed an enhancement of the Er3+ ion emission under longer-wavelength excitation. Consequently, the mechanism of the excitation process, when Si clusters and oxygen-deficient centers act as Er3+ sensitizers, has been proposed to explain an efficient rare-earth emission from Er-doped HfSiOx hosts [14] similar to that observed for the Er-doped SRSO materials [15].

In this paper, we study the microstructure and optical properties of Pr-doped hafnium silicate films fabricated by magnetron sputtering versus annealing temperature. We demonstrate that an efficient Pr3+ light emission is achievable by tuning the annealing conditions. The excitation mechanism of Pr3+ ions is also discussed.

Methods

The films were deposited onto p-type (100) 250-μm-thick Si wafers by RF magnetron sputtering of a pure HfO2 target topped by calibrated Si and Pr6O11 chips. The growth was performed in pure argon plasma with an RF power density of 0.98 W[bullet]cm−2; the Si substrate temperature was kept at 25°C. After deposition, a post-annealing treatment was carried out under a nitrogen flow, at temperatures (TA) varying from 800°C up to 1,100°C for 1 h.

The refractive index (n) (given always at 1.95 eV) and the film thicknesses were deduced from spectroscopic ellipsometry data. The chemical composition of the films was determined by Rutherford backscattering spectrometry (RBS) using a 1.5-MeV 4He+ ion beam with a normal incidence and a scattering angle of 165°. The infrared absorption properties were investigated by means of a Nicolet Nexus (Thermo Fisher Scientific, Waltham, MA, USA) Fourier transform infrared (FTIR) spectroscopy at Brewster’s incidence (65°) in the range of 500 to 4,000 cm−1. X-ray diffraction (XRD) experiments were performed using a Philips Xpert MPD Pro device (PANalytical B.V., Almelo, The Netherlands) with CuKα radiation (λ = 1.5418 Å) at a fixed grazing angle incidence of 0.5°. Cross-sectional specimens were prepared by standard procedure involving grinding, dimpling, and Ar+ ion beam thinning until electron transparency for their observation by transmission electron microscopy (TEM). The samples were observed using a FEG 2010 JEOL instrument, operated at 200 kV. The PL emission and PL excitation (PLE) measurements were carried out using a 450-W Xenon arc lamp as excitation source at room temperature corrected on spectral response with the help of a Jobin-Yvon Fluorolog spectrometer (HORIBA Jobin Yvon Inc., Edison, NJ, USA).

Results and discussion

Composition and structural characterizations

In this study, the chemical composition of the film Hf0.24Si0.20O0.52Pr0.05 was determined through the simulation of the corresponding RBS spectrum using the SIMNRA program (Figure (Figure1).1). The RBS analysis shows that the as-deposited film cannot be considered as a matrix of SiO2 and HfO2 only, as this is usually assumed for hafnium silicates. In our case, we deal with a hafnium silicate matrix enriched with silicon as well as doped with Pr3+ ions.

Figure 1
Experimental RBS spectrum (points) and simulated curve using SIMNRA (solid line) for as-deposited film. Inset table is the chemical composition of the film. Inset figure is the refractive index evolution versus TA. The pure HfO2 and pure SiO2 indices ...

The inset of Figure Figure11 displays the refractive index evolution upon annealing treatment between 800°C and 1,100°C. The uncertainty of the refractive index is 0.01. Nevertheless, it was notable that it decreased with TA. In a previous study on as-deposited film, it was found that the refractive index was about 2.2 [8], exceeding the value corresponding to the stoichiometric HfSiO4 matrix (1.7) due to Si enrichment [8]. However, upon annealing, the refractive index is found to be about 1.85 (TA = 800°C) and 1.82 (TA = 1,100°C). If we exclude the decrease of porosity, this evolution could be explained by the increasing contribution of some phases with lower refractive index upon annealing (like SiO2 (1.46)) [8].

Figure Figure2a2a represents the evolution of the FTIR spectra as a function of TA. The FTIR spectrum of as-deposited film is represented by two broad vibration bands in the ranges of 500 to 750 and 800 to 1,200 cm−1. An annealing treatment stimulates the appearance of several bands that peaked at about 827, 1,084, and 1,250 cm−1 (dashed lines in Figure Figure2a)2a) corresponding to the LO2-TO2, TO3, and LO3 vibration modes of the Si-O bond, respectively. Moreover, the increase of the LO3 mode intensity is attributed to the increase in the number of Si-O-Si bonds. This is a signature of the formation of the SiO2 phase due to a phase separation process, leading to the decrease of the refractive index for TA ≥ 800°C.

Figure 2
FTIR spectra of samples and detailed spectra between 800 and 1,020 cm−1. (a) FTIR spectra of samples measured at Brewster’s angle (65°) as a function of TA for 1 h of nitrogen flow. Si-O bands are marked by dashed lines. (b) Detailed ...

This phase separation is confirmed also by an increase of the vibration mode intensity in the range of 600 to 780 cm−1, corresponding to Hf-O bonds for the formation of the HfO2 phase [7,14]. The appearance of well-defined peaks at 760 and 660 cm−1 for TA ≥ 1,050°C attests the presence of the monoclinic HfO2 phase [16]. Besides, for TA ≥ 1,050°C, two new absorption peaks that centered at 900 and 1,000 cm−1 appeared (detailed in Figure Figure2b).2b). As we showed earlier [8], at such temperature, undoped HfSiOx did not reveal the presence of Si-O-Hf bonds. Thus, the vibration band at 900 and 1,000 cm−1 can be attributed to Si-O-Pr asymmetric mode. Similar incorporation of rare-earth ions into Si-O bonds and the formation of rare-earth silicate phase was observed earlier for SiOx materials doped with Er3+, Nd3+, or Pr3+and annealed at 1,100°C [17-19]. Thus, based on this comparison, one can conclude about the formation of Pr silicate revealed by FTIR spectra.

To get more information about the evolution of film structure, we performed XRD analyses. For as-deposited and 900°C annealed films, XRD spectra show a broad peak in the range of 25.0° to 35.0° with a maximum intensity located at 2θ ≈ 31.0° (Figure (Figure3a).3a). The shape of the XRD peak demonstrates the amorphous nature of both layers. With TA increase, several defined peaks appear, emphasizing the formation of a crystalline structure. Thus, for TA = 950°C, intense XRD peaks at 2θ ≈ 30.3°, 35.0°, and 50.2° were detected. They correspond to the (111), (200), and (220) planes of the tetragonal HfO2 phase, respectively, confirming the FTIR analysis [8]. The peak at 2θ ≈ 60.0° can be considered as an overlapping of the reflections from the (311) and (222) planes of the same HfO2 phase. When TA reaches 1,050°C, the appearance of peaks at almost 2θ ≈ 24.6° and 28.5° occurs. The first peak is attributed to the monoclinic HfO2 phase (Joint Committee on Powder Diffraction Standards (JCPDS) no. 78–0050). The second one, at 28.5°, could be ascribed to several phases such as Pr2O3 (2θ[222] ≈ 27.699°) (JCPDS no. 78–0309), Pr6O11 (2θ[111] ≈ 28.26°) (JCPDS no. 42–1121), Si (2θ[111] ≈ 28.44°) (JCPDS no. 89–5012), or Pr2Si2O7 (2θ[008] ≈ 29.0°) (JCPDS no. 73–1154), due to the overlapping of corresponding XRD peaks. This observation is in agreement with the FTIR spectra (Figure (Figure2b)2b) showing the Hf-O vibrations and formation of Pr clusters.

Figure 3
XRD and SAED patterns. (a) XRD patterns of as-deposited and annealed films. (b) SAED pattern of the 1,100°C-annealed film. Table one is the d spacing list obtained from (b) and the corresponding phases.

In some oxygen-deficient oxide films [20,21], the phase separation is observed with the crystallization of the stoichiometric oxide matrix in the initial step and then in metallic nanoclustering. The aforesaid results are also coherent with our previous study of nonstoichiometric Hf-silicate materials in which we have evidenced the formation of HfO2 and SiO2 phases as well as Si nanoclusters (Si-ncs) upon annealing treatment [14,22]. To underline this point, we performed a TEM observation of 1,100°C annealed sample and observed a formation of crystallized Si clusters. Figure Figure3b3b exhibits the corresponding selected area electron-diffraction (SAED) pattern. The analysis of dotted diffraction rings indicates the presence of several phases. Among them, one can see the signature of monoclinic and tetragonal HfO2 phases, Pr2O3 phase, and crystallized Si phase (the Table one found in Figure Figure3b).3b). This latter confirms the presence of Si-ncs but in a small amount (a few spots on the corresponding ring).

Photoluminescence properties

Figure Figure4a4a shows the PL spectra of Pr3+-doped hafnium silicate films, which were excited by a 285-nm wavelength for Pr3+ ions. Remarkable emission is observed with peaks centered at about 475, 487, 503, 533, 595, 612, 623, 640, 667, 717, and 753 nm. They are associated to the Pr3+ energy level transitions 3P13H4, 3P03H4, 3P03H5, 1D23H4, 3P03H6, 3P03F2, 3P03F3, and 3P03F4, respectively, as shown in Figure Figure44b [23]. The maximum emission intensity corresponds to the peak centered at 487 nm due to the 3P03H4 transition.

Figure 4
PL spectra, schematics, and PL behavior. (a) PL spectrum in logarithmic scale for 1,000°C annealed layer. (b) The schematics of the Pr3+ intra-4f transitions. (c) PL spectra of the films annealed at different annealing temperatures (TA= 800°C ...

On the first step, the effect of annealing on Pr3+ PL properties was investigated (Figure (Figure4c).4c). The PL intensity evolution is shown in Figure Figure4d4d for the representative peak at 487 nm. The PL intensity increases with TA rising from 800°C up to 1,000°C and then decreases with further TA increase. At the initial stage, the annealing process is supposed to decrease the non-radiative recombination rates [24]. Thereafter, the quenching of the Pr3+ emission that occurred for TA > 1,000°C can be due to the formation of the Pr3+ silicate or Pr oxide clusters (Figure (Figure2)2) similar to the case observed in [17,18]. Moreover, it is interesting to note that the position of peak (Pr3+: 3P03H4) redshifts from 487 nm (TA ≤ 1,000°C) to 492 nm (TA = 1,100°C) as shown in Figure Figure4c.4c. At the same time, two split peaks contributed to the 1D23H4 transition that joined as one sharp peak which centered at 617 nm. All these results can be explained by the dependence of Pr3+ PL parameters on the crystal field associated with the type of Pr3+ environment [25]. Furthermore, the Pr3+ surrounding has been influenced by the crystallization of the HfO2 phase for films annealed at TA > 1,000°C.

Taking into account the formation of Si-ncs in Pr-doped HfSiOx samples annealed at 1,100°C for 1 h, one can expect the appearance of a PL emission due to exciton recombination inside Si-ncs, which is usually observed in the 700- to 950-nm spectral range [17,18]. However, our study of these samples did not reveal the Si-nc PL emission. Two reasons can be mentioned. The first one is the low density of Si-ncs, confirmed by the SAED pattern (Figure (Figure3b).3b). The second one is the efficient energy transfer from the Si-ncs to Pr3+ ions. However, based on the comparison of energetic diagrams of Pr3+ ions and Si-ncs, we observed that the energy levels of Si-ncs and Pr3+ ions have no overlapping. Thus, the energy transfer from Si-ncs toward Pr3+ ions should be very weak, contrary to an efficient sensitizing of other rare-earth ions such as Er3+ or Nd3+ in SiOx or HfSiOx matrices [23,24]. Thus, in the case of Pr-doped HfSiOx samples, Si-ncs do not seem to be a major actor for the energy transfer. Nevertheless, due to the low amount of Si-ncs, their PL signal is not detectable.

Thus, the second step of our investigation was to study the mechanism of Pr3+ energy transfer under the 285-nm excitation wavelength. The energy diagram of Pr3+ ions does not present such an absorption band wavelength at 285 nm (Figure (Figure4b).4b). In addition, the 4f to 5d transition is witted in upper energy level between 250 and 220 nm [26]. This evidences the indirect excitation of Pr3+ ions by the 285-nm wavelength and confirms an energy transfer behavior. To investigate this behavior in detail, we take interest in the strong background PL from 350 to 550 nm for the layers annealed at 800°C to 900°C in Figure Figure4c.4c. This broad band may be ascribed to more than one kind of defect [5,6,27]. For the layers annealed at higher TA such as 1,000°C, the intensity of this PL band drops deeply while the Pr3+ PL intensity increases notably. This suggests that the energy transfers from host defects to Pr3+ ions.

To understand this point, PLE spectra were recorded for the ‘optimized’ sample (annealed at 1,000°C) at different detection wavelengths (400, 487, and 640 nm, corresponding almost to the background emission for the former and to Pr3+ PL for the two latter), and they are presented in Figure Figure5.5. All the PLE spectra show a remarkable peak at about 280 nm (4.43 eV), and this peak position is in good agreement with that observed for oxygen vacancies [28]. According to some references [6,29], the O vacancies in the host matrix introduce a series of defect states (at about 1.85 to 4.45 eV) in the bandgap of HfO2, which might provide recombination centers for excited e and h pairs. These excitons can effectively transfer energy to the nearby Pr3+ ions due to the overlapping with absorption levels of Pr3+ and, thus, to enhance the Pr3+ PL emission. Therefore, the Hf-related O vacancies in the host matrix serve as effective sensitizers to the adjacent Pr ions. An additional argument for this interaction is the increasing of Pr3+ PL intensity with TA (from 900°C to 1,000°C) which caused the formation of HfO2 grains, providing more Hf-related O vacancies. However, due to a decomposition process, formation of the Si-rich phase (Pr-doped SiOx and/or Pr silicate) occurs too. The decrease of the intensity of the PL band that peaked at 400 nm and the increase of corresponding Pr3+ emission are a signature of the contribution of these Si-rich phase to the Pr3+ ion excitation (Figure (Figure44c).

Figure 5
PLE spectra in logarithmic scale for 1,000°C annealed layer detected for different emission peaks.

The excitation mechanism of Pr3+ ions was further explored by comparing two matrices. We carried out the PL experiments for three kinds of samples annealed at 1,000°C: undoped HfO2, undoped HfSiOx films, and Pr-doped HfSiOx films excited by a 285-nm source (Figure (Figure6).6). According to [6], in HfSiOx films, two types of O vacancies coexist: one is an O vacancy surrounded by Si atoms (Si-related O vacancy), while the other is an O vacancy surrounded by Hf atoms (Hf-related). Since the HfO2 phase is ionic, it is obvious that it forms easier in the HfSiOx film upon annealing, and thus, Hf-related O vacancy formation is most preferable than Si-related O vacancy [6]. Herein, a particular interest is focused on the emissions from the defects: the Pr-doped film shows a broad band peaked at 420 nm, while the peak positions redshift to about 450 and 490 nm for HfSiOx and HfO2 films, respectively. The 450-nm band can be fitted in energy into four Gaussian bands centered at 3.1, 2.84, 2.66, and 2.11 eV (table inset of Figure Figure6).6). The former two peaks are related to defects of the SiOx phase, for instance, Si-related oxygen deficient centers [13,28]. The peak at 2.66 eV is ascribed to O vacancies related to the HfO2 phase. The disappearance of the 2.66-eV PL component is accompanied with the appearance of the strong 487-nm emission and series of other Pr3+ transitions in Pr-doped HfSiOx film, which implies the energy transfer from O vacancies to the Pr sites.

Figure 6
PL spectra of Pr-doped and undoped HfSiOxand undoped pure HfO2films excited at 285 nm. The films were annealed at 1,000°C. Inset table is data of the fitting peaks.

As a result, the Si-rich HfO2 host not only serves as a suitable matrix to achieve efficient Pr3+ emission, but also provides a sufficient amount of O vacancies acting as effective sensitizers of rare-earth ions.

Conclusions

In summary, we have fabricated the Pr3+-doped hafnium silicate layers by RF magnetron sputtering. The effect of the annealing temperature on the film properties has been investigated by means of ellipsometry, XRD, and FTIR spectroscopies. We showed that the highest Pr3+ PL intensity is obtained for 1,000°C annealing. The PL and PLE measurements demonstrate that the Pr3+ ions were efficiently excited by oxygen vacancies in the films, and thus, remarkable Pr3+ PL can be obtained by a non-resonant excitation process. The present results show the promising application of Pr-doped films for future optoelectronic devices.

Competing interests

The authors declare that they have no competing interests.

Authors’ contributions

YTA fabricated the Pr-doped layers, carried out the characterization studies, as well as wrote the draft of manuscript. LK fabricated the undoped layers. MM performed the RBS measurements and refinements. XP performed the TEM study. CL and FG coordinated the study. All authors discussed and commented on the manuscript. All authors read and approved the final manuscript.

Acknowledgments

The authors would like to thank Dr. Ian Vickridge from SAFIR, Institut des NanoSciences de Paris for the RBS data as well as Dr. Sophie Boudin from CRISMAT Lab for the measurement of PL and PLE spectra. This work is supported by the CEA/DSM/ENERGY contract (Project HOFELI) and the Chinese Scholarship Council (CSC) program.

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