Constructing ultra-sensitive dual-mode optical thermometers: Utilizing FIR of Mn4&#x002B;/Eu3&#x002B; and lifetime of Mn4&#x002B; based on double perovskite tellurite phosphor

Li Li; Guang Tian; Yongsen Deng; Yongjie Wang; Zhongmin Cao; Faling Ling; Yanhong Li; Sha Jiang; Guotao Xiang; Xianju Zhou

doi:10.1364/OE.409242

1. Introduction

Optical thermometry technology based on rare earth (RE) and transition metal (TM) ions doped luminescent materials has attracted much attention thanks to non-contact, high spatial resolution, rapid response, and anti-electromagnetic interference [1,2]. In recent years, temperature-sensitive optical parameters, such as the luminescent intensity, spectral position, decay lifetime, bandwidth shift, and fluorescence intensity ratio (FIR) were adopted to measure temperature [3,4]. Especially, FIR and decay lifetime-based sensing of temperature independent of spectral losses, external interferences were attracted wide attention [5,6]. FIR strategy was usually concentrated on two thermally coupled levels (TCL) of RE, such as ²H_11/2 and ⁴S_3/2 states of Er³⁺, and non-thermally coupled levels are often adopted [7,8]. However, there are inherent limitations in this strategy such as low relative sensitivity and low signal discriminability owing to the restricted energy gap (200 <ΔE < 2000cm⁻¹⁾ [9,10]. For TM ions, although the luminescence intensity is very susceptible to variation of temperature owing to strong electron-phonon coupling, there are limitations in practicality [11]. Therefore, it is vital to design a new FIR temperature-sensing strategy and improve the performance of the optical thermometers.

A number of studies that showed that FIR strategy based on dual-emitting centers (such as Tb³⁺-Eu³⁺, Bi³⁺-Eu³⁺, Eu²⁺-Eu³⁺ and Pr³⁺-Tb³⁺, etc.) obeying diﬀerent temperature dependence has been proposed [12,13]. This FIR strategy gives high relative sensitivity owing to independent of energy gap spacing [14,15]. To obtain a high dramatic variation of FIR value with temperature, choosing suitable dopant ions and matrix is very crucial. It was known that RE ions with 4fⁿ electronic conﬁgurations have a weak electron-lattice interaction, whereas TM ions as well as 3dn conﬁgurations possess a strong electron-phonon coupling. Consequently, different thermal quenching were achieved for RE and TM ions. TM/Ln dopants exhibit high feasibility for a FIR optical thermometer [16–18]. In order to realize it, considerable research efforts have been devoted to develop appropriate hosts to achieve efficient dual emissions for both RE and TM activators. Moreover, decay lifetime-based thermometry have attracted enormous attention, which is independent of calibration measurement and insusceptible to external electromagnetic interference [19,20]. Generally, RE³⁺ (Eu³⁺, Sm³⁺) and TM³⁺ (Mn⁴⁺, Cr³⁺) doped phosphors, nanocrystals, and glass ceramics were beneficial for decay lifetime-based optical thermometers [21,22]. Thus, it is very necessary for exploring novel dual-mode optical temperature sensors based on the FIR of TM³⁺/ RE³⁺ and the lifetimes of TM³⁺ ions.

As we all know, perovskite materials are well-known for its versatile optoelectronic applications in light-emitting diodes, solar cells, photon detection, photocatalyst and temperature sensor [23]. Cation substitution based on the A-site or B-site of the basic ABX₃ structure of the perovskites accommodate for novel materials with fascinating properties. Especially, double perovskite compounds such as A₂BB′O₆, AA′BB′O₆, and AA′B₂O₆ were extensively investigated owing to allowing for various radii and valence state ions [24]. Much work so far has focused on Mn⁴⁺ and RE³⁺ (Eu³⁺, Dy³⁺) doped double perovskite phosphor. Yin et al. have reported on double perovskite A₂LaNbO₆:Mn⁴⁺,Eu³⁺ and BaLaMgNbO₆:Mn⁴⁺,Dy³⁺ phosphors for the application of optical temperature sensing [25,26]. Tellurates are intrigued to consider as host materials for optoelectronic applications owing to excellent chemical stabilities and lower phonon energy. The structure of SrLnLiTeO₆ (Ln = La, Gd, Eu) was pointed out that smaller radius of A site in the SrLnLiTeO₆ would result in bigger structure distortion [27]. Subodh has reported the phonon energy of ALaLiTeO₆ (A = Ba, Sr) and showed that smaller phonon energy (725 cm^-1) can suppress non-radiative multi-phonon transition, which indicating that these materials can be regarded as good luminescent matrix materials [28]. The crystal structure, luminescent properties and thermal quenching of Eu³⁺ doped SrLnLiTeO₆ (Ln = Gd, La) phosphors had been investigated [29,30]. However, Mn⁴⁺ doped SrLnLiTeO₆ (Ln = Gd, La) phosphors have not yet been investigated. Furthermore, the temperature sensing based on decay lifetime for Sm³⁺ doped Lu₂MoO₆ and Tb³⁺,Eu³⁺ codoped Ca₈ZnLa(PO₄)₇ phosphors was already investigated in our previous work [31,32]. However, to the best of knowledge, the temperature sensing based on fluorescent intensity ratio of Mn⁴⁺/RE³⁺ and decay lifetimes of Mn⁴⁺ for SrLnLiTeO₆ phosphors have not yet been investigated so far.

Herein, in view of this, we chose the SGLT as the matrix. The novel Mn⁴⁺, Eu³⁺ singly and codoped SGLT phosphors were synthesized by a facile high-temperature solid-state reaction method. The lifetime of Mn⁴⁺ and the FIR of Mn⁴⁺ and Eu³⁺ are both susceptible to temperature and are independent on measurement conditions and smaller measurement errors such as excitation power fluctuation, geometry change of the sample, and atmospheric pressure change, etc., so the dual-mode non-contact optical thermometry strategy was constructed based on fluorescent intensity ratio of Mn⁴⁺/Eu³⁺ and luminescence decay lifetimes of Mn⁴⁺. The dual-mode temperature readout can provide more accurate measurement than readout using only one type. The experimental results demonstrate that the resultant SGLT: Mn⁴⁺, Eu³⁺ phosphors have promising application in self-referencing optical thermometers. It was believed that this work provides a guidance for the exploration of well-performing temperature sensors.

2. Experimental

Mn⁴⁺, Eu³⁺ singly and codoped SGLT phosphors were prepared by high temperature solid state reaction method. The SrCO₃, Li₂CO₃ (Analytical Reagent (A.R.)), TeO₂ (A.R.), Gd₂O₃ (99.99%), Eu₂O₃ and MnCO₃ (99.99%) were the raw materials. All powders with stoichiometric molar ratio were weighed and ground finely in an agate mortar. Subsequently, the powders were further calcined at 1300 °C for 8 hours in a muffle furnace. Finally, the resultant phosphors were obtained. The X-ray diffraction (XRD) patterns of all phosphors were examined by a powder diffractometer XD-2 (Persee General Instrument Co., Ltd., Beijing) with CuK_α radiation (λ=1.5406 Å). The morphology and elemental composition were recorded by a field-emission scanning electron microscope (Hitachi, SU3500) with an attached energy dispersive X-ray (EDX) spectrometer. The room temperature excitation, emission spectra as well as luminescence decay kinetics were measured with a FLS1000 steady state spectrometer (Edinburgh Instrument Ltd., Livingston, UK). The temperature-dependent PL spectra and luminescence decay curves with the range of 298-573 K were measured using the same spectrometer equipped with high temperature attachments.

3. Results and discussion

The XRD patterns of SGLT, SGLT: 5%Eu³⁺, SGLT: 0.7%Mn⁴⁺, and SGLT: 5%Eu³⁺, 0.7%Mn⁴⁺ phosphors were measured and shown in Fig. 1(a). It can be found that the structure of these phosphors is identical with that of SrEuLiTeO₆ (JCPDS card no.80-0078), which belongs to the B site ordered double perovskite of AA′BB′O₆ structures [29]. The prepared SGLT phosphors possess monoclinic structure with space group P21/n. The crystal structure of samples was not changed by doping Eu³⁺ and Mn⁴⁺, manifesting that the solid solution was obtained. Additionally, a new minor Li₃Eu₃Te₂O₁₂ (JCPDS no. 25-1178) impurity phase (marked with *) can be found in the XRD patterns of the SGLT: 5%Eu³⁺ and SGLT: 5%Eu³⁺,0.7%Mn⁴⁺ samples and was very weak to be neglected. The crystal structure of SGLT was shown in Fig. 1(b). The Li and Te atoms for the B-site cations were both coordinated by six O atoms with B-site rock-salt ordering structure, which presented octahedral centers appropriate for doping Mn⁴⁺ ions in the SGLT host. The Sr²⁺,Gd³⁺/Eu³⁺ cations occupy the A sites at random and form A-site layered ordering structure. Furthermore, the ions radii of Te⁶⁺ and Mn⁴⁺ (coordinated number (CN) =6) are 0.56 Å and 0.53 Å, respectively, indicating that the Mn⁴⁺ ions substituted for Te⁶⁺ ions in the SGLT matrix [33]. Eu³⁺ ions occupy without inversion center and prefer to replace for the Gd³⁺ ions owing to the similar radii between Eu³⁺ (r=1.12 Å, CN=9) and Gd³⁺ (r=1.107 Å, CN=9), which is beneficial for Eu³⁺ luminescence.

Fig. 1. XRD patterns of SGLT, SGLT: 0.7%Mn⁴⁺, SGLT: 5%Eu³⁺ and SGLT: 5%Eu³⁺, 0.7%Mn⁴⁺ compared with ICSD no. 067852 of SrEuLiTeO₆ (a).The crystal structure of SGLT (b).

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The emission spectra of SGLT: x%Mn⁴⁺ (x = 0.1, 0.3, 0.5, 0.6, 0.7, 0.8) phosphors under 302 nm excitation are shown in Fig. S1. As expected, the dominant red emission band centered at 695 nm is assigned to the²E_g→⁴A_2g transition of Mn⁴⁺. It was shown that the emission intensity at 695 nm increases initially as a consequence of increased amount of Mn⁴⁺ and reaches maximum when the doping concentration is 0.7%, and subsequently decreases due to the concentration quenching effect at higher Mn⁴⁺ concentrations. Therefore, the Mn⁴⁺ doping concentration was fixed at 0.7%. In order to investigate the room temperature and temperature-dependent luminescent properties, the excitation and emission spectra of singly doped Eu³⁺, singly doped Mn⁴⁺, and Eu³⁺, Mn⁴⁺ codoped SGLT samples were recorded as shown in Fig. 2, respectively. As depicted in Fig. 2(a), the excitation spectrum (the blue line) of Eu³⁺ single-doped SGLT monitored at 615 nm includes a wide excitation band and a few of sharp excitation peaks. The broad excitation band centered at 292 nm in the range from 243 nm to 334 nm was assigned to the overlap of Eu-O and Te-O charge transfer state. While the sharp excitation peaks located at 362 nm (⁷F₀→⁵D₄), 377 nm (⁷F₀→⁵L₇), 382 nm (⁷F₀→⁵L₈), 385 nm (⁷F₀→⁵G_J), 395 nm (⁷F₀→⁵L₆), 416 nm (⁷F₀→⁵D₃), 465 nm (⁷F₀→⁵D₂), 527 nm (⁷F₀→⁵D₁), 535 nm (⁷F₁→⁵D₁) are due to the characteristic excitation of the intra-4f transition of Eu³⁺, respectively [34]. The photoluminescence spectrum (The red line) of Eu³⁺ single-doped SGLT excited by 302 nm appears two dominant emission peaks centered at 591 nm and 615 nm, which belong to the ⁵D₀→⁷F₁ magnetic transition and ⁵D₀→⁷F₂ electric transition of Eu³⁺, respectively. As depicted in Fig. 2(b), the excitation spectrum monitored at 695 nm of Mn⁴⁺ single-doped SGLT are composed of two broad excitation bands, one band centered at 323 nm is corresponding to the Mn-O charge transfer and the transition of Mn⁴⁺: ⁴A_2g→⁴T_1g. The other one with strongest excitation at 468 nm is attributed to Mn⁴⁺: ⁴A_2g→⁴T_2g. Under the excitation of 302nm, the emission spectrum presents an emission band ranging from 641 nm to 794 nm with the strongest emission at 695 nm, which belongs to the ²E_g→⁴A_2g transition of Mn⁴⁺ [35]. Figure 2(c) reveals the excitation and emission spectra of Eu³⁺, Mn⁴⁺ codoped SGLT sample. The excitation spectra exhibits the spectral overlap monitored at 615 nm of Eu³⁺ and 695 nm of Mn⁴⁺ ions, making probable of simultaneous excitation of Mn⁴⁺ and Eu³⁺ ions under 302 nm excitation. Therefore, the emission spectrum at 302 nm excitation includes two emission peaks centered at 591 nm and 615 nm originating from the ⁵D₀→⁷F_1,2 transitions of Eu³⁺ and the emission band of 695 nm owing to the ²E_g→⁴A_2g transition of Mn⁴⁺, respectively.

Fig. 2. Excitation and emission spectra of SGLT: 5%Eu³⁺ (a), SGLT: 0.7%Mn⁴⁺ (b) and SGLT: 5%Eu³⁺,0.7%Mn⁴⁺ (c) phosphors.

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The emission spectra of SGLT:5%Eu³⁺,0.7%Mn⁴⁺ phosphor with the temperature of 300-550 K were displayed in Fig. 3(a). It can be observed that both the Eu³⁺ and Mn⁴⁺ intensities declined with elevating temperature owing to thermal quenching effect. Notably, the ²E_g→⁴A_2g emission intensity of Mn⁴⁺ decreases much more rapidly as compared with that of the ⁵D₀→⁷F₂ and⁵D₀→⁷F₁ intensities of Eu³⁺ with the increase of temperature. Therefore, Eu³⁺ serves as a natural self-referencing for thermal decay of Mn⁴⁺ so that the self-referencing optical thermometry of Mn⁴⁺/Eu³⁺ can be constructed. The two-dimensional fluorescence topographical mapping of SGLT: 5%Eu³⁺,0.7%Mn⁴⁺ under 302 nm excitation was shown in Fig. 3(b). Apparently, the intensities of Eu³⁺ and Mn⁴⁺ can recover after one cycle process (300K→550K→300 K), indicating the repeatability and reliability of the SGLT: 5%Eu³⁺,0.7%Mn⁴⁺ sample for optical thermometry.

Fig. 3. Temperature-dependent emission spectra (a) and two-dimensional fluorescence topographical mapping (b) of SGLT:5%Eu³⁺,0.7%Mn⁴⁺ under 302 nm excitation in the temperature range from 300 K to 550 K.

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To gain more insight into the temperature sensing, the integrated intensities of Eu³⁺: ⁵D₀→⁷F_1,2 and Mn⁴⁺: ²E_g→⁴A_2g dependence on temperature were displayed in Fig. 4(a,d), respectively. The variation of the FIR₁ of Eu³⁺: ⁵D₀→⁷F₁ (577-602 nm) and Mn⁴⁺: ²E_g→⁴A_2g (637-775 nm) and FIR₂ of Eu³⁺:⁵D₀→⁷F₂ (604-633 nm) and Mn⁴⁺: ²E_g→⁴A_2g (637-775 nm) dependence on temperature are shown and fitted in Fig. 4(b, e), respectively. Obviously, the FIR_1,2 of Eu³⁺: ⁵D₀→⁷F₁ (577-602 nm), ⁵D₀→⁷F₂ (604-633 nm) and Mn⁴⁺: ²E_g→⁴A_2g (637-775 nm) exhibits the linear dependence on temperature. Consequently, the temperature dependence on decay curve can be respectively expressed by the following Eqs. (1) and (2):

(1)$$FI{R_1} ={-} 0.094T + 53.929$$

(2)$$FI{R_2} ={-} 0.018T + 10.033$$

where FIR_1,2 is the intensity ratio and T is the temperature (K). In order to evaluate the performance of temperature sensing, the absolute sensitivity (S_A1,2) and relative sensitivity (S_R1,2) are displayed in Fig. 4(c, f) and estimated by the following formulas [36]:

(3)$${S_A}_1 = \left|{\frac{{d(FIR)}}{{dT}}} \right|= 9.46\%{K^{ - 1}}$$

(4)$${S_{R1}} = \left|{\frac{1}{{FIR}} \times \frac{{d(FIR)}}{{dT}}} \right|= \frac{{0.09455}}{{ - 0.09455T + 53.92894}} \times 100\%{K^{ - 1}}$$

(5)$${S_{A2}} = \left|{\frac{{d(FIR)}}{{dT}}} \right|= 1.76\%{K^{ - 1}}$$

(6)$${S_{R2}} = \left|{\frac{1}{{FIR}} \times \frac{{d(FIR)}}{{dT}}} \right|= \frac{{0.01758}}{{ - 0.01758T + 10.03374}} \times 100\%{K^{ - 1}}$$

Fig. 4. The integrated intensities of Eu³⁺: ⁵D₀→⁷F₁(577-602 nm) and Mn⁴⁺: ²E_g→⁴A_2g(637-775 nm) (a). Temperature-dependent intensity ratio of Mn⁴⁺/Eu³⁺(695/591) and the fitted curve (b). The relative sensitivity S_R (blue line) and the absolute sensitivity S_A(red line) as a function of temperature (300–550 K) (c).The integrated intensities of Eu³⁺ ⁵D₀→⁷F₂(604-633 nm) and Mn⁴⁺ ²E_g→⁴A_2g(637-775 nm) (d). Temperature-dependent intensity ratio of Mn⁴⁺/Eu³⁺ (695/615) and the fitted curve (e). The relative sensitivity S_R (blue line) and the absolute sensitivity S_A (red line) as a function of temperature (300–550 K) (f).

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Fig. 5. Temperature-dependent decay curves of Mn⁴⁺ ions monitored at 695 nm and excited at 302 nm(a), 362 nm(d) and 465 nm (g). The lifetimes as a function of temperature under 302 nm (b), (e) 362 nm and (h) 465 nm excitation. The relative sensitivity S_R as a function of temperature based on the lifetimes of Mn⁴⁺ upon 302 nm (c), 362 nm(f) and 465 nm (i) excitation.

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According to Eqs. (3–6), the absolute (S_A) and relative (S_R) sensitivities based on FIR of ⁵D₀→⁷F₁ (577-602 nm)/²E_g→⁴A_2g (637-775 nm) and ⁵D₀→⁷F₂ (604-633 nm)/ ²E_g→⁴A_2g (637-775 nm) for the SGLT: 5%Eu³⁺,0.7%Mn⁴⁺ phosphor are calculated to be 9.46%K^-1, 4.9%K^-1@550 K and 1.76%K^-1,4.8%K^-1@550 K, respectively. It was worthwhile to mention that these S_A and S_R values are superior to many other TM³⁺ / RE³⁺ codoped systems, such as 4.37% K^-1 for Ce³⁺/Mn⁴⁺ doped Lu₃Al₅O₁₂ [16], 2.08% K^-1 for Mn⁴⁺/Eu³⁺ doped Ba₂LaNbO₆ [25], 1.51% K^-1 for Mn⁴⁺/Eu³⁺ doped Ca₂LaNbO₆ [25], 4.3% K^-1 for Mn⁴⁺/Tb³⁺ doped Lu₃Al₅O₁₂ [37], 0.86% K^-1 for Mn⁴⁺/Eu³⁺ doped NaLaMgWO₆ [38], and 1.82% K^-1 for Mn⁴⁺/Dy³⁺ doped BaLaMgNbO₆ [39]. Moreover, the temperature uncertainty (ΔT) is also a crucial parameter to evaluate the temperature sensing of materials, and its value can be evaluated by the following Eq. (7) [40]:

(7)$$\Delta T = \frac{1}{{{S_R}}}\frac{{\delta FIR}}{{FIR}}$$

where δFIR/FIR is the relative error in FIR measurement whose value is approximately 0.5%. The relative sensitivity S_R1 and S_R2 is 4.9%K^-1@550 K and 4.8%K^-1@550 K, respectively.

Therefore, the minimum temperature resolution was both evaluated to be about 0.1K at 550 K for SGLT: 5%Eu³⁺,0.7%Mn⁴⁺ phosphor. These results indicate that SGLT: Eu³⁺,Mn⁴⁺ phosphor is a promising temperature sensing material and exhibits a good temperature resolution.

Both the FIR of Mn⁴⁺ and Eu³⁺ and the lifetime of Mn⁴⁺ are sensitive to temperature, thus a temperature sensing mode based on lifetime was conducted. Figure 5 (a, d, g) shows the fluorescence decay curves of SGLT: 5%Eu³⁺, 0.7%Mn⁴⁺ sample excited at 302 nm, 362 nm and 465 nm, monitoring the emission of Mn⁴⁺ at 695 nm from 300K to 550K. As presented, it was found that under different excitations, electrons are excited from the ground state ⁴A_2g to different excited states, such as ⁴T_1g or ⁴T_2g states. For various excited states, the rate of falling to²E_g is various, resulting in different lifetime of Mn⁴⁺ ions. In addition, it was supposed that the lifetime quenching can be assigned to the increment of non-radiative transition with the increase of temperature, which was attributed to the enhancement of electron-phonon coupling originating from no shielding for 3d electrons of Mn⁴⁺. Initially, the decay curves can be fitted by a double exponential function at low temperature. With elevating the temperature, the non-exponential decay curves gradually become obvious and the average lifetimes are evaluated by the following equation [41]:

(8)$${\tau _m} = \frac{{\int_0^\infty {t \times I(t)dt} }}{{\int_0^\infty {I(t)dt} }}$$

where I(t) is the luminescence intensity at a time t. It was seen that the rise of temperature results in the continuous decrease of lifetimes, which implies that the resultant phosphor is promising in application for thermometers. As we all know, cross-over model and Struck-Fonger model can be used to describe the relation between lifetime and temperature [20,42]. In our case, the temperature dependence on decay lifetimes can be more accurately fitted using Struck-Fonger model as follows:

(9)$$\tau (T) = \frac{{{\tau _0}}}{{1 + A\exp (\frac{{ - \Delta E}}{{kT}})}}$$

Where τ₀ and τ(T) are the initial lifetime at room temperature and a certain temperature T, respectively; k is Boltzmann’s constant (0.69503 cm^-1.K^-1); A is a constant, and ΔE is the thermal-quenching activation energy.

The lifetime dependence on temperature under different excitation wavelengths can be well fitted by Eq. (8), as shown in Fig. 5(b, e, h). Under 302, 362 and 465 nm excitation, the ΔE were determined to be 0.25(≈ 2016 cm^-1), 0.31(≈ 2500 cm^-1), and 0.21 eV (≈ 1694 cm^-1), respectively, while the corresponding A values were estimated to be 295, 1791.58, and 76.43, respectively. Therefore, the relative temperature sensitivity (S_R) derived from decay lifetime dependence on temperature can be expressed as the following equation [43]:

(10)$${S_R} = \left|{\frac{1}{\tau }\frac{{d\tau }}{{dT}}} \right|\times 100\%= \frac{{A\exp ( - \varDelta E/kT)}}{{1 + A\exp ( - \varDelta E/kT)}} \times \frac{{\varDelta E}}{{k{T^2}}} \times 100\%$$

The obtained S_R values calculated from Eq. (9) are displayed in Fig. 5(c, f, i). Obviously, the S_R values monotonously increase with elevating temperature ranging from 298-573K, the maximum S_R is 0.158%, 0.229%, and 0.104% K^-1@ 573K, respectively. It is worthwhile mentioning that the S_R value can be modulating by changing excitation wavelengths and the S_R values were comparable to those of previously based on decay lifetimes, such as ZrO₂:Eu³⁺(0.33%K^-1) [19], YAlO₃:Cr³⁺(0.19%K^-1) [44], Ca₃Mo_0.2W_0.8O₆:Eu³⁺ (0.142% K^-1) [5] and YNbO₄:Sm³⁺ (0.43%K^-1) [45]. Hence, these results indicated that SGLT: Eu³⁺, Mn⁴⁺ phosphors are promising candidates for non-contact optical thermometers using FIR and lifetime-based temperature readout.

4. Conclusion

A dual-mode optical thermometry based on FIR of dual-emitting Mn⁴⁺, Eu³⁺ for SGLT phosphor and decay lifetime was constructed. The double perovskite Mn⁴⁺, Eu³⁺ codoped SGLT phosphors were obtained by high-temperature solid-state reaction method. Under 302 nm excitation, the luminescent intensity of Mn⁴⁺ dropped faster than that of Eu³⁺ with the increase of temperature, so the resultant phosphors exhibit an excellent temperature sensing properties due to different thermal behaviors of Mn⁴⁺ and Eu³⁺.The maximum absolute and relative sensitivity based on FIR of ⁵D₀→⁷F₁ (577-602 nm)/²E_g→⁴A_2g (637-775 nm) were as high as 9.46%K^-1 and 4.9%K^-1@550 K, respectively. Moreover, the decay lifetime of Mn⁴⁺ can be used for temperature sensing and the maximum relative sensitivity was 0.229%@ 573K.These results demonstrate that SGLT: Mn⁴⁺, Eu³⁺ phosphor has its promising potential in temperature measurement and provides a guidance for exploring temperature sensors with high sensitivity.

Funding

Chongqing Municipal Education Commission (KJZD-M202000601); National Natural Science Foundation of China (11674044, 11704054, 12004061, 12004062); Natural Science Foundation of Chongqing (CSTC 2019jcyj-msxm1208); Venture and Innovation Support Program for Chongqing Overseas Returnees (CX2019085).

Disclosures

The authors declare no conflicts of interest.

See Supplement 1 for supporting content.

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Constructing ultra-sensitive dual-mode optical thermometers: Utilizing FIR of Mn⁴⁺/Eu³⁺ and lifetime of Mn⁴⁺ based on double perovskite tellurite phosphor

Abstract

1. Introduction

2. Experimental

3. Results and discussion

4. Conclusion

Funding

Disclosures

References

Supplementary Material (1)

Cited By

Figures (5)

Equations (10)

Optics Express