Novel optical temperature sensor based on emission in Pr3+ doped ferroelectric Ba0.7Sr0.3TiO3.

Optical temperature sensing based on the variation of the fluorescence intensity ratio of rare-earth materials has become appealing due to its multiple superiorities over electrical temperature sensing. However, confined by the largest energy separation of two thermally linked levels of rare earth ions, the highest sensitivity of such temperature sensing is essentially smaller than 2878/T 2, as reported previously from diverse systems. In this work, we demonstrate that ultrahigh-sensitive temperature sensing can be achieved from Pr3+-doped (Ba0.7Sr0.3)TiO3 based on the intensity ratio of the 1D2-3H4 emission to the 3P0-3H4 emission. The ratio can be increased as much as 90-fold when the temperature rises from room temperature to 513 K, nicely fitting a thermally linked-levels like equation and showing an ultrahigh sensitivity of 4275.1/T 2. The striking change of the ratio is attributed to the interaction between the two emission levels and the intervalence charge transfer state. This work may have provided a distinct route in the field of optical temperature sensing utilizing rare-earth-doped materials. In addition, the resultant product also possesses excellent photoluminescence and ferroelectric properties, showing promising potentials in multifunctional devices for practical applications. This journal is © The Royal Society of Chemistry.

Introduction

Currently, the optical thermometric technique based on the fluorescence intensity ratio (FIR) in a phosphor material is attracting intensive investigations, for its advantages such as non-contact, rapid response, and high spatial/temperature resolutions that facilitate temperature detecting for harsh environments or fast moving objects.[1-7] Most of the previous thermometric material studies focus on the thermally coupled level-pairs (TCL) of rare earth ions (for example, 2H11/2, 4S3/2 levels of Er3+; 3F2,3, 3H4 levels of Tm3+; and 4F7/2, 4F3/2 levels of Nd3+).[8-13] In a definite TCL phosphor, population at the upper and lower levels of TCL would change oppositely with increasing temperature, inducing variation in the FIR of these two levels. For this type of thermometric material, to avoid exceedingly low upper-level populations, it is widely accepted that the energy separation of the two thermally linked levels of rare-earth ions is less than 2000 cm−1,[14-16] which essentially confines the highest value of S to no larger than 2878/T2. Indeed, all the reported S values from diverse rare earth ions, e.g., Tm3+, Nd3+, Eu3+, Dy3+, Ho3+, and Er3+, are smaller or comparable to this value.[11,12,16-20] The limited S is apparently a big obstacle for the further promotion and practical application of optical sensors based on the fluorescence intensity ratio of rare-earth materials.

Recently, besides searching for excellent TCL thermometric materials, great efforts have also been made to develop a new thermometric strategy. For example, the phonon assisted energy transfer between Tb3+ and Eu3+ ions has been employed in optical thermometry.[1,5,21] This thermometric strategy provides better signal discriminability, but is only applicable at a temperature below 320 K. Quantum dots decorated by lanthanide–organic complexes have also been applied as thermometric materials relying on the different thermal quenching behaviors between quantum dots and lanthanide ions. However, the FIR of these quantum dots is easily influenced by the other environment parameters such as acidity and alkalinity, which would introduce errors in practical temperature detection.[22,23]

It is known that some lanthanide ions (Pr3+ or Tb3+) and the d0 electron configured transition metal ions (Mn+ = Ti4+, V5+, Nb5+, Ta5+, Mo6+ or W6+) in an oxide host could form the so-called metal-to-metal intervalence charge transfer (IVCT) state, which would interfere in emission of the f levels in the lanthanide ions, and therefore introduce a high temperature-dependence for the luminescence.[24-26] Meanwhile, in our previous work, we demonstrated that the IVCT mechanism plays a key role in Pr3+-doped (K0.5Na0.5)NbO3 optical oxygen sensing; the decreased energy position of the IVCT state with the increased oxygen concentration induced the enhanced 1D2–3H4 emission and decreased 3P0–3H4 emission, leading to the large oxygen sensing response of both the absolute 1D2–3H4 emission intensity and the 1D2–3H4/3P0–3H4 intensity ratio.[27] Based on these researches, a novel temperature sensing strategy that utilizes the IVCT state interfered Pr3+ luminescence to perform optical thermometry is proposed.

As an important member of ferroelectric materials, studies of (Ba, Sr)TiO3 materials have been a widely welcomed topic due to their high permittivity, low dielectric loss, high tunability coefficient, quick reaction velocity, anti-breakdown ability and simple fabrication process, etc. Meanwhile, among many advantages is the fact that the (Ba, Sr)TiO3 family is lead-free, and therefore compliant with nowadays requirements for environmentally benign materials.[28] Moreover, (Ba, Sr)TiO3 contains one kind of IVCT (i.e., Pr3+–Ti4+ IVCT). In this work, we studied the photoluminescence and ferroelectric properties of Pr3+ doped Ba0.7Sr0.3TiO3. The temperature sensor dependence on the fluorescence intensity ratio of the traditional thermally linked 3P1–3H5 and the 3P0–3H5 emissions has been studied, which sensitivity is not that significant.[29,30] Remarkably, FIR of the Pr3+ 3P0 and 1D2 emissions exhibits high temperature dependence, the intensity ratio of the 1D2–3H4 emission to the 3P0–3H4 emission at 513 K can be increased to as high as 90-fold of that at room temperature, and this temperature-dependent ratio can be nicely fitted by a thermally linked-levels-like equation, strikingly showing an ultrahigh S of 4271.1/T2, which is about 150% of the upper limit of S as introduced above. The configurational coordinate diagram is applied to analyze the mechanism of the temperature-dependent luminescent characteristics, and thermo-induced relaxation between the Pr3+ 3P0 and 1D2 levels through the IVCT state is further demonstrated to be the primary cause for the temperature sensing performance of Pr3+-doped Ba0.7Sr0.3TiO3. Meanwhile, it is revealed that doping with Pr3+ can further promote the ferroelectric performance of Ba0.7Sr0.3TiO3. Integrating with the excellent PL and ferroelectric properties, the ultra-high sensitivity on temperature sensing of Pr3+-doped Ba0.7Sr0.3TiO3 not only indicates its remarkable potentials in multifunctional devices, but also may have opened up a distinct and fresh route in the field of highly sensitive optical temperature sensing utilizing rare-earth-doped materials.

Experimental

Ba0.7Sr0.3TiO3 (BST) and Ba0.7Sr0.295Pr0.005TiO3 (BST:Pr3+) nanoparticles were synthesized by a hydrothermal method. Firstly, 40 ml aqueous solution of strontium nitrates and barium nitrates (1.119375 mol L−1, 99%, Aladdin) and praseodymium nitrates (0.005625 mol L−1, 99%, Aladdin) were mixed with 23 ml ethanol solution of tetrabutyl titanate (1.25 mol L−1, 99%, Aladdin). The pH value of the mixed solution was adjusted to be 13.5 by adding NaOH. The reactive solution was then sealed in a Teflon autoclave at 200 °C for 48 h. After cooling down to room temperature, the obtained product was thoroughly washed by deionized water and ethanol, eventually dried overnight in air.

The crystallization nature and morphology of the samples were characterized using powder X-ray diffraction (Rigaku D/MAX-2600/PC with Cu Kα radiation) and scanning electron microscopy (SEM; JEOL 6700F). Photoluminescence (PL) and photoluminescence excitation (PLE) spectra of the samples were measured using a spectrofluorometer (HORIBA, Fluoromax-4). The polarization vs. electric field (P–E) hysteresis loop was obtained at 50 Hz using a Precision Premier II tester (Radiant Technology USA) at room temperature (30 kV cm−1).

Results and discussion

Fig. 1 present XRD patterns of BST and BST:Pr3+ samples. All the peaks in the spectra can be assigned to the BST host structure (PDF#89-0274), and no phases related to impurities were observed. A SEM image of the as-prepared BST:Pr3+ sample is shown in the inset of Fig. 1. The average size of these particles is about 60 nm. All these nanoparticles of BST and BST:Pr3+ samples appear quasi-spherical morphology with a similar size.

Fig. 1

XRD patterns of BST and BST:Pr3+ nanoparticles. SEM image of the BST:Pr3+ nanoparticles is presented in the inset.

According to the PL of BST and BST:Pr3+ (ESI Fig. S1†). The intrinsic BST almost have no PL properties relative to BST:Pr3+, it can be inferred that the PL of BST:Pr3+ is derived from Pr3+. Fig. 2 shows PL and PLE spectra of BST:Pr3+ samples normalized by their maximum intensity. Under 325 nm excitation, the PL spectrum showed a strong blue-green emission at 490 nm (3P0–3H4), a strong red emission at 602 nm (1D2–3H4), together with two weak green emissions at 530 nm (3P1–3H5) and 547 nm (3P0–3H5) and two weak red emissions at 617 nm (3P0–3H6) and 651 nm (3P0–3F2). The PLE spectra monitored at 490 nm and 602 nm were exhibit a broad bands centered at 392 nm, which can be attributed to the BST host absorption and the IVCT absorption.[31,32] Besides, the sharp peak at 450 nm is ascribed to 3H4 → 3P2 transition of Pr3+.

Fig. 2

PL spectrum of the BST:Pr3+ nanoparticles with an excitation of 325 nm and its PLE spectra monitored at 490 nm and 602 nm.

The variation of emissions of BST:Pr3+ with the temperature over the 290 to 513 K is depicted in Fig. 3, it can be observed that the peak positions of these emission bands are hardly changed and the absolute intensities decrease gradually with temperature. The relative emission intensities for 531 and 547 nm, 490 and 602 nm emissions respond differently to the change of temperature. The intensity of two peaks corresponding to 531 nm (3P1–3H5) and 547 nm (3P0–3H5) transitions at different temperatures are shown in Fig. 4(a). It is obvious from Fig. 4(a) that the intensity of the peak 3P1–3H5 decreases more rapidly compared to 3P0–3H5 due to the thermal agitation. The 3P1 and 3P0 states of Pr3+ are closely spaced with a separation of about 550 cm−1, which belong to TCL.[33] As a result, the FIR for the emissions from TCL of Pr3+ ions can be described as:[34,35]where the emission intensities for the 531 and 547 nm are I531 and I547, respectively. The values of c1(ν1) are related to the response of the detection system. A1, g1, hν1 and β1 are the spontaneous radiative rates, the degeneracy, the photon energy and the branching ratio, respectively, for transitions from the excited 3P1 and 3P0 levels to 3H5 state. B is a constant; ΔE12 is the effective energy difference between the 3P1 to 3P0 state; k is the Boltzmann constant; and T is the absolute temperature.

Fig. 3

PL of BST:Pr3+ nanoparticles at different temperatures under 325 nm excitation.

Fig. 4

(a) PL of the BST:Pr3+ nanoparticles at different temperature (normalized by the 3P0–3H5 emission intensity); (b) the intensity ratio of the 3P1–3H5 emission to the 3P0–3H5 emission as a function of temperature in the range of 293–403 K; (c) relative sensitivity as a function of temperature in the range of 290–403 K.

The temperature dependence of these emissions at 531 and 547 nm in the range of 290–403 K (Fig. 4(b)) show clear rise in FIR value with temperature, reaching a maximum value when the temperature approaches the maximal experiment temperature 403 K. From a curve fitting of the experimental data, the fitted constants B and ΔE12 are 21.25 and 518 cm−1. The fitted ΔE1 is close to the experimental value 550 cm−1. To further understand the temperature response of the BST:Pr3+, it is important to investigate the sensing sensitivity, this can be defined from:[34]

The sensitivity as a function of temperature (Fig. 4(c)) is 745.2/T2 and reach its maximum value of 0.015 K−1 at 375 K in the temperature range of interest, this phenomenon consist with other groups.[20,28] It can found that, the PL spectrum of 531 nm and 547 nm emissions is overlap, the precise intensity reading is not very convenient. And due to the rather small energy separation of the 3P1 to 3P0 state, only S as low as 745.2/T2 was obtained. So the thermally linked 3P1–3H5 and the 3P0–3H5 emissions are not suitable for the modern development of high performance temperature detection.

Revealed by PL spectra normalized by the 1D2–3H4 emission intensity (refer to Fig. 5(a)), the intensity of all the 3P0-related emissions was reduced much faster than that of the 1D2–3H4 emission upon the temperature rise. Fig. 5(b) presents the calculated intensity ratio of the 1D2–3H4 emission to the 3P0–3H4 emission by referring the maximum emission intensity at 602 nm and 490 nm in the PL spectra, as a function of temperature in the range of 293–513 K. Excitingly, a huge increase as high as 90 fold of the ratio was achieved when the temperature increased from room temperature to 513 K. The intensity ratio can be fit nicely with a thermally linked-levels-like equation, deducing an ultrahigh sensitivity of 4275.1/T2, which is not only ∼6 times higher than that of the optical sensors based on thermally linked 3P1 and 3P0 levels of Pr3+, but also much higher than all the reported optical sensors based on the fluorescence intensity ratio of rare-earth materials[8,9,13,29,34,39,40] (as listed in Table 1), where the highest sensitivity of 2878/T2 was anticipated. The sensitivity keeps increasing in our experimental temperature range and reaches the maximum value 1.055 K−1 at 513 K as shown in Fig. 5(c).

Fig. 5

(a) Emissions of BST:Pr3+ nanoparticles at different temperatures which normalized at 602 nm. (b) Ratio of emissions between 490 and 602 nm as a function of temperature in the range of 290–513 K. (c) Relative sensitivity as a function of temperature in the range of 290–513 K.

Summarized temperature sensing performance of rare-earth ions-doped materials

Rare-earth ion (host)	Transition	Sensitivity (K−1)	Temperature range (K)	Ref.
Pr3+ (BaSrTiO3)	3P0, 1D2 → 3H4	4275.1/T2	290–513	This work
Pr3+ (BaSrTiO3)	3P1, 3P0 → 3H5	745.2/T2	290–403	This work
Er3+ (BaTiO3)	2H11/2, 4S3/2 → 4I15/2	1026.8/T2	294–923	8
Nd3+ (oxyfluoride glass ceramic)	4F7/2, 4F3/2 → 4I9/2	3010.1/T2	303–623	9
Tm3+ (NaYbF4)	3F2,3, 3H4 → 3H6	2007.0/T2	323–773	13
Pr3+ (tellurite glass)	3P1, 3P0 → 3H5	879.9/T2	293–473	29
Pr3+ (β-NaYF4)	3P1, 3P0 → 3H5	675.7/T2	120–300	34
Dy3+ (Y4Al2O9 crystal)	4I15/2, 4F9/2 → 6H13/2	1709.4/T2	296–973	39
Ho3+ (BaTiO3-(Na0.5Ho0.5)TiO3)	5F4, 5S2 → 5I8	933.8/T2	80–600	40

Given that the energy separation between 3P0 and 1D2 (∼4000 cm−1) is apparently too large to promote the multiphonon relaxation between the two states, a new viewing angle is, therefore, required to understand the intensity ratio of the two emissions. Interestingly, it has been suggested that, there is a host-dependent IVCT state in Pr3+ doped titanates.[36-38] In our present work, we demonstrate the IVCT state can interfere with the excited states of Pr3+ including the 3P0 level and the 1D2 level, and induce the reduction of the Pr3+ emissions or/and provide a de-excitation pathway from the 3P0 level to the 1D2 state. For a clear illustration for this distinct phenomenon, we depict interactions between the IVCT state and Pr3+ ions in Fig. 6. Under 325 nm excitation, the electron in the valance band is transferred to the conduction band. After fast non-radiative relaxation, the electrons in conduction band relax to the IVCT and the 3P0 states simultaneously with different non-radiative rates. The electrons in IVCT state returns to the minimum potential energy position and rapidly transfers to the 3P0 and 1D2 state with the assistance of thermal phonons. Then we can obtain the blue and red light under 325 nm excitation as shown in Fig. 2. With the rising of temperature, electrons in 3P0 state not only transfer to 3H4 state, but also transfer to IVCT state by absorbs thermal energy. Then, these electrons in IVCT state relax to 1D2 level, which induce the electrons in 1D2 state increases relative to 3P0 state with the temperature raises, and the intensity ratio of 1D2–3H4/3P0–3H4 increases constantly. From the above, it can conclude that thermo-induced relaxation from the 3P0 to 1D2 level through the IVCT state is the primary cause for the high temperature-dependent FIR in BST:Pr3+. Although the mechanism deserves further investigation, the ultrahigh sensitivity based on the ratio of 1D2–3H4 and 3P0–3H4 emissions may have provided a fresh and favourable route for optical temperature sensing.

Fig. 6

Illustration of the temperature sensing mechanisms of the BST:Pr3+ nanoparticles.

Fig. 7 shows the ferroelectric hysteresis loops of BST and BST:Pr3+ nanoparticles, measured at room temperature. The remnant polarization of the samples changed from 1.89 to 3.79 μC cm−2 when Pr3+ doped. The improved Pr in the BST:Pr3+ may be due to the Pr3+ substitution can increase the number of switchable domain by applied field. With the trivalent Pr3+ unequivalently substituting the univalent (Ba0.7Sr0.3)2+, to maintain charge neutrality A-sites ionic vacancies will occur in the BST and form defect dipole with Pr3+. In general, the electric performances of the BST depend not only on the structure of the domain and the movement of non-180 °C domain walls but also on the effect of the defect structure on the domains configuration and the interaction of between the defects and domain walls. During the testing process, the stress in the domain walls would be released by migrating to the defects, which would promote the domain walls to move laterally, leading to the reorientation and growth of the domains. And that a larger number of domains contribute to Pr for BST:Pr3+.[41] The coercive electric field (Ec) of BST and BST:0.5%Pr3+ are 0.84, 1.01 kV cm−1, respectively. When Pr3+ substitutes the (Ba0.7Sr0.3)2+, the lattice distortion is induced by the different ionic radius. And the large ion migration results in large polarization, which leads the Ec of BST:0.5%Pr3+ is larger than BST. This results conformity with other works.[42-44] The enhancement of ferroelectric and the excellent PL performance in BST:Pr3+ nanoparticles, makes it possible in applications of the ferroelectric/luminescent multifunctional devices.

Fig. 7

Polarization–electric field hysteresis loops of the BST and BST:Pr3+ samples.

Conclusions

In summary, BST:Pr3+ ferroelectric samples were prepared by a hydrothermal method. The green emissions at 531 nm and 547 nm were investigated under 325 nm optical excitation in a temperature range from 290 K to 403 K. This investigation revealed that the value of the FIR for I531/I547 increases gradually with increasing temperature, and a maximum sensitivity for the BST:Pr3+ ceramic of 0.015 K−1 at 375 K was reached. Furthermore, BST:Pr3+ operated a high sensitivity optical temperature sensor based on I490/I602 with a temperature range of 290–513 K, which could reach the maximum value 1.055 K−1 at 513 K. Instead of multiphonon relaxation between two thermally coupled states, the big variation of the intensity ratio of the 1D2–3H4 emission to the 3P0–3H4 emission upon temperature rise is closely relevant to their interaction with the IVCT state. The ultrahigh sensitivity based on the two emissions may shed a bright light on the promotion of optical temperature sensing and understanding of the involved mechanism. Moreover, the ferroelectric exhibits excellent ferroelectric properties.

Conflicts of interest

There are no conflicts to declare.