鈦酸鹽紅色長(zhǎng)余輝發(fā)光釉的制備和發(fā)光性質(zhì)英文）

李金銀　余麗萍　譚藝　張吉林?と俅河ⅹち?世勛?ぶ芪睦愍だ畛兄?

摘 要 以SiO2-Al2O3-B2O3-SrO體系為基礎(chǔ)釉，混入不同比例的Ca0.8Zn0.2TiO3： 0.2% Pr3+， 0.2% Na+， 2% Bi3+發(fā)光粉，并將其涂布在陶瓷基體上進(jìn)行高溫煅燒制備紅色長(zhǎng)余輝發(fā)光釉.通過掃描電鏡、X射線衍射及熒光光譜表征了長(zhǎng)余輝釉的微觀結(jié)構(gòu)、晶相組成及光學(xué)性質(zhì).結(jié)果表明SiO2-Al2O3-B2O3-SrO體系玻璃是Ca0.8Zn0.2TiO3： 02% Pr3+， 0.2% Na+， 2% Bi3+發(fā)光粉的良好載體，能在熔融溫度之上將熒光粉較好地包裹.當(dāng)在950 ℃煅燒2 h，涂布釉漿3層，發(fā)光粉與基礎(chǔ)釉的質(zhì)量比為1∶3時(shí)，能獲得釉面平整光潔的鈦酸鈣紅色長(zhǎng)余輝發(fā)光釉.該發(fā)光釉的色坐標(biāo)為（0.683，0.317），非常接近理想的紅光.

關(guān)鍵詞 SiO2-Al2O3-B2O3-SrO體系；Ca0.8Zn0.2TiO3： 0.2% Pr3+， 0.2% Na+， 2% Bi3+熒光粉；紅色長(zhǎng)余輝釉

As a ceramic material， the dielectric constant of calcium titanate is 140～150， αε is 1 000～1500×106 /℃， and the dielectric loss is very low in a high frequency [1]. The ceramics based on calcium titanate is extensively used in electronic devices and making the high-frequency ceramic capacitor with a small scale and a high capacity. CaTiO3 has different crystal structure at different calcination temperature. Pr3+ doped CaTiO3-base materials with orthorhombic structure are known as promising red persistent phosphors due to their chemical stability， resistant-temperature， and especially excellent chromatic coordinates （x=0.680， y=0.311） close to “ideal red” defined by CIE （Commission Internationale de lEclairage 1931） [2].

It should be noted that the emission efficiency of CaTiO3： Pr3+ is still low in practical applications. In this context， many efforts have been done to enhance luminescent intensity and persistent efficiency of CaTiO3：Pr3+ phosphors. The luminescent intensity of CaTiO3 with ABO3 type perovskite structure is remarkably improved through displacing A site or B site ions with other ions， such as Na+， Tl+， Ag+ substitution for Ca2+ [3]， or Al3+ [4-5]， Bi3+ [6-7]， Ln3+（Ln=La， Lu， Gd） [8-9]， Si4+ [10]， Zr4+ [11]， Nb5+ [12] substitution for Ti4+， which could perform charge self-compensation. As such suppressed Ca2+ and Ti4+ vacancies lead to remarkable increasing of the emission efficiency. Na+ ion was the best charge compensation ion among the alkaline metal ions and Ag+ ion， due to the similar ion radius with Ca2+ and Pr3+ ions [3， 13]. Furthermore， emission intensity of CaTiO3：Pr3+ phosphors can be significantly enhanced after Zn2+ substitution for Ca2+ [14]. Nominal composition of Ca0.8Zn0.2TiO3： 0.2% Pr3+， 0.2% Na+ had higher emission intensity than that of CaTiO3： 0.2% Pr3+， 0.2% Na+ [15-16].

Persistent phosphors have been used in persistent paintings [17-18]， glaze， enamel and floor tile for the purpose of emergency sign， route markings and dark display. So far， the excellent green SrAl2O4 persistent glazes [19-23] and blue CaAl2O4 persistent glazes [24] have been widely used due to SrAl2O4： Eu2+， Dy3+ and CaAl2O4： Eu2+， Nd3+， La3+ having more than 12 h fluorescence lifetime in the dark. However， few researches were published on red persistent glaze. Li[25] prepared ZnO-B2O3-SiO2 parent glass with a low melting temperature， and then mixed with Ca0.8Zn0.2TiO3： 0.2% Pr3+ phosphor. However the emission intensity of luminescent glazes was much lower than that of Ca0.8Zn0.2TiO3： 0.2% Pr3+ phosphors.

In this paper， the red persistent glazes were prepared by mixing SiO2-Al2O3-B2O3-SrO parent glass powders and Ca0.8Zn0.2TiO3： 0.2% Pr3+， 0.2% Na+， 2% Bi3+ phosphors， which were prepared by a high-temperature solid-state method， followed by calcination at a high temperature after coating ceramic cylinders. The fabrication technology of the red persistent glazes was optimized.

1 Experimental

1.1 Preparation of ceramic cylinders

Aged petunses were dried， crushed and passed through 180-mesh. The dried powders were sprayed with 10 wt% of deionized water， and then screened with a 40-mesh sieve to produce pellets； subsequently the powders were molded into small cylinders （ 42 mm × 5 mm） under a single-axial pressure of 50 MPa. The cylinders were dried at 100 ℃ for 12 h， and then calcinated at 1 350 ℃ for 2 h.

1.2 Preparation of glass frits

The raw materials used for preparation of the SiO2-Al2O3-B2O3-SrO frits were ground quartz， talc， potassium feldspar， dolomite， borax in industry grade and strontium carbonate， barium carbonate， lithium carbonate in analytical pure. The component of glaze in mole ratio was 54%～60% SiO2， 6%～10% Al2O3， 8%～12% B2O3， 8%～14% SrO， 5%～6% Na2O， 2%～3% K2O， 1%～1.5% ZnO， 0.5% BaO， 0.5% CaO and 0.3% MgO. Raw materials， after thorough mixing in a planetary ball mill， melted in a porcelain crucible in an electric furnace at 1350 ℃ for 1 h. The fluid melts were quenched into deionized water to obtain glassy frits. The frits were ground and passed through 180-mesh to make sure that the sizes of frits were smaller than 80 μm.

1.3 Preparation of phosphorescent glaze

The glaze slips consisted of frits， Ca0.8Zn0.2TiO3： 0.2% Pr3+， 0.2% Na+， 2% Bi3+ luminescent powders （prepared by a high-temperature solid-state method in our laboratory） and deionized water with a mass ratio of （60～75）∶（25～40）∶57. The batches were mixed for 30 min in a planetary ball mill to make sure that the sizes of particles in glaze slips were smaller than 63 μm. Then， the slips were applied on ceramic cylinders. The dried samples were heated from room temperature to a specified temperature （in the range of 850～1 000 ℃） for 2 h with a ramp rate of 200～300 ℃/h， and then the samples were left cool freely in the furnace.

1.4 Characterization of persistent glazes

The microstructure and photoluminescent properties were characterized by a Rigaku D/MAX-2550VB + 18 kW X-ray diffractometer （XRD） with Cu Ka radiation at 40 kV and 300 mA， a JMS-5600LV scanning electron microscope （SEM）， and a Hitachi F-4500 fluorescence spectrophotometer operated at 400 V photomultiplier tube voltage （Tokyo， Japan）， equipped with a 175 W Xenon lamp as an excitation source and a UV 390 nm filter， respectively.

2 Results and Discussion

2.1 Excitation and emission spectra of persistent glazes and Ca0.8Zn0.2TiO3： Pr 3+， Na+， Bi3+ phosphors

Fig.1 is the emission and excitation spectra of the persistent glazes calcinated at 900 ℃ for 2 h and Ca0.8Zn0.2TiO： Pr3+， Na+， Bi3+ phosphors. The excitation spectrum is a broad band ranged from 275 nm to 425 nm. According to Gaussian fitting， there are three excitation peaks located at 310 nm， 334 nm and 365 nm. The former two excitation peaks are assigned to the 4f → 5d transition of Pr3+[13]， the valence to conduction band transition of 2p（O2-）→3d（Ti4+）[2]， respectively. And the third one is remarkably stronger than that of Ca0.8Zn0.2TiO3： 02% Pr3+， 0.2% Na+ [13-16， 26] due to the addition of Bi3+ ions. It is well know that the charge transfer transition from Pr3+/Ti4+ to Pr4+/Ti3+ （IVCT） [26] and the 6s2（Bi3+）/ 3d0（Ti4+） → 6s1（Bi4+）/ 3d1（Ti3+）/ MMCT（metal-to-metal charge transition） band [27] occur at about 370 nm. Bi3+→Pr3+ sensitization process involves the formation of Bi-related trapped excitations that transport the NUV excitation energy to Pr3+ centers by diffusion through the CaTiO3 lattice [28]. Herein， the band around 365 nm should be the mixture of IVCT of Pr/Ti and MMCT of Bi/Ti states. There is also weak excitation in the range of 450～495 nm， which is originated from 3H4 → 3Pj （j=0， 1， 2） transition of Pr3+ ion.

The emission spectrum of persistent glazes is a narrow band with a half-width of 30 nm （which is wider than that of Ca0.8Zn0.2TiO3： Pr3+， Na+， Bi3+ phosphors due to the different coordinated environment in the persistent glazes） and a maximum at 617 nm， which is in accordance with 1D2 → 3H4 transition of Pr3+ ion. The substitution of Ca2+ ions with Pr3+ ions requires charge compensation， which is achieved by introducing Na+ ions to substitute Ca2+ in this work.

The emission and excitation profiles of persistent glazes have a similar shape to that of Ca0.8Zn0.2TiO3： Pr3+， Na+， Bi3+ phosphors， except a little red shift and a lower intensity， indicating that the SiO2-Al2O3-B2O3-SrO system has little effects on the luminescent properties of Ca0.8Zn0.2TiO3： Pr3+ phosphors.

2.2 Effects of calcination temperature on luminous performance

The excitation spectra and decay curves of persistent glazes fired at different temperatures are shown in Fig.2. With the elevated calcination temperature， the luminous intensity passes through a maximun and then decreases， and the sample calcined at 900 ℃ has the highest intensity. Results show that the decay curves change little with firing temperatures.

Fig.3 is XRD patterns of persistent glaze fired at different temperatures. It is noted that persistent glazes fired at 850 ℃～1 000 ℃ consist of perovskite （JCPDS No. 89-6949）， Feldspar strontian （JCPDS No. 70-2121）， Tausonite （JCPDS No. 66-4356）， and Titanite phase （JCPDS No. 66-4356）. The diffraction peak intensities of pervoskite phase decrease with elevated firing temperature， while that of feldspar strontian （Sr0.84Na0.03Al1.69Si2.29O8） and titanite （CaTiSiO5） increase. The feldspar strontian phase is dominated in the based glaze， while titanite phase should be the products as a result of the reaction between phosphors and parent glass. Titanite phase appears above 800 ℃ at the expense of SiO2 （which is a component of based glaze） and CaTiO3 [29]. Sr2+ ions originated from parent glass dope into the lattice of CaTiO3 to form tausonite （Ca0.35Sr0.65TiO3） phase， which is conducive to the enhancement of excitation and emission intensities [30]. However， increasing feldspar strontian and titanite resulted in the reducing of the intensities of excitation and emission. Therefore， the maximum excitation intensity of sample was obtained at firing at 900 ℃ for 2 h.

Fig.4 is SEM micrographs of persistent glaze obtained at different calcination temperatures. It is obvious that phosphors distribute in the glass matrix at a lower firing temperature of 950 ℃ （Fig.4a）. While firing at a higher temperature of 1000 ℃ （Fig.4b）， the boundary between phosphors and glass matrix becomes indistinct， suggesting that parts of phosphors react with parent glass， resulting in the decrease of luminescent component and the luminous intensity. It was also confirmed by the XRD results. From the experimental， the lower of calcination temperature or the shorter of soaking time， the better is the luminous performance of red persistent glaze.

Parent glass does not completely vitrify at lower calcination temperature， so the surface of glaze coating is rough. When the firing temperature reaches 1 100 ℃， the surface of glaze coating is smooth with glassy luster. However， the emission of glaze disappears at the same time due to the disappearance of CaTiO3 in higher temperature. Considering the luminous performance， glassy luster and smoothness of glaze， the optimal calcination temperature of red persistent glazes is 950 ℃ for 2h.

2.3 Effect of glaze thickness on luminous performance

The persistent glazes with different thickness were obtained by coating different times on the surface of porcelain substrates. Fig.5 is the SEM micrographs of ceramics coated with one layer （a） and three layers （b） persistent glazes. It is obvious that glaze thickness is about 70 μm when coating once； while coating three times， the glaze thickness increased up to about 220 μm with more homogeneous distribution of phosphors in the microstructure. Fig.6 shows the emission spectra and the decay curves of persistent glazes with different coating times. There is no significant effect on the luminescence properties with different coating times， suggesting that coating three times is enough for smooth surface of glaze.

2.4 Effect of ratio of phosphors and base glaze on luminous performance

As we know， the persistent glazes are obtained by firing mixtures of phosphors and parent glazes with a certain mass fraction at the high temperatures. Ca0.8Zn0.2TiO3： Pr3+， Na+， Bi3+ phosphors are very important components in determining the luminous performance， while base glazes act as a carrier and protector of phosphors. Higher content of phosphors correspond to better luminous performance of persistent glaze， but the interface bond between glaze and porcelain substrate will turn worse with the increase content of phosphors， which also increases the cost of persistent glazes.

Fig.7 is the emission spectra and decay curves of persistent glazes with different mass ratio of phosphor to base galze. When the mass ratio of phosphors to base glaze is 1∶2 （sample A） or 1∶3 （sample B）， the luminous intensity of persistent glaze is remarkably superior to that of sample C with a less content of phosphors. However， the surfaces of persistent glazes in samples B and C are smoother than that of sample A. The SiO2-Al2O3-B2O3-SrO glass is transparent when it is reheated above fusion temperature， and phosphors are stable and distributed in the base glass in the temperature range of glaze formation. If the base glaze can not completely wrap phosphors， the glaze surface will turn rough due to the addition of more phosphors to glaze. Conversely， the surface will turn smoother. Considering the luminous performance， glassy luster of glaze and smoothness， the optimal mass ratio of phosphors to base glazes is 1∶3， similar to the results in Ref [25].

The red emission of persistent glaze can further be confirmed by the CIE （Commission Internationale de lEclairage 1931） coordinations from their emission spectra. As shown in Fig.8， upon excitation at 344 nm， the CIE chromaticity coordination is x=0.683 and y=0.317. It is closer to the chromaticity coordinate of the standard red light [2].

3 Conclusions

Persistent glazes were prepared by firing mixtures of Ca0.8Zn0.2TiO3： 0.2% Pr3+， 0.2% Na+， 2% Bi3+ phosphors and SiO2-Al2O3-B2O3-SrO glass at a high temperature. The optimal technology is firing at 950 ℃ for 2 h， coating three times， and 1∶3 for the mass ratio of phosphors to base glaze. The CIE chromaticity coordination is x=0683 and y= 0.317. The obtained red long-lasting titanate luminescent glazes are smooth and glabrous， exhibiting perfect red emission， which could be applied in emergency sign， route markings and dark display.

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（編輯 楊春明）