Abstract
This invention relates to new phosphor materials exhibiting luminescence and methods for their production. More particularly, the invention relates to new europium-doped zinc sulfide-manganese (ZnS:Mn,Eu) phosphors and use thereof for radiation detection.
Claims
1. A luminescent phosphor material comprising ZnS:Mn that is doped with Eu.sup.2+ ions.
2. The material of claim 1, wherein the material has the formula: Zn.sub.xS:Mn.sub.yEu.sub.z.sup.2+, where 0<x<1; 0<y<1; 0<z<1 and x+y+z equals 1, and y, z and y+z are present in an amount less than 0.5.
3. The material of claim 1 wherein, the concentration of the Eu.sup.2+ ions ranges from 0.05% to 10%.
4. The material of claim 1 wherein, the concentration of the Eu.sup.2+ ions is 0.2%.
5. The material of claim 1 wherein, the Eu ions enhances the photoluminescence of the phosphor material by 5.5 fold relative to ZnS:Mn.
6. The material of claim 1 wherein, the Eu.sup.2+ ions enhances the X-ray luminescence of the phosphor material by 2.5 fold relative to ZnS:Mn.
7. A process for the preparation of a particle dispersion of zinc sulfide doped with manganese and europium ions (ZnS:Mn, Eu.sup.2+) comprising the step of mixing powders of zinc sulfide, MnCl.sub.2 and EuCl.sub.2 and sintering in the presence of charcoal.
8. The process of claim 7 wherein, the mixture of the powders is sintered at 800 C.
Description
BRIEF DESCRIPTION OF THE DRAWINGS
(1) Preferred embodiments of the invention will now be described, by way of example only, with reference to the drawings, in which:
(2) FIG. 1 shows the photoluminescence spectra of ZnS:Mn,Eu with Eu concentrations (2%, 4%, 6%, 8% 10%, and 15%) by excitation at 390 nm. The spectrum of ZnS:Mn,Eu(10%) has been reduced by a factor of . The dash curve is the spectrum of ZnS:Mn by its best excitation (346 nm). The Mn concentration is always 2%;
(3) FIG. 2 shows the photoluminescence spectra of ZnS, ZnS:Mn (2%), and ZnS:Eu (5%, 10% and 15%) excited by 390 nm;
(4) FIGS. 3A to 3D shows the radiation effects on Eu and Mn fluorescence emission in ZnS:Mn,Eu phosphors at Eu concentration (A) 6%, (B) 8%, and (C) 10%. FIRs of 420 nm emission/583 nm emission is plotted at different X-ray exposure doses (in black dots) and exponential fittings of the plots are in red curves as shown in (D);
(5) FIGS. 4A and 4B shows representative TEM images of ZnS:Mn,Eu phosphors. Both large size (about 5 microns) and nanoparticles of the ZnS:Mn,Eu phosphors are observed;
(6) FIG. 5 shows X-ray diffraction patterns of ZnS:Mn,Eu phosphors before and after radiation treatment. Several main standard peak positions of pure sphalerte ZnS (JCPDS 05-0566) and wurtzite ZnS (JCPDS 36-1450) are displayed in dash lines for comparison purpose; and
(7) FIG. 6A to 6B shows (A) Emission spectra of ZnS:Eu(10%) before and after heating at 150 C. for 3 hours (excitation at 390 nm). The plot (B) is an enlarged plot of (a) in the range from 580 nm to 720 nm;
(8) FIGS. 7A to 7B shows the luminescence decay curve of 420 nm emission of ZnS: Eu,Mn under excitation at 355 nm. The decay curve was recorded (A) by the digital oscilloscope (Tektronix, TDS 2022C) and (B) by the multichannel scalar. The fitting curves are shown in black curves. Residuals for the fittings are shown above the decay curves respectively;
(9) FIG. 8 shows the photoluminescence spectra of ZnS:Mn, ZnS:Eu and ZnS:Mn, Eu;
(10) FIG. 9 shows the photoluminescence spectra of ZnS:Eu at different Eu2+ concentrations where the excitation is carried out at 330 nm;
(11) FIG. 10 shows the photoluminescence spectra of ZnS:Mn,Eu at different Eu concentrations where the excitation is carried out at 330 nm;
(12) FIG. 11 shows a comparison of ZnS:Eu and ZnS:Mn,Eu photoluminescence intensities with Eu concentration;
(13) FIG. 12 shows an X-ray luminescence spectra of ZnS:Mn (0.5%), ZnS:Eu (0.2%) and ZnS:Mn (0.5%), Eu (0.2%);
(14) FIG. 13 shows an X-ray luminescence spectra of ZnS:Eu at different Eu concentrations;
(15) FIG. 14 shows an X-ray luminescence spectra of ZnS:Mn,Eu at different Eu concentrations;
(16) FIG. 15 shows a comparison of X-ray induced luminescence emission intensity on Eu.sup.2+ concentration;
(17) FIG. 16 shows powder XRD patterns of ZnS:Mn, ZnS:Eu and ZnS:Mn,Eu;
(18) FIGS. 17A and 17B shows Raman spectra of ZnS:Mn, ZnS:Mn,Eu, and ZnS:Eu for various concentration of Eu;
(19) FIG. 18 shows ESR spectra of ZnS:Eu; E1=ZnS:Eu 0.05%, E2=ZnS:Eu 0.1%, E3=ZnS:Eu 0.5%, E4=ZnS:Eu 1%, E5=ZnS:Eu 6%;
(20) FIG. 19 shows a ESR spectra of ZnS:Mn,Eu. In all samples, the concentration of Mn is 0.025%. The concentrations of Eu are 0.05, 0.1, 0.5, 1.0 and 6.0% for samples of ME1, ME2, ME3, ME4, and ME5;
(21) FIG. 20 shows luminescence lifetimes of ZnS:Eu.sup.2+ with different Eu.sup.2+ concentrations where the excitation is at 300 nm and emission is at 500 nm;
(22) FIG. 21 shows Mn.sup.2+ luminescence Lifetimes for ZnS:Mn,Eu with different Eu.sup.2+ concentrations where the excitation is at 300 nm and emission is at 600 nm;
(23) FIG. 22 shows lifetime versus Eu.sup.2+ concentration; and
(24) FIG. 23 shows a ZnS:Mn Photoluminescence excitation spectrum (monitored at 595 nm) and ZnS:Eu photoluminescence spectrum.
DESCRIPTION OF EXEMPLARY EMBODIMENTS
(25) Embodiments of the invention are directed to a ZnS:Mn,Eu co-doped phosphor material. In an embodiment of the invention, the photoluminescence of the ZnS:Mn,Eu material is enhanced about 5.5-fold relative to the undoped control material. In a further embodiment of the invention, the X-ray luminescence is enhanced about 2.5-fold relative to ZnS:Mn. The co-doping of Eu.sup.2+ into ZnS:Mn does not change the ratio of the wurtzite and zinc blend phases or the Mn.sup.2+ luminescence lifetime in the samples. An embodiment of the invention provides a ZnS:Mn,Eu co-doped phosphor material, wherein the energy transfer and the phonon modification by Eu.sup.2+ enhance the intensity of Mn.sup.2+ emission. In certain embodiments, the concentration of the Eu.sup.2+ ions ranges from 0.05% to 10%.
(26) Zinc sulfide (ZnS, 99.99%), Manganese chloride (MnCl.sub.2, 99%+), and Europium chloride (EuCl.sub.2, 99.99%) were purchased from Sigma-Aldrich in USA. All the chemicals were used as obtained. The ZnS:Mn,Eu, ZnS:Mn, and ZnS:Eu phosphors are prepared using solid-state diffusion method. Briefly, calculated amounts of ZnS, MnCl.sub.2 and/or EuCl.sub.2 were ground together thoroughly and loaded into ceramic crucibles. The crucibles were then be embedded in carbon charcoal and sintered at 800 C. for 3 hours before cooled to room temperature.
(27) The identity, crystalline structure, size of the ZnS:Mn,Eu phosphors were observed by X-ray diffraction (XRD) and transmission electron microscopy (TEM). The X-ray powder diffraction was recorded in a Rigaku Ultima IV X-ray diffractometer with a radiation beam of =1.5406 . The ZnS:Mn,Eu phosphors were first dispersed in pure water and then placed onto holey carbon-covered copper grids for TEM observations. The TEM images of the particles were obtained with a Hitachi 9500 electron microscope with accelerating voltage of 300 kV. The photoluminescence spectra were measured by using a Shimadzu RF-5301PC fluorescence spectrophotometer. The X-ray radiation was performed using a Faxitron RX-650 (Faxitron X-ray Corp, IL, USA) cabinet X-ray system. Luminescence decay curves were collected using a nanosecond optical parametric oscillator/amplifier (Spectra-Physics MOPO-730) operating at a 10 Hz repetition rate and tunable between 440 and 1800 nm. The output of the MOPO system was frequency doubled in a KDP crystal and directed onto the particles. Emission was collected at right angles to the excitation and focused into a -meter monochromator equipped with a standard photomultiplier tube. Raman spectra were recorded with a Horiba Jobin Yvon LabRAM Aramis Raman Spectrometer with laser excitation at 472.97 nm Electron Spin Resonance (ESR) spectra were measured on Bruker EMX spectrometer operating at 9.8 GHz. Spectral intensities are scaled per unit mass for comparison. All measurements were carried out at room temperature.
(28) FIG. 1 shows the photoluminescence spectra of ZnS:Mn,Eu phosphors with various Eu concentrations (2%, 6%, 8% 10%, and 15%) under 390 nm excitation. The Mn concentration is 2% for all samples. The red emission at 583 nm is from Mn.sup.4T.sub.1-.sup.6A.sub.1 transition and is observed for all the samples. Its intensity gradually increases when Eu.sup.2+ concentration increases from 2% to 6%, then continuously drops when the Eu.sup.2+ concentration increases to 8%, 10%, and 15%. Remarkably, an intense and narrow (FWHM=30 nm) violet emission appears at about 420 nm with Eu.sup.2+ concentrations of 6%, 8% and 10%. This emission peak slightly shifts from 417 nm to 420 nm with increasing Eu.sup.2+ concentration. Its intensity increases gradually with increasing Eu.sup.2+ and reaches its maximum at the Eu.sup.2+ concentration of 10% where the emission is about 13 times stronger than the Mn.sup.2+ emission of 583 nm. With further increasing of Eu.sup.2+, the 420 nm emission is quenched and disappeared. For intensity comparison, a sample of ZnS:Mn(2%) is prepared by the same method. The dash line in FIG. 1 displays the highest emission intensity that ZnS:Mn(2%) can reach by using the its best excitation (346 nm). It is seen that the intensity of the 420 nm emission from ZnS:Mn,Eu(10%) is still 3 times higher than it.
(29) FIG. 2 displays the emission spectra of ZnS, ZnS:Mn (2%), and ZnS:Eu that were synthesized under the same conditions. It can be seen that pure ZnS has almost no emission or a very weak and broad emission band centered at about 460 nm due to defects. The spectrum of ZnS:Mn overlaps with ZnS except its Mn emission at 583 nm, which is the same to the previous Mn emission in the ZnS:Mn,Eu samples. For ZnS:Eu(10%), an intensive emission appears at 420 nm which matches the violet emission displayed in the ZnS:Mn,Eu samples. A broad band emission band from blue to green at 520 nm is also observed from this sample. This emission band is much weaker comparing to the strong violet emission. Therefore, the intense violet emission from those ZnS:Mn,Eu samples is related to Eu.sup.2+ doping in ZnS. Moreover, both ZnS:Eu(5%) and ZnS:Eu (15%) have only a blue emission centered at 460 nm and a green emission centered at 520 nm, there is no 420 nm violet emission found in these samples. Thus, the 420 nm emission occurs only at proper Eu.sup.2+ doping concentrations from 6% to 10%.
(30) Interestingly, the intensive violet emission is found sensitive to X-ray irradiation as shown in FIG. 3. As a UV excitation (390 nm) is used in the fluorescence measurement, its potential influence to ZnS:Mn,Eu fluorescence should be considered. We carefully measured the fluorescence spectra of ZnS:Mn, Eu samples using the UV excitation for more than 10 times, both emissions of 420 nm and 583 nm always remained constantly without any changes in their position and intensity. This means that the UV excitation used in fluorescence measurement does not affect the two emissions. However, when X-ray radiation is applied (i.e. the sample is exposed under X-ray), the intensity of 420 nm emission gradually decreases with increasing X-ray doses. Meanwhile, the 583 nm emission is observed remaining as the same. FIGS. 3a, 3b, and 3c display these observations with radiation exposure doses for sample A(ZnS:Mn,Eu(6%)), B(ZnS:Mn,Eu(8%)), and C(ZnS:Mn,Eu(10%)), respectively.
(31) These fluorescence characters of the two emissions from ZnS:Mn,Eu phosphors can be used for radiation detection. It is known that an absolute fluorescence intensity may vary its value by many factors, such as measurement setups, concentrations and instruments. However, the intensity ratio of two emissions from a same sample relies only on the sample's intrinsic characters and consequently provides a reliable method for detections. Here, we use the FIR of 420 nm emission (violet)/583 nm emission (red) to indicate the X-ray radiation doses quantitatively. FIG. 3D shows the plots of FIRs of violet/red emissions as a function of X-ray dose. The experimental data are shown in black dots. Further curve fitting (in red) has found that FIRs are decreasing exponentially with X-ray doses. The fitting equations for sample A, B, and C are given as equation (1), (2), and (3), respectively.
FIR=1.28(0.03)exp(Rad/31.72(1.90)+0.95(0.03)(1)
FIR=3.18(0.04)exp(Rad/62.94(2.39))+1.50(0.05)(2)
FIR=10.26(0.08)exp(Rad/105.91(1.94))+3.21(0.09)(3)
Where Rad is the radiation exposure dose, the values in brackets are standard deviations. We may then change the equation (1), (2) and (3) to (4), (5) and (6), respectively.
Rad=7.83ln(FIR0.95)(4)
Rad=72.81ln(FIR1.50)(5)
Rad=246.56ln(FIR3.21)(6)
Thus, using the FIR by fluorescence measurement on ZnS:Mn,Eu, X-ray radiation doses can be calculated from above empirical equations.
(32) In bulk ZnS:Eu, the excited states of Eu.sup.2+ is generally considered degenerated or even higher than its host conduction band, therefore Eu.sup.2+ emission could not be observed in bulk ZnS:Eu materials. It has been reported that the intra-ion d-f transition from Eu.sup.2+ in ZnS:Eu.sup.2+ can be observed only in ZnS: Eu.sup.2+ nanoparticles with size smaller than 3.5 nm. The TEM observations show that most of the ZnS:Mn,Eu phosphors are in the size of several micrometers. Some nanoparticles are seen in the samples by HRTEM but their size are larger than 20 nm. (FIG. 4). These indicate that the emission at 420 nm is not from the intra-ion d-f transition from Eu.sup.2+ in ZnS:Eu.sup.2+. In addition, ZnS: Eu.sup.2+ nanoparticles usually found their green emission due to Eu.sup.2+ 4f.sup.65d.sup.14f.sup.7 transition at about 530 nm A violet emission of 420 nm from Eu.sup.2+ could be seen in other hosts but not in ZnS. Here, as shown in FIG. 2, the emissions of 420 nm, 460 nm and 520 nm should be related to Eu.sup.2+ doping. ZnS may have defect emissions in those wavelength ranges due to sulfur or zinc defects. In this work, it is suggested that the Eu.sup.2+ doping contributes on defect formations and enhance their emissions consequently. These Eu.sup.2+ related defects are much more effective to emit light (7-30 times higher in emission intensities than ZnS defects shown in FIG. 2). Notably, the emission enhancement at 420 nm limits in a certain Eu.sup.2+ doping level (e.g. 6% to 10%), as the 420 nm emission only shows up in the case of Eu.sup.2+ concentration from 6% to 10%. While the emissions enhancement at 460 nm and 520 nm occur at all Eu.sup.2+ concentrations.
(33) In order to study possible mechanism of the 420 nm fluorescence quenching by radiation, the crystal structures of sample A, B, and C before and after X-ray treatment using XRD measurement were studied (FIG. 5). The diffraction peaks are indexed with the lattice planes respectively as displayed on the top of the figure. Both ZnS wurtzite(w) and sphalerte(s) phases are observed for all the samples. The measured peaks fit very well with standard X-ray diffraction peak positions of pure sphalerte ZnS (JCPDS, No. 05-0566) and wurtzite ZnS (JCPDS, No. 36-1450). No impurity phases are observed so that Mn.sup.2+ and Eu.sup.2+ are doped into ZnS host. There is almost no difference in the XRD patterns before and after X-ray treatment, indicating that the ZnS:Mn,Eu crystal structure is hardly affected by radiation treatment or Eu.sup.2+ doping.
(34) For further investigation, heat treatment in air was conducted on the ZnS:Eu(10%) which has the most intense 420 nm emission. FIG. 6A shows the emission spectra of the sample before and after the heat treatment (heating at 150 C. for 3 hours in air). After the treatment, the 420 nm emission is almost disappeared, meanwhile the 460 nm and 520 nm emissions are also decreased in intensity. The heat treatment phenomenon suggests that these emissions are likely from some defects because it is very common that defects are bleached by heat treatment. Besides, we noticed four characteristic emissions of Eu.sup.3+ at 596 nm, 617 nm, 652 nm and 699 nm, which are corresponding to the transitions of Eu.sup.3+ excited .sup.5D.sub.0 level to the .sup.7F.sub.J (J=1, 2, 3 and 4) levels, respectively. These Eu.sup.3+ emissions are very weak and there are almost no changes in intensity before and after the heating (FIG. 6B). This indicates that no Eu.sup.2+ ions were oxidized to Eu.sup.3+ during the heat treatment at 150 C. in air. It also indicates that the 420 nm emission is from some defects rather than the intra-ion d-f transition from Eu.sup.2+ in ZnS:Eu.sup.2+.
(35) X-ray irradiation may generate different effects in materials. It has been reported that Eu.sup.2+ can be converted/oxidized to Eu.sup.3+ upon X-ray irradiation in CaF:Eu and fluoroaluminate glasses. The process is suggested through either direct X-ray ionization or tapping holes. On the other hand, X-ray irradiation has also been found able to reduce Eu.sup.3+ to Eu.sup.2+ in BaFBr:Eu phosphors and phosphate glass. Meanwhile, both formation of X-ray-induced (Eu.sup.2+).sup.+ and (Eu.sup.3+).sup. ions were reported in phosphate glasses, in which the radiation-induced (Eu.sup.2+).sup.+ or (Eu.sup.3+).sup. ions have different local environment to the chemically created Eu.sup.2+ or Eu.sup.3+ ions. What is more, X-ray irradiation can induce defects. In our case, as the 420 nm emission is demonstrated as a defect emission that is largely enhanced by Eu.sup.2+ doping, both X-ray-induced (Eu.sup.3+ and defects are possible. The former can reduce the effective Eu.sup.2+ concentration by changing Eu.sup.2+ to (Eu.sup.3+ and the latter affects original defects, they both quench the 420 nm defect emission. Therefore, it is reasonable that the defect emission at 420 nm is highly sensitive to radiation and can be used for radiation detection and dosimetry.
(36) A very intense violet emission at 420 nm in ZnS host has been observed for the first time. This emission as well as the other two emissions at 460 nm and 520 nm is significantly related to Eu.sup.2+ doping in ZnS. The 420 nm fluorescence only exists at certain Eu.sup.2+ concentrations. X-ray irradiation quenches its emission intensity but does not affect the Mn emission at 583 nm. The fluorescence intensity quenching is suggested due to X-ray induced (Eu.sup.2+).sup.+ and defects. The FIR of the two emissions in ZnS:Mn,Eu may provide a new, sensitive and reliable method for radiation detection.
(37) The emission spectra of ZnS:Mn (0.5%), ZnS:Mn(0.5%), Eu(0.2%) and ZnS:Eu (0.2%) are shown in FIG. 8. The emission peaking at 595 nm in ZnS:Mn and ZnS:Mn,Eu is from the .sup.4T.sub.1(.sup.4G).sup.6A.sub.1(.sup.6S) transition of Mn.sup.2+. However, the luminescence intensity of ZnS:Mn,Eu is more than 5 times stronger than that of ZnS:Mn even though the concentration of Mn.sup.2+ is the same in the two samples. This implies that co-doping of Eu.sup.2+ in ZnS:Mn,Eu can enhance the emission of Mn.sup.2+. The luminescence properties of ZnS:Eu and ZnS:Mn,Eu as a function of Eu.sup.2+ concentration are shown in FIGS. 9 and 10, respectively. ZnS:Eu has a blue emission at 475 nm which is likely from defects. In bulk ZnS:Eu, no intra-ion transition of Eu.sup.2+ is observed because the excited states of Eu.sup.2+ are degenerate with the continuum of the ZnS conduction band. The intra-ion d-f transition from Eu.sup.2+ in ZnS:Eu.sup.2+ can be observed only in ZnS:Eu.sup.2+ nanoparticles with size smaller than 3.5 nm Both the blue emission intensity in ZnS:Eu and the orange emission intensity of Mn.sup.2+ in ZnS:Mn,Eu are highly dependent on the concentration of Eu.sup.2+ (FIGS. 8, 9 and 10). For Eu.sup.2+ concentrations less than 1%, the variation trends in ZnS:Eu and ZnS:Mn,Eu are similar, while for concentrations higher than 1%, the blue emission of ZnS:Eu increases in intensity with increasing Eu.sup.2+ concentration, while for ZnS:Mn,Eu, the change is just the opposite (FIG. 11). It is possible that at concentrations above 1% the nature of the defects giving rise to the blue emission changes. This results in additional blue emission intensity as the concentration of Eu.sup.2+ increases while the Mn emission decreases either due to concentration quenching or reduced coupling to the defect-related emission.
(38) In this instance, X-ray luminescence is luminescence excited by X-ray, so it is also called X-ray excited luminescence. The co-doping of Eu.sup.2+ in ZnS:Mn results in not only photoluminescence enhancement but also in X-ray luminescence as shown in FIG. 12. The X-ray emission at 595 nm in FIG. 12 is attributed to the .sup.4T.sub.1(.sup.4G).sup.6A.sub.1(.sup.6S) transition of Mn.sup.2+ analogous to the photoluminescence emission. However, the X-ray luminescence intensity of ZnS:Mn,Eu is a factor of 2.5 times stronger than that of ZnS:Mn for identical Mn.sup.2+ concentrations. This implies that Eu.sup.2+ co-doping in ZnS:Mn,Eu can enhance the Mn.sup.2+ X-ray emission. As in photoluminescence, ZnS:Eu has a blue X-ray luminescence band peaking at 475 nm which is attributed to defects as discussed above. Both the blue emission intensity in ZnS:Eu and the orange emission intensity of Mn.sup.2+ in ZnS:Mn,Eu are highly dependent on the concentration of Eu.sup.2+ (FIGS. 13, 14, 15). However, the variation of the X-ray luminescence intensities with Eu.sup.2+ concentration is somewhat different from that of the photoluminescence. In the concentration range studied, the blue emission intensity in ZnS:Eu follows the orange emission intensity in ZnS:Mn,Eu. Samples prepared with even higher Eu concentrations of 8% and 10% showed decreased emission intensity, presumably due to concentration quenching.
(39) To investigate the possible mechanisms for the enhancement, we measured the crystal structures of the samples by XRD, their phonon structures by Raman spectroscopy, the valence states of Mn and Eu by ESR and the luminescence dynamics. These studies provide detailed information about the crystal structures, surface properties, compositions and luminescence processes that are critical for the understanding of the luminescence enhancement. The XRD patterns of ZnS:Eu, ZnS:Mn and ZnS:Mn,Eu are shown in FIG. 16 and the XRD lines from different planes are labeled. Both Wurtzite (W) and Sphalerite (S) phases are observed in the samples but the wurtzite phase is dominant in all the samples based on the XRD line intensities. No impurity phases are observed implying that Eu.sup.2+ and Mn.sup.2+ ions are doped into the crystals. The results show that co-doping with Eu.sup.2+ does not appreciably change the ratio of the two phases in the samples. Therefore we may exclude the possibility that Eu.sup.2+ co-doping affects the phosphor crystal structures and is responsible for the luminescence enhancement.
(40) FIGS. 17A and 17B shows the Raman spectra of ZnS:Eu, ZnS:Mn and ZnS:Mn,Eu with different doping concentrations. As the samples contain both Wurtzite (W) and Sphalerite (S) phases of ZnS, it is likely that the Raman signals derive from both phases. However, it is difficult to distinguish between Raman signals of the two phases because most of their Raman frequencies are very similar. For example, the T.sub.2(TO) phonon frequency of sphalerite ZnS is at 271 cm.sup.1 while the A.sub.1(TO) phonon frequency of wurtzite ZnS is at 273 cm.sup.1, and the T.sub.2(LO) phonon frequency of sphalerite ZnS is at 351 cm.sup.1 while the A.sub.1(LO) phonon frequency of wurtzite ZnS is also at 351 cm.sup.1. As the wurtzite phase is dominant in our samples, we assign the Raman signals to wurtzite ZnS. In the first-order Raman spectra in FIG. 10a, the Raman peak at 215 cm.sup.1 is assigned to [TOTA].sub.x and the peak at 233 cm.sup.1 is attributed to [La+TA].sub. by comparing with the Raman spectra of ZnS:Cu,Cl phosphors. For ZnS:Mn, both the peaks at 215 and 233 cm.sup.1 are very weak. When Eu.sup.2+ is co-doped into ZnS:Mn,Eu, both peaks become stronger as the concentration of Eu.sup.2+ increases, while in ZnS:Mn and ZnS:Mn,Eu, the [TOTA].sub.x peak at 215 cm.sup.1 is stronger in intensity than the [La+TA].sub. peak at 233 com.sup.1. In ZnS:Eu, the [TOTA].sub.x peak shifts to 208 cm.sup.1 and the [TOTA].sub.x peak at 208 cm.sup.1 is weaker in intensity than the [La+TA].sub. peak at 233 cm.sup.1. The Raman peak at 267 cm.sup.1 is attributed to A.sub.1 (TO) and the 347 cm.sup.1 is from the A.sub.1(LO) phonon of wurtzite ZnS. The A.sub.1 (TO) phonon is only observed in ZnS:Eu but not in ZnS:Mn or ZnS:Mn,Eu. On the contrary, the A.sub.1(LO) phonon is only observed in ZnS:Mn samples but not in ZnS:Eu samples. The A.sub.1(LO) phonon frequency is shifted from 349 cm.sup.1 in ZnS:Mn to 347 cm.sup.1 in ZnS:Mn,Eu and the Raman intensity increases with the increase of the co-doping concentration of Eu.sup.2+.
(41) The second-order Raman spectra are shown in FIG. 17B. For ZnS:Eu samples, no second-order Raman peaks are observed in the range of 550-800 cm.sup.1. Four Raman peaks are observed in ZnS:Mn at 581, 634, 669 and 730 cm.sup.1, respectively. By comparing to the second-order Raman spectra of ZnS, the 634 cm.sup.1 is from the combination of TO+LO modes and the 669 cm.sup.1 is from the overtones of the LO mode. The 581 and 730 cm.sup.1 peaks are new phonons observed in ZnS:Mn. The 730 cm.sup.1 peak can be attributed to the E2 mode in ZnS and the most likely origin of the 581 cm.sup.1 is from a ZnO impurity because ZnO has a Raman peak at 583 cm.sup.1 which is attributed to the E.sub.1(LO) mode. It is highly possible that some oxygen impurity in the ZnS lattice is responsible for the formation of trace ZnO in ZnS:Mn phosphors. When Eu.sup.2+ is doped into ZnS:Mn, a new peak appears at 612 cm.sup.1 which is attributed to the overtone of the TO mode, while the two new peaks of ZnS:Mn at 581 and 730 cm.sup.1 decrease largely and disappear with the increase of Eu.sup.2+ concentration. The three Raman peaks at 612, 634 and 669 cm.sup.1 in ZnS:Mn,Eu increase in intensity with increasing Eu.sup.2+ concentration. These phenomena indicate that the co-doping of Eu.sup.2+ into ZnS:Mn does affect and modify the phonon dynamics of the host ZnS materials as reported in Raman spectra of ZnS:Mn and ZnS:Cu,Cl phosphors. Consequently, this would influence the luminescence processes and the emission efficiency of Mn.sup.2+ in ZnS:Mn,Eu phosphors. The modification of the host material phonon properties by doping with Eu.sup.2+ could be one of the key reasons leading to the luminescence enhancement observed in ZnS:Mn,Eu phosphors.
(42) ESR spectra of Eu doped ZnS are shown in FIG. 18 and the spectra of Mn, Eu co-doped ZnS are shown in FIG. 19. The ESR spectrum of Eu.sup.2+ in ZnS consists of six lines as expected from Eu.sup.2+ which is an ion with a half-filled 4f shell in the .sup.8S.sub.7/2 state. This 4f.sup.7 ion behaves as an effective spin system. The six lines observed arise from the nuclear 5/2 spin of .sup.151Eu.sup.2+ (47.8%) and .sup.153Eu.sup.2+ (52.2%). The intensities of the lines are scaled to the mass for quantitative analysis. However, they do not seem, at first glance, to follow the same trend as observed in the optical measurements. There is a fivefold increase in intensity when comparing 0.05% to 0.5% Eu.sup.2+ and an eight fold decrease in intensity when comparing 0.5% to 6.0%. These two spectra have consistent scaling with concentration of Eu.sup.2+. Also, the pattern of line intensities and line shapes are similar for 0.05%, 0.5% and 6.0% Eu.sup.2+ doping. The intensity at 0.1% Eu.sup.2+ was divided by 50 to fit on the composite graph and there is extremely low intensity at 1.0% Eu.sup.2+. The first spectrum in FIG. 18 shows the second and third lines expanded illustrating the differing intensity, line shape and linewidth that account for the appearance of the spectrum. The line shape accounts for the varying intensities of the lines in each spectrum. The ESR spectrum is represented by the magnetic hyperfine, nuclear quadrupole, and nuclear Zeeman interactions.
(43) The ratio of the .sup.153Eu/.sup.151Eu quadrupole moment and the magnetic moment are 2.54 and 0.442, respectively. The nuclear interactions are significant and contribute to the linewidth and lineshapes but not large enough to shift the entire spectrum to show resolved multiple spectra. The linewidth of the three similar spectra is five times smaller than that at 0.10% Eu.sup.2+ doping. This increase in linewidth of the S state ion, which has sufficiently long lifetime at room temperature to be observed, suggests a decrease in the spin relaxation time and a change in the spin lattice relaxation. This is attributed to crystal symmetry and dopant-dopant interaction or dopant lattice interaction. A more careful inspection of the spectra shows that there is a residual broad background in 0.1%, 0.5% and 1.0% Eu.sup.2+ doped samples. This background is not observed in the 0.5% and the 6% Eu.sup.2+, which implies that there is an environment giving rise to fast relaxation and that the relaxation time becomes shorter with concentration. The observation of a flat line at 6% indicates that the relaxation time is concentration dependent and too short for observation of any signal at room temperature.
(44) The ESR spectra of ZnS:Mn,Eu co-doped spectra are shown in FIG. 19. These spectra are dominated by the Mn.sup.2+ signal. This .sup.6S.sub.5/2 ground state ion gives rise to a sextet spectrum. The spectra are of equal intensity but seem to be of varying resolution. In this case the spectra are a combination of the transition ions occupying two or more sites. The bulk site gives rise to a broad background due to fast relaxation whereas the surface-type sites have slower relaxation. Co-doping with Eu.sup.2+ competes with the Mn.sup.2+ for the bulk sites resulting in reduced intensity of the broad spectrum. The sum of the Mn.sup.2+ spectra show an apparent increased resolution as the Eu.sup.2+ concentration is increased. However, the line widths of all the lines in the five spectra displayed are the same and indicates that the surface Mn.sup.2+ are not involved in any perturbation of the energy transfer mechanism or spin in lattice relaxation. On the other hand, the Mn.sup.2+ concentration remains constant and the surface composition does not change, so the Mn.sup.2+ in the bulk or lattice must relax faster with increased concentration of Eu.sup.2+. This faster relaxation of Mn.sup.2+ is due to a relaxation pathway created by the presence of Eu.sup.2+. The Eu.sup.2+ increases the spin lattice relaxation, allowing for faster energy transfer. The Eu.sup.2+ is not substituting for the Mn.sup.2+, therefore there will be spin-spin interaction between the ions that are in the lattice. This interaction will account for some broadening of the Mn.sup.2+ lines from the lattice centers and energy transfer between the two S state ions, which could result in the variance of optical emission intensity with concentration of Eu.sup.2+.
(45) The ZnS:Eu.sup.2+ luminescence decay curves with different Eu.sup.2+ concentrations are shown in FIG. 20. The lifetimes of the ZnS:Eu emission at 500 nm all show multi-exponential behavior and must be fit with at least two time constants. The shorter lifetime is on the order of a few hundred nanoseconds while the longer lifetime varies between 1.5 to 3.2 s. The shorter lifetime is significantly shorter and the longer lifetime longer than the typical lifetime of Eu.sup.2+ which is 0.8 s. This indicates that the blue emission from ZnS:Eu is not from the 4f.sup.65d.sup.1.fwdarw.4f.sup.7 transition of Eu.sup.2+. Therefore, the blue emission from ZnS:Eu is assigned to defect states.
(46) The luminescence decay curves of ZnS:Mn,Eu powder samples are shown in FIG. 21. In the ZnS:Mn,Eu samples, the concentration of Mn.sup.2+ is kept constant at 2% while the Eu.sup.2+ concentration varies from 0.05 to 6%. The luminescence decays are clearly multi-exponential likely reflecting fast contributions from the tail of the blue luminescence or emission from trap states. The longest lifetimes obtained from fits to the data in FIG. 21 are in agreement with the luminescence lifetime of Mn.sup.2+ in ZnS:Mn phosphors. The results from FIG. 21 show that co-doping of Eu.sup.2+ into ZnS:Mn,Eu does not appreciably change the Mn.sup.2+ luminescence lifetime except for very high Eu.sup.2+ doping of 6% which increases the Mn.sup.2+ lifetime to 1.2 ms. The variation of the luminescence lifetimes with Eu.sup.2+ concentration for the blue emission at 500 nm in ZnS:Eu.sup.2+ and the emission of Mn.sup.2+ at 600 nm in ZnS:Mn,Eu are displayed in FIG. 22. The change of the lifetime of the blue emission in ZnS:Eu with Eu.sup.2+ concentration closely follows the Mn.sup.2+ lifetime in ZnS:Mn,Eu. This indicates that the two emissions are closely correlated. It is noted the blue emission is observed in ZnS:Eu but not in ZnS:Mn,Eu. One reason may be that the blue emission band largely overlaps with the excitation bands of Mn.sup.2+ in ZnS:Mn phosphors as shown in FIG. 23. Thus, in ZnS:Mn,Eu phosphors, there can be efficient Forster energy transfer from the defect states to Mn.sup.2+ in ZnS:Mn,Eu and this energy transfer suppresses the blue emission in the co-doped phosphors. This implies that the mean distance between the Eu.sup.2+ and Mn.sup.2+ is on the order of 10 nm or less. Energy transfer may likely be the main reason for the dependence of Mn.sup.2+ emission on Eu.sup.2+ concentration in ZnS:Mn,Eu. Due to energy transfer, as the Eu.sup.2+ concentration increases the emission of Mn.sup.2+ would also approach the strongest intensity. Thus, the dependence of Mn.sup.2+ emission efficiency on Eu.sup.2+ concentration in ZnS:Mn,Eu can be used to design and optimize ZnS:Mn,Eu phosphors for practical applications.
(47) The present invention has been shown and described with reference to the foregoing exemplary embodiments. It is to be understood, however, that other forms, details and embodiments may be made without departing from the spirit and scope of the invention that is defined in the following claims.
