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Afterglow Luminescence of Lu2O3Eu Ceramics Synthesized at Different Atmospheres

Afterglow Luminescence of Lu2O3Eu Ceramics Synthesized at Different Atmospheres
Afterglow Luminescence of Lu2O3Eu Ceramics Synthesized at Different Atmospheres

Afterglow Luminescence of Lu2O3:Eu Ceramics Synthesized at Different Atmospheres

J.Trojan-Piegza*and E.Zych

Faculty of Chemistry,Uni V ersity of Wroc?aw,14F.Joliot-Curie Street,50383Wroc?aw,Poland

Recei V ed:October23,2009;Re V ised Manuscript Recei V ed:February1,2010

Three series of Lu2O3:Eu ceramic materials doped with different concentrations of Eu3+ions(0.05-5atom

%)were prepared by sintering at the temperature of1700°C of nanocrystalline powders.The heat-treatments

were performed in oxidizing,slightly reducing,and strongly reducing atmosphere of air,vacuum,and a N2-H2

mixture(9:1by volume),respectively.The radioluminescent properties of these materials have been

systematically studied.After exposure to X-rays,independent of the atmosphere of the preparation,the ceramics

exhibited an extensive afterglow,especially long and strong for low Eu concentrations.The afterglow and

radioluminescence spectra differed signi?cantly with the former showing much more emission resulting from

Eu3+ions occupying the S6symmetry site in the host compared to the activator in the C2position.The effect

was especially signi?cant within the range of low and medium Eu concentrations,0.05-1atom%.From the

decay traces of the persistent luminescence of Lu2O3:Eu ceramics it was concluded that the mechanism of the

process is governed by the second order kinetics.It is postulated that only Eu3+ions located within the layer

containing both S6and C2metal ion sites are active in the afterglow emission,while those placed within the

layer consisting of only the C2metal ion sites do not contribute to the afterglow.Another option is that

electronic levels of Eu3+in S6site are more favorably positioned to intercept migrating from their traps

excited carriers.

Introduction

Lu2O3crystallizes in a cubic C-type structure,1,2which host

offers two different sites for the Eu3+dopant ion replacing Lu3+,

each of them with6-fold coordination:noncentrosymmetric,C2,

and centrosymmetric,C3i(S6),1,3,4as is shown in Figure1.The

population of the C2site triples the abundance of the S6one in

the host.It was shown by Mossbauer spectroscopy that Eu3+

entering the host at high temperatures has some tendency to

preferentially occupy the C2site.5This was,however,found

for heavily doped materials(10atom%)and may not be valid

for low concentration systems.As a matter of fact,contrary to

the experimental results,recently published theoretical analysis

suggested that Eu3+may tend to preferentially occupy the S6

position in the host,especially at low concentration systems.6

All of that is important for analysis of the afterglow emission

in Lu2O3:Eu.Unfortunately,as will be shown shortly,the

contradictory?ndings hamper analysis of the afterglow phe-

nomenon in Lu2O3:Eu ceramics.

For the noncentrosymmetric Eu(C2)ions the electric dipole

induced f-f transitions are only partially forbidden and they

appear quite strong in both absorption and emission spectra.4,7-9

The selection rules for them are not that restricting and the

spectra of the Eu3+ion positioned in the C2symmetry site of

Lu2O3,similarly to isostructural Y2O3and Gd2O3,are quite rich

as was proved in numerous papers.4,9-11The situation is quite

different for the centrosymmetric Eu(S6)ions.The selection rules

are much more restricted in this case and allow only for

magnetic dipole induced transitions which are characterized by

?J)0,(1(yet,0f0is also forbidden).7-9In practice for

Lu2O3:Eu only two emission lines resulting from radiative relaxation of excited Eu(S6)ions,both related to the5D0f7F1 transition,can be recorded and they were found to appear at 582.8and593.6nm.4,9The transitions within the Eu(S6)are not only much less numerous,but they are also signi?cantly less probable,and consequently emissions related to them are considerably longer and much less intense compared to those characteristic for Eu(C2).4,9

*To whom correspondence should be addressed.Tel:+48713757265. E-mail:

jtp@eto.wchuwr.pl.

Figure1.Top:Arrangements of the oxygen ligands and vacancies

around the S6and C2symmetry sites of Lu3+ion.Bottom:A general

view of the unit cell of Lu2O3showing the mutual arrangement of Lu

with C2symmetry(blue balls)and with S6symmetry(brown balls).

J.Phys.Chem.C2010,114,4215–42204215

10.1021/jp910126r 2010American Chemical Society

Published on Web02/17/2010

Lutetium oxide,Lu2O3,was recognized as a very good host lattice for X-ray phosphors.Exceptionally high absorption coef?cient for ionizing radiation,very good photofraction,and high effective atomic number make lutetia-based compositions especially attractive for medical imaging.Particularly Eu-doping converts this host into ef?cient X-ray phosphor attractive for modern planar digital imaging,12-22as its ef?cient,red lumi-nescence matches perfectly the highest quantum ef?ciency of the CCD camera.

However,the Lu2O3:Eu phosphor is not free of drawbacks, the most important of which is quite a signi?cant afterglow appearing after irradiation with X-rays.14,23,24This problem was studied quite thoroughly but only for materials containing5% of the Eu dopant.23,24Recently,in scant studies,it was shown that important information about the afterglow luminescence characteristics could be obtained from experiments performed on lightly doped compositions.25The main observation was that for low Eu concentrations(0.05-1%)the afterglow lumines-cence spectra differed strongly from analogous emissions of samples containing3-5%of Eu.The lightly doped composi-tions produced afterglow luminescence with Eu(S6)emission intensity comparable or even stronger than that from Eu(C2). These limited studies were restricted to materials sintered in air,which opened the question if the atmosphere of preparation could alter this property.

In general terms,an afterglow results from a temporal interception of excited carriers in traps from which they can be continuously released regaining the ability to migrate to the activator,excite it,and thus produce delayed emission.Accord-ing to the Arrhenius equation the mean time,τ,a carrier spends in its trap at a speci?c temperature,T,is given by eq1: where p gives the probability per unit of time that a carrier escapes the trap,s is a constant called the frequency factor,and E is the trap depth.Hence,to observe an afterglow the traps cannot be too deep as then the intercepted carriers(electrons and/or holes)are not at all able to escape from them.On the other hand,the traps cannot be too shallow as then the carriers could not be immobilized for a time long enough to produce a delayed emission.26

The traps can be of various characters.Mostly,these are lattice defects of various types always present in materials. Cation or anion vacancies,interstitial ions,and impurities (intentional or unintentional)can produce local potentials able to serve as traps for electrons or holes migrating in the material. The traps(defects)may also be created upon the impact of a high-energy particle,as frequently occurs in halides.Population of some of the defects can be strongly altered changing the material preparation conditions,for example,the fabrication atmosphere.Therefore we decided to signi?cantly broaden the super?cial research we performed in the past25to learn more about the properties of the afterglow in Lu2O3:Eu ceramics.We hoped to get some indications about the possible methods of reducing the phenomenon intensity and/or duration in this phosphor as well as to learn more about the mechanism governing the afterglow phenomenon in the Lu2O3:Eu phosphor. Materials and Experiments

Three sets of Lu2O3:Eu ceramics were prepared by sintering of cold-pressed powders at1700°C.The series differed only in the atmosphere at which the sintering was performed:ambient

air(oxidizing),vacuum with pressure of about10-2hPa(slightly

reducing),and N2-H2mixture(9:1by volume)(strongly

reducing;normal,atmospheric pressure).The starting powders

for sintering were prepared by coprecipitation method as was

previously reported.25Each series consisted of samples contain-

ing0.05,0.1,0.2,0.5,1,3,and5atom%of Eu with respect

to Lu.

The radioluminescence and luminescence afterglow spectra

were recorded with an Ocean Optics HR2000-CG Spectrometer

equipped with25μm slits assuring the resolution of about1.2

nm.The samples were irradiated with white X-rays taken from

a copper lamp of a DRON-1powder diffractometer applying a

voltage of160V and10mA current.The sample-lamp distance

was4cm.All spectra were recorded in the200-1100nm range

but only the Eu3+-related emissions were observed therefore

they are presented truncated to the550-650nm region to

expose their most important features.Both luminescence

afterglow spectra and kinetics of the afterglow decays were

measured following10min irradiation of the samples with the

white X-rays from the tube.For technical reasons,the measure-

ments started10s after ceasing the irradiation.For the afterglow

kinetics measurements the Eu(C2)luminescence was monitored

at611nm and the Eu(S6)one at582.8nm.

Results

Figure2a shows a series of the radioluminescence(RL)

spectra of the samples sintered in air.These spectra are

indistinguishable from RL recorded for the two other sets of

samples(sintered in vacuum and in N2-H2mixture).Also the

intensity of RL is not affected by the atmosphere in which the

materials were fabricated.All spectra within a series are very

similar with the dominant emission located around611nm and

resulting from the5D0f7F2transition within the Eu3+ion located at the C2symmetry site.The RL from Eu(S6)appears

only as a vestige and with increasing concentration of Eu3+it

almost completely vanishes.

After irradiation with X-rays it could be seen by eye that

samples exhibited a profound afterglow,most signi?cant for

the lightly doped specimens.Panels b,c,and d of Figure2show

the afterglow luminescence spectra of the three series of

materials recorded3min after ceasing their stimulation.Two

effects are evident.First,the afterglow emission spectra strongly

differ from their regular RL counterparts,at least for the Eu

content in the range of0.05-1%.Second,the afterglow spectra

are strongly concentration dependent.Taking into account the

literature data discussed in the Introduction,8,9,25the reasons for

the differences appear obvious:for materials with lower Eu

contents a signi?cant fraction of the afterglow emissions comes

from Eu(S6)ions.The positions of the two characteristic lines

are indicated with arrows in Figure2.Yet another observation

is that the afterglow luminescence spectra do not practically

change with the atmosphere of the materials preparation.Both

the intensities as well as spectral distributions of the afterglow

emissions are very similar for samples prepared at the three

different atmospheres.In each series the relative intensity of

the Eu(S6)afterglow emission is the highest for materials

containing0.2%and0.5%Eu.When the Eu concentration is

3%or5%the afterglow from the Eu(S6)could not be recorded

3min after ceasing the irradiation.This effect is not a surprise

as it is known that an ef?cient Eu(S6)f Eu(C2)energy transfer

for higher concentrations takes place leading to a strong

quenching of the Eu(S6)luminescence.9Consequently,even if

the energy happens to reach Eu(S6)it is being transferred to a

p)τ-1)s exp(-E kT)(1)

4216J.Phys.Chem.C,Vol.114,No.9,2010Trojan-Piegza and Zych

nearby located Eu(C 2)and thus this is the latter which sends off the photon of light.Hence,what is observed for higher concentrations is not surprising.However,the difference between RL and afterglow spectra for lower Eu concentrations is spectacular as is the lack of dependence of this property on the synthesis atmosphere within oxidation and reduction condi-tions that were applied.

The Eu(S 6)/Eu(C 2)luminescence intensity ratios for the regular RL spectra as well as for the afterglow emissions recorded 30s and 10min after ceasing the irradiation were calculated and are presented in Figure 3.Within the experimental error,the concentration dependences are practically the same for all series.It can be easily noted that for lightly doped samples the Eu(S 6)/Eu(C 2)afterglow luminescence intensity ratio is even higher at longer delay time.Hence,the differences between RL and afterglow spectra,as seen in Figure 2(3min after irradiation),become even more profound at later stages of the afterglow.Results presented in Figure 3once more prove that the behavior of samples prepared at different atmospheres is very similar.It is seen in Figure 3that shortly after the

irradiation the highest ratio of the afterglow intensities from both Eu sites,Eu(S 6)/Eu(C 2),is observed for 0.5%Eu concen-tration,while at later stages of the measurement this ratio is uppermost for the 0.2%material.Again,this effect does not much depend on the atmosphere of preparation of the materials.As a consequence of these observations it can be stated that the kinetics of the afterglow emissions generated by Eu(S 6)and Eu(C 2)ions differ to some extent and are concentration dependent becoming much faster for higher Eu contents.

Having concluded that the afterglow spectra are not only concentration but also time dependent it was decided to record decay traces of the emissions from both Eu sites.The results of such measurements are presented in Figure 4for all three series of samples.Clearly,there are striking similarities between materials of different series.Again it has to be concluded that the preparation atmosphere does not have any signi?cant in?uence on the properties of the afterglow emissions in the materials.

For higher Eu contents,3%and 5%,the traces for both Eu(S 6)and Eu(C 2)ions decay relatively quickly.Yet,the afterglow from the Eu(S 6)site disappears much faster,practically within 1min after stopping the irradiation.This observation con?rms what was already concluded from the spectra presented in Figure 2and the data shown in Figure 3.An interesting situation is seen for the materials with very low Eu contents,0.05-0.2%,hence when the Eu(S 6)f Eu(C 2)energy transfer is negligible.Right after ceasing irradiation the intensity of the emission from the Eu(C 2)is noticeably higher than that from Eu(S 6).This is true independent of the atmosphere of preparation of the materials.The effect becomes progressively stronger when the content of the dopant decreases.However,both traces cross after some time and consequently at later stages of the phenomenon this is the Eu(S 6)afterglow intensity,which surpasses the Eu(C 2)one.The lower the Eu content the later the crossing point comes into view.For the 0.2%materials the intersection of both decay lines is observed about 4min after ceasing the irradiation.After this time the Eu(S 6)afterglow intensity becomes stronger than from Eu(C 2).However,for 0.1%materials it takes about 8-10min for the Eu(S 6)afterglow intensity to surpass the one resulting from Eu(C 2).When the Eu content is further reduced to 0.05%both traces cross yet later,after about 15-20min.Again,not much in?uence of the preparation atmosphere on these effects can be

noted.

Figure 2.Eu concentration dependence of radioluminescence (a)and persistent luminescence spectra (b -d)recorded 3min after X-ray excitation of the Lu 2O 3:Eu materials produced in air (b),vacuum (c)and N 2-H 2mixture (d).Radioluminescence does not change with the atmosphere of

preparation.

Figure 3.Concentration dependence of ratios of emission intensities of Eu(S 6)and Eu(C 2)ions in radioluminescence and afterglow spectra.The latter were calculated 30s and 10min after ceasing irradiation of the materials with X-rays.Materials were prepared in air (a),vacuum (b),and N 2-H 2mixture (c).

Afterglow Luminescence of Lu 2O 3:Eu Ceramics J.Phys.Chem.C,Vol.114,No.9,20104217

A closer analysis of the afterglow decay kinetics delivers new information.In Figure 5the ?rst 20min of the decay traces of the lightly doped materials (0.05-1%)sintered in the N 2-H 2mixture drawn as the time dependence of the reciprocal of the square root of the afterglow intensity (I -1/2(t ))are presented.For the two other series (sintered in air and in vacuum)the results are identical and therefore are not shown in the ?gure.It is striking that the I -1/2(t )relationships for the afterglow of both the Eu(S 6)and Eu(C 2)ions are linear,with maybe some small disparity at the very beginning (1-2min)of the process.This perturbation may well result from the Eu(S 6)f Eu(C 2)energy transfer between spatially correlated (closely positioned)ions.Even for the lowest Eu concentration,0.05%,a certain number of Eu 3+ion pairs may exist in the materials.27According to the literature,28such a linear dependence of the I -1/2vs t

may be taken as a proof for the second order kinetics of the afterglow phenomena of both Eu(S 6)and Eu(C 2)ions.Discussion

The time spent by the electron and/or hole carrying the excessive energy in its trap circumscribes the afterglow duration while the trap population de?nes the phenomenon intensity.By an appropriate chemical treatment it is often possible to alter types of traps,their population,and even depths modifying materials behavior.29-33In this context it is interesting that Tb-activated Lu 2O 3shows a profound afterglow when prepared in a reducing atmosphere and no afterglow at all when fabricated in air.34,35

Starting the research it was believed that treating the Lu 2O 3:Eu ceramics at atmospheres ranging from oxidizing (air)through mildly reducing (vacuum)to strongly reducing (N 2-H 2mixture)it would be possible to modify either the type of defects acting as traps for excited carriers (electrons and/or holes)or at least alter their population and thus change (presumably reduce)the intensity and/or duration of the afterglow luminescence.As lutetia is an oxide material,it was supposed that the different atmospheres of preparation would strongly change the antici-pated defect (traps);oxygen vacancies and/or oxygen intersti-tials ;and consequently that improvement of the decay kinetics of Lu 2O 3:Eu ceramics radioluminescence could be achieved,as it was done for Lu 2O 3:Tb.35

From the results presented above beyond any doubts it can be stated that (1)the Eu(S 6)ions are relatively more active in the afterglow process than the Eu(C 2)ones,especially when compared to regular RL and (2)the intensity,duration,and kinetics of the afterglow in Lu 2O 3:Eu ceramics is not affected by the atmosphere at which the materials were prepared.From (1)it appears that,although the population of Eu(C 2)roughly triples the population of Eu(S 6),the energy from traps is being delivered preferentially to Eu(S 6)rather than to Eu(C 2)ions.This may further indicate that the carriers possessing excessive energy are preferentially trapped in the vicinity of Eu(S 6)ions at the expense of the Eu(C 2)ones.On the other hand,the Eu(S 6

)/

Figure 4.Persistent luminescence decays traces of sintered Lu 2O 3:Eu ceramics obtained in air (a),vacuum (b),and N 2-H 2mixture (c).Simultaneously the 611nm Eu(C2)(9)and 582.8nm Eu(S6)(red O )emission intensities were recorded after X-ray

excitation.

Figure 5.Time dependence of the reciprocal of the square root of the afterglow intensity (I -1/2vs t )of the Lu 2O 3:Eu 3+ceramics sintered in N 2-H 2mixture (Eu(C2)(black solid symbol 9)and Eu(S6)(red open symbol O )).Data for materials prepared in air and vacuum are practically identical.For the highest concentrations (not shown)the dependence is no longer linear,most probably due to an ef?cient Eu(S 6)f Eu(C 2)energy transfer.

4218J.Phys.Chem.C,Vol.114,No.9,2010Trojan-Piegza and Zych

Eu(C2)ratio of afterglow intensities was not much different from unity up to the Eu content of1%,hence when the Eu(S6)f Eu(C2)energy transfer does not play a signi?cant role.This observation may signify that the populations of Eu(S6)and Eu(C2)ions acti V e in the afterglow luminescence are similar. This temporary conclusion can be confronted with the Lu2O3 structure.

In the Introduction it was already mentioned that in the Lu2O3 lattice the metal ions are organized into two types of layers. Those containing exclusively ions of C2symmetry are separated by layers with equal numbers of ions of C2and S6symmetry, see Figure1.Altogether this gives the3:1population of both types of sites in Lu2O3.It is postulated that the temporary immobilized carriers after being thermally freed migrate either exclusively or at least with much preference to Eu3+ions located within the layers consisting of both S6and C2sites,basically omitting those with only the C2metal site.Consequently only these Eu3+ions(whose populations may be taken as roughly 1:1in the investigated systems)are active in the afterglow.It is pure speculation but it corresponds to the observed similar intensities of the afterglow from Eu(S6)and Eu(C2)sites for low concentration systems.Unfortunately,at present we do not see a good experiment that could settle the veracity of this hypothesis.Yet another possibility is that the electronic levels of Eu(S6)ions are simply positioned more favorably to be reached by charge carriers escaping their traps compared to levels of the Eu(C2).This may well be as indeed the levels of Eu(S6)were reported to be situated noticeably above their counterparts of the Eu(C2),36hence closer to the conduction band of the host lattice.

The second clear observation that the intensity duration and kinetics of the afterglow of Lu2O3:Eu ceramics are not in?uenced by the atmosphere at which the materials were prepared indicates that the traps in which the excited carriers are being temporary immobilized are not connected with oxygen vacancies or interstitials,as their populations have to signi?cantly vary when the oxide is treated at high temperatures at oxidizing and strongly reducing atmospheres.Moreover,it was also found, but not presented in this paper,that analogous afterglow properties as reported here for ceramics occur for powders of different sizes of crystallites(50-1000nm)prepared at various atmospheres and temperatures in the range of800-1300°C. Altogether,the obtained picture convinces that the afterglow is an intrinsic property of Lu2O3:Eu materials.It cannot be excluded that defects(traps)standing behind the afterglow in Lu2O3:Eu are created upon the impact of the ionizing radiation or the carriers are temporarily immobilized in the(neighborhood of)empty ligand sites inherited to the structure,as is shown in Figure1.While all that does not exclude that the afterglow phenomenon still can be altered by some other technological tricks,now there is much less hope for that.It is a pity,as reducing the afterglow would make Lu2O3:Eu materials even more attractive for practical applications.

The afterglow in Lu2O3:Eu materials cannot be triggered irradiating the materials into the Eu3+f O2-charge transfer absorption band located around250-260nm.Only high energy radiation leads to afterglow.This allows us to conclude that the carriers reach their traps taking advantage of some mobility when they are raised into conduction(electron)and valence (hole)bands.This differentiates the afterglow mechanism in Lu2O3:Eu from a similar effect in Lu2O3:Tb,34,35where the tunneling seems to take place.Finally,it is noteworthy that Eu-activated Y2O3does not show similar behavior despite an analogous crystal structure and great similarity in other spec-troscopic properties.

Conclusions

Lu2O3:Eu ceramics produce the ef?cient radioluminescence, which is associated with a signi?cant afterglow lasting for more than1h in lightly doped compositions.Up to the Eu concentra-tion of1atom%the afterglow spectra are characterized by roughly equally intense emissions from Eu3+occupying both C2and S6sites while in regular radioluminescence luminescence from Eu3+in the C2site totally dominates the spectra.The afterglow phenomenon appears to be totally independent of the atmosphere of the materials fabrication:its intensity,duration, and kinetics,as well as spectral distribution,could not be altered by changing the preparation atmosphere from oxidizing to strongly reducing.Analysis of the I-1(t)dependence leads to the conclusion that the phenomenon is governed by the second order kinetics.

Acknowledgment.Financial support by Minister of Science and Higher Education under Grant No.N20502431/1207and partially under Grant No.N N205015934is gratefully acknowledged.

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JP910126R

4220J.Phys.Chem.C,Vol.114,No.9,2010Trojan-Piegza and Zych

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