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Orthorhombicity and oxygen uptake by YBa2Cu3O6 + x
Michel Ain, Jean-Marc Delrieu, Alain Menelle, George Parette, Jocelyne Jegoudez
To cite this version:
Michel Ain, Jean-Marc Delrieu, Alain Menelle, George Parette, Jocelyne Jegoudez. Orthorhombic- ity and oxygen uptake by YBa2Cu3O6 + x. Journal de Physique, 1989, 50 (12), pp.1455-1461.
�10.1051/jphys:0198900500120145500�. �jpa-00211008�
1455
Orthorhombicity and oxygen uptake by YBa2Cu3O6 + x
Michel Ain (1), Jean-Marc Delrieu (1), Alain Menelle (2), George Parette (2)
and Jocelyne Jegoudez (3)
(1) Service de Physique du Solide et de Résonance Magnétique, Direction de la Physique, CEN-Saclay, 91191 Gif-sur-Yvette Cedex, France
(2) Laboratoire Léon Brillouin (CEA-CNRS) CEN-Saclay, 91191 Gif-sur-Yvette Cedex, France
(3) Chimie des Solides, Université de Paris-Sud, 91405 Orsay, France (Reçu le 6 janvier 1989, accepté
sousforme définitive le 8
mars1989)
Résumé.
2014Nous
avonsmesuré, à différents taux d’oxygène, les paramètres de maille de
YBa2Cu3O6+x entre 24 et 260 K à l’aide de neutrons froids. L’affinement de
nosrésultats, présenté
surla figure 1,
ne nouspermet pas de confirmer les
mesuresde rayons-X, récemment publiées [1], montrant
uneanomalie de l’orthorhombicite b - a,
auvoisinage de la température
de transition supraconductrice. Il
aaussi, été mis
enévidence que le volume de la maille
cristallographique
secontractait par absorption d’oxygène.
Abstract.
2014We have measured, at different oxygen contents, the cell parameters of
YBa2Cu3O6+x between 24 and 260 K using cold neutrons. The results of profile refinement of
ourhigh resolution data is shown in figure 1 ; it does not confirm the X-ray finding, recently reported [1], showing
acusp in the orthorhombic splitting b 2014 a, around the superconducting transition temperature. It has also been evidenced that the volume of the crystallographic cell is contracted
by oxygen uptake.
J. Phys. France 50 (1989) 1455-1461 15 JUIN 1989,
Classification
Physics Abstracts
74.70 - 61.12
Introduction.
It is a major issue, to examine the structural transformations, at the onset of superconductivity
in YBa2CU307 ; to the extent that coupling between pairs of carriers and the lattice could
provide information on the underlying microscopic mechanism of the superconductivity in high 7c superconducting oxides. Unfortunately, the lattice strain observable in the vicinity of
the superconducting transition temperature, is so weak that this work brings no confirmation of the observations reported by Horn et al. [1], and reproduced on the insert of figure 1, showing a maximum at T,, on the plot of the parameter
cl =2 (b - a )/ (b + a ) defining the
orthorhombic strain of the structure.
This is not the first attempt to reproduce the results of Horn et al. [1], by neutron diffraction, and to our knowledge, nearly all attempts have been unsuccessful. David et al. [2]
have seen no evidence of anomalous behavior of a ; on the other hand, François et al. [3]
measured an 06,91 sample and observed a bump in the temperature dependence of
o,, they concluded that it was in agreement with the X-rays measurements. And finally, in a
first account of this work reporting on a YBa2CU306.88 sample we did in fact observed, near
Article published online by EDP Sciences and available at http://dx.doi.org/10.1051/jphys:0198900500120145500
1456
Fig. 1.
-The orthorhombicity parameter o-
versustemperature for YBa2Cu306.98 and YBa2Cu306.99. An
error
bar is drawn
on onesingle point at 83 K ; the
errors arenearly constant
overthe temperature range. The insert is the result of X-rays diffraction from reference [1], showing
adifferent behaviour for
a versus
T.
90 K, a little ondulation smaller than the error bar but we concluded that it was not a
confirmation of the behavior published in reference [1].
Concerning the afore-mentioned account, it was suggested by the referee, to remake the experiment on a powder that was as close as possible to YBa2CU307.
Expérimental settings.
Abiding by these prescriptions, a new sample was prepared from a mixture of BaCo3, Y203, and CuO powders, in stochiometric proportion according to the formula YBa2CU307.
The powders were gently grounded together and pressed by hand (to preserve a certain
porosity) into three cylindrically shaped samples of 22 mm height and 18 mm in diameter and
fired at 950 °C, in air. The preceding process was then repeated and the powder was fired
again for 24 hours at 950 °C, and then slowly cooled down to 450 °C. After 6 hours at 450 °C it
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was then brought to room temperature. The oxygen content was found to be 06.96, as
determined by the reiinement of the neutron diffraction pattern recorded at 83 K ; this same sample was then replaced in the oven, at 450 °C under circulating oxygen, for 16 hours ; and a
new refinement of the oxygen occupancy was performed, using the same technique as above,
and it gave O6.9g. A last heat treatment under oxygen for 100 hours, resulted in a
06.99 sample.
Horn et al. [1], did not measure the oxygen content of their sample. But we can estimate
that it falls between 06.95 and 07 after 2 hours spent betweerr400 and 500 °C in flowing
oxygen.
The neutron diffraction data were collected by a position sensitive detector, with incident
wave-length of À
=4.757 Â obtained from a vertically bent monochromator, this value being slightly beyond the cut off wave-length of aluminium at À
=4.7 Â. The incident beam was
filtered by cold berrylium. The position sensitive detector (a bank of 400 cells subtending an angle of 80 degrees, filled with BF3) had to be positionned twice in order to scan the whole
accessible sample’s diffraction pattern.
1 -The sample was mounted in an aluminium cell in thermal contact with the cold finger of a
closed cycle displex cryogenerator. Neutron diffraction patterns were recorded on all three stages of oxygenation of the sample, as already said. At one single temperature of
83 K for the 06.96, at several temperatures between 40 and 130 K for the 06.98 ; and last, the 06.99 was measured between 24.1 K and 260 K by steps of 5 then 10 and finally
20 K ; in the range 72.5-115 K, the steps were narrowed to 2.5 K. The spectrometer, as well as the temperature regulator, were driven by a desktop computer, according to the following procedure : the temperature was stabilized to a drift not exceeding 0.03 K/min ; afterwards
the detector was positionned at his low-angle location for a one hour counting, then it was
moved to its high angle position for another one hour counting, and so on.
Treatment of the spectra.
Profile refinement of the spectra were performed, on basis of space group Pmmm, using the
Rietveld program [4] modified by Hewat [5]. The spectra collected at 83 K, were used, as said, to determine the oxygen content after each heat treatment. Oxygen occupancy of sites 04 and 05 (see Fig. 2) were allowed to vary in these particular runs of the refinement program. As a result, we obtained an unambiguous convergence of site 05 occupancy towards 0 %, and site 04 occupancy towards respectively 96 %, 98 % and 99 % (± 3 %) after
each of the three heat treatments the sample has gone through. The exact final formula of our
compound being then, YBa2CU306.99. The transition temperature is expected to be around
92 K, as indicated by figure 3 of reference [6].
In the subsequent refinements, only 17 parameters were allowed to vary, (two less than above, namely the oxygen occupancies of site 04 and 05, that were held constant) they were
distributed as follows : 5 for the
zatomic coordinates of all atoms in the unit cell, excepting yttrium and those oxygen and copper atoms, which positions are imposed by the symmetry of the space group (see Fig. 2) ; 1 overall scale factor ; 3 for the expression of the FWHM of the diffraction peaks ; 1 for the zero point of the detector ; 3 for the unit cell constant ; 3 anisotropic temperature parameters for oxygen 04 ; and only 1 parameter for all the individual isotropic temperature factors, that was used as follows. We assumed that the kinetic energies Ec of all atoms excepting 04, were equal ; then starting from the fundamental relation :
where Ud is the vibration amplitude of atom d, Md, the mass, and ud the velocity amplitude.
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Fig. 2.
-The structure of the orthorohombic cell, with space group Pmmm- Oxygene sites
arenumbered
from 1 to 5. Yttrium atom is at the center of the cell, 04, 05 and Cul lie in the basal plane. The empty site 05 is represented by
asquare. Also shown, the two unequivalent sites of copper Cul and CuII. The so-called CU02 planes squeeze the yttrium ions.
Noting that an individual isotropic temperature factor is proportional to ud, i.e. Bd
=au2d, we
write :
The preceding relation obviously shows that Bd is inversely proportional to Md. This feature has been derived here on physical grounds but it can be proved formally [7]. As a
consequence of relation (2) the unique variable parameter for the individual isotropic temperature factor was attributed to oxygens 01, 02, 03 (see Fig. 2) and all the other factors
were deduced from it by multiplication with the ratio of the atomic masses such as, for
example :
We mention that due to the large wavelength, our diffraction pattern is not significantly
reduced by the Debye-Waller factor at large angles. These simple adjustments of the temperature factors gave us, at 82 K :
With all these settings, typical values for the different refinement factors that evaluate the
quality of the fit , were :
Re is the expected value for the refinement and ought to be nearly equal to
RWp, the weighted profile refinement factor, and to Ri the Bragg refinement factor.
RP is the profile refinement factor. Ri is a criterion for the diffraction pattern corresponding to
a given structural model ; while R,p is a criterion for the peak shapes being well described as
1459
well as for the goodness of the determination of the lattice parameters. In the present case all these parameters have the same order of magnitude indicating a very satisfactory refinement.
Since we merely aimed to make a measurement of the dimensionless parameter
Q =