Prime pagine RA2010FUS:Copia di Layout 1 - ENEA - Fusione
Prime pagine RA2010FUS:Copia di Layout 1 - ENEA - Fusione
Prime pagine RA2010FUS:Copia di Layout 1 - ENEA - Fusione
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094<br />
progress report<br />
2010<br />
Intensity (Arb. units)<br />
1200<br />
800<br />
400<br />
As grown<br />
Annealed<br />
42 43<br />
(200) MgO<br />
0<br />
35 45 55<br />
2θ (deg)<br />
Figure 4.8 – X–ray <strong>di</strong>ffraction θ–2θ scan of MgO<br />
film grown on Pd–buffered Ni–Cu–W. The<br />
spectra refer to the as–grown sample (full<br />
dots) and after annealing at 800 °C in vacuum<br />
(empty dots). In the inset, a detail of (200)MgO<br />
peaks. The thickness of MgO, Pd and Ni–Cu–W<br />
is 120 nm, 10 nm and 50 mm, respectively<br />
Realtive–peak–to–peak<br />
intensity (Arb. units)<br />
2×10 3<br />
a)<br />
(200) Pd<br />
b)<br />
(200) Ni–Cu–W<br />
Zr<br />
Y<br />
O<br />
Ce<br />
Ni<br />
Pd<br />
0 400 800<br />
oriented (fig. 4.8). The MgO layer is adequate for the<br />
deposition of a cap layer before YBCO deposition as tested by<br />
the heat treatment at 800 °C in vacuum.<br />
Oxidation behaviour of the Ni–W and CeO 2<br />
interface: role of<br />
Pd inter–layer<br />
Considering that oxidation at the substrate interface could<br />
influence the epitaxial growth and the mechanical stability of<br />
the whole coating architecture, the role of the Pd interlayer at<br />
the interface between NiW and CeO 2<br />
/YSZ/CeO 2<br />
buffer layer<br />
structure has been stu<strong>di</strong>ed by x–ray techniques and electron<br />
Auger spectroscopy. Extended x–ray absorption fine structure<br />
(EXAFS) analyses reveal that the inter–<strong>di</strong>ffusion process<br />
between the Pd layer and the substrate mo<strong>di</strong>fies the substrate<br />
interface composition due to the formation of an ordered<br />
Ni–Pd alloy even at temperatures as low as 600°C. At high<br />
temperatures, the oxidation mechanism is dependent on the Pd<br />
layer thickness, and competition between the NiO and the<br />
NiWO 4<br />
formation is observed. Oxidation also affects the CeO 2<br />
interface with the substrate. Auger electron spectroscopic (AES)<br />
analyses, reported in figure 4.9, reveal that the interface region<br />
is more extended than that of samples in vacuum annealed,<br />
and that outward migration of Ni and Pd in the CeO 2<br />
layer<br />
occurs. The CeO 2<br />
layer contamination results to be reduced as<br />
the Pd layer increases. The lower CeO 2<br />
contamination and the<br />
lower NiO formation could be associated to the good adhesion<br />
obtained in coated conductor samples with a Pd interlayer.<br />
4×10 3 400 800 1200 1600<br />
Realtive–peak–to–peak<br />
intensity (Arb. units)<br />
0<br />
0<br />
8×10 4<br />
4×10 4<br />
Sputtering time (s)<br />
c)<br />
Zr<br />
Y<br />
O<br />
Ce<br />
Ni<br />
Pd<br />
0<br />
0 400 800 1200 1600<br />
Sputtering time (s)<br />
Figure 4.9 – AES depth profiles for CeO 2 /YSZ<br />
samples deposited on Ni–W substrate buffered<br />
with a 50 nm Pd over layer annealed at 800 °C<br />
a) in vacuum and b) in 10 mTorr of oxygen back<br />
ground pressure. c) AES depth profiles for<br />
CeO 2 /YSZ samples deposited on Ni–W<br />
substrate buffered with a 200 nm Pd over layer<br />
annealed at 800 °C in 10 mTorr of oxygen back<br />
ground pressure. W signal is multiplied for 50<br />
Low fluorine YBCO MOD<br />
In this low fluorine method, only the Ba precursor is introduced<br />
in the coating solution as a trifluoroacetate, while other<br />
precursors are (Cu and Y)–acetate treated with an excess of<br />
propionic acid. The reaction path for YBCO formation was<br />
investigated by x–ray photoelectron spectroscopy (XPS) and<br />
<strong>di</strong>ffraction (XRD). From these analyses it resulted that the<br />
YBCO formation occurs through a rather complex mechanism<br />
involving hydrolysis of both Y and Ba fluorides and the<br />
reaction with CuO. However, this path is probably hindered by<br />
a competing reaction taking place at the same temperature<br />
range as YBCO formation (around 700–800°C). In figure 4.10,<br />
the evolution of the reaction path can be derived through<br />
x–ray <strong>di</strong>ffraction θ–2θ patterns. Within the 700–795°C<br />
temperature range the YBCO phase coexists with both<br />
Y 2<br />
Cu 2<br />
O and BaF 2<br />
phases. At 795°C, the XRD spectrum<br />
shows the presence of sharp and intense (00l) reflection of<br />
YBCO together with other <strong>di</strong>stinct peaks ascribable to the<br />
presence of residual Y 2<br />
Cu 2<br />
O 5<br />
phase, while BaF 2<br />
phase<br />
<strong>di</strong>sappears.<br />
Transport properties improvement in low fluorine YBCO MOD with artificial pinning sites<br />
The possibility of enhancing the pinning efficiency by means of artificial pinning sites created by ad<strong>di</strong>tion of<br />
BaZrO 3<br />
(BZO) has been investigated in YBa 2<br />
Cu 3<br />
O 7–x<br />
(YBCO) films grown by metallorganic decomposition<br />
(MOD) methods. YBCO and BZO coating solutions were prepared and subsequently mixed in molar ratios<br />
correspon<strong>di</strong>ng to 5, 7.5, 10, 15 mol.% BZO. A marked increase in the J c<br />
(0) value has been measured in MOD