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Context and Summary of Baking Knowledge
• cavity is assembled, ready for RF test
• full equipped with antennas, thermal sensors
• inner part of the cavity is maintained under vacuum
• baking at 120°C for 2 days
“In-Situ” Baking
Ultra High Vacuum
120 °C / 48 hours
I n- S i tu Ba k i n gPu m p in gVe n t R e s i s t iv eH e a t e rT h e r m a lR e gu l a t io nP t 1 0 0T h e r m a lS e n so r sCe r n o x R Fc a b l e
i n Cr y o s ta t w i t h He1,E+09
1,E+10
1,E+11
0 5 10 15 20 25 30
Q0
Eacc ( MV/m )
C1-05 Chemical Etching (BCP)
Sans étuvage
Etuvage 110°C / 48h
1E+09
1E+10
1E+11
0 10 20 30 40 50
Q0
Eacc ( MV/m )
C1-03 - Electropolishing (EP)
J1 = EP / no baking
I1 = EP + UHV Baking 120°C/48h
quench
“Fast” Baking
Correspondence with 110°C / 60h
O Diffusion
( Semi Infinite Solid )
C/CS = erfc ( … )
0,4
0,5
0,6
0,7
0,8
0,9
1,0C/CS
110 °C / 60 h
145 °C / 3 h
160 °C / 1 h
UHV or Argon (1 atm.)
145 °C / 3 hours
Positron Annihilation Spectroscopy
PAS - DBS (Doppler broadening of positron annihilation radiation)
e+ → thermalisation (1ps)
→ diffusion
→ trapping in open-volume defects (voids, vacancies, VNb clusters , dislocation lines, grain boundaries…)
→ annihilation with e-→ 2γ (511 keV) → γ detection
γDoppler broadening of annihilation line, only due to e- momentum in propagation direction
(e+ momentum is negligible due to thermalisation)
sharpness parameter S = AS/A0 is determined by annihilations with valence electron (low momentum)
wing parameter W = AW/A0 is determined by annihilations of core electrons (high momentum) and gives
chemical information of the annihilation site
e+ is easily trapped in vacancy (repulsion by lattice ions) increases its lifetime and annihilation is preferentially
done with valence electron (lack of core electron), smaller momenta, smaller Doppler shift, narrow
curve, S↑ W↓
positron implantation profiles
Experimental Results
POSITRON ANNIHILATION SPECTROSCOPY
ON NIOBIUM SAMPLES
Bernard VISENTIN - CEA Saclay DSM / IRFU / SACM - 91191 Gif / Yvette - FRANCE
Marie France BARTHE, Virginie MOINEAU, Pierre DESGARDIN - CNRS / CEMHTI - 45071 Orléans cedex 2 - FRANCETUPPO047
Slow Positron Beam Facility in Orléans
Positron source (22Na)
Moderator (polycrystalline W foil - 4 µm): e+ (1.10-4@ 3eV)
Extraction (48 eV) – Acceleration (0 to 25 keV)
Beam diameter: 2 mm
γ Detection: high purity Ge detector
Reference sample: UO2Vacuum pressure: 5.10-8mbar
after baking : S ↑ & W↓ : vacancy number ↑
whole sample but particularly at the RF layer5 0µµ
0, 3 7 70, 3 7 90, 3 8 10, 3 8 30, 3 8 50, 3 8 70, 3 8 90, 3 9 1 0 5 1 0 1 5 2 0 2 5 3 0LowMomentumFractionS En e r g y ( k e V )S in g le Cr y s ta l S (E ) 1234
0, 0 6 30, 0 6 50, 0 6 70, 0 6 90, 0 7 10, 0 7 30, 0 7 50, 0 7 7 0 5 1 0 1 5 2 0 2 5 3 0Hi ghMomentumFractionW En e r g y ( k e V )S in g le Cr y s ta l W (E ) 1234
0, 4 1 00, 4 1 5ionS S Ca n dF G Sa m p le s 12optical µ−scope picture
of fine grain sample C
(after 120 µm BCP)
Makhovian profiles in Niobium(after thermalization & before diffusion)
0, 3 7 50, 3 7 70, 3 7 90, 3 8 10, 3 8 30, 3 8 50, 3 8 70, 3 8 9 0, 0 6 1 0, 0 6 6 0 , 0 7 1 0, 0 7 6LowMomentumFractionS H i g h M o m e n tu m F r a c t i o n WS in g le Cr y s ta l S (W ) 1234
with z0 = zm/Γ(3/2)
and A = 2.95 µg/cm2.keV-α , α = 1.7 , ρ N b = 8.57 g/cm3(A, α) material dependent – Monte Carlo calculation
P (z, E) = 2z/z02 exp-(z/z0)
2
0, 0 00, 0 10, 0 20, 0 30, 0 40, 050, 0 60, 070, 0 8 0 5 0 1 0 0 1 5 0P (z ,E ) D e p t h z ( n m )2 ke V3 ke V5 ke V8 ke V 11 01 0 01 0 0 0 0 5 1 0 1 5 2 0 2 5MeanIm plantationde pth (nm ) S lo w Po s it ro n E n e r g y ( k e V )z m = A Eα
/ρ
Abstract :Since the ‘baking effect” discovery, a part of the Saclay R&D dedicates one’s efforts to
understand this effect and its correlated question about the High Field Q-slope origin. Experiments on “fast
baking” in Oxygen free atmosphere and SIMS analyses have shown that interstitial oxygen diffusion cannot be
involved in baking phenomenon.
Presence of Niobium vacancy near the surface could contribute to explain such phenomenon. To explore
this way, we have performed experiments on niobium samples by means of positron annihilation radiation
Doppler broadening spectroscopy. For the first time, an increase of vacancy sites is disclosed at the Nb sample
surface after baking. We suggest that the dissociation of vacancy-hydrogen complex is at the origin of the
“baking effect”. This modification is observed in 100 nm depth under the sample surface, an area where the
superconducting RF layer is located.
We have experimentally shown that number of vacancies
increases after baking treatment on SC samples
( VNB-H complex dissociation )
Suggested scenario:
• Hydrogen ( aqueous species) is absorbed during chemistry; VNb-H complex creation
• RF losses: Q-drop (like Nb Hydrides in Q-disease)
• Above 100°C complex dissociation and H diffusion out of RF layer→ Q-drop removed
• Above 120°C Oxygen diffusion in material → VNb-O complex → Q-drop restored
• Additional BCP on fine grain samples B & G (to confirm C result)
• Baking of FG samples (C,B & G) to confirm baking results on SC
• Complementary experiments (ERDA) to follow hydrogen atom
Conclusion
Correspondence with 110°C / 60h
in terms of oxygen diffusion
0,0
0,1
0,2
0,3
0 10 20 30 40 50 60
X ( nm )semi infinite solid
C(0,t) = CS
→ analytic solutions
2
2
0x
CeD
t
C RTEA
∂
∂=
∂
∂2nd Fick's law
tTD
xerfcCtxC S
)(2/),( =
• cavity is treated after HPR in Clean Room
• Infra Red Heaters
• cavity under vacuum or filled with Argon (1 atm. )
• baking at 145°C for 3 hours
1E+09
1E+10
1E+11
0 10 20 30 40
Q0
Eacc ( MV/m )
1DE14 ( Electropolishing @ Henkel )
no Baking
145°C/3h Argon Baking @ Saclay
quench
Field
Emission
RF Power
limitation
1E+09
1E+10
1E+11
0 10 20 30 40 50
Q0
Eacc ( MV/m )
IS#8 ( Ichiro shape )
Electropolishing @ KEK
A1 - EP20um + EP3um + Degreasing
A3 - Argon Baking 145°C / 1+1 hRF Power Limitations
Oxygen Free Atmosphere needed( Ultra High Vacuum or Argon )
if not : RF degradation after Baking
1E+09
1E+10
1E+11
1E+12
0 10 20 30
Q0
Eacc ( MV/m )
C1-09 ( BCP cavity )
fast baking - 145 °C / 3 h
V1 - no baking
V2 - UHV baking
Y2 - Air bakingquench
1,E-04
1,E-03
1,E-02
1,E-01
1,E+00
1,E+01
0 20 40 60 80 100
Intensity (a.u.)
Abrasion Depth (nm)
NbO+/Nb+A Reference
8 UHV baking 110°C/60h
3 UHV Fast Baking 145°C/3h
5 Air Baking 145°C/3h
Similar results for plots of
NbO+, Nb2O+, Nb3O
+, Nb4O+…
• No O diffusion @ 10 nm scale – to be avoided
• O diffusion @ local scale ? (Nb Vacancy filling)
• Vacancy complex dissociation [V.H] ?
• Vacancy diffusion (stage III ) ?
SIMS analyses
on Nb samples
e+ → moderator (W) → 3 eV
→ different behaviour at the sample surface between single crystal & fine grain:
could be explained by a surface pollution for B & G
no hard chemistry after cutting → experiment on fine grain sample C
→ no vacancy migration
→ no vacancy filling (no oxygen diffusion at nm scale)
→ vacancy number increases
Suggestion: Hydrogen role - V.H complexes existence - dissociation after baking
with hydrogen diffusion ( D0=5.10-4 cm2/s → D=2.10-5 cm2/s @ 100°C )
empty vacancies → more traps for positrons
Comments on Results
Results for Fine Grain samples:
surface pollution (B and G samples)
more vacancy in C compared to SC samples
concentration in excess at interface
structures and grain boundaries
µµµµ
m 0, 3 7 50, 3 8 00, 3 8 50, 3 9 00, 3 9 50, 4 0 00, 4 0 5 0, 0 5 6 0, 0 6 1 0, 0 6 6 0, 0 7 1 0, 0 7 6LowMomentumFracti H ig h Mo m e n tu m Fr a c t i o n W ) 3 4CBG(after 120 µm BCP)
Niobium Samples
• single crystal (SC): beam hole off cut from large grain Nb sheet provided by X. Singer – Heraeus RRR 500
• fine grain (FG): Tokyo Denkai - RRR 200
diameter ~ 8 mm
thickness ~ 1 mm
2 0 0
µµµµ
m2 0 0
µµµµ
m2 0 0
µµµµ
m optical
µ−scope (x 50)
Sa m p le N io b iu m C he m is tr y C u t t in g An n e a l in g C he m i s t r y Ba k in g1- 2 S in g le C r ys ta lH e r a e u sR R R 5 0 0 n o Wa te r J e ta b r a s iv ega r n e ts a n d( 1 5 0µµµµ
m ) 8 0 0 ° C– 4 ho u r s1. 1 0- 7 m ba r B C P- 1 0 0
µµµµ
m n o3- 4 1 4 5 ° C / 2 ho u r sA r go n – 1 a t mB F in e G r a inTo k yoDe n ka iR R R 2 0 0 E P5 0 0µµµµ
m Wa te r J e ta b r a s iv ega r n e ts a n d( 1 5 0
µµµµ
m ) H F r in s e ( 1 0 %- 3 0 mn )be fo r e & a f te r8 0 0 ° C– 2 h 3 0 mn1. 1 0- 7 m ba r n o n oG n o 1 4 5 ° C / 2 h o u r sA r go n – 1 a t mC B C P- 1 2 0
µµµµ
m n o