electromechanical properties of technical superconductors · hg] year mgb 2 nbti nb 3 sn bi2223...
TRANSCRIPT
Group of Applied SuperconductivityDepartment of Quantum Matter Physics
University of Geneva, Switzerland
Electromechanical Properties
of Technical Superconductors
Carmine SENATORE
http://supra.unige.ch
Outline
Forces, stress and strain in a magnet
• Reversible vs. irreversible effects
• Mechanisms behind the irreversible degradation of the critical current
Focus on two materials: Nb3Sn and YBCO
Technical superconductors under mechanical loads
• Intrinsic vs. extrinsic effects
From superconducting materials…
…to technical superconductors
1. Superconducting ? 10’000
2. Tc>4.2K & Bc2>10T ? 100
3. Jc>1000 A/mm2 ? ~10
1900 1940 1980 1985 1990 1995 2000 2005 2010 20150
10
20
30
40
50
100
150
200
PbMo6S
8
H2S @ 140 GPa
AEFeAs
LaFeAsO
LaFePO
FeSe-1 layer
HgBaCaCuO @ 30 GPa
Night on
the Moon
Surface of Pluto
Liquid nitrogen
Liquid neon
Liquid hydrogen
Liquid helium
FeSeTe
SmFeAsO
HgTlBaCaCuO
HgBaCaCuO
TlBaCaCuO
BiSrCaCuO
LaBaCuO
YBaCuO
YC6
CaC6
CNT
diamondCNT
K3C
60
RbCsC60
CeCoIn5UPd
2Al
3CeCu2Si
2UPt
3
MgB2
BKBONb3Ge
V3Si
Nb3Sn
NbN
NbTiNbPb
Hg
Tem
per
atu
re [
K]
Year
MgB2
NbTi
Nb3Sn
Bi2223
Bi2212
YBCO
Operate at high current density is a necessary condition for applications, but it is not sufficient
Other crucial requirements:
• Have high tolerance to stress
• Be safe in case of magnet quench
• Have low magnetization
• Have a persistent joint technology
Quench detection, NZPV
Applications to NMR, MRI, HEP magnets
Applications to NMR, MRI
Magnetic forces
Operate at high current density is a necessary condition for applications, but it is not sufficient
Other crucial requirements:
• Have high tolerance to stress
• Be safe in case of magnet quench
• Have low magnetization
• Have a persistent joint technology
Quench detection, NZPV
Applications to NMR, MRI, HEP magnets
Applications to NMR, MRI
Magnetic forces
Introduction to Forces and Stresses in a Magnet
Infinite solenoidthin wall
B=B0 B=0
0 0B JdThe magnetic field is
The expression of the magnetic force density (per unit of volume) is
f J B
The average field in the winding is 0
2
B
F
dr
0 2
BJ r z d
20
0
2
Br z
20
02m
Bs p s
The (radial) force on a winding volume element is
0
2
BF J v
0( 1 ) 4 mp B T bar 0( 10 ) 400 mp B T bar
Hoop stress in a ring
r
loop
F dvf dvJ B
A ring carrying a current I in a field B
2 R I BB
I = J·Swire
The total radial magnetic force on the ring is
R
x x x x x x x x
x x x x x x x x
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x x x x x x x x
x x x x x x x x
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x x x x x x x x x x x x x
x x x x x x x x x x x x x
x x x x x x x x x x x x x
x x x x x x x x x x x x x
Hoop stress in a ring
r
loop
F dvf dvJ B
A ring carrying a current I in a field B
2 R I B
radial force2
rF F
A tension is developed within the ringTT /2/2
2 sin 22 2
T T T
R I B2
rFT
The so-called “hoop stress” on the wire is wire
TR J B
S
The total radial magnetic force on the ring is
Hoop stress levels above 100 MPa are common, the NHMFL 32 T magnet operates at 400 MPa
Electromagnetic stresses in a finite solenoidIn a winding adjacent turns will press on each other and develop a radial stress r which modifies the hoop stress
The condition for equilibrium between radial stress r , hoop stress and body force BJr is given by the equation
2
2
1 1d du ur BJ
r dr dr Er
Considering the solenoid as a continuous uniform medium, from the Hooke’s law
21r
E du u
dr r
21
E u du
r dr
and
where u is the local displacement in the radial direction, E is the Young’s modulus and is the Poisson’s ratio
F
Electromagnetic stresses in a finite solenoid
magnetic lines of force vectors of electromagnetic force per unit volume
20
02
Bp
r
bore radius
' BJr
Example: for B0 of the order of 10 T, on the winding of > 200 MPa (> 2000 bar)
Colour mapping of and r in a finite solenoid
Hoop stress Radial stress
Electromagnetic stresses in an accelerator dipole
magnetic lines of force vectors of electromagnetic force per unit volume
In straight-sided coils such as dipolesand quadrupoles the conductor is unableto support the magnetic forces in tension
20
02
Bp
For B0=6T and (a+b)/2=100 mm
Fx=200 tons/m
Collaring and Pre-stress in accelerator magnets
175 tons/m
85 tons/mF
The windings of accelerator magnets are clamped in a solid collar
Collar provide pre-stressing to prevent the movement of the coil in the presence of electromagnetic forces
Thermal precompression of the superconductor
Mismatch in thermal contraction within the composite induces a precompression in the SC
650°C 4.2 K
m
When the SC is cooled at the operating temperature,its crystal structure deforms and this induces changeson Tc , Bc2 (and thus on Jc)
MgB2
NbTi
Nb3Sn
All technical superconductors are composite
Bi2223
Bi2212
YBCO
In the following, the focus will be on
Today high field superconductor, up to 23.5 T in
solenoidal coils, the material for and
and only candidate material for the 16 T dipoles of
Nb3Sn
YBCO Tomorrow high field superconductor, more than 40 T
demonstrated in solenoidal insert coils, the way to get
20 T dipoles and beyond
In the following, the focus will be on
Today high field superconductor, up to 23.5 T in
solenoidal coils, the material for and
and only candidate material for the 16 T dipoles of
Nb3Sn
YBCO Tomorrow high field superconductor, more than 40 T
demonstrated in solenoidal insert coils, the way to get
20 T dipoles and beyond
Industrial fabrication of Nb3Sn wires
Three technologies have been developed at industrial scale
• Bronze route
• Internal Sn diffusion
• Powder-In-Tube (PIT)
The Sn source is the main difference
Presently produced by
Nb
Sn
Critical current density vs. magnetic fieldBest performance achieved so far in industrial wires
12 14 16 18 20 220
500
1000
1500
2000
2500
3000
FCC Target
n
on
-Cu
Jc [
A/m
m2]
B [T]
PIT - BKr
= 26.5 T
Internal Sn - BKr
= 24.9 T
Bronze - BKr
= 25.6 T
@ 4.2 K
J. Parrell et al., AIP Conf. Proc. 711 (2004) 369
T. Boutboul et al., IEEE TASC 19 (2009) 2564
V. Abächerli et al., IEEE TASC 17 (2007) 2564
Strain-induced changes in the critical current
m irr applied strain
crit
ica
l cu
rren
t
The applied force reduces the effects of the thermal precompression and the critical current increases up to a maximum
The applied force induces breakages within the filaments and the critical current is irreversibly degraded
0
Effects of the longitudinal strain
Strain-induced changes in the critical current
m irr applied strain
crit
ica
l cu
rren
t
0
Effects of the longitudinal strain
REVERSIBLE REGIONIc recovers after force unload
IRREVERSIBLE REGIONIc does not recover after force unload
Technology = m-irr [%]
Bronze Route 0.4 – 0.6
Internal Sn 0.05 – 0.2
Powder-In-Tube
0.15 – 0.3
Wire cabling for the ITER coils
CICC = Cable-In-Conduit Conductor
Wire cabling for the ITER coilsReversible variation of Ic under strain matters
CICC = Cable-In-Conduit Conductor
Because of the thermal precompression, wires in a CICC experience an effective axial compressive strain ranging between -0.6% and -0.8%
-0.8 -0.6 -0.4 -0.2 0.00.0
0.2
0.4
0.6
0.8
1.0 01UL0299A01
no
rmal
ize
d I c
intrinsic strain [%]
@ 4.2 K, 12 T
The performance of the superconductor is limited to ~40% of the maximum achievable current
How to measure Ic vs. axial strain The WASP (Walters Spring) probe
Ti-6Al-4V
Cu
B. Seeber et al., Rev. Sci. Instr. 76 (2005) 093901
Motor @ room temperature
Max current 1000 A
Sample length 1.1 meter
Voltage taps distance 126 mm
Electrical field criterion 0.01 μV/cm
Strain (ε) up to ± 1.2 %
Why do superconducting properties depend on strain ?
1. Reversible effects of strain
Why superconducting properties depend on strainReversible effects of strain
*
1.04 1exp
1.2 1 0.62c
B
Tk
2
FN E
Nb3Sn exhibits strong-coupling superconductivity
is an average phonon frequency
* gives the Coulomb repulsion at the Fermi surface
2
0
F2 d
McMillan parameter
electron-phonon coupling phonon DOS
So far the question whether the strain sensitivity is due mainly to electrons orphonons has not been settled
Strain induces change both in the phonon spectrum and the electronic bands
Why superconducting properties depend on strainReversible effects of strain
Some recent theoretical studies
G. De Marzi et al., J. Phys.: Condens. Matter 25 (2013) 135702Investigation of the strain sensitivity of Nb3Sn from first principle calculations based on the density functional theory
M. Mentink, PhD thesis (2014), University of Twente
Ab-initio calculations used to evaluate electronic, and vibrational properties, as well as Tc and Bc2 as a function of disorder, crystal orientation, and strain
D. Valentinis et al., Supercond. Sci. Technol. 27 (2014) 025008A theory of the strain-dependent critical field in Nb3Sn based on anharmonic phonon generation
D. Taylor and D. Hampshire., Supercond. Sci. Technol. 18 (2005) S241Microscopic theory analysis suggests that the uniaxial strain effects are predominantly due to changes in the average phonon frequencies
D. Markiewicz, Cryogenics 44 (2004) 767This work enphasizes the role of anharmonicity as a source of the strain dependence in Nb3Sn
Critical temperature vs. hydrostatic compression Reduced critical temperature vs. unaxial strain
D. Markiewicz, Cryogenics 44 (2004) 767S. Tanaka et al., J. Phys. Soc. Jpn. 81 (2012) SB026
Reversible effects of strainHydrostatic vs. uniaxial
Cubic-shaped stress-free cell for Nb3Sn
Precompression induced by cooling to low temperature has two components
HYDROSTATICChange of the cell volume
DEVIATORICChange of the cell shape
Reversible strain effects in Nb3Sn wires
Reversible strain effects in Nb3Sn wires: lattice parameters
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.85.260
5.265
5.270
5.275
5.280
5.285
5.290
5.295
5.300
latt
ice
par
ame
ter
[Å]
applied strain [%]
C. Scheuerlein et al., IEEE TAS 19 (2009) 2653
XRD experiments @ ESRF Grenoble
L. Muzzi et al., SUST 25 (2012) 054006
Bronze route wire: Nb3Sn lattice parameters vs uniaxial strain @ 4.2 K
ZERO APPLIED STRAINNb3Sn is precompressedHydrostatic+Deviatoric
CROSSING POINTCubic cell recoveredHydrostatic component still present
HIGH APPLIED STRAIN Again Hydrostatic+Deviatoric
Lattice parameters and Ic under axial strain
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.85.260
5.265
5.270
5.275
5.280
5.285
5.290
5.295
5.300
#26
latt
ice
par
ame
ter
[Å]
applied strain [%]
@ 19T, 4.2K
50
100
150
200
250
300
crit
ical
cu
rren
t [
A]
Bronze Route wire
MAXIMUM OF Ic
The maximum of the critical current occurs when the cubic cell is restored
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.80.0
0.2
0.4
0.6
0.8
1.0 PIT Internal Sn Bronze
0.4
2%
< ir
r<0.4
5%
irr=0
.62
%
I c / I cm
ax
applied strain [%]
0.4
1%
< ir
r<0.4
4%
@ 19T, 4.2K
Bronze Route, Internal Sn and PIT
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.80
50
100
150
200
250
300
350
400
450
E0=125 GPa
Rp0.2
=218 MPa
@ 4.2K
stre
ss [
MP
a] strain [%]
Bronze
Ic vs. axial strain
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.80
50
100
150
200
250
300
350
400
450
E0=125 GPa
Rp0.2
=218 MPa
@ 4.2K
stre
ss [
MP
a] strain [%]
Internal Sn
Bronze E0=101 GPa
Rp0.2
=194 MPa
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.80
50
100
150
200
250
300
350
400
450
E0=111 GPa
Rp0.2
=115 MPa
E0=101 GPa
Rp0.2
=194 MPa
E0=125 GPa
Rp0.2
=218 MPa
@ 4.2K
stre
ss [
MP
a] strain [%]
PIT
Internal Sn
Bronze
Technology irr
Bronze Route 330 MPa
Internal Sn 210 MPa
Powder-In-Tube 150 MPa
0 50 100 150 200 250 300 350 4000.0
0.2
0.4
0.6
0.8
1.0
PIT Internal Sn Bronze
20
7 M
Pa
<
irr<
22
0 M
Pa
ir
r=32
8 M
Pa
I c / I cm
axaxial stress [MPa]
15
3 M
Pa
<
irr<1
64
MP
a
@ 19T, 4.2K
Ic vs. axial stress
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.80
50
100
150
200
250
300
350
400
450
E0=111 GPa
Rp0.2
=115 MPa
E0=101 GPa
Rp0.2
=194 MPa
E0=125 GPa
Rp0.2
=218 MPa
@ 4.2K
stre
ss [
MP
a] strain [%]
PIT
Internal Sn
Bronze
Reversible behaviour and irreversible limit
Why do superconducting properties depend on strain ?
2. Irreversible effects of strain
Irreversible degradation phenomenaTwo irreversible phenomena play together
• Crack formation in Nb3Sn
• Plastic deformation of the Cu matrix
PIT Nb3Sn wire under transverse loadStress map of the Cu matrix
Yield strength of Cu y ~ 90 MPa
Plastically deformed Cu imposes a stress on Nb3Sn after force unload (= lattice deformation)
What is the residual stress on Cu after unload ?
resCu = max(Mises
Cu – y , 0 )
Nb3Sn is a brittle material and is characterized by a strong propensity to fracture
Voids formed during the reaction cause localized stress concentrations where cracks nucleate
Voids in Nb3Sn wires
Bronze Route121 x 121 filaments
Internal Sn132/169 subelements
PIT192 filaments
XRD microtomography reconstruction
Can we quantify the impact of voids on the electromechanical limits?
XRD microtomography at ESRF Grenoble
sample
- XRD photon energy = 89 keV
- 360° rotation of the sample
- 30’000 projections
- 2560 x 2160 pixels
- 0.57 m/pixel resolution
ab
sorp
tio
n
parallel XRD beam
rotate
Non-destructive 3D volume reconstruction with separation of internal features
Bronze Route wire
Virtual longitudinal cut
XRD microtomography at ESRF Grenoble
A case study on Bronze Route Nb3Sn wires
Why Bronze Route wires ?
Because by Hot Isostatic Pressing (HIP) treatment we can reduce the void fraction without degrading the critical current
What did we do ?
Experimental determination of the electromechanical limits
Statistical analysis of the voids size, shape and distribution
Finite Element Modelling (FEM) to quantify the impact of voids
Possibility to investigate the same wire type with and without voids
A case study on Bronze Route Nb3Sn wires
NbCu
Bronze
Nb3Sn
manufacturer
wire diameter 1.25 mm
# of filaments 121 x 121
filament size 4.5 m
irr =
0.6
8 %
max
= 0
.20
%
0.0 0.2 0.4 0.6 0.8 1.00
50
100
150
200
regular HT
crit
ical
cu
rre
nt
I c [A
]
applied strain [%]
@ 4.2 K, 19 T
Regular HT: 600°C/100h + 670°/150hc = irr– max = 0.48 %
HIP 550°C/1h/200MPa + Regular HT
c = irr– max = 0.65 %
irr =
0.6
8 %
irr =
0.8
9 %
max
= 0
.24
%
max
= 0
.20
%
0.0 0.2 0.4 0.6 0.8 1.00
50
100
150
200
regular HT
HIP + regular HT
crit
ical
cu
rre
nt
I c [A
]
applied strain [%]
@ 4.2 K, 19 T
With HIP treatment c increases by +0.17 %
Bronze route wire: Void detection
Without HIP treatmentVoid fraction = 2.1 %
With HIP treatmentVoid fraction = 0.05 %
Void reduction by a factor 50 !!
Void detection and analysis
- A brightness distribution analysis is
used to detect voids
- Voids are approximated with ellipsoids
- Size and orientation are determined
• Major axis length
• Major axis angles and
• Eccentricity (sphericity)
- Position is recorded, including distance
to the nearest neighbors and location
(matrix, filament bundle, interface)
These data become input for FEM
Bronze route wire: Void analysis
Void size Void shape
0.0 0.2 0.4 0.6 0.8 1.01
10
100
1k
10k
100k regular HT
cou
nt
sphericity, 0.0 0.2 0.4 0.6 0.8 1.01
10
100
1k
10k
100k regular HT
HIP + regular HT
cou
nt
sphericity,
HIP voids are morespherical
0 5 10 15 20 251
10
100
1k
10k
100k
cou
nt
principal axis length [m]
regular HT
HIP void size is reduced
0 5 10 15 20 251
10
100
1k
10k
100k
cou
nt
principal axis length [m]
regular HT
HIP + regular HT
Statistical FEM analysis
- 3D model, real dimensions, 0.1 mm long wire
- Bottom side is fixed, top side is displaced to apply a mechanical strain
The output of the model is the
von Mises stress distribution in the
Nb3Sn volume at a given strain
Statistical FEM analysis: 1) no voids - The experimental c corresponds to an irreversible reduction of Ic by 5%
- Working hypothesis: 5% of Ic degradation damage in 5% of the filaments
Wire with HIP treatment
SIMULATION done at c = 0.65%
The 5% of the Nb3Sn volume at the highest
stress is highlighted in red
Here the red regions are at 275 MPa
The critical stress is thus c = 275 MPa
Statistical FEM analysis: 2) with voids - Voids are generated from the statistical analysis until the void fraction
of the wire is reached
- The goal is to predict the reduction of c induced by the voids
- Simulation runs at increasing until c in 5% of the filaments
c = 275 MPa
c = 0.65%
0.3 0.4 0.5 0.6 0.7 0.8150
200
250
300
350
400
HIP + regular HT
regular HT
up
pe
r 5
% s
tre
ss,
up
pe
r 5
% [
MP
a]
intrinsic strain, [%]
c = 275 MPa
c = 0.65%
0.3 0.4 0.5 0.6 0.7 0.8150
200
250
300
350
400
HIP + regular HT
regular HT
up
pe
r 5
% s
tre
ss,
up
pe
r 5
% [
MP
a]
intrinsic strain, [%]
c = 275 MPa
c = 0.65%
0.3 0.4 0.5 0.6 0.7 0.8150
200
250
300
350
400
HIP + regular HT
regular HT
up
pe
r 5
% s
tre
ss,
up
pe
r 5
% [
MP
a]
intrinsic strain, [%]
c = 275 MPa
c = 0.65%
0.3 0.4 0.5 0.6 0.7 0.8150
200
250
300
350
400
HIP + regular HT
regular HT
up
pe
r 5
% s
tre
ss,
up
pe
r 5
% [
MP
a]
intrinsic strain, [%]
c = 0.50%
c = 275 MPa
c = 0.65%
0.3 0.4 0.5 0.6 0.7 0.8150
200
250
300
350
400
HIP + regular HT
regular HT
up
pe
r 5
% s
tre
ss,
up
pe
r 5
% [
MP
a]
intrinsic strain, [%]
In the presence of voids the model predicts c = 0.50%
Irreversible limit in the presence of voidsExperiment vs Prediction
0.0 0.2 0.4 0.6 0.8 1.00
50
100
150
200
regular HT
HIP + regular HT
crit
ical
cu
rre
nt
I c [A
]
applied strain [%]
@ 4.2 K, 19 T
c = 0.48%
c = 0.65%
Ic vs strain measurement
c = 0.65%
FEM simulations
c = 275 MPa
0.3 0.4 0.5 0.6 0.7 0.8150
200
250
300
350
400
regular HT
HIP + regular HT
up
pe
r 5
% s
tre
ss,
up
pe
r 5
% [
MP
a]
intrinsic strain, [%]
c = 0.50%
The simulations predict the correct value of c when voids are introduced
What did we learn ?
Changes in the voids correlate quantitatively with the changes in the electromechanical limits
More details in
Case study on Bronze Route, what about Internal Sn and PIT ?
The same approach may lead to the prediction of how much c can be increased by reducing the void fraction
Reversible effects of strain
Influence on the stress tolerance of the way the mechanical stresses are exerted
Intrinsic mechanisms behind the irreversible degradation of the critical current
Strain-induced changes in Nb3Sn wires
Electromagnetic stresses in an accelerator dipole
magnetic lines of force vectors of electromagnetic force per unit volume
Accelerator magnets operate at ~10 kA to keepinductance low and ease magnet protection
Rutherford cables are used to get these largeoperating currents
LHC27 km, 8.33 T
14 TeV (c.o.m.)1300 tons NbTi
FCC-hh100 km, 16 T
100 TeV (c.o.m.)~9000 tons Nb3Sn
HE-LHC27 km, 16 T
27 TeV (c.o.m.)~3000 tons Nb3Sn
Geneva
PS
SPS
LHC
Courtesy of L. Bottura (CERN)
The Future Circular Collider Study
Degradation upon transverse loads
The 16 T FCC dipoles are being designed with a peak stress of 200 MPaat operation
Nb3Sn Rutherford cable for HL-LHC, 40 strands
Are the Nb3Sn wires in the cable able to withstand such a high stress level? Which degradation is tolerable?
• Nb3Sn wires are deformed during cabling
• Cables are braided with glass fiber
• The winding is impregnated with resin
The irreversible limit under transverse stress is influenced by parameters extrinsic to the wire
• the type of impregnation (the elastic modulus of the resin)
• the redistribution of the applied stress on the wire i.e. the deformation of the wire during cabling
Tested Epoxy L, Glass fiber + Epoxy L, Stycast
The WASP concept for Ic vs. transverse stress
4-WALL + impregnation
Pulling force
Resin
Sample
collaboration agreement K1629/TE (2009-2012)
Ic vs. transverse stressPIT 192 + Epoxy L
0 5 10 15 20 25 30 350.2
0.4
0.6
0.8
1.0
@ 4.2K, 19 T
I c / I c0
Transverse force [kN]
#31712-1 unload
95% Ic0
0 30 60 90 120 150 180 210 240Transverse stress [MPa]
ForceStress
groove length groove w th id
irr = 110 MPa
The corresponding irreversible stress limit is
where
The irreversible limit is defined at the force level leading to a 95% recovery of the initial Ic after unload
Here Firr = 16 kN
60 80 100 120 140 160 180
0.0
0.5
1.0
1.5
2.0
2.5
F = 0.5 kN
F = 15 kN
unload to 0.5 kN
@ 4.2 K, 19 T
Elec
tric
fie
ld [
V/c
m]
Current [A]
Epoxy L
Sample
Glass fiber
Ic vs. transverse stress: wire in a glass fiber sleeve
0 30 60 90 120 150 180 210 2400.2
0.4
0.6
0.8
1.0
PIT #31712 Ø = 1.0 mm
@ 4.2K, 19 T
95% Ic0
Transverse stress [MPa]
I c / I c0
sample #1 round
with glass fiber sleeve
PIT #14310 Ø = 1.0 mm
0 30 60 90 120 150 180 210 2400.2
0.4
0.6
0.8
1.0
PIT #31712 Ø = 1.0 mm
@ 4.2K, 19 T
95% Ic0
Transverse stress [MPa]
I c / I c0
sample #1 round
after force unload
with glass fiber sleeve
after force unload
PIT #14310 Ø = 1.0 mm
Glass fiber adds rigidity to the impregnation Shift of irr by > 50 MPa
Ic vs. transverse stress: Epoxy L vs. Stycast
0 5 10 15 20 25 30 350.2
0.4
0.6
0.8
1.0
PIT #31712 Ø = 1.0 mm
@ 4.2K, 19 T
I c / I c0
Transverse force [kN]
epoxy impregnation
stycast impregnation
95% Ic0
0 30 60 90 120 150 180 210 240
Transverse stress [MPa]
0 5 10 15 20 25 30 350.2
0.4
0.6
0.8
1.0
PIT #31712 Ø = 1.0 mm
@ 4.2K, 19 T
I c / I c0
Transverse force [kN]
epoxy impregnation
epoxy impregnation after force unload
stycast impregnation
stycast impregnation after force unload
95% Ic0
0 30 60 90 120 150 180 210 240
Transverse stress [MPa]
The change of resin, from epoxy to stycast, leads to an increase of irr by > 50 MPaThe result is comparable to the value found with epoxy + glass fiber sleeve
The Young modulus ofStycast is 3 to 4 timeshigher compared to thevalue of Epoxy L
Ic vs. transverse stress on flattened wires
0 50 100 150 200 250
60
80
100
120
140
160
180
sample #1 round
sample #1 round after force unload
sample #2 15% rolled
sample #2 15% rolled after force unload
Transverse stress [MPa]
PIT #31712 Ø = 1.0 mm
@ 4.2K, 19 T
I c [A
]
PIT 192
~7.5% Ic reduction by rollingShift of irr by ~ 40 MPa
NO Ic reduction by rollingShift of irr by ~ 15 MPa
50 100 150 200 250
60
80
100
120
140
160
180
@ 4.2K, 19 T
95% Ic0
Transverse stress [MPa]
I c [A
]
sample #1 round
sample #1 round after force unload
sample #2 15% rolled
sample #2 15% rolled after force unload
RRP 132/169 #114163 Ø = 1.0 mm
Internal Sn 132/169
Effects of the stress redistribution
This wire can withstand the peak stress of the FCC dipoles !!
12 14 16 18 20 220
500
1000
1500
2000
2500
3000
FCC Target
no
n-C
u J
c [A
/mm
2]
B [T]
PIT - Bc2
Kr= 26.5 T
Internal Sn - Bc2
Kr= 24.9 T
@ 4.2 K
T. Boutboul et al., IEEE TASC 19 (2009) 2564
@ 200 MPaCritical current density vs. magnetic field
Don’t forget the reversible effects of stress !!
12 14 16 18 20 220
500
1000
1500
2000
2500
3000
FCC Target
no
n-C
u J
c [A
/mm
2]
B [T]
PIT - Bc2
Kr= 23.2 T @ 200 MPa
Internal Sn - Bc2
Kr= 23.8 T @ 200 MPa
@ 4.2 K, 200 MPa
J. Parrell et al., AIP Conf. Proc. 711 (2004) 369
Best performance achieved so far in industrial wires
High Temperature Superconductors are
different animals …
Bi2212Bi2Sr2CaCu2O8+x
Bi2223Bi2Sr2Ca2Cu3O10+x
Y123YBa2Cu3O7-x
3 CuO2 planes
2 CuO2 planes
CuO chains
2 CuO2 planes
O
Ca
Cu
Sr
Bi
O
Cu
Y
Ba
HTS materials for applications
Y123 Coated Conductor
Bi2212Powder-In-Tube wire
Bi2223 Powder-In-Tube tape
YBa2Cu3O7-x (YBCO) coated conductors
Ag cap layer
Cu stabilisation
YBCO layer metallic substratebuffer layers
~1 µm of YBCO in a ~100 µm thick tape
[001] tilt grain boundaryH. Hilgenkamp and J. Mannhart, RMP 74 (2002) 485
Ag cap layer
Cu stabilisation
YBCO layer metallic substratebuffer layers
Biaxial texturing – within < 3° – is obtained
a
b
a
b
a
b
a
b
a a
b
a
b
Top view
The template is a metallic substrate coated with a multifunctional oxide barrier
Presently produced by
• complex and expensive manufacturing process
• pronounced anisotropic behaviour
but with some also drawbacks:
YBa2Cu3O7-x (YBCO) coated conductors
~1 µm of YBCO in a ~100 µm thick tape
Goyal et al., APL 69 (1996) 1795
Iijima et al., APL 60 (1992) 769
REBCO, RE = Rare Earth
Tc
Tc
Tc , Ic
0.00 0.05 0.10 0.15 0.20 0.25 0.3090.6
90.8
91.0
91.2
91.4
91.6
91.8
p // a
p // c
T c [K
]
p [GPa]
p // b
Critical temperature vs. uniaxial strain in single crystals
U. Welp et al., Phys. Rev. Lett. 69 (1992) 2130
a
b
a
b
a
Critical current vs. uniaxial strain in coated conductors
D. van der Laan et al.,Supercond. Sci. Technol. 24 (2011) 115010
@ 76 K, s.f.
Reversible effects of strain on YBCO
In the following, the focus will be on
Today high field superconductor, up to 23.5 T in
solenoidal coils, the material for and
and only candidate material for the 16 T dipoles of
Nb3Sn
YBCO Tomorrow high field superconductor, more than 40 T
demonstrated in solenoidal insert coils*, the way to get
20 T dipoles and beyond
*tested in a resistive outsert
All superconducting magnets beyond LTS The World cup of high magnetic fields
Maximum field [T]
HTS insertHTS coil field
[T]Winding
technology
32 REBCO 17 DP
27.6Bi2223 / REBCO
4.5 (Bi2223) 6 (REBCO)
LW
IEE CAS 27.2 REBCO 12.2 DP
26.4 REBCO 26.4 DP
IEE CAS 25.7 REBCO 10 DP
25 REBCO 4 LW
HFLSM 24.6 Bi2223 10.6 DP
24.2 Bi2223 3.66 LW
Stress management in Ultra High Field magnets
Hoop stress levels above 100 MPa are common, the NHMFL 32 T magnet operates at 400 MPa
In the case of layer winding the directionchanges going from one layer to the next impose in-plane hard bending of the tape
Other constrains to the winding come from the tape geometry of the conductor
F I B hoop
wire
IBR
S
B I
Ic vs. axial strain
C. Barth, G. Mondonico and CS, Supercond. Sci. Technol. 28 (2015) 045011
REBCO CCs: Dependence of Ic on axial loads
0.0 0.2 0.4 0.6 0.8 1.0
0.6
0.7
0.8
0.9
1.0
SuperPower
0.66 < irr
< 0.68 %
Bruker HTS
0.70 < irr
< 0.72 %
SuNAM
0.67 < irr
< 0.69 %
Fujikura
0.55 < irr
< 0.57 %
SuperOx
0.45 < irr
< 0.47 %
no
rmal
ized
cri
tica
l cu
rren
t, I c /
I c,m
ax
Applied strain [%]
@ 4.2 K, 19 T
• Very low stress effect curves are flat in rev. region
• Irreversible stress limits above 500 MPa
• The only weakness is delamination...
• REBCO CCs are inherently strong, ~50% is a high strength alloy
0.0 0.2 0.4 0.6 0.8 1.00
200
400
600
800
1000
4.2 K
Stre
ss [
MP
a]
Strain [%]
SuperPower:
E = 155 GPa, Rp0.2
= 893 MPa
Bruker HTS:
E = 187 GPa, Rp0.2
= 736 MPa
SuNAM:
E = 168 GPa, Rp0.2
= 846 MPa
Fujikura:
E = 176 GPa, Rp0.2
= 787 MPa
SuperOx:
E = 172 GPa, Rp0.2
= 1083 MPa
Ic vs. axial stress
0 200 400 600 800 1000
0.6
0.7
0.8
0.9
1.0
SuperPower
800 < irr
< 830 MPa
Bruker HTS
740 < irr
< 750 MPa
SuNAM
830 < irr
< 840 MPa
Fujikura
750 < irr
< 760 MPa
SuperOx
770 < irr
< 800 MPa
no
rmal
ized
cri
tica
l cu
rren
t, I c /
I c,m
ax
Applied stress [MPa]
Reversible behaviour and irreversible limit
HTS for accelerator magnets
The goal of 20 T in an accelerator quality dipole calls for HTS
1970 1980 1990 2000 2010 2020 2030 20400
2
4
6
8
10
12
14
16
18
20
FCC-hh
HTS Dipole
HL-LHC
LHCSSC
HERA
Tevatron
Mag
ne
tic
fie
ld [
T]
Year
SPS
Accelerator magnets operate at ~10 kA tokeep inductance low and ease magnetprotection
The most promising HTS CONDUCTOR for
accelerator magnets is the Roebel Cable (10
kA-class cable)
A coil of Roebel cable: a Short Dipole Demonstrator
A 5 T, 40 mm bore HTS based dipole demonstrator
J. Van Nugteren, PhD thesis, 2016
~1000 m of REBCO tape
~70 m of Roebel cable
5 T in standalone configuration
40 mm aperture
A coil of Roebel cable: a Short Dipole Demonstrator
A 5 T, 40 mm bore HTS based dipole demonstrator
J. Van Nugteren, PhD thesis, 2016
Are Roebel cables able to withstand
large transverse loads?
The answer is YES: Irreversible stress limit 400 MPa
50 100 150 200 250 300 350 400 450 5006.5
7.0
7.5
8.0
8.5
@ 4.2 K, 10.5 T
Cri
tica
l cu
rren
t, I c [
kA]
Transverse stress [MPa]
Bruker tape - CTD-101K impregnation
50 100 150 200 250 300 350 400 450 5002.5
3.0
3.5
@ 4.2 K, 10.5 T
Cri
tica
l cu
rren
t, I c [
kA]
Transverse stress [MPa]
SuperPower tape - Araldite + filler
SuperPower tape - CTD-101K impregnation
Short Dipole Demonstrator results
3.35 T
1st coil wound with moderate Ic SuNAM cable (~40% of the Bruker cable)
J. Van Nugteren @ EUCAS2017
New coil with ultra-high Ic cable from Bruker already wound Expected field in stand-alone test ~7T
What we have learned…
• Why we care about mechanical loads
• What hides behind the reversible degradation of Ic
• How the stress tolerance depends also on factors extrinsic to the wire
Electromagnetic forces in solenoids and accelerator magnets
Deviatoric strain, intrinsic anisotropy,…
Load geometry, impregnation…
• Which are the intrinsic mechanisms that lead to the irreversible degradation of Ic
Detailed study of the stress concentration at the voids in Nb3Sn
• An overview of the electromechanical properties of Nb3Sn and YBCO
Thank you for the attention !
Carmine SENATORE
http://supra.unige.ch
…time for questions…
If you want to know more about applied superconductivity in Geneva, visit http://supra.unige.ch