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Physica C 397 (2003) 95–98
www.elsevier.com/locate/physc
Stress/strain characteristics of PIT MgB2 tapeswith nickel sheath––effect of indium addition to the core
Kazumune Katagiri a,*, Akifumi Iwamoto b, Yoshitaka Shoji a,Kyoji Tachikawa c, Yutaka Yamada c, Kazuo Watanabe d, Toshiyuki Mito b
a Faculty of Engineering, Iwate University, 4-3-5 Ueda, Morioka 020-8551, Japanb National Institute for Fusion Science, 322-6 Oroshi-cho, Toki 509-5292, Japan
c Faculty of Engineering, Tokai University, 1117 Kitakaname, Hiratsuka 259-1292, Japand Institute for Materials Research, Tohoku University, 2-1-1 Katahira, Sendai 980-8577, Japan
Received 5 June 2003; accepted 6 August 2003
Abstract
The electro-mechanical characteristics of the nickel sheathed powder-in-tube MgB2 mono-core tapes with 10 vol%
indium powder were evaluated. No marked change in the stress–strain curve was found by indium addition. On the
other hand, the irreversible strain for the tape where a drastic degradation of critical current Ic begins increased from
0.25% to 0.50% by the addition of indium. The indium addition also suppressed the slight increase in Ic with strain.
These characteristics of Ic with strain were compared with those reported by other researchers. Scanning electron
microscope observations of the longitudinal section of degraded samples revealed that the number of micro-cracks was
appreciably smaller in the indium added tapes.
� 2003 Elsevier B.V. All rights reserved.
PACS: 74.70.Ad; 74.25.Fy; 74.25.Ld
Keywords: MgB2 tape; Indium addition; Mechanical property; Critical current
1. Introduction
MgB2 superconductors fabricated by the pow-
der-in-tube (PIT) process are expected to be less
expensive superconducting conductors because
simple and low cost fabrication procedures areapplicable. Many studies on the processing have
been conducted [1–4]. The transport critical cur-
* Corresponding author. Tel./fax: +81-19-621-6412.
E-mail address: [email protected] (K. Katagiri).
0921-4534/$ - see front matter � 2003 Elsevier B.V. All rights reserv
doi:10.1016/j.physc.2003.08.006
rent density, Jc, of the core in the PIT MgB2
conductors, which depends on the raw powder
quality, sheath material, fabrication procedure,
heat treatment condition and so on, is in the range
of 104–105 A/cm2 at 4.2 K and 0 T. In order to
improve the Jc, addition of metal powders, such assilver, nickel, copper, indium and tin, to MgB2
core has been tried by some of the present authors
[5,6]. Among them, it has been shown that the 10
vol% indium addition and annealing at 473 K for
10 h enhances Jc by a factor of 6–7. It has also
been shown that the indium is well elongated in
ed.
96 K. Katagiri et al. / Physica C 397 (2003) 95–98
the MgB2 core by scanning electron microscope
(SEM) observations. Therefore, the addition of
indium was assumed to contribute for the im-
provement of weak MgB2 grain linkage.
For practical applications, it is important to
study the stress/strain characteristics of the con-ductor. Strain dependencies of critical current, Ic,in PIT MgB2 tapes or round wires with the stain-
less steel or the iron/stainless steel sheaths have
been investigated at 4.2 K and 5 T [7,8]. The Icvalues are reported to increase with the applied
tensile strain up to 0.4–0.5% in the stainless steel
sheathed tapes and 0.47% in the Fe/stainless steel
sheathed wires. The tape with the indium powderin the core is expected to have better stress/strain
characteristics than that without indium. In this
study, the effect of the indium addition to the
MgB2 core on the stress/strain characteristics is
investigated.
0.0 0.2 0.4 0.6 0.8 1.00.0
0.2
0.4
0.6
0.8
1.0
1.2
(b)
4.2K, 2T
I c/Ic0
0.0 0.2 0.4 0.6 0.8 1.00
100
200
300
400
500
600
(a)
Tensile strain (%)
Tens
ile s
tres
s (M
Pa)
Ni/MgB2 10% In Ic0=87ANi/MgB2 0% In Ic0=31A
Fig. 1. Stress–strain curves (a) and strain dependence of Ic (b)for nickel sheath/MgB2 tapes with and without 10 vol% indium
addition.
2. Experimental
Two nickel sheathed mono-core PIT tapes with
10 vol% indium addition in the core and without
it, for reference, were prepared. The commercial
Alfa-Aesar MgB2 powder with the purity of 98%
and grain size less than 106 lm was used. The
purity and grain size of the indium powder are
99.9% and less than 40 lm, respectively. The MgB2
powder with or without 10 vol% indium powder
was encased in a nickel tube with an outer/inner
diameter of 8/6 mm to form a sheath/core com-
posite. The final tape width and thickness after
rolling were about 4 and 0.3 mm, respectively. The
nickel/MgB2 ratio was estimated to be about 1.3
by the SEM photographs. Then, only the tape with
10 vol% indium addition was annealed at 473 Kfor 10 h in flowing argon/5 vol% hydrogen gas.
The details of the specimen preparation are found
in Ref. [5].
The stress/strain characteristics evaluation of
the tapes at 4.2 K and 2 T was conducted by using
an apparatus inserting in the bore of the 15 T su-
perconducting magnet at the Institute for Materi-
als Research, Tohoku University. The detaileddescription of the apparatus is available in Ref. [9].
The gauge length and the voltage tap distance of
the specimen were 17.5 and 8 mm, respectively.
Both ends of the specimen were soldered to each
copper terminal. The specimen can be contracted
freely during cool down, so that we do not have to
consider the pre-strain caused by the difference of
thermal contraction between the specimen and theapparatus. The strain was measured by a clip on-
gage, which was set between the copper current
terminals. It was calibrated at liquid helium tem-
perature. The Ic was evaluated with the criterion of
1 lV/cm. Two specimens were measured for each
PIT tapes.
3. Results and discussion
Fig. 1(a) shows the stress–strain curves of the
tapes. Square symbols represent the points on
unloading. They are almost linear excepting for
K. Katagiri et al. / Physica C 397 (2003) 95–98 97
high and low stress region. Although some dis-
crepancy is seen in the initial region of straining,
the stress–strain curves for two tapes are almost
comparable within the accuracy of the strain
measurement, 0.05%.
Fig. 1(b) shows the strain dependence of Ic forthe two tapes. The Ic is normalized by Ic0, Ic at 0%external strain. The tapes with and without indium
addition have Ic0 of 87 and 31 A, respectively. In
the case of indium added tape, Ic is constant,
within the accuracy of measurement, irrespective
of strain applied and then suddenly degraded be-
yond 0.5% strain. On the other hand, the Ic of thetape without indium increased very slightly up to0.2% with the external strain and then gradually
decreased until 0.25% where it begins to decrease
rather steeply. After the degradation, Ic could not
reversibly recovered on unloading. The compres-
sive strain levels of the cores of MgB2 subjected
from Ni sheath for indium added tape and that
without it appear almost the same. The increase in
the strain for the irreversible degradation onset byindium addition will be ascribed to the improved
connectivity of MgB2 grains as evidenced by the
increase in the Ic before straining mentioned above.
The mechanisms how the indium addition sup-
presses the slight increase in Ic with strain is not
known at present.
The strain dependence of Ic in Fig. 1(b) is re-
plotted in Fig. 2 together with those available
-0.1 0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.70.0
0.2
0.4
0.6
0.8
1.0
1.2
I c/Ic0
Tensile strain (%)
Ni/MgB2 10 In addition [4.2K, 2T]Ni/MgB2 [4.2K, 2T]SS25/Fe/MgB2(Goldacker[8])[4.2K, 5T]SUS316/MgB2(Kitaguchi[7]) [4.2K, 5T]
Fig. 2. Comparison of strain dependence of Ic with those re-
ported by Kitaguchi et al. [7] and Goldacker and Schlachter [8].
reported by Kitaguchi et al. [7] and Goldacker
and Schlachter [8]. According to the higher ther-
mal contraction coefficient of nickel (12.8 · 10�6
K�1 at 300 K) as compared with that of MgB2
(8.3 · 10�6 K�1) [10], the slight increase in Ic in the
tape without indium in the present study is as-cribed to the relaxation of the compressive strain
generated in the MgB2 core during cooling down
to 4.2 K [7,8]. However, the amount of the in-
crease, less than 1.5%, is quite small compared
with those, 7% and 13%, in Refs. [7] and [8], re-
spectively. One of the main reasons for the dif-
ference in the amount of increase might be that
our measurement was performed at relativelylower magnetic field of 2 T as compared with the
measurements at 5 T [7,8]. Another possible rea-
son is the difference in the shape of the cross
section. The aspect ratio in the tapes used in the
present study and Ref [7] are larger than those of
round wire [8]. Difference in the three-dimensional
strain state due to the aspect ratio has already
been reported [11]. Amount of the pre-strainsubjected to thermal history has possibility to
explain both the degree of enhancement of Icmentioned above and the irreversible strain where
the Ic steeply decreases. Because the materials of
the sheath as well as the sheath to superconductor
ratio are different, the differences in the irrevers-
ible strains for the four tapes cannot be discussed
quantitatively at present.Fig. 3 shows SEM photographs of the longi-
tudinal section of the tape specimen without in-
dium addition after the tensile test. The axis of
tensile loading is horizontal in the photographs.
Many cracks could be observed for the tape
without indium addition. On the other hand, ra-
ther small number of cracks is found in the tape
with indium addition. The cracks appear topropagate mainly along the grain boundary in the
magnified view (Fig. 3(b)). The cracks are sup-
posed to have caused the irreversible Ic degrada-
tion. According to the transmission electron
microscopic study, it has been observed that the
indium distributed so as to fill the gap of the MgB2
grains [5]. We believe that the indium powder
addition contributes to the improvement of theweak MgB2 grain linkage and, therefore, both the
Ic and its strain characteristics.
Fig. 3. SEM photographs in longitudinal section for tapes
without indium powder after tensile test. (a) Low magnification
view and (b) magnified view.
98 K. Katagiri et al. / Physica C 397 (2003) 95–98
4. Summary
The stress/strain characteristics at 4.2 K and 2 T
of the PIT nickel sheathed MgB2 tapes with andwithout 10 vol% indium addition to its core were
evaluated. In the latter tape, the Ic slightly in-
creased as the strain is increased. Beyond the peak,
it gradually and then steeply degraded. On the
other hand, no peak of Ic is found in the tape with
indium addition. After the degradation, Ic did not
recover on unloading. The irreversible steep Icdegradation begins at the strains of 0.5% and
0.25% for the tapes with and without indium
powder, respectively. The cracks in the longitudi-
nal section of both tapes with and without indium
powder after the tensile test appeared to grow
mainly along the grain boundary of MgB2. Thus,
we believe that the indium powder addition con-tributes to the improvement of the mechanical
linkage of the MgB2 grain.
Acknowledgements
We wish to thank T. Tsukinokizawa, K. Hiroi
T. Araya and R. Takaya, Graduate students ofIwate University for their help in the experiments
at HFML, Tohoku University and SEM ob-
servations. This work was performed with the
support and under the auspice of the NIFS Col-
laborative Research Program.
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