2009 APPLIED SUPERCONDUCTIVITYMagnetic field behaviour of ex-situ processed MgB 2 multifilam<strong>en</strong>tary wiresIn order to make MgB 2 useful not only for dc but also for acapplications further conductor developm<strong>en</strong>t and optimizationare still needed, in particular to reduce the ac lossescaused by magnetic hysteresis in the MgB 2 core, filam<strong>en</strong>tcoupling and eddy curr<strong>en</strong>ts flowing through the metallicmatrix. In this context research work should be focused onmultifilam<strong>en</strong>tary strands with a large number of very finefilam<strong>en</strong>ts, twisted filam<strong>en</strong>ts and non-magnetic and high resistivitysheath.We have focused our work on obtaining multifilam<strong>en</strong>taryconductors with a large number of very fine filam<strong>en</strong>ts. Inthis context, the powder’s granulometry can play a crucialrole. In this experim<strong>en</strong>t we have prepared two MgB 2 startingpowders which are either not milled (NM) or milled(M) with differ<strong>en</strong>t granulometries (NM= 1.5 µm and M=450 nm) and by the ex-situ powder in tube (PIT) methodwe have realized multifilam<strong>en</strong>tary wires with 19, 91 and361 filam<strong>en</strong>ts and an average size of each filam<strong>en</strong>t of 279,110 and 30 µm respectively. In figure 143 the cross sectionsof the three wire types are shown.We have studied the relationship betwe<strong>en</strong> grain and filam<strong>en</strong>tsize in terms of transport properties. The measuredcritical curr<strong>en</strong>t d<strong>en</strong>sities (J C ) for the samples with NM powderand M powder are reported in figure 144. The criticalcurr<strong>en</strong>t d<strong>en</strong>sity improves with milling for all samples asreported in our previous work [A. Malagoli et al J. Appl.Phys. 104, 103908 (2008)]. Focusing on the behaviour ofthe not milled samples, passing from 19 to 91 filam<strong>en</strong>ts aremarkable critical curr<strong>en</strong>t d<strong>en</strong>sity degradation is evid<strong>en</strong>t,that is partially recovered going to 361 filam<strong>en</strong>ts. On thecontrary for the milled samples 19M and 91M have almostid<strong>en</strong>tical critical curr<strong>en</strong>t d<strong>en</strong>sity - a slightly better behaviourin field being observed in 91M. Wh<strong>en</strong> the number of filam<strong>en</strong>tsincreases up to 361, critical curr<strong>en</strong>t d<strong>en</strong>sity decreasesstaying though above the 361NM.Such a behaviour of the critical curr<strong>en</strong>t d<strong>en</strong>sity in field cannotbe explained or well understood simply considering theeffects of milling. In these complex conductors several factorshave to be tak<strong>en</strong> into account which have an effect onthe transport properties: the starting granulometry of theMgB 2 powders, the cold deformation force and the final filam<strong>en</strong>tsize. Therefore, in the final analysis, the capabilityof these conductors to transport high critical curr<strong>en</strong>ts cruciallydep<strong>en</strong>ds on a proper balance of these parameters. Inthis work we have obtained the best ratio filam<strong>en</strong>t size/grainsize on a 91 filam<strong>en</strong>ts wire with an average filam<strong>en</strong>t size ofabout 110 µm and a powder starting average grain diameterof about 450 nm. A finer MgB 2 granulometry seems to b<strong>en</strong>eeded to realize very thin filam<strong>en</strong>ts (10−30 µm) with highcritical curr<strong>en</strong>t d<strong>en</strong>sity.Figure 143: Images of differ<strong>en</strong>t cross sections through the wireswith 19, 91 and 361 filam<strong>en</strong>ts respectively.Figure 144: Transport critical curr<strong>en</strong>t d<strong>en</strong>sity (J C ) for differ<strong>en</strong>tmilled (M) and not milled (NM) samples measured up to magneticfields of 13 T using a wide bore resistive magnet and a Heliumbath cryostat (T = 4.2 K).E. MossangA. Malagoli, G. Romano, M. Vignolo, C. Ferdeghini, M. Putti (CNR-INFM LAMIA, G<strong>en</strong>ova, Italy), S. Brisigotti, G.Grasso, A. Tumino (Columbus Superconductors S.p.A., G<strong>en</strong>ova, Italy)101
APPLIED SUPERCONDUCTIVITY 2009Superconductivity of C and TiC doped multi-filam<strong>en</strong>tary MgB 2 wiresRec<strong>en</strong>tly a great deal of both fundam<strong>en</strong>tal and technical researchhas be<strong>en</strong> carried out on carbide-doped MgB 2 dueto its high upper critical field (H c2 ) which pres<strong>en</strong>ts considerableinterest for the fabrication of practical magnets, especiallythe GM-cryocooled MRI magnet. For <strong>en</strong>gineeringapplications, it is necessary to make MgB 2 superconductorsinto multi-filam<strong>en</strong>tary wires or tapes. The in-situ and exsitupowder-in-tube (PIT) processes have become the dominantor standard methods due to their commercial pot<strong>en</strong>tialfor large-scale and low-cost production of MgB 2 wires andtapes.Figure 145: Cross section of the differ<strong>en</strong>t multi-filam<strong>en</strong>tMgB 2 /NbCu wires.In this work, various multi-filam<strong>en</strong>t MgB 2 /NbCu roundwires with carbon or TiC doping have be<strong>en</strong> fabricated byin-situ PIT method at the Northwest Institute for NonferrousMetal Research (NIN). The typical diameter of the finalwire is 1 mm. The MgB 2 coil was fabricated using thewind and react method with a 1.5 m long wires and a heattreatm<strong>en</strong>t at 680 ◦ C for 1.5 h. The transport critical curr<strong>en</strong>tof the MgB 2 coils was measured with magnetic fields upto 10 T at various temperatures using a standard four probemethod. The critical curr<strong>en</strong>t d<strong>en</strong>sity, J c , of the coil was calculatedfrom the measured critical curr<strong>en</strong>t I c divided by thecross sectional area of the MgB 2 core.Figure 145 shows the 6-, 12- and 36-filam<strong>en</strong>taryMgB 2 /NbCu wires with amorphous carbon doping. Thevolume of MgB 2 in whole wires is around 20%, 14% and14%, respectively. Figure 146 shows the transport criticalcurr<strong>en</strong>t d<strong>en</strong>sity J c values as a function of applied field at20 K for the multi-filam<strong>en</strong>tary MgB 2 coils with amorphouscarbon or TiC doping. The 6-filam<strong>en</strong>t wires with carbondoping has the largest J c , as high as 4.5×10 4 A/cm 2 at 2 T.The large value of J c in this sample may be due to the goodgrain connectivity and strong flux pinning force. This resultindicates that carbon doping is b<strong>en</strong>eficial for the fabricationof high performance long l<strong>en</strong>gth multi filam<strong>en</strong>tary MgB 2wires.Figure 146: Transport critical curr<strong>en</strong>t d<strong>en</strong>sity of differ<strong>en</strong>t multi–filam<strong>en</strong>tary MgB 2 coils at T = 20 K.Figure 147 shows the result of the transport J c versus Hmeasurem<strong>en</strong>ts at temperatures from 4.2 to 30 K measuredfor 6-filam<strong>en</strong>t wires with carbon doping. This value islower than the best values found in the literature, but webelieve that the transport J c could be improved by optimizingvarious processing parameters.In summary, the J c of multi-filam<strong>en</strong>tary long l<strong>en</strong>gth MgB 2wires were <strong>en</strong>hanced by amorphous carbon doping. Thehighly reactive amorphous carbon can easily substitute intothe lattice of MgB 2 ev<strong>en</strong> with a heat-treatm<strong>en</strong>t at lower temperature.On the other hand, the lower heat-treatm<strong>en</strong>t temperatureresults in a smaller MgB 2 grain size, which introduceda high d<strong>en</strong>sity of flux-pinning c<strong>en</strong>ters.Figure 147: Transport critical curr<strong>en</strong>t d<strong>en</strong>sity of a 6-filam<strong>en</strong>tMgB 2 coil at various temperatures.E. MossangQ.Y. Wang, G. Yan (Northwest Institute for Non-Ferrous Metal Research, Xi’an, China), A. Sulpice (Institut Neel,Gr<strong>en</strong>oble102
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LABORATOIRE NATIONAL DES CHAMPS MAG
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TABLE OF CONTENTSPreface 1Carbon Al
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Coexistence of closed orbit and qua
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2009PrefaceDear Reader,You have bef
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2009 CARBON ALLOTROPESInvestigation
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2009 CARBON ALLOTROPESPropagative L
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2009 CARBON ALLOTROPESEdge fingerpr
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2009 CARBON ALLOTROPESObservation o
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2009 CARBON ALLOTROPESImproving gra
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2009 CARBON ALLOTROPESHow perfect c
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2009 CARBON ALLOTROPESTuning the el
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2009 CARBON ALLOTROPESElectric fiel
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2009 CARBON ALLOTROPESMagnetotransp
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2009 CARBON ALLOTROPESGraphite from
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2009Two-Dimensional Electron Gas25
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TWO-DIMENSIONAL ELECTRON GAS 2009Di
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TWO-DIMENSIONAL ELECTRON GAS 2009Sp
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TWO-DIMENSIONAL ELECTRON GAS 2009Cr
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TWO-DIMENSIONAL ELECTRON GAS 2009Re
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TWO-DIMENSIONAL ELECTRON GAS 2009In
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TWO-DIMENSIONAL ELECTRON GAS 2009Ho
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TWO-DIMENSIONAL ELECTRON GAS 2009Te
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2009 SEMICONDUCTORS AND NANOSTRUCTU
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2009 SEMICONDUCTORS AND NANOSTRUCTU
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2009 SEMICONDUCTORS AND NANOSTRUCTU
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- Page 84 and 85: 2009 MAGNETIC SYSTEMSY b 3+ → Er
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- Page 136 and 137: 2009 PROPOSALSProposals for Magnet
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Lawrence Berkeley National Laborato