The room temperature elastic and plastic properties under uniaxial tensile loading of the different phases of an un-reacted, internal-tin process, Nb$_{3}$Sn wire have been determined by tensile tests of whole wires and of extracted Ta, Nb and Nb alloy filaments, as well as by indentation hardness measurements in metallographic wire cross sections

Devred, A

El-Kallassi, P

Fedelich, B

Finn, M

Griepentrog, M

Lecouturier, F

Oberli, L

Rehmer, B

Scheuerlein, C

Sgobba, Stefano

Thilly, L

Vidal, V

CERN Document Server

EUROPEAN ORGANIZATION FOR NUCLEAR RESEARCHLaboratory for Particle Physics(MCS)TENSILE PROPERTIES OF THE INDIVIDUAL PHASESIN UNREACTED MULTIFILAMENT Nb3Sn WIRESC. Scheuerlein1, A. Devred1,2, B. Fedelich3, M. Finn3, M. Griepentrog3, P. El-Kallassi1,F. Lecouturier4, L. Oberli1, B. Rehmer3, S. Sgobba1, L. Thilly5, V. Vidal41 CERN, Accelerator Technology Department, Geneva, Switzerland2 CEA/Saclay, DSM/DAPNIA/SACM, Gif-sur-Yvette CEDEX, France3 Bundesanstalt für Materialforschung und -prüfung (BAM), Berlin, Germany4 LNCMP, CNRS-UPS-INSA, 143 avenue de Rangueil, Toulouse, France5 LMP, Université de Poitiers, SP2MI, Futuroscope, FranceCERN/AT 2007-3Presented at the Cryoprague 2006 Conference17-21 July 2006 - Praha,  Czech Republic10 April 2007Departmental ReportCERN, Accelerator Technology DepartmentCH - 1211 Geneva 23SwitzerlandThe room temperature elastic and plastic properties under uniaxial tensile loading of the different phases of anun-reacted, internal-tin process, Nb3Sn wire have been determined by tensile tests of whole wires and of extractedTa, Nb and Nb alloy filaments, as well as by indentation hardness measurements in metallographic wire crosssections. 1Tensile properties of the individual phases in unreacted  multifilament Nb3Sn wires  C. Scheuerlein1, A. Devred1,2, B. Fedelich3, M. Finn3, M. Griepentrog3, P. El-Kallassi1,  F. Lecouturier4, L. Oberli1, B. Rehmer3, S. Sgobba1, L. Thilly5, V. Vidal4 1European Organization for Nuclear Research (CERN), 1211 Genève 23, Switzerland 2CEA/Saclay, DSM/DAPNIA/SACM, 91191 Gif-sur-Yvette CEDEX, France 3Bundesanstalt für Materialforschung und –prüfung (BAM), 12200 Berlin, Germany 4LNCMP, CNRS-UPS-INSA, 143 avenue de Rangueil, 31400 Toulouse, France 5LMP, Université de Poitiers, SP2MI, 86962 Futuroscope, France  The room temperature elastic and plastic properties under uniaxial tensile loading of the different phases of an un-reacted, internal-tin process, Nb3Sn wire have been determined by tensile tests of whole wires and of extracted Ta, Nb and Nb alloy filaments, as well as by indentation hardness measurements in metallographic wire cross sections.  INTRODUCTION  As part of the EU-supported Next European Dipole (NED) Joint Research Activity [1] an effort has been launched in European industry to promote the development of high performance superconducting multifilament composite Nb3Sn wires and cables. To simulate cabling degradation and optimise wire design, a Finite Element (FE) model of the wire is under development [1]. FE simulations require the input of relevant materials properties. In this article, we report room temperature tensile strength and E-modulus results for the different phases in an Internal Tin (IT) Nb3Sn wire and describe how these materials properties have been measured.  EXPERIMENTAL PROCEDURES AND RESULTS  The samples The mechanical properties of the different phases in an un-reacted IT Nb3Sn wire produced by Alstom/MSA for CEA and described in detail in reference 2, have been determined. The wire with a nominal diameter of 0.825 mm consists of a Cu stabiliser, 19 Sn sub-elements made up of 198 Nb-7.5wt.% Ta filaments (nominal filament diameter: 4 µm) embedded in a Cu matrix and arranged in concentric circles around 19 pure Sn pools, and a mixed Nb and Ta diffusion barrier, surrounding the multifilament area.  The E-modulus of Ta has been measured on single filaments extracted from Ta/Cu monofilament samples produced at LNCMP for the development of resistive pulsed magnets. These monofilament wires are precursors for nanofilamentary wires, whose microstructure and mechanical properties have been extensively studied [3,4]. The Nb and Nb-7.5wt.%Ta E-moduli have been measured on filaments extracted from Nb-Ta/Cu and Nb/Cu monofilament samples provided by Alstom/MSA.  2Tensile tests Tensile tests of Nb3Sn wires and binary composite monofilament samples were performed according to DIN EN 61788-6(2001-07) [5]. For the determination of the wire proof stress (Rp0.2), the raw-data stress-strain curve is fitted by a 2nd order polynomial and displaced so as to intercept the zero stress-strain position, as described in [6]. The tensile test results are summarised in Table 1 for the whole Nb3Sn composite wire and for samples of the same wire but where the Cu stabiliser has been removed by chemical etching. Rm of the wire without stabiliser shows an unusually large variation, which is possibly due to the roughness of the sample surface (Nb barrier).  Table 1  EA, Rp0.2 and Rm, Nb3Sn composite wire, with and without stabiliser (an average of 5 tensile tests).  Sample EA (GPa) Rp0.2 (MPa) Rm (MPa) Whole wire 108±0.9 374±14.0 523±3.6 Wire without stabiliser 93.3±0.8 516±2.8 612±99  The E-moduli obtained for the filaments extracted from the binary composite monofilament samples are: EA(Nb-Ta)=94.1±0.14 GPa, EA(Nb)=91.7±0.99 GPa and EA(Ta)=170±0.5 GPa (an average of three tensile tests).  Tensile tests of single Nb-Ta filaments extracted from the IT Nb3Sn wire were performed with a dedicated apparatus built by BAM. The filament cross section is measured with an optical system. Since an extensometer can not be attached to the filaments, the filament E-modulus and Rp0.2 can not be measured. The measured filament ultimate tensile strength is Rm=977±303 MPa (an average of ten measurements). The tensile test result obtained for a Nb-7.5wt.%Ta monofilament extracted from the precursor binary composite is Rm=734±0.4 MPa (an average of three measurements).  DISCUSSION  Elastic anisotropy in the cold-drawn wire phases Since the E-modulus is mainly determined by the binding forces between atoms, it is much less influenced by cold work and heat treatments than the tensile strength. Nevertheless, as a consequence of the asymmetric materials flow during wire processing, an important elastic anisotropy can be observed [7]. For the Cu matrix in Nb-Ti/Cu multifilament wire an E-modulus of 116 GPa [8] has been measured, which is about 10% lower than the E-modulus value of 128 GPa reported for isotropic Cu and similar to the Cu E-modulus in the Nb3Sn wire [9]. The E-modulus measured for the Nb filament extracted from the monofilament Nb/Cu sample is 92 GPa, 11% lower than the value for isotropic Nb (103 GPa [10]) and the Ta filament E-modulus is 170 GPa, 8% lower than the value reported for isotropic Ta (185 GPa [11]). These results indicate a strong elastic anisotropy in the heavily cold worked phases and it can be expected that the E-moduli perpendicular to the wire drawing direction are higher than those measured in the drawing direction. A Sn E-modulus of 49 GPa has been derived from instrumented indentation measurements on a wire cross section. The E-modulus reported for self-annealed, fine  3grain Sn is 44.3 GPa [10]. Due to the very low annealing temperature of Sn it is assumed that the Sn in the Nb3Sn wire is elastically isotropic.  Composite wire E-modulus calculated according to the ROM Assuming isostrain conditions, the wire stress is the volume average of the local stresses and the composite modulus follows a Rule Of Mixtures (ROM) [12]. In Table 2, the ROM result is compared with the experimentally determined composite wire E-moduli. For the whole wire and the wire without stabiliser, the ROM result exceeds the experimentally determined composite E-modulus by 2% and 9%, respectively.  Table 2  E-modulus calculation of the Nb3Sn wire without and with stabiliser according to the ROM.  Wire without stabiliser Whole wire Material E (GPa) Vol.% weighted E (GPa) Vol.%  weighted E (GPa) Cu 116 [8] 51.1 59 80.2 93 Nb-Ta 94 21.9 21 8.9 8.4 Sn 49 13.9 6.8 5.6 2.7 Nb 92 8.7 8.0 3.5 3.2 Ta 170 4.4 7.5 1.8 3.1 ROM   102  110 Experiment   93.3  108  Plastic properties For fully work-hardened and isotropic materials the plastic materials properties can be estimated from the indentation hardness according to Equation 1, or when elastic deformation can be neglected, the yield stress (YS) is about one third of the Vickers hardness (HV) expressed in identical units [13,14,15]. HV/YS=0.065+0.6ln(E/YS)     1 Table 3 summarises the HV values that have been measured for the different phases in the Nb3Sn wire cross section, together with the YS calculated as YS=HV/3 or using Equation 1 (for E/HV<44.3). The experimental details of the indentation hardness measurements are described in references 8 and 16. For the textured wire phases it is assumed that Rp0.2 exceeds the YS values derived from the HV/YS ratio, which is valid for isotropic materials, by about 10% [8].  Table 3  HV, E-modulus and YS derived from HV for Nb, Ta, Cu and Nb-Ta in the un-reacted wire. It is estimated that due the wire texture Rp0.2 exceeds YS by 10%. Material HV (MPa) E (GPa) E/HV HV/YS YS (MPa) Rp0.2 (MPa) Nb 2420 92 38 2.9 830 910 Ta 3340 170 51 3 1110 1220 Cu  1050 115 110 3 350 385 Nb-7.5wt.%Ta  2110 94 45 3 700 770  The YS derived for the heavily cold worked Nb-7.5wt.%Ta alloy is about 16% lower than the YS of cold worked Nb. The reported tensile strength of annealed Nb-10wt.%Ta  4is about 10% lower than the strength of unalloyed, annealed Nb [17]. It has been found from tensile tests of monofilament samples with similar cold work as the phases in the Nb3Sn wire that the Nb, Ta and Nb-Ta elongation at fracture is smaller than 2%, and that Rm is about 100 MPa higher than Rp0.2. For cold-worked Cu wire, ε=1.5% and  Rm-Rp0.2≈35 MPa [10].  CONCLUSION  Table 4  Room temperature tensile properties under uniaxial tensile loading for the strongly cold-worked materials in the IT Nb3Sn wire.   E (GPa) Rp0.2 (MPa) Rm (MPa) ε (%) Nb 92 910 1010 <2 Ta 170 1220 1320 <2 Nb-Ta 94 770 870 <2 Cu 116  385 420 1.5  The measured E-moduli and estimated strength for the different phases in an un-reacted IT Nb3Sn wire under uniaxial tensile loading at room temperature are summarised in Table 4. The estimated accuracy of the E-moduli and tensile strength is better than ±3% and ±10%, respectively. The determination of the mechanical properties perpendicular to the wire drawing direction and under compression is subject for further studies.  ACKNOWLEDGEMENTS  This work was supported in part by the European Community–Research Infrastructure Activity under the FP6 “Structuring the European Research Area” program (CARE, contract number RII3-CT-2003-506395).    REFERENCES  1 A. Devred et al., Supercond. Sci. Technol., (2006), 19 67-83 2 M. Durante et.al., Physica C, (2001), 354 449-453 3 L. Thilly, F. Lecouturier, J. von Stebut, Acta Materiala, (2002), 50 5049-5065 4 V. Vidal, L. Thilly, F. Lecouturier, P.-O. Renault, Acta Materialia, (2006), 54 1063-1075 5 International standard, DIN EN 61788-6(2001-07), (2001) 6 K. Katagiri et al., Physica C, (2001), 357-360 1302-1305 7 S.R. Agnew, J.R. Weertman, Materials Science and Engineering, (1998), A242 174-180 8 C. Scheuerlein, T. Boutboul, D. Leroy, L. Oberli, B. Rehmer, “Hardness and tensile strength of multifilamentary metal-matrix composite superconductors for the Large Hadron Collider”, Accepted for publication in J. Mat. Sci. 9 C. Scheuerlein, B. Rehmer, “CERN, AT-MAS technical note 2005-08, (2005) 10 ASM Handbook Volume 2, “Properties and Selection: Nonferrous Alloys and Special-Purpose Materials”, (1990) 11 M. Merkel, K.-H. Thomas, “Taschenbuch der Werkstoffe”, Fachbuchverlag Leipzig, 5th edition, (2000) 12 M.F. Ashby, Y. Bréchet, Acta Materialia, (2003), 51 5801-5821 13 D.M. Marsh, Proc. Roy. Soc. A, (1963), 279 420-435 14 E.W. Collings, “Applied Superconductivity, Metallurgy, and Physics of Titanium Alloys”, Vol.1, Plenum Press, New York, (1986) 15 D. Tabor, “The hardness of solids”, Review of Physics in Technology 1, (1970), 145-179 16 C. Scheuerlein et al., “Vickers hardness of the individual phases in multifilament Nb3Sn superconducting wires”, for submission to Materials Characterization 17 N. Chamdawalla et al., Metall, (1986), 40(2) 141-145 

Tensile Properties of the Individual Phases in Unreacted Multifilament Nb$_{3}$Sn Wires

EU contract number RII3-CT-2003-506395 CARE-Conf-06-084-NED       Tensile properties of the individual phases in un-reacted multifilament Nb3Sn wires  C. Scheuerlein, P. El-Kallassi, L. Oberli, S. Sgobba1  European Organization for Nuclear Research (CERN), 1211 Genève 23, Switzerland  A. Devred CEA/Saclay, DSM/DAPNIA/SACM, 91191 Gif-sur-Yvette CEDEX, France  B. Fedelich, M. Finn, M. Griepentrog, B. Rehmer, Bundesanstalt für Materialforschung und –prüfung (BAM), 12200 Berlin, Germany  F. Lecouturier, V. Vidal LNCMP, CNRS-UPS-INSA, 143 avenue de Rangueil, 31400 Toulouse, France  L. Thilly,  LMP, Université de Poitiers, SP2MI, 86962 Futuroscope, France   Abstract   The room temperature elastic and plastic properties under uniaxial tensile loading of the different phases of an un-reacted, internal-tin process, Nb3Sn wire have been determined by tensile tests of whole wires and of extracted Ta, Nb and Nb alloy filaments, as well as by indentation hardness measurements in metallographic wire cross sections    Contribution to the ICFA HB2006, KEK (Japan)      Work supported by the European Community-Research Infrastructure Activity under the FP6 “Structuring the European Research Area” programme (CARE, contract number RII3-CT-2003-506395)  1 ICMC’06 abstract 136  Tensile properties of the individual phases in un-reacted  multifilament Nb3Sn wires  C. Scheuerlein1, A. Devred1,2, B. Fedelich3, M. Finn3, M. Griepentrog3, P. El-Kallassi1,  F. Lecouturier4, L. Oberli1, B. Rehmer3, S. Sgobba1, L. Thilly5, V. Vidal4 1European Organization for Nuclear Research (CERN), 1211 Genève 23, Switzerland 2CEA/Saclay, DSM/DAPNIA/SACM, 91191 Gif-sur-Yvette CEDEX, France 3Bundesanstalt für Materialforschung und –prüfung (BAM), 12200 Berlin, Germany 4LNCMP, CNRS-UPS-INSA, 143 avenue de Rangueil, 31400 Toulouse, France 5LMP, Université de Poitiers, SP2MI, 86962 Futuroscope, France  The room temperature elastic and plastic properties under uniaxial tensile loading of the different phases of an un-reacted, internal-tin process, Nb3Sn wire have been determined by tensile tests of whole wires and of extracted Ta, Nb and Nb alloy filaments, as well as by indentation hardness measurements in metallographic wire cross sections.  INTRODUCTION  As part of the EU-supported Next European Dipole (NED) Joint Research Activity [1] an effort has been launched in European industry to promote the development of high performance superconducting multifilament composite Nb3Sn wires and cables. To simulate cabling degradation and optimise wire design, a Finite Element (FE) model of the wire is under development [1]. FE simulations require the input of relevant materials properties. In this article, we report room temperature tensile strength and E-modulus results for the different phases in an Internal Tin (IT) Nb3Sn wire and describe how these materials properties have been measured.  EXPERIMENTAL PROCEDURES AND RESULTS  The samples The mechanical properties of the different phases in an un-reacted IT Nb3Sn wire produced by Alstom/MSA for CEA and described in detail in reference 2, have been determined. The wire with a nominal diameter of 0.825 mm consists of a Cu stabiliser, 19 Sn sub-elements made up of 198 Nb-7.5wt.% Ta filaments (nominal filament diameter: 4 !m) embedded in a Cu matrix and arranged in concentric circles around 19 pure Sn pools, and a mixed Nb and Ta diffusion barrier, surrounding the multifilament area.  The E-modulus of Ta has been measured on single filaments extracted from Ta/Cu monofilament samples produced at LNCMP for the development of resistive pulsed magnets. These monofilament wires are precursors for nanofilamentary wires, whose microstructure and mechanical properties have been extensively studied [3,4]. The Nb and Nb-7.5wt.%Ta E-moduli have been measured on filaments extracted from Nb-Ta/Cu and Nb/Cu monofilament samples provided by Alstom/MSA.  2 Tensile tests Tensile tests of Nb3Sn wires and binary composite monofilament samples were performed according to DIN EN 61788-6(2001-07) [5]. For the determination of the wire proof stress (Rp0.2), the raw-data stress-strain curve is fitted by a 2nd order polynomial and displaced so as to intercept the zero stress-strain position, as described in [6]. The tensile test results are summarised in Table 1 for the whole Nb3Sn composite wire and for samples of the same wire but where the Cu stabiliser has been removed by chemical etching. Rm of the wire without stabiliser shows an unusually large variation, which is possibly due to the roughness of the sample surface (Nb barrier).  Table 1  EA, Rp0.2 and Rm, Nb3Sn composite wire, with and without stabiliser (an average of 5 tensile tests).  Sample EA (GPa) Rp0.2 (MPa) Rm (MPa) Whole wire 108±0.9 374±14.0 523±3.6 Wire without stabiliser 93.3±0.8 516±2.8 612±99  The E-moduli obtained for the filaments extracted from the binary composite monofilament samples are: EA(Nb-Ta)=94.1±0.14 GPa, EA(Nb)=91.7±0.99 GPa and EA(Ta)=170±0.5 GPa (an average of three tensile tests).  Tensile tests of single Nb-Ta filaments extracted from the IT Nb3Sn wire were performed with a dedicated apparatus built by BAM. The filament cross section is measured with an optical system. Since an extensometer can not be attached to the filaments, the filament E-modulus and Rp0.2 can not be measured. The measured filament ultimate tensile strength is Rm=977±303 MPa (an average of ten measurements). The tensile test result obtained for a Nb-7.5wt.%Ta monofilament extracted from the precursor binary composite is Rm=734±0.4 MPa (an average of three measurements).  DISCUSSION  Elastic anisotropy in the cold-drawn wire phases Since the E-modulus is mainly determined by the binding forces between atoms, it is much less influenced by cold work and heat treatments than the tensile strength. Nevertheless, as a consequence of the asymmetric materials flow during wire processing, an important elastic anisotropy can be observed [7]. For the Cu matrix in Nb-Ti/Cu multifilament wire an E-modulus of 116 GPa [8] has been measured, which is about 10% lower than the E-modulus value of 128 GPa reported for isotropic Cu and similar to the Cu E-modulus in the Nb3Sn wire [9]. The E-modulus measured for the Nb filament extracted from the monofilament Nb/Cu sample is 92 GPa, 11% lower than the value for isotropic Nb (103 GPa [10]) and the Ta filament E-modulus is 170 GPa, 8% lower than the value reported for isotropic Ta (185 GPa [11]). These results indicate a strong elastic anisotropy in the heavily cold worked phases and it can be expected that the E-moduli perpendicular to the wire drawing direction are higher than those measured in the drawing direction. A Sn E-modulus of 49 GPa has been derived from instrumented indentation measurements on a wire cross section. The E-modulus reported for self-annealed, fine  3 grain Sn is 44.3 GPa [10]. Due to the very low annealing temperature of Sn it is assumed that the Sn in the Nb3Sn wire is elastically isotropic.  Composite wire E-modulus calculated according to the ROM Assuming isostrain conditions, the wire stress is the volume average of the local stresses and the composite modulus follows a Rule Of Mixtures (ROM) [12]. In Table 2, the ROM result is compared with the experimentally determined composite wire E-moduli. For the whole wire and the wire without stabiliser, the ROM result exceeds the experimentally determined composite E-modulus by 2% and 9%, respectively.  Table 2  E-modulus calculation of the Nb3Sn wire without and with stabiliser according to the ROM.  Wire without stabiliser Whole wire Material E (GPa) Vol.% weighted E (GPa)  Vol.%  weighted E (GPa) Cu 116 [Error! Bookmark not defined.] 51.1 59 80.2 93 Nb-Ta 94 21.9 21 8.9 8.4 Sn 49 13.9 6.8 5.6 2.7 Nb 92 8.7 8.0 3.5 3.2 Ta 170 4.4 7.5 1.8 3.1 ROM   102  110 Experiment   93.3  108  Plastic properties For fully work-hardened and isotropic materials the plastic materials properties can be estimated from the indentation hardness according to Equation 1, or when elastic deformation can be neglected, the yield stress (YS) is about one third of the Vickers hardness (HV) expressed in identical units [13,14,15]. HV/YS=0.065+0.6ln(E/YS)     1 Table 3 summarises the HV values that have been measured for the different phases in the Nb3Sn wire cross section, together with the YS calculated as YS=HV/3 or using Equation 1 (for E/HV<44.3). The experimental details of the indentation hardness measurements are described in references 8 and 16. For the textured wire phases it is assumed that Rp0.2 exceeds the YS values derived from the HV/YS ratio, which is valid for isotropic materials, by about 10% [8].  Table 3  HV, E-modulus and YS derived from HV for Nb, Ta, Cu and Nb-Ta in the un-reacted wire. It is estimated that due the wire texture Rp0.2 exceeds YS by 10%. Material HV (MPa) E (GPa) E/HV HV/YS YS (MPa) Rp0.2 (MPa) Nb 2420 92 38 2.9 830 910 Ta 3340 170 51 3 1110 1220  4 Cu  1050 115 110 3 350 385 Nb-7.5wt.%Ta  2110 94 45 3 700 770  The YS derived for the heavily cold worked Nb-7.5wt.%Ta alloy is about 16% lower than the YS of cold worked Nb. The reported tensile strength of annealed Nb-10wt.%Ta is about 10% lower than the strength of unalloyed, annealed Nb [17]. It has been found from tensile tests of monofilament samples with similar cold work as the phases in the Nb3Sn wire that the Nb, Ta and Nb-Ta elongation at fracture is smaller than 2%, and that Rm is about 100 MPa higher than Rp0.2. For cold-worked Cu wire, !=1.5% and  Rm-Rp0.2"35 MPa [Error! Bookmark not defined.].  CONCLUSION  Table 4  Room temperature tensile properties under uniaxial tensile loading for the strongly cold-worked materials in the IT Nb3Sn wire.   E (GPa) Rp0.2 (MPa) Rm (MPa)   (%) Nb 92 910 1010 <2 Ta 170 1220 1320 <2 Nb-Ta 94 770 870 <2 Cu 116  385 420 1.5  The measured E-moduli and estimated strength for the different phases in an un-reacted IT Nb3Sn wire under uniaxial tensile loading at room temperature are summarised in Table 4. The estimated accuracy of the E-moduli and tensile strength is better than ±3% and ±10%, respectively. The determination of the mechanical properties perpendicular to the wire drawing direction and under compression is subject for further studies.  ACKNOWLEDGEMENTS  This work was supported in part by the European Community–Research Infrastructure Activity under the FP6 “Structuring the European Research Area” program (CARE, contract number RII3-CT-2003-506395).    REFERENCES  1 A. Devred et al., Supercond. Sci. Technol., (2006), 19 67-83 2 M. Durante et.al., Physica C, (2001), 354 449-453 3 L. Thilly, F. Lecouturier, J. von Stebut, Acta Materiala, (2002), 50 5049-5065 4 V. Vidal, L. Thilly, F. Lecouturier, P.-O. Renault, Acta Materialia, (2006), 54 1063-1075 5 International standard, DIN EN 61788-6(2001-07), (2001) 6 K. Katagiri et al., Physica C, (2001), 357-360 1302-1305 7 S.R. Agnew, J.R. Weertman, Materials Science and Engineering, (1998), A242 174-180 8 C. Scheuerlein, T. Boutboul, D. Leroy, L. Oberli, B. Rehmer, “Hardness and tensile strength of multifilamentary metal-matrix composite superconductors for the Large Hadron Collider”, Accepted for publication in J. Mat. Sci. 9 C. Scheuerlein, B. Rehmer, “CERN, AT-MAS technical note 2005-08, (2005) 10 ASM Handbook Volume 2, “Properties and Selection: Nonferrous Alloys and Special-Purpose Materials”, (1990) 11 M. Merkel, K.-H. Thomas, “Taschenbuch der Werkstoffe”, Fachbuchverlag Leipzig, 5th edition, (2000) 12 M.F. Ashby, Y. Bréchet, Acta Materialia, (2003), 51 5801-5821  5 13 D.M. Marsh, Proc. Roy. Soc. A, (1963), 279 420-435 14 E.W. Collings, “Applied Superconductivity, Metallurgy, and Physics of Titanium Alloys”, Vol.1, Plenum Press, New York, (1986) 15 D. Tabor, “The hardness of solids”, Review of Physics in Technology 1, (1970), 145-179 16 C. Scheuerlein et al., “Vickers hardness of the individual phases in multifilament Nb3Sn superconducting wires”, for submission to Materials Characterization 17 N. Chamdawalla et al., Metall, (1986), 40(2) 141-145 

Tensile Properties of the Individual Phases in Un-Reacted Multifilament Nb$_{3}$Sn Wires

Tensile Properties of the Individual Phases in Unreacted Multifilament Nb $_{3}$ Sn Wires

Abstract

Similar works

Full text

Available Versions

CERN Document Server

CERN Document Server

Tensile Properties of the Individual Phases in Unreacted Multifilament Nb3_{3}3​Sn Wires

Abstract

Similar works

Full text

Available Versions

CERN Document Server

CERN Document Server

Tensile Properties of the Individual Phases in Unreacted Multifilament Nb $_{3}$ Sn Wires