Melt-texture processing and high-temperature reactions of Bi-2212 thick films

Matheis, D. P.; Misture, Scott T.; Snyder, Robert L.

doi:10.1016/0921-4534(93)90335-n

Cited by 20 publications

(8 citation statements)

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“…6 )Cu0 2 , but there are large differ- ences in intensity. The pattern on 42-534 is strongly 0£0 textured, which is commonly observed when the phase crystallizes from a melt (Misture et al, 1995;Matheis et al, 1993;Hasegawa et al, 1994;Polonka et al, 1991;Xu et al, 1993).…”

Section: Resultsmentioning

confidence: 93%

“…Identification of the (Ca,Sr)_ c Cu > ,O z phases is often complicated by a large shift in lattice parameters across the solid solution range and textured crystal growth leading to large intensity variations in melt-textured or mechanically deformed materials (Misture et al, 1995;Matheis et al, 1993;Hasegawa et al, 1994;Polonka et al, 1991;Xu et al, 1993).…”

Section: Introductionmentioning

confidence: 99%

“…Supersolidus phase studies using high-temperature XRD have shown that the (Ca^r^CUyO., phases are the major crystalline phases present in the melt of Bi 2 Sr 2 CaCu 2 0 8 (Misture et al, 1995;Matheis et al, 1993;Xu et al, 1993;Hasegawa et al, 1994;Oka et al, 1989). Although in situ XRD is the preferred method for supersolidus studies, some disagreement still remains over the phases present in the melted state, clearly demonstrating the need for standard powder patterns.…”

Section: Introductionmentioning

confidence: 99%

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Powder-diffraction data for several solid solutions with the compositions (Ca_xSr_1−x)CuO₂ and (Ca_xSr_1−x)₂CuO₃

et al. 1995

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Section: Resultsmentioning

confidence: 93%

Section: Introductionmentioning

confidence: 99%

Section: Introductionmentioning

confidence: 99%

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Powder-diffraction data for several solid solutions with the compositions (Ca_xSr_1−x)CuO₂ and (Ca_xSr_1−x)₂CuO₃

et al. 1995

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“…In each cycle, samples were heated up to 1100 °C and cooled back to room temperature in a pure argon atmosphere at 10 °C min -1 . We identify the main endothermic DSC peaks as follows: The peak near 890 °C in the B1P sample corresponds to the melting of the Bi2Sr2CaCu2O8 phase and the peaks near ~940 °C in B1P corresponds to melting of the (Sr,Ca)CuO2 and (Sr,Ca)2CuO3 phases that grow from the Bi2Sr2CaCu2O8 melt [32,33]. After milling, these melting temperatures were lowered.…”

Section: X-ray Diffractionmentioning

confidence: 99%

The cause of ‘weak-link’ grain boundary behaviour in polycrystalline Bi₂Sr₂CaCu₂O₈and Bi₂Sr₂Ca₂Cu₃O₁₀superconductors

Wang

Raine

Hampshire

2018

Supercond. Sci. Technol.

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Publisher's copyright statement:Original content from this work may be used under the terms of the Creative Commons Attribution 3.0 licence. Any further distribution of this work must maintain attribution to the author(s) and the title of the work, journal citation and DOI. Use policyThe full-text may be used and/or reproduced, and given to third parties in any format or medium, without prior permission or charge, for personal research or study, educational, or not-for-prot purposes provided that:• a full bibliographic reference is made to the original source • a link is made to the metadata record in DRO • the full-text is not changed in any way The full-text must not be sold in any format or medium without the formal permission of the copyright holders.Please consult the full DRO policy for further details. Manuscript version: Accepted Manuscript Accepted Manuscript is "the version of the article accepted for publication including all changes made as a result of the peer review process, and which may also include the addition to the article by IOP Publishing of a header, an article ID, a cover sheet and/or an 'Accepted Manuscript' watermark, but excluding any other editing, typesetting or other changes made by IOP Publishing and/or its licensors"This Accepted Manuscript is © 2017 IOP Publishing Ltd.As the Version of Record of this article is going to be / has been published on a gold open access basis under a CC BY 3.0 licence, this Accepted Manuscript is available for reuse under a CC BY 3.0 licence immediately.Everyone is permitted to use all or part of the original content in this article, provided that they adhere to all the terms of the licence https://creativecommons.org/licences/by/3.0Although reasonable endeavours have been taken to obtain all necessary permissions from third parties to include their copyrighted content within this article, their full citation and copyright line may not be present in this Accepted Manuscript version. Before using any content from this article, please refer to the Version of Record on IOPscience once published for full citation and copyright details, as permissions may be required. All third party content is fully copyright protected and is not published on a gold open access basis under a CC BY licence, unless that is specifically stated in the figure caption in the Version of Record.View the article online for updates and enhancements. AbstractThe detrimental effects of grain boundaries have long been considered responsible for the low critical current densities ( c ) in high temperature superconductors. In this paper, we apply the quantitative approach used to identify the cause of the 'weak-link' grain boundary behaviour in YBa2Cu3O7 [1], to the Bi2Sr2CaCu2O8 and Bi2Sr2Ca2Cu3O10 materials that we have fabricated. Magnetic and transport measurements are used to characterise the grain and grain boundary properties of micro-and nanocrystalline material. Magnetisation measurements on all nanocrystalline materials show non-Bean-like behaviour and are consistent with sur...

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“…2(a), the tapes were uniaxially cold pressed at a peak stress of 300 MPa (to ensure good contact between the silver sheath and oxidized core) and then exposed to the heat treatment shown in Fig. After 15 min, the furnace was heated at a rate of 1°C/min to a peak temperature of 897 ± 1°C (i.e., above the reported incongruent melting point of the Bi 2 Sr 2 Ca 1 Cu 2 O 8type compound in pure oxygen and in contact with silver [30][31][32][33] ). After purging at room temperature with flowing, purified oxygen, the silica enclosure was thrust into a horizontal tube furnace preheated to 860°C.…”

Section: Partial-melt Processing Of the Oxidized Tapesmentioning

confidence: 99%

Fabrication of Ag/Bi₂Sr₂Ca₁Cu₂O_8±x superconducting tapes by the oxidation and postoxidation (partial melt) annealing of malleable, metal-bearing precursors

Detrie

Sandhage

2000

J. Mater. Res.

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A solid metal-bearing precursor route has been used to fabricate Ag-sheathed Bi 2 Sr 2 Ca 1 Cu 2 O 8± x (2212) superconducting tapes. Intimately mixed Bi 2 O 3 -Sr-Ca-Cubearing powder was first synthesized by a two-stage, high-energy/low-energy mechanical alloying process. The powder was then packed into silver tubes and formed into tapes by drawing and biaxial (Turk's-head) rolling. The precursor tapes were oxidized and converted into Ag-sheathed 2212 by heat treatment at 350-860°C in oxygen. Subsequent annealing at 897°C, followed by slow cooling and subsolidus annealing at 850°C, yielded 2212 grains with enhanced c-axis alignment. The resulting tapes exhibited average and maximum transport J c (4.2 K, self-field) values of 3.2 × 10 4 and 6.8 × 10 4 A/cm 2 , respectively. desired superconducting phases can form with minimal carbon contamination via novel, low-temperature reaction sequences. Indeed, prior work has shown that mechanically alloyed, alkaline-earth-metal-bearing precursors can be converted into multicomponent ceramics at appreciably lower temperatures than alkaline-earthcarbonate-bearing precursors. For example, 26-28 have formed at 550-750°C during annealing of Y-Ba-Cu-bearing, Ba-Al-bearing, Ba-Fe-bearing, Bi 2 O 3 -Sr-Ca-bearing, and Ba-Pb-Ti-TiO 2 -bearing precursors, respectively, in oxygen. Although several papers have been published on the use of the powder metallurgical MPIT method to produce (Bi,Pb) 2 Sr 2 Ca 2 Cu 3 O 10±x / Ag 19,20,22 and (Y,Ca)Ba 2 Cu 4 O 8 /Ag 21 composite superconductors, detailed descriptions of the mechanical alloying, forming, and heat treatment conditions, and of the phase and microstructural evolution during oxidation and postoxidation annealing, were not provided. The fabrication of melt-processed, Ag-sheathed 2212 superconductors from mechanically alloyed, metal-bearing precursors has also not been reported.The purpose of the present paper is to demonstrate the feasibility of fabricating Ag-sheathed 2212 superconducting tapes by the oxidation and postoxidation (partial melt) annealing of mechanically alloyed, malleable, metal-bearing precursors. The mechanical alloying, deformation processing, and heat-treatment conditions used to produce such conductors will be discussed. A detailed investigation of the reaction sequence to 2212 is the subject of another paper. 29 II. EXPERIMENTAL PROCEDURES A. Fabrication of metal-bearing precursor tapesMetal-bearing precursors to Ag-sheathed, Bi-2212based tapes were fabricated by a powder metallurgical route. Intimate powder mixtures of Bi 2 O 3 , Sr, Ca, and Cu were first synthesized by mechanical alloying (ball milling). The milled, metal-rich powder was then sealed within silver tubes that were cold drawn into wires and cold rolled into tapes.

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Melt-texture processing and high-temperature reactions of Bi-2212 thick films

Cited by 20 publications

References 11 publications

Powder-diffraction data for several solid solutions with the compositions (Ca_xSr_1−x)CuO₂ and (Ca_xSr_1−x)₂CuO₃

Powder-diffraction data for several solid solutions with the compositions (Ca_xSr_1−x)CuO₂ and (Ca_xSr_1−x)₂CuO₃

The cause of ‘weak-link’ grain boundary behaviour in polycrystalline Bi₂Sr₂CaCu₂O₈and Bi₂Sr₂Ca₂Cu₃O₁₀superconductors

Fabrication of Ag/Bi₂Sr₂Ca₁Cu₂O_8±x superconducting tapes by the oxidation and postoxidation (partial melt) annealing of malleable, metal-bearing precursors

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Melt-texture processing and high-temperature reactions of Bi-2212 thick films

Cited by 20 publications

References 11 publications

Powder-diffraction data for several solid solutions with the compositions (CaxSr1−x)CuO2 and (CaxSr1−x)2CuO3

Powder-diffraction data for several solid solutions with the compositions (CaxSr1−x)CuO2 and (CaxSr1−x)2CuO3

The cause of ‘weak-link’ grain boundary behaviour in polycrystalline Bi2Sr2CaCu2O8and Bi2Sr2Ca2Cu3O10superconductors

Fabrication of Ag/Bi2Sr2Ca1Cu2O8±x superconducting tapes by the oxidation and postoxidation (partial melt) annealing of malleable, metal-bearing precursors

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Powder-diffraction data for several solid solutions with the compositions (Ca_xSr_1−x)CuO₂ and (Ca_xSr_1−x)₂CuO₃

Powder-diffraction data for several solid solutions with the compositions (Ca_xSr_1−x)CuO₂ and (Ca_xSr_1−x)₂CuO₃

The cause of ‘weak-link’ grain boundary behaviour in polycrystalline Bi₂Sr₂CaCu₂O₈and Bi₂Sr₂Ca₂Cu₃O₁₀superconductors

Fabrication of Ag/Bi₂Sr₂Ca₁Cu₂O_8±x superconducting tapes by the oxidation and postoxidation (partial melt) annealing of malleable, metal-bearing precursors