Method of producing superconductor

Abstract

The following two problems arise when carbon is added to a starting material powder in the process of production of an MgB.sub.2 superconductor: (1) an impurity phase increases; and (2) the degree of substitution of carbon at boron sites is spatially non-uniform. This superconductor production method comprises: a mixing step of mixing a starting material powder and an additive; and a heat treatment step of heat-treating the mixture prepared in the mixing step. The starting material powder is MgB.sub.2 powder or a mixed powder of magnesium and boron, and the additive is an Mg—B—C compound containing three elements of magnesium, boron and carbon.

Claims

1. A method of producing a superconductor, the method comprising: a mixing step in which a raw material powder and an additive are mixed to produce a mixture; and a heat treatment step in which the mixture is subjected to a heat treatment; the raw material powder being an MgB.sub.2 powder or a mixed powder of magnesium and boron, the additive being an Mg—B—C compound containing three elements of magnesium, boron, and carbon.

2. The method of producing a superconductor according to claim 1, wherein the Mg—B—C compound is MgB.sub.2C.sub.2.

3. The method of producing a superconductor according to claim 1, wherein the Mg—B—C compound is MgB.sub.2-xC.sub.x (0<x<0.4).

4. The method of producing a superconductor according to claim 1, wherein the method comprises, prior to the heat treatment step, a compression step in which the mixture is compressed.

5. The method of producing a superconductor according to claim 1, wherein the method comprises, prior to the heat treatment step, a wire elongation processing step in which the mixture is charged in a metal tube and is subjected to a wire elongation processing.

6. The method of producing a superconductor according to claim 1, wherein the Mg—B—C compound powder is synthesized by mixing a magnesium powder, a boron powder, and a carbon containing material and subjecting the resulting mixture to a heat treatment.

Description

BRIEF DESCRIPTION OF DRAWINGS

(1) FIG. 1 shows an X-ray powder diffraction profile of synthesized MgB.sub.2C.sub.2.

(2) FIG. 2 illustrates a crystal structure of MgB.sub.2C.sub.2.

(3) FIG. 3 shows an SEM image of the appearance of a synthesized MgB.sub.2C.sub.2 powder.

(4) FIG. 4 shows dependency of critical current density on magnetic field in each of an additive-free, a B.sub.4C-added, and an MgB.sub.2C.sub.2-added MgB.sub.2 superconducting bulk sample.

(5) FIG. 5 shows X-ray powder diffraction profiles in an additive-free, a B.sub.4C-added, and an MgB.sub.2C.sub.2-added MgB.sub.2 superconducting bulk sample.

(6) FIG. 6 shows dependency of critical current density on magnetic field in each of an additive-free and an MgB.sub.1.88C.sub.0.12-added MgB.sub.2 superconducting bulk sample.

DESCRIPTION OF EMBODIMENTS

(7) The method of producing an MgB.sub.2 superconductor according to this embodiment includes: a mixing step in which a raw material powder and an additive are mixed to produce a mixture; and a heat treatment step in which the mixture is subjected to a heat treatment. As the additive agent, an Mg—B—C compound containing at least three elements of magnesium, boron, and carbon is used. Examples of such Mg—B—C compounds include MgB.sub.2C.sub.2 and MgB.sub.2 in which the B sites are excessively substituted with carbon. In an example of a process of synthesizing MgB.sub.2 through addition of an Mg—B—C compound, an Mg powder, a B powder, and an Mg—B—C compound powder are mixed, compressed, and then subjected to a heat treatment. In another example of such a process, an MgB.sub.2 powder and an Mg—B—C compound powder are mixed, compressed, and then subjected to a heat treatment. Such an Mg—B—C compound can be synthesized by mixing a magnesium powder, a boron powder, and a carbon powder, and then subjecting the mixture to a heat treatment at about 1000° C. Another carbon containing material may be added in addition to the Mg—B—C compound.

(8) The method of producing an MgB.sub.2 superconductor may include, prior to the heat treatment step, any one of a compression step in which the mixture is compressed and a wire elongation processing step in which the mixture is charged in a metal tube and is subjected to a wire elongation processing.

(9) Embodiments of the present invention will be described below with reference to drawings. Note that a superconductor includes both of a superconducting wire rod and a superconducting bulk.

EXAMPLE 1

(10) <Synthesis of MgB.sub.2C.sub.2 powder>

(11) MgB.sub.2C.sub.2 powder is not commercially available as far as the inventors know. Thus, synthesis of MgB.sub.2C.sub.2 powder was tried. A magnesium powder (99.8%, 200 mesh), a boron powder (99%, 0.8 μm), and a carbon powder were weighed in a molar ratio of 1:2:2, and were mixed in a mortar. The mixture was charged in a metal tube (SUS316), and the metal tube, after crushing both the ends thereof, was further put and sealed in a quartz tube, which was then subjected to a heat treatment at 1000° C. for 18 hours. The powder was then taken out of the metal tube. By the above procedure, an MgB.sub.2C.sub.2 powder was synthesized.

(12) FIG. 1 shows an X-ray diffraction profile of the synthesized powder. It was found that the main phase of the synthesized powder was MgB.sub.2C.sub.2. FIG. 2 illustrates a crystal structure of the powder. FIG. 3 shows a scanning electron microscope image of the MgB.sub.2C.sub.2 powder. The particle size of the powder was about 1 μm.

EXAMPLE 2

(13) MgB.sub.2 in which the MgB.sub.2C.sub.2 powder was added to raw material powders was synthesized, and the generated phase and the critical current density thereof were evaluated. For comparison, additive-free MgB.sub.2 and B.sub.4C-added MgB.sub.2 were synthesized and evaluated.

(14) As starting materials, a magnesium powder (200 mesh, 99.8%), a boron powder (0.8 μm, 95%), an MgB.sub.2C.sub.2 powder (produced in Example 1), and a B.sub.4C powder (99%, 50 nm) were used. Table 1 shows the mixing ratio by mole of the starting materials for each sample.

(15) TABLE-US-00001 TABLE 1 Sample name Mg B B.sub.4C MgB.sub.2C.sub.2 Mg:B:C Remarks Sample 1 1 2 0 0 1:2:0 Comparative Example A Sample 2 1 1.75 0.050 0 1:1.95:0.05 Comparative Example B Sample 3 1 1.50 1.100 0 1:1.90:0.10 Comparative Example C Sample 4 0.975 1.90 0 0.025 1:1.95:0.05 Example A Sample 5 0.950 1.80 0 0.050 1:1.90:0.10 Example B

(16) The starting materials were weighed as shown in Table 1 and were mixed in a mortar. The mixture was charged in a metal tube (SUS316) and the metal tube, after crushing and sealing both the ends thereof, was further put and sealed in a quartz tube, which was then subjected to a heat treatment at 800° C. for 3 hours. An MgB.sub.2 sample produced by the heat treatment was taken out of the metal tube. The MgB.sub.2 sample was cut into a rectangular parallelepiped shape and the magnetic hysteresis loop at 20 K was acquired with a SQUID flux meter (Quantum Design, MPMS) to derive the critical current density based on the Extended Bean Model. 20 K is the most expected temperature in application of MgB.sub.2.

(17) FIG. 4 shows the dependency of the critical current density (J.sub.c) on the magnetic field (B) at 20 K. Higher critical current densities than in the additive-free sample 1 were obtained, over the magnetic field range in the MgB.sub.2C.sub.2-added sample 4, and in the region of higher magnetic field than 2T in the sample 5. In comparison with respect to the critical current density in the magnetic field of 3 T, the samples 4 and 5 have superior values which are about twice the value of the sample 1. On the other hand, in the B.sub.4C-added samples 2 and 3, no higher critical current density than in the additive-free sample 1 was achieved at 20 K. At a low temperature such as the liquid helium temperature (4.2 K), a high critical current density is relatively easily achieved whatever carbon-additive material is selected, whereas at a relatively higher temperature such as 20 K, it is difficult to achieve a superior critical current density. The critical current density is even decreased in some cases, for example, the case of B.sub.4C addition. However, an MgB.sub.2C.sub.2 powder has an effect of significantly increasing the critical current density at 20 K at which application of MgB.sub.2 is expected.

(18) The reason why higher critical current densities were achieved by addition of an MgB.sub.2C.sub.2 powder supposedly recites in the following two points: (1) newly production of the impurity phase is less likely to occur even when the additive is added to raw materials; and (2) the actual carbon substitution ratio in the boron sites is uniform in a spatial view.

(19) The reasons will be explained using X-ray powder diffraction profiles of samples 1, 3, and 5 in FIG. 5.

(20) For all the samples, MgB.sub.2 as a main phase and a small amount of MgO are observed. Note that the peaks of Si are derived from Si powder which was mixed as an internal standard sample and are not intrinsic ones. Accordingly, by the addition of the MgB.sub.2C.sub.2 powder, newly introduction of impurity phase into MgB.sub.2 does not occur as with the case of B.sub.4C powder.

(21) When carbon substitution in the boron sites occurs, the a-axis length of the MgB.sub.2 crystal is reduced and the (110) peak shifts to the higher angle side. In the MgB.sub.2C.sub.2-added sample 5, the (110) peak shifts to the higher angle side relative to the peak in the additive-free sample 1, and the peak shape is relatively sharp. On the other hand, the (110) peak in the B.sub.4C-added sample 3 has a shape like that of two overlapping peaks. This suggests that the actual carbon substitution ratio is spatially uniform in the case of MgB.sub.2C.sub.2 addition whereas that is spatially non-uniform in the case of B.sub.4C addition. Since an excessive actual carbon substitution ratio leads to significant decrease of the critical temperature, resulting in an adverse effect on the critical current density, the actual carbon substitution ratio has to be controlled to a proper value. Thus, as carbon substitution occurs in a more spatially-uniform manner, the actual carbon substitution ratio is more easily controlled to a proper value. From this viewpoint, MgB.sub.2C.sub.2 powder is more effective as a carbon additive material as compared with B.sub.4C powder.

(22) The more spatially-uniform occurrence of the carbon substitution in MgB.sub.2C.sub.2 powder as compared with that in B.sub.4C powder is attributable to Mg contained in the composition thereof. Mg has a lower melting point, a lower boiling point, and a higher saturated vapor pressure as compared with B and C. For this reason, MgB.sub.2C.sub.2 is more unstable and is more liable to decompose as compared with B.sub.4C, which supposedly contributes to the uniformity of the spatial distribution of the carbon concentration.

(23) Example 2 uses a process (in-situ method) in which a magnesium powder, a boron powder, and an additive are mixed and the mixture was subjected to a heat treatment. However, a process (ex-situ method) in which an MgB.sub.2 powder is previously produced from a magnesium powder and a boron powder, the MgB.sub.2 powder is mixed with an additive, and the mixture is subjected to a heat treatment may be used. In general, the former in-situ process provides a higher critical current density, and the latter ex-situ process is more easily produce a uniform wire rod.

EXAMPLE 3

(24) In Example 1, an MgB.sub.2C.sub.2 powder was synthesized as a carbon source. In Example 3, MgB.sub.2-xC.sub.x (0<x<0.4), which is MgB.sub.2 in which a part of the boron sites is substituted with carbon, was synthesized as a carbon source. Here, a synthesis procedure of MgB.sub.2-xC.sub.x (0<x<0.4) will be explained as an example thereof.

(25) A magnesium powder (99.8%, 200 mesh), a boron powder (99%, 0.8 μm), and a carbon powder were weighed in a molar ratio of 1:1.88:0.12 and were mixed in a mortar. The mixture was charged in a metal tube (SUS316), and the metal tube, after crushing both the ends thereof, was further put and sealed in a quartz tube, which was then subjected to a heat treatment at 1000° C. for 18 hours. Then the powder was taken out of the metal tube. The main phase of the resulting powder had the same crystal structure as MgB.sub.2, and a part of the boron sites thereof was substituted with carbon. The powder is hereinafter referred to as Mg(B.sub.1.88C.sub.0.12) powder.

EXAMPLE 4

(26) MgB.sub.2 in which MgB.sub.2-xC.sub.x (0<x<0.4) was added as an additive material to raw material powders was synthesized and the critical current density thereof was evaluated. For comparison, additive-free MgB.sub.2 was also synthesized and evaluated.

(27) A magnesium powder (200 mesh, 99.8%), a boron powder (0.8 μm, 95%), an Mg(B.sub.1.88C.sub.0.12) powder (produced in Example 3) were used as starting materials. The boron powder and the Mg(B.sub.1.88C.sub.0.12) powder were weighed in a molar ratio shown in Table 2 and were mixed in a mortar. In a metal tube (SUS316) with one end crushed, the magnesium powder was charged, the mixed powder was then charged, and the magnesium powder was charged again, and then the other end was crushed and sealed. The metal tube was put and sealed in a quartz tube, which was then subjected to a heat treatment at 800° C. for 72 hours. By the heat treatment, magnesium at both the ends of the metal tube diffused into the central mixed powder area to produce MgB.sub.2. The MgB.sub.2 sample was taken out of the metal tube.

(28) TABLE-US-00002 TABLE 2 Sample name Mg B MgB.sub.1.88C.sub.0.12 B:C Remarks Sample 6 — 1 0 2:0 Comparative Example D Sample 7 — 1 0.25 1.96:0.04 Example C

(29) The MgB.sub.2 sample was cut into a rectangular parallelepiped shape, and the magnetic hysteresis loop at 20 K was acquired with a SQUID flux meter (Quantum Design, MPMS) to derive the critical current density based on the Extended Bean Model. FIG. 6 shows the dependency of the critical current density (J.sub.c) on the magnetic field (B). In the MgB.sub.2C.sub.2-added sample 7, higher critical current densities than in an additive-free sample 6 were observed in a higher magnetic field region.

(30) Here, only the Mg(B.sub.1.88C.sub.0.12) powder was mentioned as an example of MgB.sub.2-xC.sub.x (0<x<0.4), but the same result was obtained for the critical current density as long as the condition of x 0<x<0.4 was satisfied.

(31) As observed in Examples mentioned above, an Mg—B—C compound containing three elements of magnesium, boron, and carbon (for example, MgB.sub.2C.sub.2 or MgB.sub.2 in which a part of the boron sites is substituted) is effective as a carbon additive material in synthesis of MgB.sub.2. This substance contains no unnecessary element which may cause an impurity phase, and the carbon substitution in the boron sites of MgB.sub.2 occurs in a uniform manner

(32) The effectiveness of the addition of an Mg—B—C compound was demonstrated, in an in-situ method in which an MgB.sub.2 superconducting bulk is synthesized from a mixed body of magnesium powder and boron powder in Example 2, and in a diffusion method in which an MgB.sub.2 superconducting bulk is synthesized by diffusing magnesium in a boron powder area in Example 4. However, the effect of the addition is not limited to in-situ methods and diffusion methods. For example, the addition is effective in ex-situ methods in which an MgB.sub.2 superconducting bulk is synthesized by sintering of MgB.sub.2 powder, and furthermore, is effective not only for MgB.sub.2 superconducting bulks but also for MgB.sub.2 superconductors.

(33) In Examples mentioned above, only an Mg—B—C compound was added as a carbon additive material, but an Mg—B—C compound may be added together with a second carbon additive material. Even if an element that may cause an impurity is contained in the second carbon additive material, the co-addition with the Mg—B—C compound enables reduction of the amount of the generated impurity without reduction of the amount of carbon as compared with the case of adding only the second carbon additive material.