JP2011113951A - Magnesium based composite material - Google Patents
Magnesium based composite material Download PDFInfo
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- JP2011113951A JP2011113951A JP2009272344A JP2009272344A JP2011113951A JP 2011113951 A JP2011113951 A JP 2011113951A JP 2009272344 A JP2009272344 A JP 2009272344A JP 2009272344 A JP2009272344 A JP 2009272344A JP 2011113951 A JP2011113951 A JP 2011113951A
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- magnesium
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- composite material
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- 239000011777 magnesium Substances 0.000 title claims abstract description 35
- 239000002131 composite material Substances 0.000 title claims abstract description 33
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 title claims abstract description 22
- 229910052749 magnesium Inorganic materials 0.000 title claims abstract description 22
- 239000002245 particle Substances 0.000 claims abstract description 32
- 229910000861 Mg alloy Inorganic materials 0.000 claims abstract description 9
- 238000000465 moulding Methods 0.000 claims description 3
- 238000001816 cooling Methods 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 abstract description 14
- 229910052751 metal Inorganic materials 0.000 description 14
- 239000002184 metal Substances 0.000 description 14
- 229910052782 aluminium Inorganic materials 0.000 description 8
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 8
- 239000000843 powder Substances 0.000 description 6
- 238000002360 preparation method Methods 0.000 description 6
- 239000002887 superconductor Substances 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 239000011159 matrix material Substances 0.000 description 5
- 238000002844 melting Methods 0.000 description 5
- 238000000034 method Methods 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 230000007423 decrease Effects 0.000 description 4
- 229910002804 graphite Inorganic materials 0.000 description 4
- 239000010439 graphite Substances 0.000 description 4
- 230000005484 gravity Effects 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 3
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 235000010627 Phaseolus vulgaris Nutrition 0.000 description 2
- 244000046052 Phaseolus vulgaris Species 0.000 description 2
- 229910010413 TiO 2 Inorganic materials 0.000 description 2
- 229910002091 carbon monoxide Inorganic materials 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 230000001747 exhibiting effect Effects 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000006082 mold release agent Substances 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000000498 cooling water Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000012466 permeate Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000011800 void material Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Classifications
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E40/00—Technologies for an efficient electrical power generation, transmission or distribution
- Y02E40/60—Superconducting electric elements or equipment; Power systems integrating superconducting elements or equipment
Abstract
Description
本発明は超伝導特性を発現する、マグネシウム又はマグネシウム合金を母相とする複合材料に関する。 The present invention relates to a composite material having magnesium or a magnesium alloy as a parent phase and exhibiting superconducting properties.
超伝導特性を発現するマグネシウム系の複合材料としては、Ｍｇ，ＭｇＨ，ＭｇＯ粉末等のＭｇ含有粉末と、Ｂ，Ｂ４Ｃ，Ｂ２Ｏ３等のＢ含有粉末とを混合し、銅や鉄製のパイプにつめて線引き、あるいは圧延し、その後に焼結することでＭｇＢ２を生成させる方法（ＰＩＴ法）が公知である。
また、Ｍｇ合金にＢ含有粉末を混合し、複合材料の作製工程でＭｇＢ２を生成させる技術も公知である。
しかし、これらの方法は複合材料中に粒子に起因する空隙欠陥が生じやすく、高温で焼結処理する際に原料粉末を充填した金属管と一部反応したり、粒子が酸化する問題もあった。
また、製造工程そのものが複雑であり、焼結材料のため製造後に曲げ加工等が難しい問題もあった。
As a magnesium-based composite material that exhibits superconducting properties, Mg-containing powders such as Mg, MgH, and MgO powders and B-containing powders such as B, B 4 C, and B 2 O 3 are mixed to produce copper or iron. A method (PIT method) is known in which MgB 2 is produced by drawing or rolling the pipe and then sintering it.
In addition, a technique is also known in which B-containing powder is mixed into an Mg alloy, and MgB 2 is generated in the composite material manufacturing process.
However, these methods tend to cause void defects due to particles in the composite material, and there is a problem that when the sintering process is performed at a high temperature, the metal tube partially reacts with the raw material powder and the particles are oxidized. .
In addition, the manufacturing process itself is complicated, and since it is a sintered material, it is difficult to bend after manufacturing.
そこで、特許文献１にＭｇＢ２粒子のプリフォーム体にアルミニウムの溶湯を加圧浸透させることで超伝導特性を発現するＭｇＢ２粒子−Ａｌ複合材料を開示し、特許文献２に鋳型のキャビティ内に無機粉体を充填し、これに半溶融状態のアルミニウムを加圧浸透させるＭｇＢ２粒子−Ａｌ複合材料を開示する。
なお、特許文献２は文面上、半溶融状態の軽金属を加圧浸透させると記載されているが、超伝導材料としては母相にアルミニウムを用いた具体例のみが開示されているに過ぎない。
Therefore, the molten aluminum into a preform of MgB 2 particles disclose MgB 2 particles -Al composite material exhibiting superconducting properties by causing pressurized permeate, into the mold cavity in Patent Document 2 to Patent Document 1 Disclosed is an MgB 2 particle-Al composite material that is filled with inorganic powder and into which aluminum in a semi-molten state is pressed and infiltrated.
In addition, Patent Document 2 describes that a semi-molten light metal is pressed and infiltrated on the text, but only a specific example using aluminum as a matrix is disclosed as a superconductive material.
しかし、上記母相を用いたアルミニウムは純アルミニウムで融点が９３３Ｋ（６６０℃）で半溶融状態はその前後の固液共存領域となるのに対して、マグネシウムを母相に用いると、純マグネシウムの融点が９２３Ｋ（６５０℃）でその前後の温度範囲が半溶融状態となる固液共存領域となり、アルミニウムよりもマグネシウムの方が融点で１０Ｋ低温である。
また、半溶融温度域は約９１３〜９６３Ｋである。
また、Ａｌの比重は約２．７であるのに対してＭｇの比重は約１．７と軽い。
このように、ＭｇはＡｌよりも融点が低く、軽い点に着目し、本発明に至った。
However, aluminum using the above mother phase is pure aluminum and has a melting point of 933 K (660 ° C.), and the semi-molten state is a solid-liquid coexistence region before and after that. The melting point is 923 K (650 ° C.) and the temperature range before and after that becomes a semi-liquid coexisting region, and magnesium has a melting point that is 10 K lower than aluminum.
The semi-melting temperature range is about 913 to 963K.
The specific gravity of Al is about 2.7, while the specific gravity of Mg is as light as about 1.7.
Thus, Mg has a melting point lower than that of Al, and has focused on the light point, leading to the present invention.
本発明は、超伝導特性に優れた、母相にマグネシウム又はマグネシウム合金を用いたＭｇＢ２粒子との複合材料の提供を目的とする。 The present invention is excellent in superconducting characteristics, and an object thereof is to provide a composite material of MgB 2 particles using magnesium or magnesium alloy in the matrix.
本発明に係るマグネシウム系複合材料は、鋳型のキャビティ内にＭｇＢ２粒子を充填し、一方から溶融又は半溶融状態のマグネシウム又はマグネシウム合金を加圧浸透させると同時に他方から冷却して製造されたことを特徴とする。
ここで、ＭｇＢ２粒子は平均粒子径が５０μｍ以下であるのが好ましい。
平均粒子径が５０μｍを超えると脆くなり、機械加工性が低下するからである。
The magnesium-based composite material according to the present invention was manufactured by filling MgB 2 particles in a cavity of a mold, pressure-penetrating molten or semi-molten magnesium or a magnesium alloy from one side, and simultaneously cooling from the other side. It is characterized by.
Here, the MgB 2 particles preferably have an average particle size of 50 μm or less.
This is because when the average particle size exceeds 50 μm, the material becomes brittle and the machinability is lowered.
ＭｇＢ２粒子は、鋳型のキャビティ内に直接０．０５〜１０ＭＰａの圧力で加圧充填してもよいが、予め０．０５〜１０ＭＰａの圧力で加圧成形したプリフォーム体を用いてもよい。
ここで加圧するのは、ＭｇＢ２の体積率を高くすることで複合材料中のＭｇＢ２の密度を向上させるのが目的であり、ＭｇＢ２の体積率は３０〜７０％の範囲が好ましい。
ＭｇＢ２の体積率が７０％を超えると複合材料が脆くなる。
The MgB 2 particles may be pressurized and filled directly into the mold cavity at a pressure of 0.05 to 10 MPa, or a preform body that has been previously pressure-molded at a pressure of 0.05 to 10 MPa may be used.
Here pressurize is for the purpose of the improving the density of the MgB 2 in the composite by increasing the volume fraction of MgB 2, the volume ratio of the MgB 2 is preferably in the range of 30% to 70%.
When the volume ratio of MgB 2 exceeds 70%, the composite material becomes brittle.
本発明に係るマグネシウム系複合材料は、ＭｇＢ２粒子に母相としてマグネシウム又はマグネシウム合金を加圧浸透させたので４０Ｋ以下の３７〜３８Ｋ付近で超伝導特性を発現し、公知のアルミニウムを母相としたものに比較して、優れた超伝導特性を示し、しかも軽量である。 In the magnesium-based composite material according to the present invention, magnesium or a magnesium alloy is pressed and infiltrated into the MgB 2 particles as a parent phase, so that superconducting properties are exhibited in the vicinity of 37 to 38K of 40K or less, and known aluminum is used as the parent phase. Compared to these, it exhibits excellent superconducting properties and is lightweight.
以下、具体的に本発明に係るマグネシウム系複合材料の製造例を説明するが、これに限定されるものではない。 Hereinafter, although the manufacture example of the magnesium type composite material which concerns on this invention is demonstrated concretely, it is not limited to this.
［製造例１］
図１に金型の構造を模式的に示す。
金型１０は軟鋼製で、φ７０ｍｍ×１１７ｍｍの外観をしている。金型内部は二段構造となっており、下段に複合材料作製部１１、上段に溶湯保持部１２がある。
下段の複合材料作製部１１はφ３２．６ｍｍ×５５ｍｍであり、溶湯保持部１２はφ４９．７ｍｍ×５０ｍｍである。
＜母相金属の成形＞
純度９９．９％のＭｇをφ４９ｍｍ×２５ｍｍに成形した。
＜プリフォームの作製＞
株式会社高純度化学研究所製の平均粒子径４０μｍ以下のＭｇＢ２粒子３０ｇを０．１ＭＰａの圧力で加圧成形し、φ３０ｍｍ×４２ｍｍの形状のプリフォーム（Ｐ）を製造した。
＜複合材料の製造＞
金型１０の複合材料作製部１１に離型剤としてＴｉＯ２を塗布する。
その後、金網、プリフォーム（Ｐ）を金型に挿入し、そのプリフォームの上に黒鉛１３を設置し、その黒鉛の上に軟鋼で作製した孔径φ１２ｍｍの絞り板１４を載せた。
絞り板の上にＭｇ（Ｍ）を設置した。
この状態で金型を９９％ＣＯ２＋１％ＳＦ６混合ガス雰囲気中で環状炉にて加熱した。
Ｍｇの温度が９３３Ｋに達して溶解した後、溶湯の上に黒鉛蓋１５を載せ、上部より油圧プレスにて２分間加圧して、プリフォーム内にＭｇ溶湯を浸透させた。
また、加圧と同時に金型の下部を冷却水で冷却した。
その後、製造したＭｇＢ２／Ｍｇ複合材料ビレットを取り出した。
このようにして得られたＭｇＢ２／Ｍｇ複合材料ビレットの内容を下記に示す。
ビレット寸法 ：φ２７．２ｍｍ×３５．１ｍｍ
ビレット重量 ：５０．５ｇ
ビレット体積 ：２２．８２３ｃｍ３
ビレット比重 ：２．２１２ｇ／ｃｍ３
粒子体積率 ：５１％
[Production Example 1]
FIG. 1 schematically shows the structure of the mold.
The mold 10 is made of mild steel and has an appearance of φ70 mm × 117 mm. The inside of the mold has a two-stage structure, with a composite material preparation section 11 at the lower stage and a molten metal holding section 12 at the upper stage.
The lower composite material preparation part 11 is φ32.6 mm × 55 mm, and the molten metal holding part 12 is φ49.7 mm × 50 mm.
<Molding of matrix metal>
Mg having a purity of 99.9% was molded into a diameter of 49 mm × 25 mm.
<Preform production>
30 g of MgB 2 particles having an average particle size of 40 μm or less manufactured by Kojundo Chemical Laboratory Co., Ltd. were pressure-formed at a pressure of 0.1 MPa to produce a preform (P) having a shape of φ30 mm × 42 mm.
<Manufacture of composite materials>
TiO 2 is applied as a mold release agent to the composite material preparation part 11 of the mold 10.
Thereafter, a wire mesh and a preform (P) were inserted into the mold, graphite 13 was placed on the preform, and a diaphragm plate 14 having a hole diameter of 12 mm made of mild steel was placed on the graphite.
Mg (M) was installed on the diaphragm plate.
In this state, the mold was heated in a ring furnace in a 99% CO 2 + 1% SF 6 mixed gas atmosphere.
After the Mg temperature reached 933 K and melted, the graphite lid 15 was placed on the molten metal, and pressurized with a hydraulic press for 2 minutes from the top to infiltrate the molten Mg into the preform.
Further, simultaneously with the pressurization, the lower part of the mold was cooled with cooling water.
Thereafter, the manufactured MgB 2 / Mg composite billet was taken out.
The contents of the MgB 2 / Mg composite billet thus obtained are shown below.
Billet size: φ27.2mm × 35.1mm
Billet weight: 50.5g
Billet volume: 22.823 cm 3
Billet specific gravity: 2.212 g / cm 3
Particle volume ratio: 51%
［製造例２］
使用した金型１０ａの模式図を図２に示し、軟鋼製で、φ７０ｍｍ×８５ｍｍの外観をしている。
金型内部は二段構造となっており、下段に複合材料作製部１１ａ、上段に半溶融金属保持部１２ａがある。
下段の複合材料作製部１１ａはφ１０ｍｍ×３０ｍｍであり、半溶融金属保持部１２ａはφ４９．７ｍｍ×４３ｍｍである。
＜母相金属の成形＞
ＡＳＴＭ規格のＡＺ９１（Ａｌ：８．３〜９．２ｗｔ．％，Ｚｎ：０．４５〜０．９ｗｔ．％，Ｍｎ：０．１７〜０．５０ｗｔ．％，Ｓｉ：＜０．２０ｗｔ．％，Ｃｕ：＜０．０１５ｗｔ．％，Ｎｉ：＜０．００１ｗｔ．％，Ｆｅ：＜０．００４ｗｔ．％）相当の合金をφ４９ｍｍ×２５ｍｍに成形した。
＜複合材料の製造＞
金型の複合材料作製部１１ａに離型剤としてＴｉＯ２を塗布する。
その後、金網、金型の複合材料作製部１１ａにＭｇＢ２粒子を０．１ＭＰａの圧力をかけて充填する。
その後、金型の半溶融金属保持部１２ａにＡＺ９１合金を設置した。
この状態で金型を９９％ＣＯ２＋１％ＳＦ６混合ガス雰囲気中で環状炉にて加熱した。
ＡＺ９１合金の温度が８２３Ｋで、半溶融状態に達した後、ＡＺ９１合金の半溶融金属の上に黒鉛蓋１５を載せ、上部より油圧プレスにて１分間加圧して、粒子内にＡＺ９１合金の半溶融金属を浸透させ、金型を直接水冷した。
その後、製造したＭｇＢ２／ＡＺ９１複合材料ビレットを取り出した。
このようにして得られたＭｇＢ２／ＡＺ９１複合材料ビレットの内容を下記に示す。
ビレット寸法 ：φ１０ｍｍ×２７．６ｍｍ
ビレット重量 ：４．５ｇ
ビレット体積 ：１．９９ｃｍ３
ビレット比重 ：２．２６２ｇ／ｃｍ３
粒子体積率 ：５２％
[Production Example 2]
A schematic diagram of the mold 10a used is shown in FIG. 2, which is made of mild steel and has an appearance of φ70 mm × 85 mm.
The inside of the mold has a two-stage structure. The lower part has a composite material preparation part 11a and the upper part has a semi-molten metal holding part 12a.
The lower composite material preparation part 11a is φ10 mm × 30 mm, and the semi-molten metal holding part 12a is φ49.7 mm × 43 mm.
<Molding of matrix metal>
ASTM standard AZ91 (Al: 8.3 to 9.2 wt.%, Zn: 0.45 to 0.9 wt.%, Mn: 0.17 to 0.50 wt.%, Si: <0.20 wt.%, An alloy corresponding to Cu: <0.015 wt.%, Ni: <0.001 wt.%, Fe: <0.004 wt.%) Was formed into a diameter of 49 mm × 25 mm.
<Manufacture of composite materials>
TiO 2 is applied as a mold release agent to the composite material production part 11a of the mold.
Then, MgB 2 particles are filled in the metal mesh / mold composite material preparation part 11a under a pressure of 0.1 MPa.
Then, AZ91 alloy was installed in the semi-molten metal holding part 12a of the mold.
In this state, the mold was heated in a ring furnace in a 99% CO 2 + 1% SF 6 mixed gas atmosphere.
After the temperature of the AZ91 alloy reaches a semi-molten state at 823 K, a graphite lid 15 is placed on the semi-molten metal of the AZ91 alloy and pressed from above with a hydraulic press for 1 minute. The molten metal was infiltrated and the mold was directly water cooled.
Thereafter, the manufactured MgB 2 / AZ91 composite billet was taken out.
The contents of the MgB 2 / AZ91 composite billet thus obtained are shown below.
Billet size: φ10mm × 27.6mm
Billet weight: 4.5g
Billet volume: 1.99 cm 3
Billet specific gravity: 2.262 g / cm3
Particle volume ratio: 52%
上記製造例１，２にて製造した複合材料の評価結果を次に示す。
図３（ａ）は、ＭｇＢ２／純Ｍｇ超伝導体ビレットを縦方向に切断し、その断面を接写した図である。
濃いグレーの部分が超伝導粒子とマグネシウムが複合している領域であり、矢印で記した両端は、粒子がほとんど存在していない純マグネシウムの部分である。
この図から明らかなように、鋳造による巣や、凝固収縮による割れ、あるいは粒子のみが凝集している部分など、ビレットとしての顕著な欠陥は観察されない。
図３（ｂ）は、（ａ）中に四角で記した部分を、ＳＥＭで拡大して観察した画像である。濃いグレーがＭｇＢ２粒子で、薄いグレーの部分がマグネシウム母相である。
この倍率においても、粒子の凝集や巣、割れなどの欠陥らしきものは観察されないことから、きわめて良好なビレットが得られたと判断される。
図３（ｃ）は、ＭｇＢ２／ＡＺ９１超伝導体ビレットの切断面を示し、（ｄ）（ｃ）中に四角で記した部分のＳＥＭ拡大画像を示す。
ＭｇＢ２／ＡＺ９１ビレットも内部が良好であった。
図４は、このビレットを用いて電気抵抗率の温度依存性を測定した結果である。
図中には、ＭｇＢ２／Ａｌ超伝導体の結果も示した。
いずれの試料も、電気抵抗は３８Ｋあたりから減少し、とくに母相をＡＺ９１とした合金では、残留抵抗が高く、電気抵抗率の大きな減少が顕著に確認される。
図５は、これらの試料で測定した磁化率の温度依存性である。
ここでも３７Ｋあたりから磁化率の低下がみられ、電気抵抗率同様、超伝導材料としての特徴を示した。
特にＭｇＢ２／Ｍｇの方がＭｇＢ２／Ａｌよりも約１Ｋ高い温度から磁化率の低下が認められる。
図６は、磁化率の外部磁場に対する依存性の結果を用いて、Ｂｅａｎの式で算出された臨界電流密度Ｊｃである。
高いＪｃを達成しており、特にＡＺ９１では、３００００Ｇ（３Ｔ）で１０５Ａ／ｃｍ２であり、実用されているＮｂ−Ｓｎ超伝導体で達成されている値に等しい。
以上のことから、母相にマグネシウム又はマグネシウム合金を用いた方がアルミニウムを用いたものより超伝導特性に優れ、且つ軽量であった。
The evaluation results of the composite materials produced in Production Examples 1 and 2 are shown below.
FIG. 3A is a close-up view of a cross section of an MgB 2 / pure Mg superconductor billet cut in the longitudinal direction.
The dark gray portion is a region where superconducting particles and magnesium are combined, and both ends indicated by arrows are portions of pure magnesium in which almost no particles are present.
As is apparent from this figure, no significant defect as a billet such as a nest formed by casting, a crack due to solidification shrinkage, or a portion where only particles are aggregated is not observed.
FIG. 3B is an image obtained by magnifying and observing a portion indicated by a square in FIG. The dark gray is MgB 2 particles, and the light gray part is the magnesium matrix.
Even at this magnification, no defects such as particle agglomeration, nests and cracks were observed, and it is judged that a very good billet was obtained.
FIG. 3 (c), MgB 2 / AZ91 shows the cut surface of the superconductor billet shows SEM enlarged image of a portion marked by a square in (d) (c).
The inside of the MgB 2 / AZ91 billet was also good.
FIG. 4 shows the results of measuring the temperature dependence of the electrical resistivity using this billet.
In the figure, the result of the MgB 2 / Al superconductor is also shown.
In any of the samples, the electrical resistance decreases from around 38K, and particularly in the alloy having the parent phase AZ91, the residual resistance is high, and a large decrease in electrical resistivity is remarkably confirmed.
FIG. 5 shows the temperature dependence of the magnetic susceptibility measured for these samples.
Here, a decrease in magnetic susceptibility was observed from around 37K, and the characteristics as a superconducting material were exhibited as well as the electrical resistivity.
In particular, a decrease in magnetic susceptibility is observed from MgB 2 / Mg at a temperature about 1 K higher than MgB 2 / Al.
FIG. 6 shows the critical current density Jc calculated by the Bean equation using the result of the dependence of the magnetic susceptibility on the external magnetic field.
A high Jc is achieved, especially AZ91, 10 5 A / cm 2 at 30000 G (3T), which is equal to the value achieved with a practical Nb—Sn superconductor.
From the above, the use of magnesium or magnesium alloy for the parent phase was superior in superconducting properties and lighter than that using aluminum.
１０ 金型 10 Mold
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| JP2018016777A (en) * | 2016-07-29 | 2018-02-01 | 国立大学法人富山大学 | Stress-induced light emitting material and method for producing the same |
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