CN87101149A - 超导陶瓷 - Google Patents
超导陶瓷 Download PDFInfo
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- CN87101149A CN87101149A CN87101149.2A CN87101149A CN87101149A CN 87101149 A CN87101149 A CN 87101149A CN 87101149 A CN87101149 A CN 87101149A CN 87101149 A CN87101149 A CN 87101149A
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- 239000000919 ceramic Substances 0.000 title claims abstract description 35
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 24
- 230000007704 transition Effects 0.000 claims description 13
- 239000002887 superconductor Substances 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 8
- 239000011575 calcium Substances 0.000 claims description 7
- 239000000126 substance Substances 0.000 claims description 7
- 239000013078 crystal Substances 0.000 claims description 4
- 229910052751 metal Inorganic materials 0.000 claims description 2
- 239000002184 metal Substances 0.000 claims description 2
- 238000005245 sintering Methods 0.000 claims description 2
- JTCFNJXQEFODHE-UHFFFAOYSA-N [Ca].[Ti] Chemical compound [Ca].[Ti] JTCFNJXQEFODHE-UHFFFAOYSA-N 0.000 claims 1
- 238000002360 preparation method Methods 0.000 claims 1
- 239000010949 copper Substances 0.000 abstract description 14
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 abstract description 5
- 229910052784 alkaline earth metal Inorganic materials 0.000 abstract description 3
- 150000001342 alkaline earth metals Chemical class 0.000 abstract description 3
- 229910052802 copper Inorganic materials 0.000 abstract 1
- 230000007547 defect Effects 0.000 abstract 1
- 150000002910 rare earth metals Chemical class 0.000 abstract 1
- 239000000463 material Substances 0.000 description 27
- 239000000843 powder Substances 0.000 description 9
- 230000001590 oxidative effect Effects 0.000 description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 6
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 6
- 229910052788 barium Inorganic materials 0.000 description 6
- 239000004570 mortar (masonry) Substances 0.000 description 6
- 239000001301 oxygen Substances 0.000 description 6
- 229910052760 oxygen Inorganic materials 0.000 description 6
- 238000012856 packing Methods 0.000 description 6
- 229910052727 yttrium Inorganic materials 0.000 description 6
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 description 6
- DSAJWYNOEDNPEQ-UHFFFAOYSA-N barium atom Chemical group [Ba] DSAJWYNOEDNPEQ-UHFFFAOYSA-N 0.000 description 5
- 229910052769 Ytterbium Inorganic materials 0.000 description 4
- 125000004430 oxygen atom Chemical group O* 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 229910052688 Gadolinium Inorganic materials 0.000 description 3
- 229910052786 argon Inorganic materials 0.000 description 3
- 229910052791 calcium Inorganic materials 0.000 description 3
- 239000008246 gaseous mixture Substances 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 229910052712 strontium Inorganic materials 0.000 description 3
- NAWDYIZEMPQZHO-UHFFFAOYSA-N ytterbium Chemical compound [Yb] NAWDYIZEMPQZHO-UHFFFAOYSA-N 0.000 description 3
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 2
- 125000004429 atom Chemical group 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 230000002950 deficient Effects 0.000 description 2
- UIWYJDYFSGRHKR-UHFFFAOYSA-N gadolinium atom Chemical compound [Gd] UIWYJDYFSGRHKR-UHFFFAOYSA-N 0.000 description 2
- 229910052706 scandium Inorganic materials 0.000 description 2
- CIOAGBVUUVVLOB-UHFFFAOYSA-N strontium atom Chemical compound [Sr] CIOAGBVUUVVLOB-UHFFFAOYSA-N 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910002480 Cu-O Inorganic materials 0.000 description 1
- 229910052692 Dysprosium Inorganic materials 0.000 description 1
- 229910052691 Erbium Inorganic materials 0.000 description 1
- 229910052693 Europium Inorganic materials 0.000 description 1
- 229910052689 Holmium Inorganic materials 0.000 description 1
- 229910052765 Lutetium Inorganic materials 0.000 description 1
- 229910052772 Samarium Inorganic materials 0.000 description 1
- 229910003808 Sr-Cu Inorganic materials 0.000 description 1
- 229910052771 Terbium Inorganic materials 0.000 description 1
- 229910052775 Thulium Inorganic materials 0.000 description 1
- ARLFUQRPUZQCIV-UHFFFAOYSA-N barium;bismuth;oxolead Chemical compound [Ba].[Bi].[Pb]=O ARLFUQRPUZQCIV-UHFFFAOYSA-N 0.000 description 1
- 229910052790 beryllium Inorganic materials 0.000 description 1
- 238000005056 compaction Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052747 lanthanoid Inorganic materials 0.000 description 1
- 150000002602 lanthanoids Chemical class 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- QSHDDOUJBYECFT-UHFFFAOYSA-N mercury Chemical compound [Hg] QSHDDOUJBYECFT-UHFFFAOYSA-N 0.000 description 1
- 229910052753 mercury Inorganic materials 0.000 description 1
- 230000000737 periodic effect Effects 0.000 description 1
- 229910052705 radium Inorganic materials 0.000 description 1
- SIXSYDAISGFNSX-UHFFFAOYSA-N scandium atom Chemical compound [Sc] SIXSYDAISGFNSX-UHFFFAOYSA-N 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
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- C04B35/45—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on copper oxide or solid solutions thereof with other oxides
- C04B35/4504—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on copper oxide or solid solutions thereof with other oxides containing rare earth oxides
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- H10N60/00—Superconducting devices
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- H10N60/855—Ceramic superconductors
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- Y10S505/775—High tc, above 30 k, superconducting material
- Y10S505/776—Containing transition metal oxide with rare earth or alkaline earth
- Y10S505/779—Other rare earth, i.e. Sc,Y,Ce,Pr,Nd,Pm,Sm,Eu,Gd,Tb,Dy,Ho,Er,Tm,Yb,Lu and alkaline earth, i.e. Ca,Sr,Ba,Ra
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- Y10S505/00—Superconductor technology: apparatus, material, process
- Y10S505/775—High tc, above 30 k, superconducting material
- Y10S505/776—Containing transition metal oxide with rare earth or alkaline earth
- Y10S505/779—Other rare earth, i.e. Sc,Y,Ce,Pr,Nd,Pm,Sm,Eu,Gd,Tb,Dy,Ho,Er,Tm,Yb,Lu and alkaline earth, i.e. Ca,Sr,Ba,Ra
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Abstract
本发明是具有较高临界温度的超导陶瓷,它由稀土金属、碱土金属和铜组成,缺陷很少,具有有限的多晶界面面积。
Description
本发明涉及具有高临界温度的超导陶瓷。
先有技术曾提出过用诸如汞和铅之类的金属,和诸如NbNd、Nb3Ge和Nb3Ga之类的金属间化合物,以及诸如Nb3(Al0.8Ge0.2)之类的三元材料作为超导体。美国专利US3,932,315号介绍了另一种超导材料,即钡-铅-铋氧化物超导材料。然而,在这类传统的超导材料中,仅仅发生三维电子导电,因而这类传统超导材料的临界转变温度(Tc)不会超过25°K。
近年来,超导陶瓷已引起了广泛的兴趣,IBM公司在苏黎士实验室的研究人员首先报导了一种新材料,即Ba-La-Cu-O型高温超导氧化物。此外,还提出了La-Sr-Cu(Ⅱ)-O型超导氧化物。这种类型的超导材料看来似乎形成一种准分子晶体结构,其晶胞具有一层状结构,其中电子基本上作单维的运动。然而,这种超导材料的临界转变温度Tc低于30°K。
本发明旨在提供临界转变温度较以往更高的超导陶瓷,其缺陷很少,且其多晶结构中的界面面积较小。
本发明提供了一种超导陶瓷材料,这种材料最主要的形式可由以下通式表示:
(A1-xBx)yCuzOw(ⅰ)
其中:0.1≤X<1
Y=2.0~4.0
Z=1.0~4.0
W=4.0~10.0
A为一种或多种稀土元素。当A为一种稀土元素时,B为一种以上碱土元素;而当A为一种以上稀土元素时,B为一种或多种碱土元素。
通式(ⅰ)中,较为可取的是:
Y=2.5~3.5
Z=1.5~3.5和
W=6.0~8.0。
上述通式(ⅰ)包括若干亚形(sub-species)超导体陶瓷材料。其中之一可由以下通式来表示:
(A1-xBx)yCuzOw·(A1-x′B′x′)y′Cuz′Ow′(ⅱ)
其中0.1≤X<1
0.1≤X′<1
Y=2.0~4.0,较为可取的是2.5~3.5,
Y′=2.0~4.0,较为可取的是2.5~3.5,
Z=1.0~4.0,较为可取的是1.5~3.5,
Z′=1.0~4.0,较为可取的是1.5~3.5,
W=4.0~10.0,较为可取的是6.0~10.0
W′=4.0~10.0,较为可取的是6.0~8.0,
A为一种或多种稀土元素。
B和B′为两种或多种碱土元素。
通式(ⅱ)的材料中包括其中A为一种稀土元素,由YbBaSrCu3O6-8、YBaCaCu3O6-8和YbBa0.7Sr0.7Ca0.6Cu3O6-8代表的材料;以及其中A为一种以上的稀土元素、由Y0.5Yb0.5BaSrCu3O6-8和Y0.5Yb0.5BaCaCu3O6-8代表的材料。
通式(ⅰ)的超导陶瓷材料的亚形之二可由以下通式表示:
〔A1-x(B1-gB′ g)x〕yCuzOw(ⅲ)
式中0.1≤X<1
0<q<1
Y=2.0~4.0,较为可取的是2.5~3.5,
Z=1.0~4.0,较为可取的是1.5~3.5,
W=4.0~10.0,较为可取的是6.0~8.0
A为稀土元素,
B和B′为不同的碱土元素。
(ⅰ)的亚形之三可由以下通式表示:
〔(A1-pA′ p)1-x(B1-gB′ g)x〕yCuzOw(ⅳ)
式中0.1≤X<1,
0<p<1,
0<q<1,
Y=2.0~4.0,较为可取的是2.5~3.5,
Z=1.0~4.0,较为可取的是1.5~3.5,
W=4.0~10.0,较为可取的是6.0~8.0,
A和A′为不同的稀土元素,
B和B′为不同的碱土元素。
(ⅰ)的亚形之四可由以下通式表示:
〔(A1-pA′ p)1-xBx〕yCuzOw(ⅴ)
式中0.1≤X<1,
0<p<1,
Y=2.0~4.0,较为可取的是2.5~3.5,
Z=1.0~4.0,较为可取的是1.5~3.5,
W=4.0~10.0,较为可取的是6.0~8.0,
A和A′为不同的稀土元素,
B为碱土元素。
通式(ⅴ)材料的例子为Y0.5Gd0.5Ba2Cu3O6-8和Y0.5Yb0.5Ba2Cu3O6-8。
图1为类钙钛矿型结构超导陶瓷的透视图。
上述通式中,除非另有合理的说明或前后关系不允许,A、A′、B和B′的每一个均可共同使用,即:A可代表任何序数的稀土元素A1、A2、A3…An,依次类推。
这里所用的术语“稀土元素”的含意须与“Chambers Dictionary of Science and Technology”中给出的含意相同,就是指原子序数57至71的镧系元素以及钪(原子序数21)和钇(原子序数39),即:La、Ce、Pr、Nb、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu、Sc和Y。碱土金属是指属于周期表的2A族的元素,即:Be、Mg、Ca、Sr、Ba和Ra。
超导材料具有类钙钛矿型结构,其晶胞由附图图1图解说明。图1中,铜原子2和8分别被棱锥形排列的5个氧原子5所包围;在两个棱锥体之间,位于中心的铜原子3被四个氧原子(其中两个氧原子位于环绕铜原子2和8的棱锥体的锥顶)和两个空位7所包围。稀土元素1的原子位于晶胞的角上,碱土金属4的原子位于晶胞的棱边。图中所示的结构可表示为(YBa2)Cu3O7-x。在这个结构中,超导电性产生于层状结构中的电子,这种结构是由环绕每个中心铜原子的四个氧原子3而形成的。
本发明的超导陶瓷同先有技术的超导陶瓷一样,具有一种类钙钛矿型结构。然而,本发明的超导陶瓷中采用了两种或多种稀土元素和/或两种或多种碱土元素,以致在形成多晶结构的同时形成若干大晶粒。这样,由于晶粒间界面面积的减少,而提高了临界转变温度。当然,理想的结构是单晶体。
超导陶瓷可很方便地生产。例如,首先,在球磨机中,按照规定的化学计量,将纯度为99.9%或99.99%的氧化物和(如果需要的话)碳化物研磨成粉末,并一起混合。然后,将粉末压制成小片,接着,细磨并再次压制成小片。最后,在高温下将小片烧结。
以下实施例说明了本发明。虽然这些实施例不包括可用于生产本发明材料的所有元素组合,但是其他组合也可有效地形成改良的超导材料。
实施例1
将全部呈细粉末状、纯度为99.95%或更高的Y2O3、BaCO3、CaCO3和CuO按式(ⅱ)所要求的比例进行混合,这里,X=0.67(A∶B=1∶2);X′=0.33(A∶B′=2∶1);Y=1.0;Y′=1.0,Z=3.0;Z′=3.0;W=6至8;W′=6至8;A为钇;B为钡;B′为钙(B∶B′=1∶1)。在研钵内将这些材料充分地混合,装进包囊,压制成直径为10mm、厚度为3mm的小片。然后,在氧化气氛下,例如在空气中,于500~900℃,例如于700℃,对小片烧固8小时。
然后,在研钵内将小片研磨成粉末,其平均颗粒半径小于10μm。再次封入包囊,并在高温时,于50kg/cm2的压力下,再次压制粉末成小片。在氧化气氛下,例如在空气中,于500~900℃,例如于900℃时,将小片烧固10~50小时,例如15小时。最后,于600~1100℃时,例如于800℃时,在含有少量氧气的氧气/氩气的混合气中,加热3~30小时,例如20小时,使小片还原。最后终于观察到到一种新的结构。这种材料可由化学计量的化学式YBaCaCu3O6-8表示。
研究了温度与这种小片状材料的电阻率之间的关系。可以看到,当温度下降至底于104°K(临界转变的起始温度)时,开始出现向超导态的相变;93°K(Tco)时,观察到电阻消失。
实施例2
将全部呈细粉末状、纯度为99.95%或更高的Yb2O3、BaCO3、Sr2O3和CuO,按式(ⅱ)所需要的比例进行混合,这里,X=0.67(A∶B=1∶2);X′=0.33(A∶B=2∶1);Y=1.0;Y′=1.0;Z=3.0;Z′=3.0;W=6至8;W′=6至8,A为钇,B为钡,B′为锶(B∶B′=1∶1)。接着采用例1所述的步骤。生成的材料可由化学计量的化学式YbBaSrCu3O6-8表示。
研究了温度与这种小片状材料的电阻率之间的关系。当温度降至低于109°K(临界转变起始温度)时,观察到向着超导态的相变,37°K(Tco)时,观察到电阻消失。
实施例3
重复实施例2的步骤,但用Ca(作为CaCO3引入)取代30%的Ba和Sr。结果,使临界转变起始温度进一步提高了3~5°K。所得到的材料可由化学计量的化学式YbBa0.7Sr0.7Ca0.6Cu3O6-8表示。
实施例4
按式(ⅱ)所要求的比例,将全部呈粉末状、纯度为99.95%或更高的Y2O3、Yb2O3、BaCO3、CaCO3和CuO混合,这里X=0.33(A∶B=2∶1);X′=0.66(A∶B=1∶2);Y=1.0;Y′=1.0;Z=3.0;Z′=3.0;W=6至8;W′=6至8,A为钇,A′为镱,B为钡,B′为钙(B∶B′=1∶1;A∶A′=1∶1,1∶2,或1∶5)。在研钵中充分地混合这些材料,将其装进包囊,压制(3kg/cm2)成直径为10mm、厚度为5mm的小片。然后,在氧化气氛下,例如在空气中,于500~1000℃,例如于700℃,将小片烧固8小时。
然后,在研钵中将小片研磨成粉末,其平均颗粒半径小于10μm。将粉末再封入包囊,并于300℃~800℃,在50kg/cm2的压力下,再次压制成小片。在氧化气氛下,例如在空气中,于500~900℃,例如900℃,将小片烧固10~50小时,例如15小时。在这种小片中,除了观察到具有通常的类钙钛矿型结构外,还观察到一种不同的结构。最后,在含有少量氧气的氧气/氩气混合气中,在600~1100℃,例如在800℃下,加热3~30小时,例如20小时,使小片还原。最后终于清楚地观察到一种新结构。这种材料可由化学计量的化学式Y0.5Yb0.5BaCaCu3O6-8表示。
研究了温度与这种小片状材料电阻率之间的关系。当温度降至低于107°K时,观察到向着超导电态的相变,101°K(Tco)时,观察到电阻消失。
实施例5
重复实施例4的步骤,但用钆(作为Gd2O3引入)和锶取代钇和钡,并且X∶X′=1∶1,Y∶Y′=1∶1。分别在104°K和84°K时,观察到临界转变起始温度Tc和电阻变为零或实质为零的温度Tco。这种材料可由化学计量式Y0.5Yb0.5BaSrCu3O6-8表示。
实施例6
重复实施例4的步骤,但用Nb(作为Nb2O3引入)取代30%的Y和Yb。这样,临界转变起始温度进一步提高了3~5°K。
实施例7
按式(ⅰ)所需的比例,将纯度为99.95%或纯度更高的、全部呈细粉末状的Yb2O3、Y2O3、BaCO3、Sr2O3和CuO混合,这里X=0.67(A∶B=1∶2);Y=1.0;Z=3.0;W=6至8,A为钇和镱,B为钡(Y∶Yb为1∶1,1∶2或1∶5)。在研钵中充分地混合这些材料,将其封入包囊,并压制(3kg/cm2)成直径为10mm、厚度为3mm的小片。然后,在氧化气氛下,例如在空气中,于500~1000℃,例如于700℃,将小片烧固8小时。
然后,在研钵中将小片研磨成平均颗粒半径小于10μm的粉末。将粉末再封入包囊,并在50mg/cm2压力下,于300~500℃,例如于400℃,再次压制成小片。升温有益于减少小片中的缺陷。然后,在氧化气氛中,例如在空气中,于500~1000℃,例如于900℃,将小片烧固10~15小时,例如15小时。最后,在含有少量氧气的氧气/氩气混合气中,于600~1100℃,例如于800℃,加热3-30小时,例如20小时,使小片还原。最后终于清楚地观察到一种新结构。这种材料可由化学计量的化学式Y0.5Yb0.5Ba2Cu3O6-8表示。
研究了温度和这种小片状材料电阻率之间的关系。当温度降至低于105°K(临界转变起始温度Tc)时,观察到向超导电态的相变;89°K(Tco)时,观察到电阻消失。
实施例8
重复实施例7的步骤,但用钆(作为Gd2O3引入)取代镱。分别在95°K和88°K时,观察到临界转变起始温度Tc和电阻变为零的温度Tco。这种材料可由化学计量的化学式Y0.5Gd0.5Ba2Cu3O6-8表示。
实施例9
重复实施例7的步骤,但用Nb(作为Nb2O3引入)取代20~30%的Y和Yb。临界转变起始温度进一步提高了6~10°K。
本发明不限于上面例举的材料,还可使用许多变更和改良的材料。例如,也可以将经烧固的原料粉末溶于溶剂,以溶液的形式涂覆于衬底,以形成薄膜超导陶瓷。然后,可以在氧化气氛中,对经过涂覆的衬底进行烧固,最后在还原气氛下烧固。
Claims (21)
1、一种具有以下通式的超导陶瓷,
(A1-XBX)yCuZOW(i)
式中:0.1≤
X<1
Y=2.0~4.0
Z=1.0~4.0
W=4.0~10.0
A为一种或多种稀土元素;当A为一种稀土元素时,B为一种以上的碱土元素;当A为一种以上的稀土元素时,B为一种或多种碱土元素。
2、按照权利要求1的超导陶瓷,其中
Y=2.5~3.5
Z=1.5~3.5
W=6.0~8.0
3、按照权利要求1的超导陶瓷,其通式(ⅱ)为
(A1-xBx)yCuzOw·(A1-x′B′x′)y′Cuz′Ow′(ⅱ)
式中:0.1≤X<1
0.1≤X′<1
Y=2.0~4.0,
Y′=2.0~4.0,
Z=1.0~4.0,
Z′=1.0~4.0,
W=4.0~10.0
W′=4.0~10.0
A为一种或多种稀土元素,B和B′为两种或多种碱土元素。
4、按照权利要求3的超导陶瓷,其中
Y=2.5~3.5,
Y′=2.5~3.5,
Z=1.5~3.5,
Z′=1.5~3.5,
W=6.0~8.0,
W′=6.0~8.0。
5、按照权利要求3或权利要求4的超导陶瓷,其中A为一种稀土元素。
6、按照权利要求5的超导陶瓷,它具有化学计量的化学式YbBaSrCu3O6-8。
7、按照权利要求5的超导陶瓷,它具有化学计量式YBaCaCu3O6-8。
8、按照权利要求5的超导陶瓷,它具有化学计量式YbBa0.7Sr0.6Ca0.6Cu3O6-8。
9、按照权利要求3或权利要求4的超导陶瓷,其中A为一种以上的稀土元素。
10、按照权利要求9的超导陶瓷,它具有化学计量式Y0.5Yb0.5BaSrCu3O6-8。
11、按照权利要求9的超导陶瓷,它具有化学计量式Y0.5Yb0.5BaCaCu3O6-8。
12、按照权利要求1的超导陶瓷,其通式(ⅲ)为
〔A1-x(B1-gB′ 8)x〕yCuzOw(ⅲ)
式中0.1≤X<1
0<q<1
Y=2.0~4.0,
Z=1.0~4.0,
W=4.0~10.0
A为稀土元素,B和B′为不同的碱土元素。
13、按照权利要求12的超导陶瓷,其中
Y=2.5~3.5,
Z=1.5~3.5,
W=6.0~8.0。
14、按照权利要求1的超导陶瓷,其通式(ⅳ)为
〔(A1-pA′ p)1-x(B1-gB′ g)x〕yCuzOw(ⅳ)
式中0.1≤X<1
0<p<1
0<q<1
Y=2.0~4.0,
Z=1.0~4.0,
W=4.0~10.0,
A和A′为不同的稀土元素,B和B′为不同的碱土元素。
15、按照权利要求14的超导陶瓷,其中
Y=2.5~3.5,
Z=1.5~3.5,
W=6.0~8.0。
16、按照权利要求1的超导陶瓷,其通式(ⅴ)为
〔(A1-pA′ p)1-xBx〕yCuzOw(ⅴ)
式中:0.1≤X<1
0<p<1
Y=2.0~4.0,
Z=1.0~4.0,
W=4.0~10.0,
A和A′为不同的稀土元素,B为碱土元素。
17、按照权利要求16的超导陶瓷,其中
Y=2.5~3.5
Z=1.5~3.5
W=6.0~8.0。
18、按照权利要求17的超导陶瓷,它具有化学计量式Y0.5Gd0.5Ba2Cu3O6-8。
19、按照权利要求17的超导陶瓷,它具有化学计量式Y0.5Yb0.5Ba2Cu3O6-8。
20、一种权利要求1至19之任一项的超导陶瓷的制备方法,它包括将粉末状金属组分的氧化物和/或其碳化物按化学计量一起混合,将混合物压制成所需形状,并在高温下对该混合物进行烧结。
21、一种超导陶瓷包括两种或两种以上稀土元素和/或两种或两种以上碱土元素,并具有大晶粒的多晶式类钙钛态矿型结构,这种大晶粒能在晶粒间提供较小界面面积,同时相应提高超导体临界转变的起始温度。
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JP072487/87 | 1987-03-25 | ||
JP62072483A JP2588399B2 (ja) | 1987-03-25 | 1987-03-25 | 超電導セラミツクス |
JP072483/87 | 1987-03-25 | ||
JP62072481A JP2588398B2 (ja) | 1987-03-25 | 1987-03-25 | 超電導セラミツクス |
JP072481/87 | 1987-03-25 | ||
JP62072487A JP2588400B2 (ja) | 1987-03-25 | 1987-03-25 | 超電導セラミツクス |
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CN90101336A Division CN1020518C (zh) | 1987-03-25 | 1987-12-12 | 铜氧化物超导陶瓷的制法 |
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US (1) | US7112556B1 (zh) |
EP (1) | EP0283620A1 (zh) |
KR (2) | KR910001345B1 (zh) |
CN (1) | CN1027329C (zh) |
AU (3) | AU598118B2 (zh) |
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EP0275343A1 (en) * | 1987-01-23 | 1988-07-27 | International Business Machines Corporation | New superconductive compounds of the K2NiF4 structural type having a high transition temperature, and method for fabricating same |
AU598115B2 (en) * | 1987-03-18 | 1990-06-14 | Semiconductor Energy Laboratory Co. Ltd. | Superconducting oxide ceramics |
JPS63242922A (ja) * | 1987-03-30 | 1988-10-07 | Sumitomo Electric Ind Ltd | 超電導材料 |
CN1027406C (zh) * | 1987-04-07 | 1995-01-11 | 藤仓电线株式会社 | 氧化物超导体及其制造方法 |
EP0292940A3 (en) * | 1987-05-25 | 1989-12-06 | Nippon Steel Corporation | Superconductor |
US5036044A (en) * | 1988-09-29 | 1991-07-30 | University Of Arkansas | R-Tl-Sr-Ca-Cu-O superconductors |
JPH04501407A (ja) * | 1988-10-26 | 1992-03-12 | イー・アイ・デユポン・ドウ・ヌムール・アンド・カンパニー | 超伝導金属酸化物組成物及びその製造及び使用方法 |
NZ228820A (en) * | 1989-04-19 | 1992-07-28 | Nz Scientific & Ind Res | Superconducting metal oxide and its preparation |
WO1990015023A1 (en) * | 1989-05-27 | 1990-12-13 | Foundational Juridical Person International Superconductivity Technology Center | Oxide superconductor |
DE3923845A1 (de) * | 1989-07-19 | 1991-01-31 | Hoechst Ag | Dichte, supraleitende koerper mit textur |
JPH04175224A (ja) * | 1990-09-18 | 1992-06-23 | Kokusai Chodendo Sangyo Gijutsu Kenkyu Center | 酸化物超電導体とその製造方法 |
EP1843988B1 (en) * | 2004-12-23 | 2013-02-13 | Superconductor Technologies, Inc. | Rf-properties-optimized compositions of (re)ba2cu3o7-d thin film superconductors |
KR101576206B1 (ko) | 2014-08-18 | 2015-12-11 | 한국에너지기술연구원 | 촉매 과열방지 시스템 및 방법 |
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US2976505A (en) * | 1958-02-24 | 1961-03-21 | Westinghouse Electric Corp | Thermistors |
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DE1646988B2 (de) * | 1965-03-19 | 1973-06-14 | Siemens AG, 1000 Berlin u 8000 München | Verfahren zum herstellen polykristalliner scheiben-, stabrohr- oder folienfoermiger keramischer kaltleiter- bzw. dielektrikums- bzw. heissleiterkoerper |
AT363380B (de) * | 1975-01-28 | 1981-07-27 | Siemens Ag | Keramisches dielektrisches material |
JPS51150692A (en) * | 1975-06-20 | 1976-12-24 | Arita Kosei | High conductivity composed substance |
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EP0341266B1 (en) * | 1987-01-12 | 1995-08-30 | University Of Houston | Superconductivity in square-planar compound systems |
EP0275343A1 (en) * | 1987-01-23 | 1988-07-27 | International Business Machines Corporation | New superconductive compounds of the K2NiF4 structural type having a high transition temperature, and method for fabricating same |
DE3854626T2 (de) | 1987-03-12 | 1996-07-04 | Semiconductor Energy Lab | Verfahren zur Herstellung von Komponenten aus supraleitenden oxidkeramischen Materialien. |
JPS63225572A (ja) | 1987-03-13 | 1988-09-20 | Tokyo Univ | 超伝導性素材 |
JPS63225531A (ja) | 1987-03-13 | 1988-09-20 | Nippon Telegr & Teleph Corp <Ntt> | 酸化物超伝導材料 |
JPS63230563A (ja) | 1987-03-18 | 1988-09-27 | Semiconductor Energy Lab Co Ltd | 超電導セラミツクス |
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NZ231390A (en) * | 1989-08-02 | 1992-07-28 | Nz Government | Metal oxide superconducting material containing copper and barium |
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-
1987
- 1987-10-14 EP EP87309081A patent/EP0283620A1/en not_active Withdrawn
- 1987-12-12 CN CN87101149A patent/CN1027329C/zh not_active Expired - Fee Related
- 1987-12-21 KR KR1019870014637A patent/KR910001345B1/ko not_active IP Right Cessation
-
1988
- 1988-03-24 AU AU13569/88A patent/AU598118B2/en not_active Ceased
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1990
- 1990-03-08 AU AU51193/90A patent/AU632312B2/en not_active Ceased
- 1990-03-08 AU AU51192/90A patent/AU5119290A/en not_active Abandoned
- 1990-10-31 KR KR1019900017568A patent/KR910001346B1/ko not_active IP Right Cessation
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AU1356988A (en) | 1988-09-29 |
AU598118B2 (en) | 1990-06-14 |
AU5119390A (en) | 1990-07-05 |
EP0283620A1 (en) | 1988-09-28 |
KR910001345B1 (ko) | 1991-03-04 |
CN1027329C (zh) | 1995-01-04 |
US7112556B1 (en) | 2006-09-26 |
KR910001346B1 (ko) | 1991-03-04 |
AU5119290A (en) | 1990-06-28 |
AU632312B2 (en) | 1992-12-24 |
KR880011826A (ko) | 1988-10-31 |
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