CN111423228A - 一种高储能效率陶瓷及其制备方法 - Google Patents
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Abstract
本发明公开了一种高储能效率陶瓷,化学表达式为(1‑x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3‑xBi(Mg0.5Ti0.5)O3,其中x为0.05~0.2。先将BaCO3、CaCO3、ZrO、TiO2、Bi2O3及MgO粉料按照化学计量比混合,制备陶瓷粉料,再经压力成型、排胶后,于1350~1450℃烧结,制得高储能效率陶瓷。本发明储能效率为88.8%~98.1%,可作为储能元件应用于相关领域。
Description
技术领域
本发明属于一种以成分为特征的陶瓷组合物,特别涉及一种高储能效率陶瓷及其制备方法。
背景技术
由于储能陶瓷具有功率密度高、充放电速度快、输出电流大等优势,逐渐成为脉冲功率系统中的关键元件。陶瓷的储能效率作为衡量储能性能的关键因素之一,严重影响了储能陶瓷在脉冲功率系统中的应用。储能效率越高,意味着对能量的利用率越高。然而,现有的储能陶瓷很难在工作压电范围内保持较高的储能效率,因此急需研发一种高储能效率的储能陶瓷。
发明内容
本发明的目的,是为克服现有储能陶瓷储能效率低的缺点,提供一种高储能效率的储能陶瓷材料。
本发明通过如下技术方案予以实现。
一种高储能效率陶瓷,化学表达式为(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,其中x为0.05~0.2。
该高储能效率陶瓷的制备方法,具有如下步骤:
(1)制备(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,x为0.05~0.2陶瓷粉料
a.将BaCO3粉料、CaCO3粉料、ZrO粉料、TiO2粉料、Bi2O3以及MgO粉料按照化学计量比进行混合;
b.将混合后的粉料球磨12小时,球磨介质为去离子水或无水乙醇;
c.将球磨后的粉料在800~1000℃下预烧2小时,从而形成(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3主相;
d.向(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3粉料中外加5wt.%~12.5wt.%的石蜡,之后在200℃下炒蜡15分钟,制得(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,x为0.05~0.2陶瓷粉料;
(2)成型
称取步骤(1)的(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,x为0.05~0.2陶瓷粉料放入模具中,压制成型为陶瓷生坯;
(3)排胶
将步骤(2)压制成型后的陶瓷生坯放入低温炉中进行排胶,排胶温度400~700℃;
(4)烧结
将步骤(2)排胶后的陶瓷生坯于1350~1450℃进行烧结,保温时间为4小时,制得(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,x为0.05~0.2高储能效率陶瓷。
所述步骤(1)的预烧升温速率为3~5℃/min。
所述步骤(2)的陶瓷生坯压制成型过程中采用的压力为4MPa。
所述步骤(4)的烧结升温速率为5℃/min。
所述步骤(4)的烧结温度为1350℃。
本发明制备的(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,其中x为0.05~0.2的储能陶瓷,储能效率为88.8%~98.1%,可作为储能元件应用于相关领域。
附图说明
图1为本发明制备的(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,其中x为0.05~0.2的高储能效率陶瓷的储能效率随x的变化关系图。
图2为实施例3制备的0.85(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-0.15Bi(Mg0.5Ti0.5)O3高储能效率陶瓷在小于击穿电场强度下的储能效率图。
具体实施方式
下面通过具体实施例对本发明作进一步描述。
实施例中所用的BaCO3粉料、CaCO3粉料、ZrO粉料、TiO2粉、Bi2O3以及MgO,均为市售分析纯原料。
实施例1
(1)制备0.95(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-0.05Bi(Mg0.5Ti0.5)O3陶瓷粉料
a.将BaCO3粉料、CaCO3粉料、ZrO粉料、TiO2粉、Bi2O3以及MgO粉料按照化学计量比进行混合;
b.将混合后的粉料球磨12小时,球磨介质为去离子水或无水乙醇;
c.将球磨后的粉料预烧2小时,预烧升温速率为5℃/min,从而形成0.95(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-0.05Bi(Mg0.5Ti0.5)O3主相;
d.向0.95(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-0.05Bi(Mg0.5Ti0.5)O3粉料中加入5wt.%的石蜡,之后在200℃下炒蜡15分钟,制得0.95(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-0.05Bi(Mg0.5Ti0.5)O3陶瓷粉料。
(2)制备0.95(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-0.05Bi(Mg0.5Ti0.5)O3陶瓷
称取0.15g0.95(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-0.05Bi(Mg0.5Ti0.5)O3粉料放入模具中,采用压力为4MPa,压制成型为陶瓷生坯。
(3)排胶
将压制成型后的陶瓷生坯放入低温炉中进行排胶,排胶温度700℃。
(4)烧结
排胶完成后,于1350℃进行烧结,烧结升温速率为5℃/min,保温时间为4小时,制得0.95(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-0.05Bi(Mg0.5Ti0.5)O3储能陶瓷。
实施例1的储能陶瓷储能效率为88.89%,说明其可以应用于脉冲功率系统。
实施例2
实施例2制备工艺完全相同于实施例1,只是x为0.125,制备的储能陶瓷储能效率为98.15%,说明其可以应用于脉冲功率系统。
实施例3
实施例3制备工艺完全相同于实施例1,只是x为0.15,制备的储能陶瓷储能效率为在127kV/cm电场以下工作时,仍然具有大于97%的储能效率,说明其可以应用于脉冲功率系统。
图1为本发明制备的(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,其中x为0.05~0.2的高储能效率陶瓷的储能效率随x的变化关系图。其储能效率均是在各自击穿电场下测试得出。图中插图则为高储能效率陶瓷击穿电场强度随x的变化关系。图1表明,本发明制备的高储能效率陶瓷储能效率为88.8%~98.1%,可作为储能元件应用于脉冲功率系统。
图2则表明,实施例3制备的0.85(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-0.15Bi(Mg0.5Ti0.5)O3储能陶瓷在击穿电场电场以下工作时,仍然具有大于97%的储能效率。
Claims (5)
1.一种高储能效率陶瓷,化学表达式为(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,其中x为0.05~0.2。
该高储能效率陶瓷的制备方法,具有如下步骤:
(1)制备(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,x为0.05~0.2陶瓷粉料
a.将BaCO3粉料、CaCO3粉料、ZrO粉料、TiO2粉料、Bi2O3以及MgO粉料按照化学计量比进行混合;
b.将混合后的粉料球磨12小时,球磨介质为去离子水或无水乙醇;
c.将球磨后的粉料在800~1000℃下预烧2小时,从而形成(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3主相;
d.向(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3粉料中外加5wt.%~12.5wt.%的石蜡,之后在200℃下炒蜡15分钟,制得(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,x为0.05~0.2陶瓷粉料;
(2)成型
称取步骤(1)的(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,x为0.05~0.2陶瓷粉料放入模具中,压制成型为陶瓷生坯;
(3)排胶
将步骤(2)压制成型后的陶瓷生坯放入低温炉中进行排胶,排胶温度400~700℃;
(4)烧结
将步骤(2)排胶后的陶瓷生坯于1350~1450℃进行烧结,保温时间为4小时,制得(1-x)(Ba0.85Ca0.15)(Zr0.1Ti0.9)O3-xBi(Mg0.5Ti0.5)O3,x为0.05~0.2高储能效率陶瓷。
2.根据权利要求1所述的一种高储能效率陶瓷,其特征在于,所述步骤(1)的预烧升温速率为3~5℃/min。
3.根据权利要求1所述的一种高储能效率陶瓷,其特征在于,所述步骤(2)的陶瓷生坯压制成型过程中采用的压力为4MPa。
4.根据权利要求1所述的一种高储能效率陶瓷,其特征在于,所述步骤(4)的烧结升温速率为5℃/min。
5.根据权利要求1所述的一种高储能效率陶瓷,其特征在于,所述步骤(4)的烧结温度为1350℃。
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CN116063074A (zh) * | 2023-01-19 | 2023-05-05 | 同济大学 | 一种具有高储能密度的陶瓷材料及其制备方法和用途 |
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