JP2010006688A - 金属酸化物、圧電材料および圧電素子 - Google Patents
金属酸化物、圧電材料および圧電素子 Download PDFInfo
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Abstract
【解決手段】正方晶の結晶構造を有する、Ba(SixGeyTiz)O3(ただし0≦x≦1、0≦y≦1、0≦z≦0.5、x+y+z=1)で表される酸化物からなる圧電材料。上記の圧電材料が一対の電極によって挟持された圧電素子において、前記一対の電極の少なくとも一つがSrRuO3またはNiである圧電素子。
【選択図】図1
Description
また、上記の課題を解決する圧電素子は、上記の圧電材料が一対の電極によって挟持された圧電素子である。
本発明に係る金属酸化物は、正方晶の結晶構造を有する、Ba(SixGeyTiz)O3(ただし0≦x≦1、0≦y≦1、0≦z≦0.5、x+y+z=1)で表される金属酸化物である。
本発明に係る圧電材料は、正方晶の結晶構造を有する、Ba(SixGeyTiz)O3(ただし0≦x≦1、0≦y≦1、0≦z≦0.5、x+y+z=1)で表される酸化物からなることを特徴とする。
また、本発明による圧電材料は、前記Ba(SixGe1−x)O3において、x=0.25であることで、圧電定数e33のピーク値が得られる。
Si、Ge、Tiは、イオンの状態ではd電子が全く存在しない、または全てのd軌道が10個の電子で占有されている(以下、形式電荷がd^0またはd^10と表現する、但し「^」は上付きの添字を表す)。形式電荷がd^0またはd^10のSi、Ge、Tiを用いることで、絶縁性の高い圧電材料を得られる。
ここで、第一原理計算による使用可能温度領域と絶縁性の評価方法について述べる。
使用可能温度領域については、Ba(SixGeyTiz)O3を構造最適化し、テトラゴナリティー(c/a比)を導出することで分かる。一般に、テトラゴナリティーが大きい程、構造相転移温度は高い。例えばBaTiO3のテトラゴナリティーは1.01であり、130℃以上で圧電性を消失する。すなわち、BaTiO3よりも大きいテトラゴナリティーを有する材料が得られれば、使用可能温度領域は高温側に広いことが推定できる。
次に、本発明による圧電材料を得るための製法について説明する。
本実施例のBa(SixGeyTiz)O3の形態は、限定されず、焼結体であるセラミックスでも薄膜でもよい。
一方、薄膜状の圧電材料を作製する場合は、スパッタリング法、ゾルゲル法、レーザーアブレーション法、CVD法などの公知の方法を用いて成膜が可能である。例えばスパッタ装置による成膜の場合、BaCO3、及びSiO2、GeO2、TiO2を任意のモル比で混合した粉末を10MPaで一軸加圧した成型体をターゲットとして用意し、ArとO2雰囲気で、RFマグネトロンスパッタリングにより成膜する。さらに、基板加熱も同時に行うことで、結晶化が促進できる。成膜された金属酸化物に含まれるSi、Ge、Ti、の物質量の和に対するのBaの物質量の比は、波長分散型蛍光X線による組成分析をした時に0.99〜1.1の範囲となるように調整されることが望ましい。
ここで、実験サンプルの相転移温度の測定方法と、絶縁性の測定方法について述べる。
また、絶縁性の良否は、作製した圧電素子の両端の電極に直流電圧を付加し、その際の抵抗値を測定することで判断できる。実用上のデバイスとして使用するためには、10GΩ・cm以上の電気抵抗値を有することが望ましい。
実施例1から5
図1は、本発明に係るBa(SixGe1−x)O3の正方晶ペロブスカイト構造を説明する図である。
図2から分かるように、x=1.0(つまりBaSiO3)では、圧電定数e31が最も大きくなる。
図4は、Ba(SixGe1−x)O3の各xでの自発分極Pをベリーの位相により求めた計算結果である。x=1で最高値をとり、全てのxで0.94C/m2以上が得られていることから、強誘電性に優れた材料であることも証明された。このことから、本発明の圧電材料は強誘電体メモリ等のデバイスにも適用可能である。
次に、Ba(SixGeyTiz)O3(x+y+z=1、0≦x≦1、0≦y≦1、0≦z<1)のy=0の場合の第一原理計算結果について説明する。
以下ではBa(SixGeyTiz)O3のy=0の場合は、全てBa(SixTi1−x)O3と記す。
その結果、c/aが1.29となり、バンドギャップは、2.0eVであった。この事から、BiCoO3よりも絶縁性が高く、BaTiO3よりも広い温度領域で正方晶構造が安定して保たれることが分かった。
次に、Ba(SixGeyTiz)O3(x+y+z=1、0≦x≦1、0≦y≦1、0≦z<1)のx=0の場合を例に実施形態の説明を行う。
以下ではBa(SixGeyTiz)O3のx=0の場合は、全てBa(GeYTi1−Y)O3と記す。
その結果、c/aが1.24となり、バンドギャップは、1.18eVであった。この事から、BiCoO3よりも絶縁性が高く、BaTiO3よりも広い温度領域で正方晶構造が安定して保たれることが期待される。
BaSiO3薄膜の実施例を示す。
次に、実施例5に示したBaSiO3の場合を例にRFマグネトロンスパッタ装置を用いた実施形態の説明を行う。本実施例においては、BaCO3とSiO2を任意のモル比(例えば、1:1)で混合した粉末を10MPaで一軸加圧した成型体をターゲットとして用意し、ArとO2雰囲気で、基板加熱温度を600℃で50nm厚の成膜を行った。また、基板にはSTO(100)単結晶基板上に(100)配向SROが成膜された電極付き基板を用いた。
前述した方法により作製したBaSiO3は室温で正方晶構造が主相であり、室温から200℃までの温度範囲でXRD測定による構造相転移は見られなかった。この事から、BaSiO3の相転移温度は200℃以上であり、BaTiO3よりも実用温度領域が広いことが分かる。また、直流電圧(10V、室温)よる抵抗値を測定したところ、15GΩ・cmの高い絶縁性が得られた。
Ba(Si0.2Ge0.8)O3薄膜の実施例を示す。
次に、実施例8と同様にBa(Si0.2Ge0.8)O3薄膜を作製した。本実施例においては、BaCO3とSiO2、GeO2を任意のモル比(例えば、5:1:4)で混合した粉末を10MPaで一軸加圧した成型体をターゲットとして用意し、ArとO2雰囲気で、基板加熱温度を600℃で50nm厚の成膜を行った。
作製したBa(Si0.2Ge0.8)O3は室温で正方晶構造が主相であり、室温から200℃までの温度範囲でXRD測定による構造相転移は見られなかった。この事から、Ba(Si0.2Ge0.8)O3の相転移温度は200℃以上であり、BaTiO3よりも実用温度領域が広いことが分かる。また、直流電圧(10V、室温)による抵抗値を測定したところ、17GΩ・cmの高い絶縁性が得られた。
また、本実施例においては、Ba(SiXGeYTiZ)O3の単相を例に示したが、その他の正方晶構造以外の材料と組み合わせて作製し、所望の構造相転移温度、絶縁性、圧電特性に調整して使用できる。
まず本発明との比較用にBaTiO3を高圧合成により作製した。原料粉として酸化バリウム(BaO)と酸化チタン(TiO2)をAr雰囲気のグローブボックス中で1:1のモル比で混合した。この混合粉を、微量のKClO4を酸化剤として敷き詰めた白金カプセルに封入して、1200℃、6GPaの高圧合成により、BaTiO3焼結体を作製した。
次に、本発明との比較用にBa(Ge0.2Ti0.8)O3を高圧合成により作製した。比較例1と同様に炭酸バリウム(BaCO3)と酸化ゲルマニウム(GeO2)、酸化チタン(TiO2)を5:1:4のモル比で混合し、微量のKClO4を酸化剤として添加した後、1200℃、6GPaの高圧合成により、Ba(Ge0.2Ti0.8)O3焼結体を作製した。
Claims (6)
- 正方晶の結晶構造を有する、Ba(SixGeyTiz)O3(ただし0≦x≦1、0≦y≦1、0≦z≦0.5、x+y+z=1)で表される金属酸化物。
- 0.75≦x≦1、0≦y≦0.25、z=0であることを特徴とする請求項1記載の金属酸化物。
- 0.2≦x≦0.3、0.7≦y≦0.8、z=0であることを特徴とする請求項1記載の金属酸化物。
- 請求項1ないし3のいずれか一項記載の金属酸化物を含む圧電材料。
- 請求項4記載の圧電材料が一対の電極によって挟持された圧電素子。
- 前記一対の電極の少なくとも一つがSrRuO3またはNiであることを特徴とする請求項5記載の圧電素子。
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