CN102575339A - Bi-Ge-O型烧结体溅射靶及其制造方法以及光记录介质 - Google Patents
Bi-Ge-O型烧结体溅射靶及其制造方法以及光记录介质 Download PDFInfo
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Abstract
一种Bi-Ge-O型烧结体溅射靶,含有铋(Bi)、锗(Ge)和氧(O),其特征在于,Bi与Ge的原子数比为0.57<(Bi/(Bi+Ge))<0.92,并且含有Bi12GeO20、Bi4Ge3O12和GeO2三相作为结晶相。本发明涉及Bi-Ge-O型烧结体溅射靶及其制造方法以及光记录介质,特别地提供在溅射时不产生靶的破裂,粉粒的产生少,可以稳定地制作高品质的薄膜,可以得到不产生记录位的错误的光记录介质的Bi-Ge-O型烧结体溅射靶及该靶的制造方法以及光记录介质。
Description
技术领域
本发明涉及Bi-Ge-O型烧结体溅射靶及其制造方法以及光记录介质,特别地涉及在溅射时不产生靶的破裂,粉粒的产生少,可以稳定地制作高品质的薄膜,可以得到不产生记录位的错误的光记录介质的Bi-Ge-O型烧结体溅射靶及该靶的制造方法以及光记录介质。
背景技术
一写多读型(WORM:Write Once Read Many)光记录介质,是通过蓝色波长区域(350~500nm)的激光也可以进行高密度记录的光记录介质,特别是具有多层具有高记录灵敏度的记录层的光记录介质。
光盘为了应对高密度化的要求而通过多层化进行高密度化。使用蓝色LD的光盘也同样地进行了高密度记录用光记录介质的开发。
为了实现可以进行高密度多层记录的一写多读型光记录介质,肯定需要具有稳定的组成、结构的材料,而且需要透光特性优良的膜,这样的材料多数为氧化物,一般而言熔点高,因此多数情况下使用溅射法作为成膜方法。
因此,需要适合得到这样的膜的溅射靶。但是,构成靶的化合物的形态、结构等对溅射特性也有影响,因此在将构成靶的化合物形成为适合必要的膜特性的物质时,是否可以稳定地进行良好的溅射成为问题。
使用溅射法在衬底上形成光记录介质用薄膜时,根据靶的材料有时会产生许多粉粒,从而使品质下降。特别是对于高记录密度介质,由粉粒等导致记录位产生错误是重大的问题。由此,会成为不合格品,从而产生成品率下降的问题。
以往,作为提出的光记录介质,提出了许多材料。例如,在专利文献1中,记载了在衬底上至少形成有记录层的光记录介质,其中,记录层的构成元素的主成分为Bi和O(氧),含有B,并且含有选自Ge、Li、Sn、Cu、Fe、Pd、Zn、Mg、Nd、Mn和Ni中的至少一种元素X。
另外,在专利文献2中,记载了一种一写多读型光记录介质,其特征在于,记录层含有Bi、M(M为Mg、Al、Cr、Mn、Co、Fe、Cu、Zn、Li、Si、Ge、Zr、Ti、Hf、Sn、Mo、V、Nb、Y和Ta中的至少一种元素)和氧,记录有信息的记录标记部含有在该记录层中含有的元素的结晶和/或这些元素的氧化物的结晶。
此外,提出了专利文献3至专利文献8。其中,考虑了含有铋(Bi)、锗(Ge)和氧(O)的光记录介质的组合,也记载了通过烧结体靶的溅射将这些光记录介质成膜。但是,该Bi-Ge-O型烧结体溅射靶,存在如下问题:耐热冲击性弱,通过高功率进行溅射时大多会产生破裂、产生龟裂,由此产生粉粒,损害记录膜等的品质。
现有技术文献
专利文献
专利文献1:日本特开2008-210492号公报
专利文献2:日本特开2006-116948号公报
专利文献3:日本特开2003-48375号公报
专利文献4:日本特开2005-161831号公报
专利文献5:日本特开2005-108396号公报
专利文献6:日本特开2007-169779号公报
专利文献7:日本特开2008-273167号公报
专利文献8:日本专利第4271063号公报
发明内容
本发明的课题涉及Bi-Ge-O型烧结体溅射靶及其制造方法以及光记录介质,特别地提供在溅射时不产生靶的破裂,粉粒的产生少,可以稳定地制作高品质的薄膜,可以得到不产生记录位的错误的光记录介质的Bi-Ge-O型烧结体溅射靶及该靶的制造方法以及光记录介质。
为了解决上述问题,本发明人进行了广泛深入的研究,结果发现,选择适当组成的Bi-Ge-O型烧结体而控制结晶相,抑制靶的热冲击而防止靶的破裂,从而在溅射时可以有效地抑制粉粒的产生。
基于这些发现,本发明提供:
1)一种Bi-Ge-O型烧结体溅射靶,含有铋(Bi)、锗(Ge)和氧(O),其特征在于,
Bi与Ge的原子数比为0.57<(Bi/(Bi+Ge))<0.92,并且含有Bi12GeO20、Bi4Ge3O12和GeO2三相作为结晶相。
2)如上述1)所述的烧结体溅射靶,其特征在于,通过200℃、30分钟的加热对靶施加热冲击的情况下,该热冲击前后的平均弯曲强度下降率为50%以下。
3)一种光记录介质,其通过使用上述1)或2)所述的靶进行溅射而成膜。
另外,本发明提供:
4)一种Bi-Ge-O型烧结体溅射靶的制造方法,其特征在于,
将0.03~89摩尔%的GeO2粉末、11~99.97摩尔%的Bi12GeO20粉末作为起始原料,将这些原料以Bi与Ge的原子数比为0.57<(Bi/(Bi+Ge))<0.92的方式进行混合后,在600~840℃、施压150~400kg/cm2的条件下进行热压,由此制作含有Bi12GeO20、Bi4Ge3O12和GeO2三相的结晶相的烧结体。
5)如上述4)所述的Bi-Ge-O型烧结体溅射靶的制造方法,其特征在于,
将14.3摩尔%的GeO2粉末和85.7摩尔%的Bi2O3粉末混合后,使其进行固相反应,从而制作Bi12GeO20粉末。
6)如上述4)或5)所述的Bi-Ge-O型烧结体溅射靶的制造方法,其特征在于,
使用平均晶粒直径为10~50μm的氧化锗烧结原料粉末进行烧结。
发明效果
本发明的Bi-Ge-O型烧结体溅射靶,具有如下优良效果:在溅射时不产生靶的破裂,粉粒的产生少,可以稳定地制作高品质的薄膜,可以得到不产生记录位的错误的光记录介质。
具体实施方式
本发明的Bi-Ge-O型烧结体溅射靶,含有铋(Bi)、锗(Ge)和氧(O),其特征在于,Bi与Ge的原子数比为0.57<(Bi/(Bi+Ge))<0.92,并且含有Bi12GeO20、Bi4Ge3O12和GeO2三相作为结晶相。使用该组成的记录膜,为可以通过多层化实现高密度记录的适合组成,可以稳定地进行良好的溅射成膜。
一般而言,在将氧化铋(Bi2O3)和氧化锗(GeO2)的粉末作为起始原料并将其烧结来制作该组成靶的情况下,成为Bi12GeO20和Bi4Ge3O12两相共存的组成。
不过,Bi12GeO20和Bi4Ge3O12的热膨胀系数差异大,因此耐热冲击性极弱,产生在使用高功率溅射成膜时产生破裂的问题。
因此,本申请发明中,将热膨胀系数值处于Bi12GeO20和Bi4Ge3O12之间的GeO2作为中间相,将其形成在烧结体中三相共存的组织,因此GeO2相成为缓冲相,从而显著提高耐热冲击性。顺便说一下,Bi12GeO20的热膨胀系数为1.39×10-5,Bi4Ge3O12的热膨胀系数为6.00×10-6。另一方面,GeO2的热膨胀系数为7.59×10-6,为具有处于前两者之间的热膨胀系数的相,因此可以成为有效的缓冲相。
结果,可以提高靶的耐热冲击性,由此可以得到如下显著优点:可以进行高功率成膜,可以提高生产效率。
另外,可以得到如下效果:引起破裂或龟裂的粉粒的产生显著减少,可以制作稳定的高品质的薄膜,可以制作不产生记录位的错误、从而可以实现高记录密度的光记录介质。
为了防止溅射时产生粉粒,将靶的结晶平均粒度调节为100μm以下也是有效的。
另外,本发明的Bi-Ge-O型烧结体溅射靶,在通过200℃、30分钟的加热对靶施加热冲击的情况下,该热冲击前后的平均弯曲强度下降率为50%以下。
现有的Bi12GeO20和Bi4Ge3O12两相共存组成的靶的情况下,所述热冲击前后的平均弯曲强度下降率超过80%,与此相对,本发明实现了显著的改善效果。由此,可以抑制靶由于热冲击而破裂,并且可以直接评价靶的特性。
另外,所述靶的Bi12GeO20、Bi4Ge3O12和GeO2三相的比率可以在本发明的制造条件的范围内任意调节。这也取决于溅射时靶所受到的热冲击的程度、即成膜速度(生产速度)或溅射装置的结构,成为用于缓和热冲击的指标。
通过使用上述的靶进行溅射而成膜的光记录介质,为稳定的高品质的薄膜,可以得到不产生记录位的错误的光记录介质。
制造Bi-Ge-O型烧结体溅射靶时,将氧化铋和氧化锗的粉末作为起始原料,将这些原料以Bi与Ge的原子数比为0.57<(Bi/(Bi+Ge))<0.92的方式进行混合。然后,在600~840℃、施压150~400kg/cm2的条件下对该混合粉末进行热压。由此制作含有Bi12GeO20、Bi4Ge3O12和GeO2三相的结晶相的烧结体。
该烧结条件为可以得到均匀组成的靶的适合条件。在偏离上述范围的烧结条件下也可以制造靶,但是,靶的品质的重现性差,因此期望设定为上述范围。另外,所述原料阶段的Bi与Ge的原子数比0.57<(Bi/(Bi+Ge))<0.92直接反映到靶中,可以得到相同组成比的靶。
制造Bi-Ge-O型烧结体溅射靶时,作为氧化铋和氧化锗烧结原料,期望使用0.03~89摩尔%的GeO2粉末、11~99.97摩尔%的Bi12GeO20粉末。这是用于有效地得到含有Bi12GeO20、Bi4Ge3O12和GeO2三相的结晶相的烧结体的必要条件。
另外,期望使用平均晶粒直径为10~50μm的氧化锗(GeO2)粉末进行烧结。这是因为:小于上述的下限值时,容易产生粉末的凝聚,难以得到均匀的烧结体。另外,超过上述的上限值时,烧结得到的靶中产生粗大粒子,容易偏析,因此期望设定为上述范围。这是更优选的粉末的条件,通过调节烧结条件,也可以使用该范围外的粉末。
关于Bi12GeO20粉末,可以事先通过将14.3摩尔%的GeO2粉末和85.7摩尔%的Bi2O3粉末混合后进行固相反应,并将其粉碎来制作。关于Bi12GeO20粉末的粒径,没有特别限制,为约100μm以下就没有问题。这是因为:在本申请发明的烧结条件下,不会产生象GeO2一样的凝聚。
实施例
以下,基于实施例和比较例进行说明。另外,本实施例仅仅是例子,本发明无论如何不限于该实施例。即,本发明仅受权利要求书的限制,本发明也包括本发明所包括的实施例以外的各种变形。
(实施例1)
将纯度3N(99.9%)的氧化铋和氧化锗的粉末作为起始原料,并且预先准备平均粒径12μm的GeO2粉末和平均粒径20μm的Bi12GeO20粉末,将它们各自以83.3摩尔%的GeO2粉末和16.7摩尔%的Bi12GeO20粉末进行配合使得Bi与Ge的原子数比为0.67,然后进行混合,再将混合后的粉末填充到碳制模具中,在温度700℃、压力250kg/cm2的条件下进行热压。
另外,本实施例中,GeO2粉末和Bi12GeO20粉末以上述的摩尔比进行添加,但是,这些粉末的添加的综合比以符合50.0摩尔%的GeO2和50.0摩尔%的Bi2O3的配合比进行调节。
将热压后的烧结体精加工而得到靶。靶的相对密度为102%(100%密度为7.44g/cm3)。
该烧结体通过X射线衍射测定确认为Bi12GeO20、Bi4Ge3O12和GeO2的三相结构。结果如表1所示。
然后,通过200℃、30分钟的加热对该靶施加热冲击。然后,实施JIS标准1601规定的弯曲试验(从靶中的任意5个部位取宽4±0.1mm、高3±0.1mm、长40~50mm的试验片进行测定,并求出5个点的测定结果的平均值),测定该热冲击前后的平均弯曲强度比(强度的下降率)。虽然其根据测定部位的不同多少存在偏差,但是均低于50%,强度的下降率少。
然后,使用该靶,以2kW的功率进行溅射。结果,靶没有产生破裂或龟裂,与下述的比较例相比,粉粒的产生显著地少。
结果,本申请发明的实施例为具有如下优良效果的良好靶:不产生破裂,可以提高生产效率,并且可以稳定地制作高品质的薄膜,可以得到不产生记录位的错误的光记录介质。
(实施例2)
将纯度3N(99.9%)的氧化铋和氧化锗的粉末作为起始原料,并且预先准备平均粒径12μm的GeO2粉末和平均粒径20μm的Bi12GeO20粉末,将它们各自以66.7摩尔%的GeO2粉末和33.3摩尔%的Bi12GeO20粉末进行配合使得Bi与Ge的原子数比为0.80,然后进行混合,再将混合后的粉末填充到碳制模具中,在温度700℃、压力250kg/cm2的条件下进行热压。
另外,本实施例中,GeO2粉末和Bi12GeO20粉末以上述的摩尔比进行添加,但是,这些粉末的添加的综合比以符合33.3摩尔%的GeO2和66.7摩尔%的Bi2O3的配合比进行调节。
将热压后的烧结体精加工而得到靶。靶的相对密度为95.9%(100%密度为7.58g/cm3)。
该烧结体通过X射线衍射测定确认为Bi12GeO20、Bi4Ge3O12和GeO2的三相结构。结果如表1所示。
然后,通过200℃、30分钟的加热对该靶施加热冲击。然后,实施JIS标准1601规定的弯曲试验,测定该热冲击前后的平均弯曲强度比(强度的下降率)。虽然其根据测定部位的不同多少存在偏差,但是均低于50%,强度的下降率少。
然后,使用该靶,以2kW的功率进行溅射。结果,靶没有产生破裂或龟裂,与下述的比较例相比,粉粒的产生也少。
结果,本申请发明的实施例为具有如下优良效果的良好靶:不产生破裂,可以提高生产效率,并且可以稳定地制作高品质的薄膜,可以得到不产生记录位的错误的光记录介质。
(比较例1)
将纯度3N(99.9%)的氧化铋和氧化锗的粉末作为起始原料,将它们各自以平均粒径5μm的50.0摩尔%的GeO2粉末和平均粒径20μm的50.0摩尔%的Bi2O3粉末进行配合使得Bi与Ge的原子数比为0.67,然后进行混合,再将混合后的粉末填充到碳制模具中,在温度730℃、压力250kg/cm2的条件下进行热压。
将热压后的烧结体精加工而得到靶。靶的相对密度为103%(100%密度为7.44g/cm3)。
该烧结体通过X射线衍射测定确认为Bi12GeO20、Bi4Ge3O12的两相结构。结果如表1所示。
然后,通过200℃、30分钟的加热对该靶施加热冲击。然后,实施JIS 1601规定的弯曲试验。该热冲击前后的平均弯曲强度比(强度的下降率)的测定结果同样如表1所示。
结果,平均弯曲强度下降率为82%。使用该靶,以2kW的功率进行溅射。结果,在溅射过程中靶产生破裂。另外,与实施例相比,粉粒的产生显著增加。认为这是由于溅射过程中靶破裂造成的。
(比较例2)
将纯度3N(99.9%)的氧化铋和氧化锗的粉末作为起始原料,并预先准备平均粒径5μm的GeO2粉末和平均粒径20μm的Bi12GeO20粉末,将它们各自以83.3摩尔%的GeO2粉末和16.7摩尔%的Bi12GeO20粉末进行配合使得Bi与Ge的原子数比为0.67,然后进行混合,再将混合后的粉末填充到碳制模具中,在温度700℃、压力250kg/cm2的条件下进行热压。
另外,本实施例中,GeO2粉末和Bi12GeO20粉末以上述的摩尔比进行添加,但是,这些粉末的添加的综合比以符合50.0摩尔%的GeO2和50.0摩尔%的Bi2O3的配合比进行调节。
将热压后的烧结体精加工而得到靶。靶的相对密度为103%(100%密度为7.58g/cm3)。
该烧结体通过X射线衍射测定确认GeO全部反应,为Bi12GeO20、Bi4Ge3O12的两相结构。结果如表1所示。
然后,通过200℃、30分钟的加热对该靶施加热冲击。然后,实施JIS 1601规定的弯曲试验。该热冲击前后的平均弯曲强度比(强度的下降率)的测定结果同样如表1所示。
结果,平均弯曲强度下降率为80%。使用该靶,以2kW的功率进行溅射。结果,在溅射过程中靶产生破裂。另外,与实施例相比,粉粒的产生显著增加。认为这是由于溅射过程中靶破裂造成的。
产业实用性
根据本发明的Bi-Ge-O型烧结体溅射靶及其制造方法,具有如下优良效果:在溅射时不产生靶的破裂,粉粒的产生少,可以稳定地制作高品质的薄膜,可以得到不产生记录位的错误的光记录介质。本发明可以提供能够提高光记录介质的成膜的生产效率,适合制造光记录介质的靶。
Claims (6)
1.一种Bi-Ge-O型烧结体溅射靶,含有铋(Bi)、锗(Ge)和氧(O),其特征在于,
Bi与Ge的原子数比为0.57<(Bi/(Bi+Ge))<0.92,并且含有Bi12GeO20、Bi4Ge3O12和GeO2三相作为结晶相。
2.如权利要求1所述的烧结体溅射靶,其特征在于,通过200℃、30分钟的加热对靶施加热冲击的情况下,该热冲击前后的平均弯曲强度下降率为50%以下。
3.一种光记录介质,其通过使用权利要求1或2所述的靶进行溅射而成膜。
4.一种Bi-Ge-O型烧结体溅射靶的制造方法,其特征在于,
将0.03~89摩尔%的GeO2粉末、11~99.97摩尔%的Bi12GeO20粉末作为起始原料,将这些原料以Bi与Ge的原子数比为0.57<(Bi/(Bi+Ge))<0.92的方式进行混合后,在600~840℃、施压150~400kg/cm2的条件下进行热压,由此制作含有Bi12GeO20、Bi4Ge3O12和GeO2三相的结晶相的烧结体。
5.如权利要求4所述的Bi-Ge-O型烧结体溅射靶的制造方法,其特征在于,
将14.3摩尔%的GeO2粉末和85.7摩尔%的Bi2O3粉末混合后,使其进行固相反应,从而制作Bi12GeO20粉末。
6.如权利要求4或5所述的Bi-Ge-O型烧结体溅射靶的制造方法,其特征在于,
使用平均晶粒直径为10~50μm的氧化锗烧结原料粉末进行烧结。
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