JP5787671B2 - Transparent glass ceramics - Google Patents
Transparent glass ceramics Download PDFInfo
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- JP5787671B2 JP5787671B2 JP2011184531A JP2011184531A JP5787671B2 JP 5787671 B2 JP5787671 B2 JP 5787671B2 JP 2011184531 A JP2011184531 A JP 2011184531A JP 2011184531 A JP2011184531 A JP 2011184531A JP 5787671 B2 JP5787671 B2 JP 5787671B2
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C10/00—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition
- C03C10/0018—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing SiO2, Al2O3 and monovalent metal oxide as main constituents
- C03C10/0027—Devitrified glass ceramics, i.e. glass ceramics having a crystalline phase dispersed in a glassy phase and constituting at least 50% by weight of the total composition containing SiO2, Al2O3 and monovalent metal oxide as main constituents containing SiO2, Al2O3, Li2O as main constituents
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/04—Glass compositions containing silica
- C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
- C03C3/083—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound
- C03C3/085—Glass compositions containing silica with 40% to 90% silica, by weight containing aluminium oxide or an iron compound containing an oxide of a divalent metal
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/04—Glass compositions containing silica
- C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
- C03C3/089—Glass compositions containing silica with 40% to 90% silica, by weight containing boron
- C03C3/091—Glass compositions containing silica with 40% to 90% silica, by weight containing boron containing aluminium
- C03C3/093—Glass compositions containing silica with 40% to 90% silica, by weight containing boron containing aluminium containing zinc or zirconium
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- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03C—CHEMICAL COMPOSITION OF GLASSES, GLAZES OR VITREOUS ENAMELS; SURFACE TREATMENT OF GLASS; SURFACE TREATMENT OF FIBRES OR FILAMENTS MADE FROM GLASS, MINERALS OR SLAGS; JOINING GLASS TO GLASS OR OTHER MATERIALS
- C03C3/00—Glass compositions
- C03C3/04—Glass compositions containing silica
- C03C3/076—Glass compositions containing silica with 40% to 90% silica, by weight
- C03C3/097—Glass compositions containing silica with 40% to 90% silica, by weight containing phosphorus, niobium or tantalum
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Description
本発明は、透明なガラスセラミックスに関する。 The present invention relates to a transparent glass ceramic.
組成範囲Ｌｉ2Ｏ−Ａｌ2Ｏ3−ＳｉＯ2（ＬＡＳ−ガラスセラミックス）からの低い熱膨張率を有する従来のガラスセラミックスは、ＴｉＯ2及びＺｒＯ2を核生成成分として含有する。出発ガラスから、いわゆるセラミックス化（出発ガラスがガラスセラミックスに変換されること）の間に、まずＴｉＯ2及びＺｒＯ2からの種結晶が析出され、該種結晶上では、次いで負熱膨張率を有する結晶相が成長し、例えば高温石英混晶、それにβ−ユークリプタイトが挙げられる。 Conventional glass ceramics having a low coefficient of thermal expansion from the composition range Li 2 O—Al 2 O 3 —SiO 2 (LAS—glass ceramics) contain TiO 2 and ZrO 2 as nucleation components. During so-called ceramization (starting glass is converted to glass ceramics) from the starting glass, firstly seed crystals from TiO 2 and ZrO 2 are deposited, and on the seed crystals then have a negative coefficient of thermal expansion. A crystal phase grows, and examples thereof include high-temperature quartz mixed crystals and β-eucryptite.
大規模工業的に重要な、従来の原料が使用される場合、出発ガラスの製造のために、Ｆｅ2Ｏ3が出発ガラスひいてはガラスセラミックス中に取り込まれることは避けることができない。さらに、大規模工業的な溶融プラントにおいて通例のカレットサイクル(Scherbenkreislauf)は鉄汚染を必然的に伴う。 When conventional raw materials that are industrially important on a large scale are used, it is inevitable that Fe 2 O 3 is incorporated into the starting glass and thus into the glass ceramics for the production of the starting glass. Furthermore, the usual cullet cycle (Scherbenkreislauf) in large industrial melting plants necessarily involves iron contamination.
ガラス中でＦｅ2Ｏ3とＴｉＯ2との間で、専門文献中ではおよそ大体に"イルメナイト複合体"とも称される近距離秩序における相互作用が生じることは久しい以前から公知である。このＦｅ−Ｔｉ複合体により、透明な出発ガラス及び透明なガラスセラミックスにおいて黄色ないし褐色に色が変わる。 It has been known for a long time that an interaction in the short-range order occurs between Fe 2 O 3 and TiO 2 in glass, which is roughly referred to in the specialist literature as an “ilmenite complex”. The Fe—Ti composite changes the color from yellow to brown in the transparent starting glass and the transparent glass ceramic.
透明なガラスセラミックスの製造に際しては、この複合体形成を避けることが重要性をもつ。高価な、特別に精製された原料の使用及びカレット返送(Scherbenrueckfuehrung)を省くことによってＦｅ2Ｏ3の供給を減少ないし回避することができる。核生成成分ＴｉＯ2を省くことで、新しい、代替的な核生成剤の酸化物を探し求める必要性が生じる。 In the production of transparent glass ceramics, it is important to avoid this complex formation. The supply of Fe 2 O 3 can be reduced or avoided by eliminating the use of expensive, specially refined raw materials and the return of cullet (Scherbenrueckfuehrung). By omitting the nucleation component TiO 2 , there is a need to search for new, alternative nucleation agent oxides.
さらに、ガラスセラミックスの製造に際して、例えばＡｓ2Ｏ3のような毒性成分が省かれるべきである。そのため、代替的な清澄剤も見出されなければならない。 Furthermore, in the production of glass ceramics, toxic components such as As 2 O 3 should be omitted. Therefore, alternative fining agents must be found.
このことから出発して、本発明の課題は、上述の欠点を有さない透明なガラスセラミックスを提供することである。 Starting from this, the object of the present invention is to provide a transparent glass ceramic which does not have the above-mentioned drawbacks.
該課題は、請求項１に従って、以下の組成（酸化物ベースに基づき質量％で記載）を有する透明なガラスセラミックスを提供することである：
ＳｉＯ2：６５〜７２、殊に６５以上７２未満
Ａｌ2Ｏ3：１８〜２４
Ｌｉ2Ｏ：２〜５
ＭｇＯ：０〜４
ＺｎＯ：０〜４
ＺｎＯ＋ＭｇＯ：２．２未満
ＺｒＯ2：１〜５
ＳｎＯ2：０．５超え４未満
Ｎａ2Ｏ：０〜１．５
Ｋ2Ｏ：０〜１．５
ＢａＯ：０〜４
Ｆｅ2Ｏ3：０〜０．１。
The object is to provide a transparent glass ceramic according to claim 1 having the following composition (described in mass% based on oxide base):
SiO 2 : 65 to 72, especially 65 or more and less than 72 Al 2 O 3 : 18 to 24
Li 2 O: 2 to 5
MgO: 0-4
ZnO: 0-4
ZnO + MgO: less than 2.2 ZrO 2 : 1 to 5
SnO 2 : more than 0.5 and less than 4 Na 2 O: 0 to 1.5
K 2 O: 0 to 1.5
BaO: 0-4
Fe 2 O 3: 0~0.1.
好ましくは、以下の組成成分の少なくとも１つの含有率（酸化物ベースに基づき質量％で記載）は、
ＳｉＯ2：６６〜７２，殊に６６以上７２未満
ＭｇＯ：０〜３．５、殊に０〜３
ＺｎＯ：０〜３．５、殊に０〜３
ＺｒＯ2：１．６〜５
の範囲にある。
Preferably, the content of at least one of the following composition components (described in mass% based on oxide base):
SiO 2 : 66 to 72, especially 66 to less than 72 MgO: 0 to 3.5, especially 0 to 3
ZnO: 0 to 3.5, especially 0 to 3
ZrO 2 : 1.6-5
It is in the range.
さらに、本発明によるガラスセラミックスは、以下の組成成分を質量％で含有してよい：
ＣａＯ：０〜１
ＳｒＯ：０〜２
Ｆ：０〜１
Ｂ2Ｏ3：０〜１。
Furthermore, the glass ceramic according to the present invention may contain the following composition components in mass%:
CaO: 0 to 1
SrO: 0-2
F: 0 to 1
B 2 O 3: 0~1.
意想外にも、計２．２質量％未満のＭｇＯ及びＺｎＯの低い含有率を有する透明なガラスセラミックスが、従来技術と比較して特に高い透明性を示すことが見出された。 Surprisingly, it has been found that transparent glass ceramics having a low content of MgO and ZnO of less than 2.2% by weight in total show a particularly high transparency compared to the prior art.
二相材料における高い透明性は、結晶子の大きさ、相含量並びに屈折率の違いに本質的に依存する散乱効果の最小化によって達成される。 High transparency in biphasic materials is achieved by minimizing scattering effects that depend essentially on crystallite size, phase content, and refractive index differences.
さらに意想外にも、成分ＭｇＯ及びＺｎＯの全含有率（酸化物ベースに基づき質量％で記載）のＬｉ2Ｏ含有率（酸化物ベースに基づき質量％で記載）に対する比率が最大１、殊に最大０．７５であるガラスセラミックスが、従来技術と比較して特に高い透明性及び低い固有色を示すことが見出された。特に有利には、該比率は０．４〜０．７５の範囲にある。 Furthermore, surprisingly, the ratio of the total content of components MgO and ZnO (denoted in mass% based on oxide base) to the Li 2 O content (denoted in mass% based on oxide base) is at most 1, in particular It has been found that glass ceramics with a maximum of 0.75 exhibit particularly high transparency and low intrinsic color compared to the prior art. The ratio is particularly preferably in the range from 0.4 to 0.75.
好ましくは、本発明によるガラスセラミックスは、少なくとも０．５質量％のＺｎＯ、殊に少なくとも１質量％のＺｎＯを含有する。本質的にＺｎＯを含まない組成物の場合、いくらかより悪化した透過率の結果が得られた。 Preferably, the glass ceramic according to the invention contains at least 0.5% by weight of ZnO, in particular at least 1% by weight of ZnO. For compositions essentially free of ZnO, somewhat worse transmission results were obtained.
好ましくは、本発明によるガラスセラミックスは、避けることのできない痕跡量を除きＡｓ2Ｏ3、Ｓｂ2Ｏ3、ＴｉＯ2及び／又はＰ2Ｏ5を含まない。 Preferably, the glass ceramic according to the invention does not contain As 2 O 3 , Sb 2 O 3 , TiO 2 and / or P 2 O 5 except for traces which are unavoidable.
さらに、ガラスセラミックスは、好ましくは、熱膨張率ＣＴＥ（２０〜７００℃）４ｐｐｍ未満、有利には３ｐｐｍ未満及び特に有利には２ｐｐｍ未満を有する。 Furthermore, the glass ceramic preferably has a coefficient of thermal expansion CTE (20-700 ° C.) of less than 4 ppm, preferably less than 3 ppm and particularly preferably less than 2 ppm.
好ましくは、光の可視領域中（３８０〜７８０ｎｍ）での光透過率は、ガラスセラミックスの試料厚さ４ｍｍの場合に、少なくとも８７％、有利には少なくとも８７．５％及び特に有利には少なくとも８８％である。 Preferably, the light transmittance in the visible region of light (380-780 nm) is at least 87%, preferably at least 87.5% and particularly preferably at least 88 for a glass ceramic sample thickness of 4 mm. %.
ガラスセラミックスの三刺激値(Farbwert)Ｃ*は、好ましくは３未満である。 The tristimulus value C * of the glass ceramic is preferably less than 3.
ガラスセラミックスのさらなる有利な実施形態において、核生成剤の酸化物ＳｎＯ2及びＺｒＯ2の合計は少なくとも３質量％である。 In a further advantageous embodiment of the glass ceramic, the sum of the nucleating agent oxides SnO 2 and ZrO 2 is at least 3% by weight.
ＴｉＯ2の代替物として、好ましくはＳｎＯ2が核生成剤の酸化物としてＺｒＯ2に加えて使用される。その際、ＳｎＯ2は清澄剤としても作用する。 As an alternative to TiO 2 , SnO 2 is preferably used in addition to ZrO 2 as the nucleating agent oxide. At that time, SnO 2 also acts as a fining agent.
ＳｎＯ2に加えて、核生成作用を示すさらに別の成分、例えばＴａ2Ｏ3、Ｎｂ2Ｏ3も使用することができ、その際、これらの成分はたいてい相対的に高価である。 In addition to SnO 2 , further components exhibiting a nucleation effect can be used, for example Ta 2 O 3 , Nb 2 O 3 , with these components usually being relatively expensive.
たいてい高められたＦｅ2Ｏ3含有率を有する、より低コストの原料も使用することができる方法は、経済的に好ましい。 Processes that can also use lower cost raw materials, usually with increased Fe 2 O 3 content, are economically preferred.
本発明によるガラスセラミックスは、コーティング又は装飾されることができる。 The glass ceramics according to the invention can be coated or decorated.
本発明によるガラスセラミックスを目的に合わせて着色するために、着色成分、例えばＶ2Ｏ5、ＮｉＯ、ＣｕＯ、Ｃｒ2Ｏ3、ＣｅＯ2、ＭｎＯ2、ＷＯ3、ＭｏＯ3及び／又はＮｄ2Ｏ3を溶融ガラスに出発ガラスの製造のために付け加えてよい。 In order to color the glass ceramics according to the invention for the purpose, coloring components such as V 2 O 5 , NiO, CuO, Cr 2 O 3 , CeO 2 , MnO 2 , WO 3 , MoO 3 and / or Nd 2 O 3 may be added to the molten glass for the production of the starting glass.
さらに、成分、例えばＬａ2Ｏ3、Ｙ2Ｏ3、ＧｅＯ2及び／又はＧｄ2Ｏ3を溶融ガラスに添加してよく、これらは結果生じるガラスセラミック中の残りのガラス相の屈折率を上げる。 In addition, components such as La 2 O 3 , Y 2 O 3 , GeO 2 and / or Gd 2 O 3 may be added to the molten glass, which increases the refractive index of the remaining glass phase in the resulting glass ceramic. .
溶融ガラスは、公知の清澄剤により、殊にＣｅＯ2、硫黄化合物及び／又は塩化物により精製されることができる。有利な実施形態において、ガラスセラミックスの製造のために環境にとって有害な成分は使用されない。 Molten glass can be refined with known fining agents, in particular with CeO 2 , sulfur compounds and / or chlorides. In an advantageous embodiment, no components harmful to the environment are used for the production of glass ceramics.
透明なガラスセラミックスは、セラミックス化中の滞留時間の延長及び／又は温度の上昇によって半透明のガラスセラミックスに、そして熱処理をさらに行った場合には不透明のガラスセラミックスに変えられることができる。 Transparent glass ceramics can be converted to translucent glass ceramics by extending the residence time and / or increasing the temperature during ceramization and to opaque glass ceramics if further heat treatment is performed.
本発明によるガラスセミラックスは、様々な適用分野からの製品、例えば、調理面、暖炉覗き窓(Kaminsichtsscheiben)及びオーブン覗き窓(Backofensichtsscheiben)用に、例えば、熱分解炉床(Pyrolyseherden)、建築ガラス窓及び安全ガラス窓においても、例えば、高動的、機械的な負荷に対する防護ガラスといった防火のためにも使用されることができる。さらに、本発明によるガラスセラミックスは、衝撃、弾丸、破片又は衝風の影響から保護するための装置の一部として、防火ガラス窓の一部として、暖炉覗き窓として、調理領域用のガラスとして、半導体材料又は磁気ディスク(Magnetspeicherplatte)用の基板として使用されることができる。 The glass semi-lux according to the invention is used for products from various applications, for example cooking surfaces, fireplace sights (Kaminsichtsscheiben) and oven sights (Backofensichtsscheiben), e.g. Pyrolyseherden, architectural glass windows. And in safety glass windows, it can also be used for fire protection, eg protective glass against high dynamic, mechanical loads. Furthermore, the glass ceramic according to the present invention is used as a part of a device for protecting from impacts, bullets, debris or blast effects, as a part of a fireproof glass window, as a fireplace viewing window, as a glass for cooking areas, It can be used as a substrate for semiconductor materials or magnetic disks.
第１表は、本発明によるガラスセラミックの例１〜２２を示す（酸化物ベースに基づく質量％記載の組成）。 Table 1 shows Examples 1-22 of glass ceramics according to the present invention (composition according to mass% based on oxide base).
第２表は、本発明によらないガラスセラミックスの比較例２３〜３２を示す（酸化物ベースに基づく質量％記載の組成）。 Table 2 shows Comparative Examples 23 to 32 of glass ceramics not according to the present invention (composition according to mass% based on oxide base).
実施例及び比較例の製造：
出発ガラスを、市販の原料から、殊に酸化物、炭酸塩及び／又は硝酸塩から、セラミックスるつぼ材料中で約１６４０℃にて溶融した。溶融した材料を、精製し、均質化し、その後に注ぎ出し、場合により高温成形（例えばローラー法、フロート法、引き抜き法）し、かつ冷却した。
Production of Examples and Comparative Examples:
The starting glass was melted at about 1640 ° C. in a ceramic crucible material from commercially available raw materials, in particular from oxides, carbonates and / or nitrates. The molten material was purified, homogenized and then poured out, optionally hot-molded (eg roller method, float method, drawing method) and cooled.
ガラスセラミックスの製造のために、核生成温度Ｔ（ＫＢ）での核生成のための約１時間継続する第一の段階と、より高い温度Ｔ（ＭＡＸ）での約１５分の結晶成長期の第二の段階とから成る、出発ガラスのセラミックス化の２段階のプロセスを適用した。 For the production of glass ceramics, a first stage lasting about 1 hour for nucleation at a nucleation temperature T (KB) and a crystal growth period of about 15 minutes at a higher temperature T (MAX) A two-stage process of ceramization of the starting glass, consisting of a second stage, was applied.
１００ｍｍの長さのガラスセラミックスバーの２０℃から７００℃の熱膨張係数（ＣＴＥ）の測定を、膨張計を使って行った。 Measurement of the coefficient of thermal expansion (CTE) from 20 ° C. to 700 ° C. of a glass ceramic bar having a length of 100 mm was performed using an dilatometer.
透過率の測定のために、ガラスセラミックスを４ｍｍの厚さに切り取り、かつ研磨した。測定は光源Ｃ／２゜で行った。光透過率τVis及び三刺激値Ｃ*の表示は、ＤＩＮ ５０３３もしくはＤＩＮ ＥＮ ４１０に従って行った。Ｃ*は、その際、彩度(Farbsaettigung)（クロマ、彩色性）を表示する：
ＣＩＥＬＡＢ色空間内の係数は、色印象に相当する：
ａ*は、緑−赤軸の色座標の位置を表示し、その際、負の値は緑色の色調に相当し、かつ正の値は赤色の色調に相当する。
ｂ*は、青−黄軸の色座標の位置を表示し、その際、負の値は青色の色調に相当し、かつ正の値は黄色の色調に相当する。
The coefficients in the CIELAB color space correspond to the color impression:
a * indicates the position of the color coordinate of the green-red axis, where a negative value corresponds to a green color tone and a positive value corresponds to a red color tone.
b * indicates the position of the color coordinate of the blue-yellow axis, where a negative value corresponds to a blue color tone and a positive value corresponds to a yellow color tone.
ガラスセラミックスの結晶相、結晶相含有率（Ｋｒ．ｐｈ．）［体積％］及びガラスセラミックスの平均結晶子サイズｄ50を、公知技術のＸ線回折分析（ＸＲＤ、デバイ・シェラー法（Debeye-Scherrer Verfahren)）によって調べた。 The crystal phase of the glass ceramic, the crystal phase content (Kr.ph.) [volume%], and the average crystallite size d 50 of the glass ceramic were measured by X-ray diffraction analysis (XRD, Debeye-Scherrer method of the known art). Verfahren)).
Claims (8)
ＳｉＯ2：６５〜７２
Ａｌ2Ｏ3：１８〜２４
Ｌｉ2Ｏ：２〜５
ＭｇＯ：０〜４
ＺｎＯ：０〜４
ＺｎＯ＋ＭｇＯ：２．２未満
ＺｒＯ2：１〜５
ＳｎＯ2：０．５超え４未満
Ｎａ2Ｏ：０〜１．５
Ｋ2Ｏ：０〜１．５
ＢａＯ：０〜４
Ｆｅ2Ｏ3：０〜０．１
を酸化物ベースに基づき質量％で有し、Ｌｉ2Ｏに対するＭｇＯ＋ＺｎＯの質量比が、０．４〜０．７５の範囲にあり、かつ不可避の痕跡量を除きＡｓ 2 Ｏ 3 を含まないことを特徴とする、ガラスセラミックス。 In the glass ceramic, the glass ceramic has at least the following composition:
SiO 2: 65~72
Al 2 O 3 : 18-24
Li 2 O: 2 to 5
MgO: 0-4
ZnO: 0-4
ZnO + MgO: less than 2.2 ZrO 2 : 1 to 5
SnO 2 : more than 0.5 and less than 4 Na 2 O: 0 to 1.5
K 2 O: 0 to 1.5
BaO: 0-4
Fe 2 O 3 : 0 to 0.1
The has in weight percent based on the oxide basis, the weight ratio of MgO + ZnO for Li 2 O is in the range near the 0.4 to 0.75 is, and does not contain As 2 O 3 except for trace amounts of unavoidable Glass ceramics characterized by
ＣａＯ：０〜１
ＳｒＯ：０〜２
Ｆ：０〜１
Ｂ2Ｏ3：０〜１
を質量％で有することを特徴とする、請求項１に記載のガラスセラミックス。 The glass ceramic additionally has the following composition components:
CaO: 0 to 1
SrO: 0-2
F: 0 to 1
B 2 O 3 : 0 to 1
The glass ceramic according to claim 1, characterized by comprising:
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| DE102010036192 | 2010-09-02 | ||
| DE102010036192.5 | 2010-09-02 |
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| JP (1) | JP5787671B2 (en) |
| DE (1) | DE102011107831B4 (en) |
| FR (1) | FR2964378B1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| ES2444740B2 (en) * | 2013-11-13 | 2014-09-02 | Esmalglass, Sau | Translucent hob structure albite structure |
| FR3088321B1 (en) * | 2018-11-09 | 2021-09-10 | Eurokera | LOW LITHIUM TRANSPARENT QUARTZ-BETA VITROCERAMICS |
| DE102020202597A1 (en) | 2020-02-28 | 2021-09-02 | Schott Ag | Cooking surface made from a LAS glass ceramic plate |
| JP2023092780A (en) * | 2021-12-22 | 2023-07-04 | 日本電気硝子株式会社 | Li2O-Al2O3-SiO2 CRYSTALLIZED GLASS |
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| JPH0696460B2 (en) * | 1989-06-19 | 1994-11-30 | 日本板硝子株式会社 | Low expansion transparent crystallized glass |
| JP2005289790A (en) * | 2004-03-12 | 2005-10-20 | Nippon Electric Glass Co Ltd | Crystallized glass and device for optical communications using the same |
| JP2006193398A (en) * | 2005-01-17 | 2006-07-27 | National Institute Of Advanced Industrial & Technology | Crystallized glass, optical device and etalon |
| FR2909373B1 (en) * | 2006-11-30 | 2009-02-27 | Snc Eurokera Soc En Nom Collec | TRANSPARENT AND COLORLESS BETA-QUARTZ GLAZE, FREE OF TIO2; ARTICLES THEREOF VITROCERAMIC; PRECURSOR GLASSES, METHODS OF PREPARATION. |
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2011
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| FR2964378A1 (en) | 2012-03-09 |
| JP2012051786A (en) | 2012-03-15 |
| DE102011107831B4 (en) | 2016-08-18 |
| FR2964378B1 (en) | 2017-01-20 |
| DE102011107831A1 (en) | 2012-03-08 |
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