JPS63195147A - Optical fiber - Google Patents
Optical fiberInfo
- Publication number
- JPS63195147A JPS63195147A JP62027350A JP2735087A JPS63195147A JP S63195147 A JPS63195147 A JP S63195147A JP 62027350 A JP62027350 A JP 62027350A JP 2735087 A JP2735087 A JP 2735087A JP S63195147 A JPS63195147 A JP S63195147A
- Authority
- JP
- Japan
- Prior art keywords
- core
- optical fiber
- refractive index
- glass
- added
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 239000013307 optical fiber Substances 0.000 title claims abstract description 31
- 239000011521 glass Substances 0.000 claims abstract description 29
- 229910052731 fluorine Inorganic materials 0.000 claims abstract description 14
- 229910052744 lithium Inorganic materials 0.000 claims abstract description 4
- 238000005253 cladding Methods 0.000 claims description 16
- 239000011737 fluorine Substances 0.000 claims description 10
- PXGOKWXKJXAPGV-UHFFFAOYSA-N Fluorine Chemical compound FF PXGOKWXKJXAPGV-UHFFFAOYSA-N 0.000 claims 1
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract description 31
- 235000012239 silicon dioxide Nutrition 0.000 abstract description 17
- 229910052681 coesite Inorganic materials 0.000 abstract description 3
- 229910052906 cristobalite Inorganic materials 0.000 abstract description 3
- 239000000377 silicon dioxide Substances 0.000 abstract description 3
- 229910052682 stishovite Inorganic materials 0.000 abstract description 3
- 229910052905 tridymite Inorganic materials 0.000 abstract description 3
- YCKRFDGAMUMZLT-UHFFFAOYSA-N Fluorine atom Chemical compound [F] YCKRFDGAMUMZLT-UHFFFAOYSA-N 0.000 description 9
- 239000010453 quartz Substances 0.000 description 6
- 230000003287 optical effect Effects 0.000 description 5
- 238000002425 crystallisation Methods 0.000 description 4
- 230000008025 crystallization Effects 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 150000004703 alkoxides Chemical class 0.000 description 3
- 230000009477 glass transition Effects 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- 238000010521 absorption reaction Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- QQGISFDJEJMKIL-JAIQZWGSSA-N (5z)-5-[[3-(hydroxymethyl)thiophen-2-yl]methylidene]-10-methoxy-2,2,4-trimethyl-1h-chromeno[3,4-f]quinolin-9-ol Chemical compound C1=CC=2NC(C)(C)C=C(C)C=2C2=C1C=1C(OC)=C(O)C=CC=1O\C2=C/C=1SC=CC=1CO QQGISFDJEJMKIL-JAIQZWGSSA-N 0.000 description 1
- VZSRBBMJRBPUNF-UHFFFAOYSA-N 2-(2,3-dihydro-1H-inden-2-ylamino)-N-[3-oxo-3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propyl]pyrimidine-5-carboxamide Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C(=O)NCCC(N1CC2=C(CC1)NN=N2)=O VZSRBBMJRBPUNF-UHFFFAOYSA-N 0.000 description 1
- VHUUQVKOLVNVRT-UHFFFAOYSA-N Ammonium hydroxide Chemical compound [NH4+].[OH-] VHUUQVKOLVNVRT-UHFFFAOYSA-N 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- KZBUYRJDOAKODT-UHFFFAOYSA-N Chlorine Chemical compound ClCl KZBUYRJDOAKODT-UHFFFAOYSA-N 0.000 description 1
- WHXSMMKQMYFTQS-UHFFFAOYSA-N Lithium Chemical compound [Li] WHXSMMKQMYFTQS-UHFFFAOYSA-N 0.000 description 1
- QGZKDVFQNNGYKY-UHFFFAOYSA-N ammonia Natural products N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 1
- JZKFIPKXQBZXMW-UHFFFAOYSA-L beryllium difluoride Chemical compound F[Be]F JZKFIPKXQBZXMW-UHFFFAOYSA-L 0.000 description 1
- 229910001633 beryllium fluoride Inorganic materials 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000002019 doping agent Substances 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 238000001914 filtration Methods 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 238000001879 gelation Methods 0.000 description 1
- 239000003365 glass fiber Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 239000011859 microparticle Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000003980 solgel method Methods 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
- 238000001132 ultrasonic dispersion Methods 0.000 description 1
- 238000004017 vitrification Methods 0.000 description 1
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野コ
本発明は低損失な光ファイバに関し、特にガラスの固有
損失であるレーリ散乱損失が小さく、しかも安定性にす
ぐれた光ファイバに関するものである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a low-loss optical fiber, and more particularly to an optical fiber that has low Rayleigh scattering loss, which is an inherent loss of glass, and has excellent stability.
［従来の技術］
光ファイバは、低損失であること、ガラスとしての安定
性にすぐれること等から石英系ガラスを中心として発展
し、現在は、０．２ｄ［１７８ｍ以下の光損失も実現さ
れている０石英系ガラスファイバでは導波構造を形成す
るため、ＧｅＯ＊、ＰｚＯｓ等、Ｓ１０□の屈折率を増
加させるドーパントをコア部に添加するか逆にＦ、［１
，０，のように５ｉｏ２の屈折率を低下させるドーパン
トをクラッドに添加することにより屈折率分布を形成し
ている。[Prior art] Optical fibers have been developed mainly using silica glass because of their low loss and excellent stability as glass, and currently optical fibers with optical losses of less than 0.2 d [178 m] have been realized. In order to form a waveguide structure in the 0 silica glass fiber, a dopant that increases the refractive index of S10□, such as GeO* or PzOs, is added to the core part, or conversely, F, [1
, 0, etc., which lowers the refractive index of 5io2, is added to the cladding to form a refractive index distribution.
０．２ｄＤ／ｋｍ以下の光損失は、純石英系ガラスをコ
アにして製造されている。これはガラスが有している固
有損失要因（紫外吸収、赤外吸収、レーリ散乱）のうち
レーり散乱が光損失の最低値を決める主要因であること
に起因している。すなわち、純石英系ガラスの固有レー
り散乱値が低いことに対応している。このためより低い
光損失値を実現するには純石英ガラスよりもさらに低い
レーリ散乱値を有するガラスをコアにする必要がある。Optical loss of 0.2 dD/km or less is manufactured using pure silica glass as a core. This is because among the inherent loss factors (ultraviolet absorption, infrared absorption, Rayleigh scattering) possessed by glass, Rayleigh scattering is the main factor that determines the lowest value of optical loss. In other words, this corresponds to the low intrinsic Ray scattering value of pure silica glass. Therefore, in order to achieve a lower optical loss value, it is necessary to use glass having a lower Rayleigh scattering value than pure silica glass as the core.
レーリ散乱係数α１は、次の式であられされる。The Rayleigh scattering coefficient α1 is expressed by the following formula.
ａ 、 ｍ −ｒｔ ３（ｎ ” −１） ”ＢＫＴｇ
ｎ：屈折率
Ｂ：等温圧縮率
に：ボルツマン定数
Ｔ８ニガラス転穆温度
レーリ散乱係数を石英系ガラスよりも低い値にするため
には、上式において屈折率（ｎ）９等温圧縮率（Ｂ）お
よびガラス転移温度（Ｔｇ）が石英よりも小さなガラス
系を選択することが必要にな−ってくる。a, m -rt 3(n''-1)''BKTg
n: Refractive index B: Isothermal compressibility: Boltzmann constant T8 Nigaras inversion temperature In order to make the Rayleigh scattering coefficient a value lower than that of silica glass, in the above equation, refractive index (n) 9 Isothermal compressibility (B) It is also necessary to select a glass whose glass transition temperature (Tg) is lower than that of quartz.
［発明が解決しようとする問題点］
本発明は、石英ガラスと同等か、それより低い屈折率を
有するＳｉＯ２を主成分とするガラスをコアに用いた光
ファイバを実現し、より低損失化を可能とすることを目
的とする。[Problems to be Solved by the Invention] The present invention realizes an optical fiber whose core is made of glass whose main component is SiO2, which has a refractive index equal to or lower than that of quartz glass, and which achieves lower loss. The purpose is to make it possible.
［問題点を解決するための手段］
このような目的を達成するために、本発明は屈折率の高
いコアと、コアより低い屈折率のクラッドからなる５ｉ
ｏ２を主成分とする光ファイバにおいて、コアの屈折率
がＳｉＯ２の屈折率より大きくなく、コアおよびクラッ
ドの少なくとも一方を構成するガラスがＳｉよりも小さ
な原子量を有する元素である八ｆｔ 、Ｍｇ、Ｎａ、Ｂ
ｅ、Ｌｉのうちの少なくとも一種とフッ素とを同時に添
加したＳｔＯ，ガラスからなることを特徴とする。[Means for Solving the Problems] In order to achieve such an object, the present invention provides a 5i core consisting of a core with a high refractive index and a cladding with a refractive index lower than that of the core.
In an optical fiber mainly composed of O2, the refractive index of the core is not greater than the refractive index of SiO2, and the glass constituting at least one of the core and the cladding is an element having an atomic weight smaller than Si, Mg, Na. , B
It is characterized by being made of StO and glass to which at least one of e and fluorine and at least one of lithium and fluorine are added simultaneously.
［作用］
本発明によれば、Ｓｔより軽い元素とフッ素とを同時に
添加した石英ガラスをコアまたはクラッドに用いて光フ
ァイバを４’ｌ成するので、光ファイバの屈折率、ガラ
ス転移温度が小さいため、固有散乱損失であるレーり散
乱を小さく、従来の光ファイバより光損失値の低い光フ
ァイバが得られる。[Function] According to the present invention, since the optical fiber is formed by using quartz glass to which an element lighter than St and fluorine are simultaneously added for the core or cladding, the refractive index and glass transition temperature of the optical fiber are small. Therefore, it is possible to obtain an optical fiber with low Ley scattering, which is an inherent scattering loss, and a lower optical loss value than conventional optical fibers.
このようにＳｉよりも軽い元素を添加すると、５ｉｏ２
ガラスよりも小さなレーリ散乱が得られる理由は、以下
のように考えられる。When an element lighter than Si is added in this way, 5io2
The reason why Ley scattering is smaller than that of glass is thought to be as follows.
レーリ散乱は、高温時に存在する統計力学的ゆらぎが低
温まで凍結されたものであるが、本発明が対象とする多
成分系では組成変動および密度変動に起因するゆらぎが
あり、これが屈折率のゆらぎとしてレーり散乱をひき起
こしている０例えば、Ｓｉｎ、に添加した時、Ｓｔより
も重い元素は、１原子当りの屈折率への寄与も大きく同
じ組成変動に対して、より大きなゆらぎを与えることに
なる。従って、Ｓｉよりも軽い元素が、小さなレーリ散
乱を示すのは、密度０組成両方に依存する散乱が減少す
るためで、屈折率、ガラス転Ｂ温度等とあわせて考える
と、うなずけるところである。Rayleigh scattering is the result of statistical mechanical fluctuations that exist at high temperatures frozen down to low temperatures, but in the multicomponent system targeted by this invention, there are fluctuations due to compositional fluctuations and density fluctuations, which are caused by fluctuations in the refractive index. For example, when added to Sin, an element heavier than St makes a large contribution to the refractive index per atom and gives a larger fluctuation for the same composition variation. become. Therefore, the reason why elements lighter than Si exhibit small Rayleigh scattering is because the scattering that depends on both density and composition is reduced, which makes sense when considered together with the refractive index, glass transition B temperature, etc.
［実施例］ 以下に本発明の実施例を詳細に説明する。[Example] Examples of the present invention will be described in detail below.
夾直週ユ
５ｔ（ＯＣｚＨｓ）＜をアルコールで希釈した溶液に、
０．０１ｍｏｆ！、〜０．１ｍｏＪ２／ １１の濃度の
アンモニア水を１１□ｏ７ｓ ｉモル比が約４になるよ
うに添加して加水分解し、アルコール溶媒の沸点以下の
温度約６０〜８０℃に保持して、比表面積２００〜３Ｑ
Ｑｍ’／ｇの微粒子を含有するＳ１０．ゾル溶液を準備
した。これにアルコールで希釈した八りのアルコキシド
八ｆＬ （ＯＣｌｌｈ）コまたは八ｆＬ（ＯＣ４１１９
）３を添加し、さらに希釈したＳｉ （ＯＣ２１１１１
） ３Ｆを添加した。八１の添加量は＾１２０ｓの５ｉ
ｎ２に対するモル比として３モル％以下であり、Ｆの添
加量はＦ／Ｓｉ＝ ０．０７ （モル比）である。In a solution diluted with alcohol,
0.01mof! , ~0.1 moJ2/11 aqueous ammonia is added so that the molar ratio of 11□o7s i is about 4, and the mixture is hydrolyzed and maintained at a temperature of about 60 to 80 °C below the boiling point of the alcohol solvent. Specific surface area 200~3Q
S10. containing fine particles of Qm'/g. A sol solution was prepared. Add to this alkoxide diluted with alcohol, 8 fL (OCllh) or 8 fL (OC4119).
)3 and further diluted Si (OC21111
) 3F was added. The amount of addition of 81 is ^120s of 5i
The molar ratio to n2 is 3 mol% or less, and the amount of F added is F/Si=0.07 (molar ratio).
このゾルを、温度６０℃でロッド状にゲル化させ、引き
続き乾燥、高温ガラス化して透明なガラスロッドな得た
。This sol was gelatinized into a rod shape at a temperature of 60° C., followed by drying and high temperature vitrification to obtain a transparent glass rod.
第１図にこのようなガラスの比屈折率差（Δｎ（％））
をＡｌ１の添加量に対して示した。Δｎは、純石英ガラ
スを標準にして、空間フィルタリング法で測定したもの
である。八１の添加は、屈折率を増加させるため、Ａ１
添加量が増大するにしたがって−０，３％からプラスの
値までΔｎが変化していくことがわかる。このガラスロ
ッドのうち、Δｎがほぼ純石英と一致する組成（第１図
では、Δｆ１２０３２．９モル％、 Ｆ／５ｉ−０，０
７）のガラスを用い、その外周にＶＡＤ法でＦ添加Ｓ１
０．ガラスを形成して、光フアイバ母材とした。第２図
にこの母材の屈折率分布を示す。Figure 1 shows the relative refractive index difference (Δn (%)) of such glasses.
is shown with respect to the amount of Al1 added. Δn is measured using a spatial filtering method using pure silica glass as a standard. The addition of A1 increases the refractive index.
It can be seen that as the amount added increases, Δn changes from -0.3% to a positive value. This glass rod has a composition in which Δn almost matches that of pure quartz (in Figure 1, Δf12032.9 mol%, F/5i-0,0
Using the glass of 7), F addition S1 is applied to the outer periphery using the VAD method.
0. A glass was formed to serve as an optical fiber matrix. Figure 2 shows the refractive index distribution of this base material.
カーボン炉を用いて、約２０００℃に加熱し、母材の線
引きを行りた。純石英コア光ファイバ（フッ素ドープ石
英クラッド）を別に用意し、波長０．６３μｍ（Ｈｅ−
Ｎｅレーザ）において散乱損失を評価したところ、純石
英コアを１として約０．８の値が得られた。また（波長
）−４に対して損失をプロットし、レーリ散乱損失を求
めたところ、レーリ係数が、純石英コアの場合の約８０
％に減少していることがわかった。Using a carbon furnace, the base material was heated to approximately 2000°C and wire-drawn. A pure silica core optical fiber (fluorine-doped quartz cladding) was prepared separately, and a wavelength of 0.63 μm (He-
When the scattering loss was evaluated using a Ne laser), a value of about 0.8 was obtained, with the pure quartz core being 1. In addition, when the loss was plotted against (wavelength) -4 and the Rayleigh scattering loss was determined, the Rayleigh coefficient was approximately 80 for the pure silica core.
It was found that it decreased by %.
立直■ユ
実施例１と同様にして作製した５ｔ０２ゾル溶液に八１
のアルコキシドＡＪ！ （ＯＣＪｅ）コ、 Ｎａのアル
コキシドＮａ（ＯＣｚｌｌｓ）およびＳＬ （ＯＣ２Ｈ
８） ｓＦを添加し、ＳｉＯ２−八ＩＬｚｏ３− Ｎａ
２ＯＦ系ガラス（＾Ａ 、０． （２モル％） 、 Ｎ
ａ２０（１モル％） 、 Ｆ／５ｉ＝０．０７）を作製
した。 Ｎａを添加することにより、 ＡＪ！２０ｓ添
加の時、よく見られる結晶化が抑制され、ガラスとして
の安定性が増加した。Δｎは、Ｆ添加により、はぼΔｎ
αＯの値となった。このガラスをコアに光ファイバを作
製した。 Ｎａ、Ｏの添加は、屈折率を増加する。ここ
でｌ ２０３は３モル％以下の量であるが、結晶化の抑
制には、Ｎａ、ＯＯ，１モル％でも効果が現われ、はぼ
＾１２０．とほぼ等しいモルまで、この効果は続くこと
がわかった。Ｎａの代わりにＬｌ、 Ｍｇを用いても同
様に安定なガラスになり、光ファイバを作製することが
できた。81 was added to the 5t02 sol solution prepared in the same manner as in Example 1.
Alkoxide AJ! (OCJe), Na alkoxides Na (OCzlls) and SL (OC2H
8) Add sF, SiO2-8ILzo3-Na
2OF glass (^A, 0. (2 mol%), N
a20 (1 mol%), F/5i=0.07) was prepared. By adding Na, AJ! When added for 20 seconds, crystallization, which is often seen, was suppressed and stability as a glass increased. By adding F, Δn becomes almost Δn
It became the value of αO. An optical fiber was fabricated using this glass as a core. Addition of Na and O increases the refractive index. Here, the amount of l203 is 3 mol% or less, but even 1 mol% of Na, OO, and 1 mol% are effective in suppressing crystallization. It was found that this effect lasts up to a molar value approximately equal to . Even if Ll or Mg was used instead of Na, a similarly stable glass could be obtained and an optical fiber could be produced.
夫五±ユ
気相で作製した粒子径０．１μｍ以下の＾ＪＺＦ３微粒
子粉末をＳｉｎ、ゾル溶液に添加しくＡｆＬ約３ ｍｏ
ｆ１％）、超音波で分散した後、ゲル化を促進するため
、さらにＳｉ （ＯＣ２１１ｓ） ３Ｆを用いてフッ素
添加（Ｆ１５Ｉ＝ ０．１）を行い、均一なゾルを得た
。これを円柱状の容器に入れてゲル化後、乾燥、高温ガ
ス化して透明なガラスロッドを得た。Δｎは約−０，１
％であった。これをコアに用い、外側にＦ添加石英ガラ
スをＶＡＤ法で形成してクラッドとしくΔｎｗ−０，３
％）、この母材を線引きして光ファイバを得た。実施例
１と同様に０．６３μ雷で散乱（レーリ散乱）を測定１
ノたところ〜純石英コアを１とすると約０．７の値が得
られた。JZF3 microparticle powder with a particle size of 0.1 μm or less prepared in the gas phase was added to the Sin and sol solution at approximately 3 mo AfL.
f1%), and after ultrasonic dispersion, fluorine addition (F15I = 0.1) was further performed using Si (OC211s) 3F to promote gelation to obtain a uniform sol. This was placed in a cylindrical container, gelled, dried, and gasified at high temperature to obtain a transparent glass rod. Δn is approximately -0,1
%Met. This is used as the core, and F-doped silica glass is formed on the outside by VAD method to form the cladding Δnw-0,3
%), this base material was drawn to obtain an optical fiber. Measurement of scattering (Leley scattering) by 0.63 μ lightning as in Example 1 1
As a result, a value of about 0.7 was obtained, assuming that the pure quartz core is 1.
衷五■１
実施例１と同様にして作製した約３００ｍ２７Ｈの比表
面積を有する微粒子を含有するゾル溶液に、水溶液化と
かしたＢｅＦを添加しゲル化を促進するため、さらにア
ルコールで希釈した５ｉ（ＯＣ２１１＠）３Ｆを添加し
てロッド状ゲル体を得た。これを乾燥し、塩素系ガスを
数％含む）Ｉｅガス雰囲気下でガラス化して、透明なガ
ラスロッドを得た。Δｎは−０，１５％であった。Ｂｅ
はＳｉに対して約３モル％となるように添加量を選んで
あるが、フッ素は分解揮発等によ−リ、必ずしも正確な
添加量は求まらなかった。衷五■1 5i ( OC211@)3F was added to obtain a rod-shaped gel body. This was dried and vitrified in an Ie gas atmosphere (containing several percent of chlorine gas) to obtain a transparent glass rod. Δn was −0.15%. Be
The amount of fluorine to be added was selected to be about 3 mol % relative to Si, but the exact amount of fluorine to be added could not always be determined due to decomposition and volatilization.
このガラスロッドにΔｎが約−０，４％になるようにク
ラッド層を形、成して（コアとクラッドの比屈折率差は
、０．２５％である）母材とし、光ファイバに線引きし
た。この光ファイバでもＳｉＯ２コア光フアイバより小
さなレーリ散乱を示すことが確認された。 ５ｉ（ｈに
単独で、Ｌｉ、Ｎａ、Ｍｇ等を添加すると、一般には、
結晶化が起き、光ファイバに線引きできる程の安定なガ
ラスは得られない。Ｂｅも単独ドープでは結晶化を生じ
たが、ＢｅＦ２の形で添加することにより、ファイバ化
が可能になった。これは、ＢｅＦ、が５ｉｏ２と同様の
ネットワーク構造を持つためと推測され、また、５１０
２ガラス中でもＢｅの近傍にＦが存在するためと思われ
る。A cladding layer is formed on this glass rod so that Δn is about -0.4% (the relative refractive index difference between the core and the cladding is 0.25%), and it is used as a base material, and an optical fiber is drawn. did. It was confirmed that this optical fiber also exhibited smaller Rayleigh scattering than the SiO2 core optical fiber. When Li, Na, Mg, etc. are added alone to 5i (h, generally,
Crystallization occurs, and a glass that is stable enough to be drawn into optical fiber cannot be obtained. Although Be alone caused crystallization, addition in the form of BeF2 made it possible to form a fiber. This is presumed to be because BeF has a network structure similar to 5io2, and 510
This is thought to be due to the presence of F in the vicinity of Be in the two glasses.
火族■互
コアを純石英ガラスより構成し、クラッドをΔｎａｍ
−Ｑ 、 ２％とするようにｌとＦの添加量を選択した
。具体的には、八１は約１モル％、Ｆ／Ｓ ｉはモル比
で０．０７である。光は主としてコア部を伝わるが、シ
ングルモード光ファイバであるためパワー分布の広がり
が大きく約２０％のパワーがクラッド部にしみ出してい
ることが考えられる。Fire group: The core is made of pure silica glass, and the cladding is made of Δnam.
The amounts of l and F added were selected so that -Q was 2%. Specifically, 81 is about 1 mol%, and F/S i is 0.07 in molar ratio. Light mainly travels through the core, but since it is a single mode optical fiber, the power distribution is wide and approximately 20% of the power is thought to seep into the cladding.
純石英をコアにフッ素を５７０２に添加したガラスをク
ラッドにする光ファイバのレーり散乱値な１とすると約
０．９５の値が得られた。なお実施例では、コアまたは
クラッドにＳｉよりも小さな原子量を有する元素とフッ
素をコドーブして屈折率分布を形成した光ファイバが小
さなレーリ散乱損失を示すことはもちろんである。If the Ray scattering value of an optical fiber having a pure quartz core and a fluorine-doped glass cladding is 1, then a value of approximately 0.95 was obtained. In the examples, it goes without saying that an optical fiber whose core or cladding is codoped with an element having an atomic weight smaller than Si and fluorine to form a refractive index distribution exhibits a small Rayleigh scattering loss.
Ｓｉより軽い元素＾１ 、Ｍｇ、Ｎａ、Ｂｅ、Ｌｌおよ
びＦ等はＳｉＯ□中に添加することは一般には困難であ
るが、上述した実施例におけるようにゾルゲル法を適用
して、これらの元素を有効に添加することができる。It is generally difficult to add elements lighter than Si^1, Mg, Na, Be, Ll, F, etc. into SiO□, but these elements can be added by applying the sol-gel method as in the above example. can be effectively added.
［発明の効果］
以上説明したように、本発明のＳｔよりも軽い元素とフ
ッ素とを同時に添加した石英ガラスをコアまたはクラッ
ドに用い光ファイバを構成することにより、光フアイバ
用ガラスとしては今まで最も低いレーリ散乱を示すこと
で知られていた純石英ガラスよりも、さらに小さなレー
リ散乱の光ファイバを提供することができる。[Effects of the Invention] As explained above, by constructing an optical fiber by using the quartz glass of the present invention to which an element lighter than St and fluorine are added at the same time for the core or cladding, it is possible to overcome the conventional glass for optical fibers. It is possible to provide an optical fiber with even lower Rayleigh scattering than pure silica glass, which is known to exhibit the lowest Rayleigh scattering.
第１図はフッ素添加量を一定にして、 ＾Ｌの添加量を
変化した場合の比屈折率差の変化を示す図、
第２図は八にとＦを同時にＳｉＯ２に添加したガラスを
コアに、Ｆを５ＸＯ２に添加したガラスをクラッドに光
ファイバを構成した時の屈折率分布を示す図である。Figure 1 shows the change in the relative refractive index difference when the amount of fluorine added is kept constant and the amount of L added is changed. , is a diagram showing the refractive index distribution when an optical fiber is constructed with a cladding made of glass in which 5XO2 is doped with F.
Claims (1)
からなるＳｉＯ＿２を主成分とする光ファイバにおいて
、コアの屈折率がＳｉＯ＿２の屈折率より大きくなく、
前記コアおよびクラッドの少なくとも一方を構成するガ
ラスがＳｉよりも小さな原子量を有する元素であるＡｌ
、Ｍｇ、Ｎａ、Ｂｅ、Ｌｉのうちの少なくとも一種とフ
ッ素とを同時に添加したＳｉＯ＿２ガラスからなること
を特徴とする光ファイバ。In an optical fiber mainly composed of SiO_2, which consists of a core with a high refractive index and a cladding with a lower refractive index than the core, the refractive index of the core is not larger than the refractive index of SiO_2,
The glass constituting at least one of the core and the cladding is Al, which is an element having an atomic weight smaller than Si.
, Mg, Na, Be, and Li and at least one of Li and fluorine are added to the SiO_2 glass.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62027350A JPS63195147A (en) | 1987-02-10 | 1987-02-10 | Optical fiber |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62027350A JPS63195147A (en) | 1987-02-10 | 1987-02-10 | Optical fiber |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63195147A true JPS63195147A (en) | 1988-08-12 |
Family
ID=12218591
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62027350A Pending JPS63195147A (en) | 1987-02-10 | 1987-02-10 | Optical fiber |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63195147A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0915065A1 (en) * | 1996-07-16 | 1999-05-12 | Toyota Jidosha Kabushiki Kaisha | Ultralow-loss silica glass and optical fibers made using the same |
| WO2005021455A3 (en) * | 2003-08-29 | 2005-09-01 | Corning Inc | Optical fiber containing an alkali metal oxide and methods and apparatus for manufacturing same |
| US7426327B2 (en) | 2005-11-23 | 2008-09-16 | Corning Incorporated | Low attenuation non-zero dispersion shifted optical fiber |
-
1987
- 1987-02-10 JP JP62027350A patent/JPS63195147A/en active Pending
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0915065A1 (en) * | 1996-07-16 | 1999-05-12 | Toyota Jidosha Kabushiki Kaisha | Ultralow-loss silica glass and optical fibers made using the same |
| EP0915065A4 (en) * | 1996-07-16 | 1999-09-29 | Toyota Motor Co Ltd | Ultralow-loss silica glass and optical fibers made using the same |
| US6153546A (en) * | 1996-07-16 | 2000-11-28 | Toyota Jidosha Kabushiki Kaisha | Ultralow-loss silica glass and optical fibers using the same |
| WO2005021455A3 (en) * | 2003-08-29 | 2005-09-01 | Corning Inc | Optical fiber containing an alkali metal oxide and methods and apparatus for manufacturing same |
| JP2013006764A (en) * | 2003-08-29 | 2013-01-10 | Corning Inc | Optical fiber containing alkali metal oxide and method and apparatus for manufacturing the same |
| JP2013014505A (en) * | 2003-08-29 | 2013-01-24 | Corning Inc | Optical fiber containing alkali metal oxide and method for manufacturing the same and apparatus |
| US8798412B2 (en) | 2003-08-29 | 2014-08-05 | Corning Incorporated | Optical fiber containing an alkali metal oxide and methods and apparatus for manufacturing same |
| US9250386B2 (en) | 2003-08-29 | 2016-02-02 | Corning Incorporated | Optical fiber containing an alkali metal oxide and methods and apparatus for manufacturing same |
| US7426327B2 (en) | 2005-11-23 | 2008-09-16 | Corning Incorporated | Low attenuation non-zero dispersion shifted optical fiber |
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