JPS623774B2 - - Google Patents
Info
- Publication number
- JPS623774B2 JPS623774B2 JP57006110A JP611082A JPS623774B2 JP S623774 B2 JPS623774 B2 JP S623774B2 JP 57006110 A JP57006110 A JP 57006110A JP 611082 A JP611082 A JP 611082A JP S623774 B2 JPS623774 B2 JP S623774B2
- Authority
- JP
- Japan
- Prior art keywords
- base material
- optical fiber
- starting member
- geo
- fiber base
- 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.)
- Expired
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B37/00—Manufacture or treatment of flakes, fibres, or filaments from softened glass, minerals, or slags
- C03B37/01—Manufacture of glass fibres or filaments
- C03B37/012—Manufacture of preforms for drawing fibres or filaments
- C03B37/014—Manufacture of preforms for drawing fibres or filaments made entirely or partially by chemical means, e.g. vapour phase deposition of bulk porous glass either by outside vapour deposition [OVD], or by outside vapour phase oxidation [OVPO] or by vapour axial deposition [VAD]
- C03B37/01413—Reactant delivery systems
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B2201/00—Type of glass produced
- C03B2201/06—Doped silica-based glasses
- C03B2201/20—Doped silica-based glasses doped with non-metals other than boron or fluorine
- C03B2201/28—Doped silica-based glasses doped with non-metals other than boron or fluorine doped with phosphorus
-
- C—CHEMISTRY; METALLURGY
- C03—GLASS; MINERAL OR SLAG WOOL
- C03B—MANUFACTURE, SHAPING, OR SUPPLEMENTARY PROCESSES
- C03B2201/00—Type of glass produced
- C03B2201/06—Doped silica-based glasses
- C03B2201/30—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi
- C03B2201/31—Doped silica-based glasses doped with metals, e.g. Ga, Sn, Sb, Pb or Bi doped with germanium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Life Sciences & Earth Sciences (AREA)
- General Life Sciences & Earth Sciences (AREA)
- Geochemistry & Mineralogy (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Manufacture, Treatment Of Glass Fibers (AREA)
Description
【発明の詳細な説明】
本発明は脈理の少ない光フアイバ用母材の製造
方法に関する。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a method for manufacturing an optical fiber base material with less striae.
従来から、光フアイバ用母材を製造する方法と
して、原料ガス、例えばSiCl4、GeCl4、POCl4、
BBr3、水素ガスおよび酸素ガス等を回転する出
発部材の軸方向に噴出させて火災加水分解により
ガラス微粒子を生成し、生成するガラス微粒子を
堆積させてから加熱し、堆積微粒子を透明ガラス
化して光フアイバ用母材を製造する気相軸付け法
（以下、「VAD法」と略称）が知られている。 Traditionally, as a method for manufacturing optical fiber base materials, raw material gases such as SiCl 4 , GeCl 4 , POCl 4 ,
BBr 3 , hydrogen gas, oxygen gas, etc. are ejected in the axial direction of a rotating starting member to generate glass particles by fire hydrolysis, and the resulting glass particles are deposited and then heated to turn the deposited particles into transparent glass. A vapor deposition method (hereinafter abbreviated as "VAD method") for producing a base material for optical fibers is known.
このVAD法による光フアイバ用母材の製造方
法はガラス微粒子が速く堆積させることができる
ので大型の光フアイバ用母材を作製できる。 This method of manufacturing an optical fiber base material using the VAD method allows glass fine particles to be deposited quickly, so that a large optical fiber base material can be produced.
また、大量生産できるという長所ももつてい
る。 It also has the advantage of being mass produced.
しかし、屈折率制御用に添加しているGeO2の
堆積量が堆積面の温度に敏感であるため、GeO2
の濃度変化が光フアイバ用母材の長手方向に生じ
る欠点があつた。VAD法では、通常、出発部材
に対して斜め方向にバーナを配置してガラス微粒
子を堆積させる。それ故、バーナに近い側の出発
部材表面温度は高く、バーナから遠い側の出発部
材表面温度は低い。 However, since the amount of GeO 2 deposited for refractive index control is sensitive to the temperature of the deposition surface, GeO 2
There was a drawback that the concentration of the optical fiber varied in the longitudinal direction of the optical fiber base material. In the VAD method, glass particles are usually deposited by placing a burner obliquely with respect to the starting member. Therefore, the starting member surface temperature on the side closer to the burner is high, and the starting member surface temperature on the side far from the burner is lower.
しかも、GeO2は温度の高い所に堆積し易い傾
向があるため、バーナ側に近い側の出発部材表面
には多くのGeO2が堆積する。ところが、SiO2の
方はその堆積量は表面温度に依存しないから、バ
ーナからの遠近に関係なく、ほぼ一定にSiO2は
堆積する。 Moreover, since GeO 2 tends to be deposited in high-temperature areas, a large amount of GeO 2 is deposited on the surface of the starting member closer to the burner side. However, since the amount of SiO 2 deposited does not depend on the surface temperature, SiO 2 is deposited almost constantly regardless of the distance from the burner.
しかも、出発部材は回転しているため、出発部
材の軸方向にGeO2の濃度の異なるガラス微粒子
層がら旋状に堆積し、いわゆる屈折率のリツプル
が生じる。 Moreover, since the starting member is rotating, glass fine particle layers with different concentrations of GeO 2 are deposited in a spiral shape in the axial direction of the starting member, resulting in a so-called ripple in the refractive index.
この様子を、出発部材の軸方向における屈折率
制御剤（例えばGeO2）の含有量（20wt％）の変化
を示すと第１図の特性曲線が得られる。この特性
曲線は上述のVAD法で作製された透明な光フア
イバ用母材の中心部分（出発部材の軸方向）の長
手方向の屈折率制御剤の濃度変化の測定結果を示
すものである。使用測定器はＸ線マイクロアナラ
イザーである。この測定結果から、GeO2の含有
量は一定の値を中心として、その上下に小さな振
幅をもつて長手方向に周期的に変化していること
がわかる。 When this situation is shown by changing the content (20 wt%) of the refractive index controlling agent (for example, GeO 2 ) in the axial direction of the starting member, the characteristic curve shown in FIG. 1 is obtained. This characteristic curve shows the measurement result of the change in the concentration of the refractive index controlling agent in the longitudinal direction of the central portion (in the axial direction of the starting member) of the transparent optical fiber base material produced by the above-mentioned VAD method. The measuring instrument used is an X-ray microanalyzer. The measurement results show that the GeO 2 content changes periodically in the longitudinal direction with small amplitudes above and below a constant value.
このような光フアイバ用母材内の長手方向の屈
折率制御剤の含有量の周期的な揺らぎ（リツプル
という）は、この光フアイバ用母材から作製する
光学的導波管としての光フアイバの長手方向に屈
折率のリツプルをもたらし、一般に知られるいわ
ゆるガラスの脈理として観察され、光学的導波管
の性能を大きく損なう原因になつていた。 Such periodic fluctuations (ripples) in the content of the refractive index control agent in the longitudinal direction within the optical fiber base material affect the optical fiber used as an optical waveguide made from this optical fiber base material. This results in ripples in the refractive index in the longitudinal direction, which are commonly observed as so-called glass striae, and are the cause of a significant deterioration in the performance of optical waveguides.
本発明は、このような従来の光フアイバ用母材
の製造方法の欠点を除去するためになされたもの
であつて、光フアイバ用母材の長手方向の屈折率
制御剤の含有量の濃度分布に周期的なリツプルを
有しない光フアイバ用母材の製造方法を提供しよ
うとするものである。 The present invention has been made in order to eliminate the drawbacks of the conventional method for manufacturing an optical fiber preform, and is to improve the concentration distribution of the refractive index controlling agent content in the longitudinal direction of the optical fiber preform. The present invention aims to provide a method for manufacturing an optical fiber base material that does not have periodic ripples.
本発明の光フアイバ用母材の製造方法は、多重
管バーナから噴出する原料ガスを火炎加水分解さ
せてガラス微粒子を生成し、生成したガラス微粒
子を回転する出発部材の軸方向に沿つて堆積し、
さらに当該堆積物の加熱し、透明ガラス化する光
フアイバ用母材の製造方法において、生成した前
記ガラス微粒子の前記回転する出発部材の軸方向
の堆積厚さを、１回転当り１〜100μｍになるよ
うに堆積させることを特徴とするものである。 The method for manufacturing an optical fiber base material of the present invention involves flame hydrolysis of raw material gas ejected from a multi-tube burner to generate glass fine particles, and depositing the generated glass fine particles along the axial direction of a rotating starting member. ,
Furthermore, in the method for manufacturing an optical fiber base material in which the deposit is heated and vitrified to be transparent, the thickness of the generated glass particles in the axial direction of the rotating starting member is set to 1 to 100 μm per rotation. It is characterized by being deposited as follows.
次に、屈折率制御剤としてGeO2を用いた場合
の本発明に光フアイバ用母材の製造方法の実施例
について説明する。 Next, an example of a method for manufacturing an optical fiber base material according to the present invention in which GeO 2 is used as a refractive index controlling agent will be described.
多重管バーナより噴出される原料ガスを火炎加
水分解してガラス微粒子を生成し、該ガラス微粒
子を回転する出発部材の軸方向に堆積させた後、
加熱し透明ガラス化して光フアイバ用母材を得る
方法において、原料ガス中の添加剤がゲルマニウ
ム化合物及びリン化合物を含むものとする。この
原料ガスを火炎加水分解させてガラス微粒子を生
成させるが、このガラス微粒子中にはGeO2及び
P2O5が存在する。更に該ガラス微粒子を出発部
材に堆積させた後、加熱により透明ガラス化され
る。一方所定の屈折率分布を形成するように分布
されるGeO2は長手方向に含有量の濃度の揺ら
ぎ、つまりリツプルを発生しているが、しかし上
記工程中、GeO2の一部は拡散しGeO2含有量の濃
度のリツプルはの振幅は小さくなる。GeO2の拡
散が、膜厚すなわち出発部材の１回転当りのガラ
ス微粒子の堆積厚に依存する。 The raw material gas ejected from the multi-tube burner is flame-hydrolyzed to produce glass fine particles, and the glass fine particles are deposited in the axial direction of the rotating starting member.
In the method of obtaining a base material for an optical fiber by heating and vitrifying it to be transparent, the additive in the raw material gas contains a germanium compound and a phosphorus compound. This raw material gas is flame-hydrolyzed to produce glass particles, but these glass particles contain GeO 2 and
P2O5 is present. Further, after the glass particles are deposited on the starting member, it is heated to be made into transparent glass. On the other hand, GeO 2 , which is distributed to form a predetermined refractive index distribution, causes fluctuations in the content concentration in the longitudinal direction, that is, ripples, but during the above process, a part of GeO 2 diffuses and becomes GeO The amplitude of the ripple in the concentration of 2 content becomes smaller. The diffusion of GeO 2 depends on the film thickness, that is, the deposition thickness of glass particles per revolution of the starting member.
出発部材への１回当りのガラス微粒子の堆積厚
を、所定範囲の値にすれば、GeO2の含有量の濃
度分布のリツプルの振幅を小さくできることが明
らかとなつた。 It has become clear that the amplitude of ripples in the concentration distribution of GeO 2 content can be reduced by setting the thickness of glass fine particles deposited each time on the starting member within a predetermined range.
第２図に出発部材の一回転当りのガラス微粒子
の堆積厚に対するGeO2のリツプルの振幅を測定
した結果を示す。同図に示すように堆積厚の減少
に伴つて、GeO2のリツプル振幅は低減する。こ
の場合堆積厚が１μｍ以下だとガラス微粒子の粒
径（0.5〜0.1μｍ）と同程度となつて製作が困難
となる。一方、堆積厚が100μｍを越えると、
GeO2のリツプルが急激に増大し、光フアイバ用
母材の長手方向の屈折率分布のリツプルの振幅が
大きくなり、これから作製される光フアイバの性
能を損なうようになる。 FIG. 2 shows the results of measuring the amplitude of GeO 2 ripples with respect to the deposition thickness of glass particles per revolution of the starting member. As shown in the figure, the ripple amplitude of GeO 2 decreases as the deposition thickness decreases. In this case, if the deposited thickness is less than 1 .mu.m, the particle size will be about the same as the glass fine particles (0.5 to 0.1 .mu.m), making production difficult. On the other hand, when the deposition thickness exceeds 100μm,
The ripples of GeO 2 increase rapidly, and the amplitude of the ripples in the longitudinal refractive index distribution of the optical fiber base material increases, which impairs the performance of the optical fiber to be manufactured.
したがつて、１回当りのガラス微粒子の１回当
りの堆積厚は１〜100μｍが適当と考えられる。 Therefore, it is considered that the appropriate thickness of glass fine particles to be deposited each time is 1 to 100 μm.
以上の説明から明らかなように、本発明の光フ
アイバ用母材の製造方法によれば出発部材に対す
る軸方向の１回転当りのガラス微粒子の堆積厚を
１〜100μｍに制御するだけの操作によつて、得
られる光フアイバ用母材の長手方向の屈折率分布
の揺らぎを抑えることができ、脈理の少ない光フ
アイバを得ることができる。 As is clear from the above explanation, according to the method for manufacturing an optical fiber base material of the present invention, the deposition thickness of glass particles per rotation in the axial direction with respect to the starting member is simply controlled to 1 to 100 μm. Therefore, fluctuations in the longitudinal refractive index distribution of the obtained optical fiber base material can be suppressed, and an optical fiber with fewer striae can be obtained.
第１図は従来の製造方法により製造された光フ
アイバ用母材の屈折率のリツプルの状態を示す特
性図、第２図はGeO2のリツプル振幅と堆積厚と
の関係を表す特性図である。
Fig. 1 is a characteristic diagram showing the state of ripples in the refractive index of an optical fiber base material manufactured by a conventional manufacturing method, and Fig. 2 is a characteristic diagram showing the relationship between ripple amplitude and deposition thickness of GeO 2 . .
Claims (1)
水分解させてガラス微粒子を生成し、生成したガ
ラス微粒子を回転する出発部材の軸方向に沿つて
堆積し、さらに当該堆積物を加熱し、透明ガラス
化する光フアイバ用母材の製造方法において、生
成した前記ガラス微粒子の前記回転する出発部材
の軸方向の堆積厚さを、１回転当り１〜100μｍ
になるように堆積させることを特徴とする光フア
イバ用母材の製造方法。1 Flame hydrolyze raw material gas ejected from a multi-tube burner to generate glass particles, deposit the generated glass particles along the axial direction of a rotating starting member, and further heat the deposit to turn it into transparent vitrification. In the method for manufacturing an optical fiber base material, the deposited thickness of the generated glass particles in the axial direction of the rotating starting member is 1 to 100 μm per rotation.
1. A method for producing an optical fiber base material, the method comprising: depositing the base material so that the base material becomes .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP611082A JPS58125624A (en) | 1982-01-20 | 1982-01-20 | Production of parent material for optical fiber |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP611082A JPS58125624A (en) | 1982-01-20 | 1982-01-20 | Production of parent material for optical fiber |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS58125624A JPS58125624A (en) | 1983-07-26 |
| JPS623774B2 true JPS623774B2 (en) | 1987-01-27 |
Family
ID=11629355
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP611082A Granted JPS58125624A (en) | 1982-01-20 | 1982-01-20 | Production of parent material for optical fiber |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS58125624A (en) |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4339173A (en) * | 1975-09-08 | 1982-07-13 | Corning Glass Works | Optical waveguide containing P2 O5 and GeO2 |
| JPS52121341A (en) * | 1976-04-06 | 1977-10-12 | Nippon Telegr & Teleph Corp <Ntt> | Production of optical fiber base materials and production apparatus fo r the same |
| US4111525A (en) * | 1976-10-12 | 1978-09-05 | Bell Telephone Laboratories, Incorporated | Silica based optical fiber waveguide using phosphorus pentoxide and germanium dioxide |
-
1982
- 1982-01-20 JP JP611082A patent/JPS58125624A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS58125624A (en) | 1983-07-26 |
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