JPS63217311A - Dispersion-shift fiber and its production - Google Patents
Dispersion-shift fiber and its productionInfo
- Publication number
- JPS63217311A JPS63217311A JP62050276A JP5027687A JPS63217311A JP S63217311 A JPS63217311 A JP S63217311A JP 62050276 A JP62050276 A JP 62050276A JP 5027687 A JP5027687 A JP 5027687A JP S63217311 A JPS63217311 A JP S63217311A
- Authority
- JP
- Japan
- Prior art keywords
- glass body
- core
- sio2
- inner core
- refractive index
- 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.)
- Granted
Links
- 239000000835 fiber Substances 0.000 title claims abstract description 28
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 239000011521 glass Substances 0.000 claims abstract description 56
- 239000002131 composite material Substances 0.000 claims abstract description 21
- 238000009826 distribution Methods 0.000 claims abstract description 21
- 238000000034 method Methods 0.000 claims abstract description 17
- 238000005253 cladding Methods 0.000 claims description 24
- 238000010438 heat treatment Methods 0.000 claims description 18
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract description 25
- 230000005540 biological transmission Effects 0.000 abstract description 21
- 239000005373 porous glass Substances 0.000 abstract description 19
- 239000000377 silicon dioxide Substances 0.000 abstract description 13
- 229910052681 coesite Inorganic materials 0.000 abstract description 10
- 229910052906 cristobalite Inorganic materials 0.000 abstract description 10
- 229910052682 stishovite Inorganic materials 0.000 abstract description 10
- 229910052905 tridymite Inorganic materials 0.000 abstract description 10
- 239000002245 particle Substances 0.000 abstract description 9
- 235000012239 silicon dioxide Nutrition 0.000 abstract description 9
- 239000010453 quartz Substances 0.000 abstract description 6
- 230000002542 deteriorative effect Effects 0.000 abstract 1
- 238000010586 diagram Methods 0.000 description 10
- YBMRDBCBODYGJE-UHFFFAOYSA-N germanium dioxide Chemical compound O=[Ge]=O YBMRDBCBODYGJE-UHFFFAOYSA-N 0.000 description 8
- 230000006866 deterioration Effects 0.000 description 6
- RPAJSBKBKSSMLJ-DFWYDOINSA-N (2s)-2-aminopentanedioic acid;hydrochloride Chemical class Cl.OC(=O)[C@@H](N)CCC(O)=O RPAJSBKBKSSMLJ-DFWYDOINSA-N 0.000 description 5
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 5
- 238000010521 absorption reaction Methods 0.000 description 5
- 239000002253 acid Substances 0.000 description 5
- 239000006185 dispersion Substances 0.000 description 5
- 229910052739 hydrogen Inorganic materials 0.000 description 5
- 239000001257 hydrogen Substances 0.000 description 5
- 238000004891 communication Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 239000013307 optical fiber Substances 0.000 description 4
- 230000002194 synthesizing effect Effects 0.000 description 4
- 208000005156 Dehydration Diseases 0.000 description 3
- 230000018044 dehydration Effects 0.000 description 3
- 238000006297 dehydration reaction Methods 0.000 description 3
- 238000000151 deposition Methods 0.000 description 3
- 230000010354 integration Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000002360 preparation method Methods 0.000 description 3
- 238000001228 spectrum Methods 0.000 description 3
- 238000011282 treatment Methods 0.000 description 3
- 229910004014 SiF4 Inorganic materials 0.000 description 2
- 238000011276 addition treatment Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 125000002887 hydroxy group Chemical group [H]O* 0.000 description 2
- 230000002093 peripheral effect Effects 0.000 description 2
- ABTOQLMXBSRXSM-UHFFFAOYSA-N silicon tetrafluoride Chemical compound F[Si](F)(F)F ABTOQLMXBSRXSM-UHFFFAOYSA-N 0.000 description 2
- 238000003786 synthesis reaction Methods 0.000 description 2
- 238000004017 vitrification Methods 0.000 description 2
- PXGOKWXKJXAPGV-UHFFFAOYSA-N Fluorine Chemical compound FF PXGOKWXKJXAPGV-UHFFFAOYSA-N 0.000 description 1
- 229910005260 GaCl2 Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000011109 contamination Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 229920006240 drawn fiber Polymers 0.000 description 1
- 238000005553 drilling Methods 0.000 description 1
- 230000005274 electronic transitions Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910052731 fluorine Inorganic materials 0.000 description 1
- 239000011737 fluorine Substances 0.000 description 1
- 239000003292 glue Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 239000012466 permeate Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000012546 transfer Methods 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
Landscapes
- Optical Fibers, Optical Fiber Cores, And Optical Fiber Bundles (AREA)
- Glass Compositions (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、通信用石英系光ファイバの構造及びその製造
方法に関するものであり、特に波長１．５μｍ帯に零分
散波長を７フトさせたシングルモードファイバ（以下「
分散Ｖフトファイバ」と呼称する）の構造とそのプリフ
ォームの製造方法に関する。[Detailed Description of the Invention] [Field of Industrial Application] The present invention relates to the structure of a silica-based optical fiber for communications and a method for manufacturing the same, and in particular, to a silica-based optical fiber for communication, in which the zero dispersion wavelength is increased by 7 feet in the wavelength band of 1.5 μm. Single mode fiber (hereinafter referred to as “
The present invention relates to the structure of a "dispersed V-ft fiber" and a method for manufacturing its preform.
石英系光ファイバにおいてその最低損失波長領域である
１、５μｍ帯に零分散波長をシフトさせた分散シフト・
ファイバは、長距離かつ大伝送容量の光通信伝送路とし
て夾用化が進んでいる。分散シフト・ファイバの中でも
、第１図（ａ）に示すような階段型屈折率分布を有する
ものは単純なステップ型屈折率分布を有する分散シフト
ファイバに比べ曲げ損失が小さくなり、実用上の利点が
大きく開発検討が進められている。Dispersion shift, which shifts the zero dispersion wavelength to the 1.5 μm band, which is the lowest loss wavelength region in silica-based optical fibers.
Fibers are increasingly being used as long-distance, high-capacity optical communication transmission lines. Among dispersion-shifted fibers, those with a stepped refractive index distribution as shown in Figure 1(a) have a practical advantage because they have lower bending loss than dispersion-shifted fibers with a simple stepped refractive index distribution. A major development study is underway.
（＃考文献１ ： ｒデイスバージョンーシフテツド
コンヴエツクスーインデツクス Ｖングルーモード フ
ァイパース」Ｎ、クワキ他、エレクトロニクス レター
ズ １９８５年１２月５日、２１ 、ＮＯ，２５／２６
、ｐ、１１８６−１１８７）。第１図（ａ）に示した階
段型屈折率分布では、中央部の屈折率の最も高い部分１
．１（内側コアと称する）と該内側コア１．１を囲む内
側コアより低い屈折率を有する部分１．２（外側コアと
称する）、さらに該外側コア１．２を取り囲む最も屈折
率の低いクラッド部１．３から屈折率分布構造が形成さ
れている。(#Reference 1: rdisversion-shifted
"Convex Index V-Glue Mode Fipers" N, Kwaki et al., Electronics Letters December 5, 1985, 21, NO, 25/26
, p. 1186-1187). In the stepped refractive index distribution shown in Fig. 1(a), the central part 1 has the highest refractive index.
．． 1 (referred to as the inner core), a portion 1.2 (referred to as the outer core) surrounding the inner core 1.1 and having a lower refractive index than the inner core, and a cladding having the lowest refractive index surrounding the outer core 1.2. A refractive index distribution structure is formed from portion 1.3.
このような階段型屈折率分布を有する分散シフト・ファ
イバについて、その屈折率分布を形成するガラス組成と
して、内側コアがＧｅＯ２−ＳｉＯ２、外側コアが８１
０！、 クラッド部がＦ−ＳｉＯ２からなるものが提案
されている（参考文献２ ： ｒディス、バージョン−
シフチットファイバーズ ウィズ ）〜オリン アッデ
ッドクラツヂイング バイ ザ ベイバー フェイズ
アク・Ｖアル デポジッＶ：！ン メソッド」、Ｈ，ヨ
コタ他、テクニカル ダイジェスト オントビ力ｐ ミ
ーティング オン オデデイカμファイバー コミユニ
ケイＶｇン（アトランタ、１９８６）ペーパーＷＦ２）
。光ファイバの屈折率分布は、Ｓ１０．ガラスにＧｅ０
１ を屈折率増加成分として添加することによって得ら
れるのが最も一般的である。しかしながらＧｅＯ２添加
量を多くすると、ガラスのレイリー散乱が増加して伝送
損失が高くなる、或いはＧｅＯ２→ＧｅＯの還元に基づ
くと考えられる紫外域での電子４移吸収が増加し、その
影響が使用波長域である１、５μ凱帯にまで及びやはり
伝送損失が高くなる。そこで上記組成では、クラッド部
にＦを添加しクラッド部の屈折率を下げ、内側コアのみ
にＧｅ０１を添加し、（）ｅｏｌ ｍ論量を下げ、伝送
損失の低減を図ろうとしている。これまで本発明者等は
、この考えに基づき、第２図に示すような内側コア２−
１がＧａｏｌ −５ｉ０２、外側コアｚ２がＳｉｎ、、
クフー／ド部ｚ３がＦ−ＳｉＯ．であって、図示の屈
折率分布と組成を有する公衆りフトファイバを試作し、
波長１．５５μ汎における伝送損失を（Ｌ ２５ ｄＢ
／ｋｍ まで低減することができている。なお第２図中
ａ、ｂ％Ｃは各部分の直径を表し、ａは５μｍ、ｂは９
μｍ１Ｃは１２５μｍである。（参考文献ｓ ： ｒｔ
ｓμｍ帯分散シフトリング〜モードファイバの伝送特性
」重松、全会、田中、田中、渡辺、鈴木１、電子通信学
会技術研究報告 ０ＱＲ８６−９？）。Regarding the dispersion-shifted fiber having such a stepped refractive index distribution, the glass composition forming the refractive index distribution is GeO2-SiO2 for the inner core and 81% for the outer core.
0! , one in which the cladding part is made of F-SiO2 has been proposed (Reference 2: rdis, version -
Shifted Fibers With) ~ Orin Added Crutzing By The Baber Phase
Aku V Al Deposit V:! H, Yokota et al., Technical Digest Ontobi Rikip Meeting on Odedeika μ Fiber Komiyuni Kei Vgn (Atlanta, 1986) Paper WF2)
. The refractive index distribution of the optical fiber is S10. Ge0 on glass
The most common method is to add 1 as a refractive index increasing component. However, when the amount of GeO2 added is increased, Rayleigh scattering of the glass increases, resulting in higher transmission loss, or electron 4-transfer absorption in the ultraviolet region, which is thought to be based on the reduction of GeO2→GeO, increases, and this effect affects the wavelength used. The transmission loss also increases as the transmission loss reaches the 1.5μ band. Therefore, in the above composition, F is added to the cladding part to lower the refractive index of the cladding part, and Ge01 is added only to the inner core to lower the ()eol m stoichiometry and reduce the transmission loss. Based on this idea, the present inventors have so far developed an inner core 2-
1 is Gaol-5i02, outer core z2 is Sin,
Kufu/de part z3 is F-SiO. A public drift fiber having the refractive index distribution and composition shown in the figure was prototyped,
Transmission loss at wavelength 1.55μ is (L 25 dB
/km2. In addition, a, b%C in Fig. 2 represents the diameter of each part, a is 5 μm, b is 9
μm1C is 125 μm. (References: rt
sμm Band Dispersion Shift Ring - Transmission Characteristics of Mode Fiber" Shigematsu, Zenkai, Tanaka, Tanaka, Watanabe, Suzuki 1, Institute of Electronics and Communication Engineers Technical Research Report 0QR86-9? ).
上記のように、内側コアがＧｅＯ２−８１０１、外側コ
アが８１０２、クラッド部がＦ−８１０，からなる階段
型屈折率分布を有する分散シフトファイバにおいては、
波長１．５５μｍにおいてα２３ｄＢ／ｋｎ）の伝送損
失は得られているがさらに低損失化を図ることが困難で
あった。As mentioned above, in a dispersion-shifted fiber with a stepped refractive index distribution consisting of an inner core of GeO2-8101, an outer core of 8102, and a cladding of F-810,
Although a transmission loss of α23 dB/kn) was obtained at a wavelength of 1.55 μm, it was difficult to further reduce the loss.
本発明は、さらなる伝送損失の低減を可能とする新規な
構造の分散シフトファイバ及びその製造方法を提供しよ
うとするものである。The present invention aims to provide a dispersion-shifted fiber with a novel structure that enables further reduction in transmission loss, and a method for manufacturing the same.
本発明は内側コアがＧｅ−８ｉｎ、１．外側コアがＦ−
ＳｉＯ２、クラツド部がＦ’−８１０，からなっておシ
階段状屈折率分布を有することを特徴とする分散シフト
ファイバを提供する。The present invention has an inner core of Ge-8in, 1. Outer core is F-
The present invention provides a dispersion-shifted fiber comprising SiO2 with a cladding portion of F'-810 and having a step-like refractive index distribution.
さらに、本発明はＧｅ０１−５ｉ０２ からなる内側
コア用ガラス体を、Ｆ−８１０，からなるパイプ状の外
側コア用ガラス体中に挿入して加熱一体化することによ
り、内側コアと外側コアからなる複合体ＣＩ）を形成す
る工程と、該複合体（ｆ）をＦ−８１０，からなるパイ
プ状のクラッド部用ガフ１体の中空部内に挿入して加熱
一体化することによυ、内側コア、外側コアコア及びク
ラッド部からなる複合体（ＩＩ）を形成する工程とを有
することを特徴とする内側コアがＧｅ−８ｉＯ１、外側
コアがＦ−ＳｉＯ２、クラツド部がＦ−ＳｉＯ２からな
り階段状屈折率分布を有する分散シフトファイバの製造
方法を提供する。Furthermore, the present invention is capable of inserting an inner core glass body made of Ge01-5i02 into a pipe-shaped outer core glass body made of F-810, and heating and integrating the glass body made of F-810. The inner core is formed by inserting the composite (f) into the hollow part of a pipe-shaped cladding gaff made of F-810 and heating and integrating it. , forming a composite body (II) consisting of an outer core and a cladding part, characterized in that the inner core is made of Ge-8iO1, the outer core is made of F-SiO2, and the cladding part is made of F-SiO2 and has a stepped refraction. A method of manufacturing a dispersion-shifted fiber having a modulus distribution is provided.
まず、本発明の基となった考え方から説明する。第２図
に示した従来のファイバ構造において、さらなる低損失
化が困難であった理由、すなわち、伝送損失劣化要因と
しては、次のことが考えられる。■内側コアに含有され
るＧａｏｌのためにレイリー散乱損失が高くなったシ、
或いは線引等の高温加熱過程において、通常４価のＧｅ
が還元されて２価の状態に変化して、これが紫外域に吸
収を有する電子遷移の吸収中心番
となり、波長１．５μｍ帯にまでその影響が及ぶこと、
■ＧｅＯ２を含有する内側コアとＦを含有するクラッド
部に挟まれｐ８１０．からなる外側コアの部分は、他の
部分に比して線引等の高温加熱過程における粘性が高く
なり、線引時にかかる張力が外側コアの部分に集中して
外側コアの部分に欠陥を生じ、やはヤ紫外域での吸収の
原因となることなどである。First, the concept on which the present invention is based will be explained. In the conventional fiber structure shown in FIG. 2, the reason why it is difficult to further reduce the loss, that is, the cause of transmission loss deterioration can be considered as follows. ■Rayleigh scattering loss is high due to Gaol contained in the inner core.
Or, in a high-temperature heating process such as wire drawing, usually tetravalent Ge is
is reduced and changed to a divalent state, which becomes the absorption center for electronic transitions that have absorption in the ultraviolet region, and its influence extends to the wavelength band of 1.5 μm.
■ Sandwiched between the inner core containing GeO2 and the cladding containing F, p810. The outer core part, which is made up of , and may cause absorption in the ultraviolet region.
上記のような考察に基づき、本発明のととくＦを外側コ
アに添加することがより一層の低損失化にとって有効で
あることが考えられる。即ち上記伝送損失劣化要因■に
対しては、外側コアにＦを添加し、その屈折率を下げる
ことＫより内側コアの屈折率を上げるための内側コアへ
のＧｅ０１添加量をさらに低減できるので、その結果、
Ｇｅ０１ に起因するレイリー散乱損失及び紫外域での
吸収損失の影響を低減できると考えられる。Based on the above considerations, it is considered that adding F to the outer core of the present invention is effective for further reducing loss. That is, for the above-mentioned transmission loss deterioration factor (2), adding F to the outer core to lower its refractive index can further reduce the amount of Ge01 added to the inner core to increase the refractive index of the inner core. the result,
It is believed that the effects of Rayleigh scattering loss and absorption loss in the ultraviolet region caused by Ge01 can be reduced.
また伝送損失劣化要因■に対しては、外側コアにＦを添
加してその粘性を下げ、内側コア及びクラッド部に近づ
けることにより、低減可能と考えられる。It is also believed that the transmission loss deterioration factor (2) can be reduced by adding F to the outer core to lower its viscosity and bring it closer to the inner core and cladding.
但し、外側コア部とクラッド部の屈折率差を所要分だけ
保つためには、外側コアにＦを添加した場合、クラッド
部へのＦ添加量を増してクラッド部の屈折率をより下げ
ておく必要がある。However, in order to maintain the required refractive index difference between the outer core and the cladding, when F is added to the outer core, the amount of F added to the cladding should be increased to lower the refractive index of the cladding. There is a need.
尚本発明の構造を有する分散シフトファイバの製造方法
については実施例にて詳述する。A method for manufacturing a dispersion-shifted fiber having the structure of the present invention will be described in detail in Examples.
実施例
１）内側コア用ガラス体の作製
第３図に示す構成にてＧｅｏ、 −５ｉ０２ からな
る内側コア用多孔質ガラス体をＶＡＤ法にて合成した。Example 1) Preparation of glass body for inner core A porous glass body for inner core consisting of Geo, -5i02 having the structure shown in FIG. 3 was synthesized by VAD method.
第３図において五１はガラス微粒子合成用バーナーであ
り、該バーナーＡ Ｉ Ｋ ５ｉＣｔ。In FIG. 3, numeral 51 is a burner for synthesizing glass particles, and the burner is A I K 5iCt.
５３０ ｃｃ／分、ＧａＣｌ２ ５ Ｓ ｃｃ／分、Ａ
ｒ１．５ｔ／分、Ｈ，Ｌ５ｔ／分、０，７．５ｔ／分を
供給して火炎中でガラス微粒子を合成して出発石英棒五
２の先端にガラス微粒子を堆積せしめるとともに出発石
英棒五２を上方に回転させつつ引上げていくことにより
軸方向に多孔質ガラス体五３を形成した。なお五４は排
気管である。530 cc/min, GaCl2 5 S cc/min, A
R1.5 t/min, H, L5 t/min, and 0.7.5 t/min are supplied to synthesize glass particles in a flame and deposit the glass particles on the tip of the starting quartz rod 52. A porous glass body 53 was formed in the axial direction by pulling up the glass body 2 while rotating it upward. Note that 54 is an exhaust pipe.
これにより得られた内側コア用多孔質ガラス体は外径９
０■φ、長さ５００ｍ、重量６ｒＪＤｆ／であった。The porous glass body for the inner core thus obtained has an outer diameter of 9
It had a diameter of 0.0 mm, a length of 500 m, and a weight of 6 rJDf/.
該多孔質ガラス体をＨｅ：Ｃ４＝１００ ： ６の雰囲
気中で１０５０℃に加熱して脱水処理を施したのち、Ｈ
ｅｌｏＱ％Ｏ雰囲気中で１６００℃に加熱し透明ガラス
化した。透明ガラス化後の外径は３５■φ、長さは２０
０■であった。The porous glass body was heated to 1050°C in an atmosphere of He:C4=100:6 to perform dehydration treatment, and then
It was heated to 1600° C. in an eloQ%O atmosphere to form transparent glass. The outer diameter after transparent vitrification is 35■φ, and the length is 20mm.
It was 0■.
この内側コア用透明ガラス母材を電気抵抗炉で約１８０
０℃〜１９００’Ｃに加熱して１ｏ■φの径まで延伸し
たのち、４００−の長さに分割した。この際の加熱源と
して酸・水素火炎などのＯＨ分を発生するものを用いる
とガラス母材中ＫＯＨ基が拡散浸透し、伝送損失劣化の
原因となるので、電気抵抗炉などのＯＨ成分を発生しな
い熱源を用いる必要がある。This transparent glass base material for the inner core was heated to approximately 180 mm in an electric resistance furnace.
After heating to 0° C. to 1900° C. and stretching to a diameter of 10 mm, the film was divided into 400 mm lengths. If a heating source that generates OH components, such as an acid or hydrogen flame, is used as a heating source, the KOH groups in the glass base material will diffuse and permeate, causing deterioration in transmission loss. It is necessary to use a heat source that does not
２）外側コア用ガラス体の作製
第３図に示す構成にて８１０．のみからなる外側コア用
多孔質ガラス体をＶＡＤ法にて合成した。ガラス微粒子
合成用バーナー五１には５１ｃ４１５０ Ｇ ｃｃ／分
、Ａｒ１２ｔ／分、Ｈ２３０ｔ／分、０，５５ｔ／分を
供給して外径１１０ａｍφ、長さ６００■、重量１１０
０ｇの外側コア用多孔質ガラス体を形成した。2) Preparation of glass body for outer core 810. A porous glass body for the outer core was synthesized using the VAD method. Burner 51 for glass particle synthesis is supplied with 51c4150 G cc/min, Ar 12t/min, H230t/min, and 0.55t/min, and has an outer diameter of 110 amφ, a length of 600 mm, and a weight of 110 mm.
A 0 g porous glass body for the outer core was formed.
該外側コア用多孔質ガラス体をＨｅ：Ｃｌ３ ｗｌｏ
ｏ：５の雰囲気中で１０５０℃に加熱して脱水処理を施
したのち、Ｈｅ：ＳｉＦ４ ＝ １００ ： ３の雰囲
気中で１２５０℃に加熱してＦ添加処理したのち、Ｈｅ
：ＳｉＦ、 ” １０００ ： Ｓｏ雰囲気中で１６
００℃に加熱し透明ガラス化を行った。The porous glass body for the outer core is made of He:Cl3 wlo
After dehydration treatment by heating to 1050°C in an atmosphere of He:SiF4 = 100:3, heating to 1250°C in an atmosphere of He:SiF4 = 100:3 to perform F addition treatment.
:SiF, ”1000: 16 in So atmosphere
It was heated to 00°C to make it transparent and vitrified.
透明ガラス化後の外径は４５■φ、長さは２８０露であ
シ、Ｆが均一に約０６重ＩＩｋチ含有されていた。After being made into transparent vitrification, the outer diameter was 45 mm, the length was 280 mm, and F was evenly contained in about 06 times IIk times.
この外側コア用透明ガラス母材の中心に超音波穿孔機を
用いて１５ｍ＋φの穴をあけパイプ状としたのち酸水素
火炎による加熱により、外径５０８φ、内径１０■φに
なるように延伸したのち長さ５００ｍに分割した。さら
に内部にＳＦ６を流しつつ外部より加熱し、内径が１３
ｍになるまで内壁面のエツチング平滑化処理を行った。A hole of 15 m + φ was made in the center of the transparent glass base material for the outer core using an ultrasonic drilling machine to form a pipe shape, and then heated with an oxyhydrogen flame and stretched to have an outer diameter of 508 φ and an inner diameter of 10 mm. It was divided into 500m lengths. Furthermore, while flowing SF6 inside, it is heated from the outside, and the inner diameter is 13.
The inner wall surface was etched and smoothed until it reached m.
３）内側コア用ガラス体と外側コア用ガラス体の一体化
１）で作製した内側コア用透明ガラス体（直径１０ｍφ
、長さ４００■）を、２）で作製したパイプ状の外側コ
ア用透明ガラス体（外径３０■φ、内径１０１１１１φ
、長さ３００箇）の中に挿入した後、第４図に示すよう
な構成でガラス旋盤を用いて加熱一体化を行った。第４
図において、４．１は、内側コア用透明ガラス体、４．
２は外側コア用透明ガラス体であり、４．３は加熱用の
酸・水素バーナーである。４．４は支持用ダミー石英管
であり、外側コア用透明ガラス体４．２の両端に接続さ
れて図示されていない旋盤のチャックに固定される。チ
ャックを回転させつつ、酸・水素バーナー４．５を外側
コア用透明ガフス体４．２の片端よシ移動させて外側コ
ア用透明ガラス体４．２を加熱収縮させていくことによ
って、内側コア用透明ガラス体４．１と外側コア用透明
ガラス体４．２の一体化を行う。この際内側コア用ガラ
ス体４．１と外側コア用ガラス体４．２の隔間をＣｔ、
等の脱水作用のあるガスを含む雰囲気にしておくことが
、内側コアと外側コアの界面へのＯＨ基混入防止のため
に好ましい。このようにして得られた内側コアと外側コ
アからなるコア用複合ガラス体の屈折率分布を第５図に
示す。５．１は内側コア、！ｌＬ２は外側コアである。3) Integration of the glass body for the inner core and the glass body for the outer core The transparent glass body for the inner core produced in 1) (diameter 10 mφ)
, length 400 mm), and the pipe-shaped transparent glass body for the outer core (outer diameter 30 mm φ, inner diameter 101111 φ) prepared in 2).
, 300 pieces in length), and then heated and integrated using a glass lathe with a configuration as shown in FIG. Fourth
In the figure, 4.1 is a transparent glass body for the inner core;
2 is a transparent glass body for the outer core, and 4.3 is an acid/hydrogen burner for heating. 4.4 is a dummy quartz tube for support, which is connected to both ends of the transparent glass body 4.2 for the outer core and fixed to a chuck of a lathe (not shown). While rotating the chuck, the acid/hydrogen burner 4.5 is moved from one end of the transparent gaff member 4.2 for the outer core to heat and shrink the transparent glass member 4.2 for the outer core, thereby removing the inner core. The transparent glass body 4.1 for the outer core and the transparent glass body 4.2 for the outer core are integrated. At this time, the distance between the glass body 4.1 for the inner core and the glass body 4.2 for the outer core is Ct,
It is preferable to create an atmosphere containing a gas having a dehydrating effect such as the like, in order to prevent OH groups from being mixed into the interface between the inner core and the outer core. FIG. 5 shows the refractive index distribution of the core composite glass body composed of the inner core and the outer core thus obtained. 5.1 is the inner core,! lL2 is the outer core.
得られたコア用複合ガラス体は第５図のｄが１０箇、ｔ
すなわち外径が２６ｍ、長さが２５０−であった。次に
本コア用複合ガラス体の外周部は酸水素火炎によって加
熱されており、ｏＨ基によって汚染されている。そこで
外周部を機械的に外径２５■φになるまで、５Ｔ削し、
ＯＨ基汚染層を除去したのち、このコア用複合ガラス体
を電気抵抗炉加熱により五８露φにまで延伸したのち４
５０−の長さに分割した。The obtained composite glass body for core has 10 points d in FIG. 5 and t
That is, the outer diameter was 26 m and the length was 250 mm. Next, the outer periphery of the core composite glass body is heated by an oxyhydrogen flame and is contaminated with oH groups. Therefore, we mechanically cut the outer circumference by 5T until the outer diameter was 25mmφ.
After removing the OH group contamination layer, this core composite glass body was stretched to a diameter of 58 mm by heating in an electric resistance furnace.
It was divided into 50-length pieces.
これをコア用複合ガラス体（１）とする。This is designated as a core composite glass body (1).
４）クツラド用ガラス体の作製
２）にて得た外側コア用多孔質ガラス体と同様の多孔質
ガラス体をＨｅ：ＣＡ、−１００： ５の雰囲気中で１
０５０℃に加熱して脱水処理を施したのち、Ｈｅ：Ｓｉ
Ｆ４−１００ ： ４の雰囲気中で１２５０℃に加熱し
Ｆ添加処理し、しかるのちにＨｅ：ＳｉＦ４−１００
： ４の雰囲気中で有されていた。4) Preparation of glass body for cuturad A porous glass body similar to the porous glass body for outer core obtained in 2) was heated in an atmosphere of He:CA, -100:5.
After heating to 050°C and dehydrating, He:Si
F4-100: Heated to 1250°C in an atmosphere of 4, subjected to F addition treatment, and then heated to He:SiF4-100.
: It was held in an atmosphere of 4.
この透明ガラス体の中心に超音波穿孔機を用いて８■φ
の穴をあけパイプ状としたのち、酸・水素火炎による加
熱により、外径２２．５■φ、内径４Ｗφになるまで延
伸したのち、長さ５０〇−に分割した。さらに内部にＳ
Ｆ６を流しつつ外部より加熱して内径が７ＩＩＩｌｌφ
になるまで内壁面のエツチング平滑化処理を行った。Using an ultrasonic perforator, the center of this transparent glass body is 8■φ
After making a hole in the shape of a pipe, it was stretched by heating with an acid/hydrogen flame until it had an outer diameter of 22.5 mm and an inner diameter of 4 W, and then was divided into 500 mm lengths. Furthermore, S inside
By heating from the outside while flowing F6, the inner diameter becomes 7IIIllφ.
The inner wall surface was etched and smoothed until it became .
５）コア用複合ガラス体ＣＩ）とクラッド用ガラス体の
一体化
３）で作製したコア用ガラス体（Ｉ）をリテ作製したパ
イプ状りフッド用ガッス体の中空部内に挿入したのち、
３）で行ったものと同様の方法で加熱一体化処理を行っ
た。得られた内側コアと外側コアさらにクツラド部から
なる複合体０の屈折率分布構造を第１図（１））に示す
。第１図（ｂ）においてでは１．６５ｍ、ｇは五８■、
ｈは１＆５ｓｍである。5) Integration of the core composite glass body CI) and the cladding glass body After inserting the core glass body (I) produced in 3) into the hollow part of the pipe-shaped hood gas body produced by Lite,
The heating and integration treatment was performed in the same manner as in 3). The refractive index distribution structure of the obtained composite body 0 consisting of the inner core, outer core, and cuturad part is shown in FIG. 1 (1)). In Figure 1(b), it is 1.65m, g is 58■,
h is 1&5sm.
６）ファイバ化
５）で得られた複合体■を酸・水素火炎を用いて１５■
φに延伸したのち第６図に示す構成で複合体回外周部上
に５ｉＯ１のみからなる多孔質ガラス体を形成した。第
６図において＆１はガラス倣粒子合成用バーナー、＆２
は複合体（６）であり、＆３はダミー石英棒である。ガ
ラス倣粒子合成用バーナー＆ Ｉ ＫＳｉＣ６４１８０
０ｃｃ／分、Ａｒ１２ｔ／分、Ｈ２３５ｔ／分、ｏ２３
５ｔ／分を供給して火炎中でガラス微粒子を発生させて
、複合体＠＆２の上端部分にガラス微粒子を堆積せしめ
るとともに、ダミー石英棒＆３を介して複合体＠＆２を
回転させつつ上方に引上げていくことにより軸方向に多
孔質ガラス体部＆４を形成した。この多孔質ガラス体部
６．４に４）での脱水、弗素添加、透明化と同様の加熱
処理を施し透明ガラス化した。なおこの透明ガラス体の
外径は５５■であり、透明ガラス化時、多孔質ガラス部
の収縮力により複合体（社）は約２１＋ｗφにまでに太
くなった。この透明ガラス体を外径２５ｍ＋にまで延伸
したのち、外径１２５μｍに線引した。6) Fiberization The composite obtained in 5) was processed using an acid/hydrogen flame for 15 days.
After stretching to φ, a porous glass body made only of 5iO1 was formed on the supinated peripheral portion of the composite with the configuration shown in FIG. In Fig. 6, &1 is a burner for synthesizing glass imitation particles, &2
is the composite (6) and &3 is a dummy quartz rod. Burner & I KSiC64180 for glass imitation particle synthesis
0cc/min, Ar12t/min, H235t/min, o23
5 t/min is supplied to generate glass particles in the flame, depositing the glass particles on the upper end of the composite @&2, and pull the composite @&2 upwards through the dummy quartz rod &3 while rotating it. By doing so, a porous glass body portion &4 was formed in the axial direction. This porous glass body portion 6.4 was subjected to the same heat treatment as in 4) for dehydration, addition of fluorine, and transparency to make it transparent vitrified. The outer diameter of this transparent glass body was 55 mm, and when it was made into transparent glass, the shrinkage force of the porous glass part caused the composite body (manufactured by Co., Ltd.) to thicken to about 21+wφ. This transparent glass body was stretched to an outer diameter of 25 m+, and then drawn to an outer diameter of 125 μm.
７）特性
第７図に ６）で得られた本発明の階段状屈折率分布を
有する分散シフトファイバの伝送損失スペクトルを実線
で示す。波長１，５５μｍで０、２０２ ｄＢ／にのま
で低損失化が図られている。7) Characteristics In FIG. 7, the transmission loss spectrum of the dispersion shifted fiber having the stepped refractive index distribution of the present invention obtained in 6) is shown by a solid line. The loss has been reduced to 0.202 dB/ at a wavelength of 1.55 μm.
また比較例として第２図に示した構造を有するファイバ
の伝送損失スペクトルを第６図に破線で示す。１．５５
４ ｍでα２５ ｄＢ／ｋｍ と比較的低損失ではあ
るが、短波長領域にいくにつれ、両者の伝送損失の差が
広がっている。このことは本発明により前述したような
紫外域での損失劣化要因が低減できており、その結果、
１．５５ａｍにおいて０．２５ ｄＢ／ｋｍから（］、
２０２ ｄＢ／ｋｍ＋へという伝送損失低下が実現で
きていることを示している。Further, as a comparative example, the transmission loss spectrum of a fiber having the structure shown in FIG. 2 is shown by a broken line in FIG. 1.55
Although the loss is relatively low at α25 dB/km at 4 m, the difference in transmission loss between the two widens as the wavelength range gets shorter. This is because the present invention can reduce the loss deterioration factors in the ultraviolet region as described above, and as a result,
From 0.25 dB/km at 1.55 am (],
This shows that the transmission loss has been reduced to 202 dB/km+.
尚本実施例では、ファイバ外径とコア径の比率を所定値
に合わせるため内側コア、外側コア、クラッド部の複合
体０の外周部にさらにクラッド部と同組成のＦ−３ｉ○
２ガラスを合成する方法を示しているが、本発明はこの
ような方法に限定されるものではない。例えば厚肉のパ
イプ状りヲツド用透明ガラス体を用いることにより、複
合体（ロ）のみでそのまま線引ファイバ化する方法等も
本発明の一応用例として考えられる。In this example, in order to adjust the ratio of the fiber outer diameter to the core diameter to a predetermined value, F-3i○ having the same composition as the cladding part is further added to the outer periphery of the composite body 0 of the inner core, outer core, and cladding part.
Although a method for synthesizing two glasses is shown, the present invention is not limited to such a method. For example, by using a thick-walled transparent glass body for a pipe-like wire, a method in which only the composite (b) is directly made into a drawn fiber can be considered as an example of application of the present invention.
また、外側のクラッド部を合成する方法としては、第６
図で示したよりな構成に限定されるものではなく、例え
ば第９図に示すように複合体＠ａ２を水平方向或いは垂
直方向にセットして、複合体＠＆２とバーナ＆１とを相
対的に左右上下に移動させる方法を用いてもよい。第９
図のａ３はダミー石英棒である。In addition, as a method for synthesizing the outer cladding part, the sixth
The structure is not limited to the one shown in the figure, but for example, as shown in FIG. A method of moving it up and down may also be used. 9th
A3 in the figure is a dummy quartz rod.
本発明は、以上説明したように外側コアにＦを添加する
ことによりＧｅＯ２に起因するレイリー散乱、Ｇｅ○、
及び内側コア、外側コア、クラッド部間の粘度差に起因
する紫外域に吸収を有する伝送損失劣化要因を低減でき
るので、階段型分散シフトファイバの低損失化に効果が
ある。As explained above, by adding F to the outer core, the present invention can reduce Rayleigh scattering caused by GeO2, Ge○,
In addition, it is possible to reduce the transmission loss deterioration factor that has absorption in the ultraviolet region due to the viscosity difference between the inner core, outer core, and cladding, and is therefore effective in reducing the loss of the stepped dispersion-shifted fiber.
第１図（ａ）は本発明に係わる階段型屈折率分布の説明
図、第１図（ｂ）は本発明の内側１コア、外側１コアと
クラッド部からなる複合体０の屈折率分布構造を示す図
、第２図は従来の屈折率分布の偽造例を示す図である。
第３図ないし第６図は本発明のファイバを製造する実施
態様の説明図であって、第３図は内側コア用多孔質ガラ
ス体の作成方法の説明図、第４図は内側コア用透明ガラ
ス体とパイプ状外側コア用透明ガラス体の加熱一体化方
法の説明図、第５図は内側コアと外側コアの複合体（Ｉ
）の屈折率分布構造例を示す図、第６図は複合体０の外
周部に多孔質ガラス体を堆積させる方法の説明図である
。
第７図は本発明ファイバと従来ファイバの伝送損失スペ
クトＡ／の比較を示す図、第８図は本発明において複合
体０の外周部に多孔質ガラス体を堆積させる別の方法の
説明図である。FIG. 1(a) is an explanatory diagram of a stepped refractive index distribution according to the present invention, and FIG. 1(b) is a refractive index distribution structure of a composite body 0 consisting of one inner core, one outer core, and a cladding part according to the present invention. FIG. 2 is a diagram showing an example of a conventional forgery of a refractive index distribution. 3 to 6 are explanatory diagrams of an embodiment for manufacturing the fiber of the present invention, in which FIG. 3 is an explanatory diagram of a method for producing a porous glass body for the inner core, and FIG. 4 is an explanatory diagram of a method for producing a porous glass body for the inner core. An explanatory diagram of the method of heating and integrating the glass body and the transparent glass body for the pipe-shaped outer core, FIG.
) is a diagram showing an example of the refractive index distribution structure, and FIG. 6 is an explanatory diagram of a method for depositing a porous glass body on the outer peripheral part of the composite body 0. Fig. 7 is a diagram showing a comparison of the transmission loss spectrum A/ of the fiber of the present invention and a conventional fiber, and Fig. 8 is an explanatory diagram of another method of depositing a porous glass body on the outer periphery of the composite body 0 in the present invention. be.
Claims (2)
ｉＯ＿２、クラツド部がＦ−ＳｉＯ＿２からなつており
階段状屈折率分布を有することを特徴とする分散シフト
フアイバ。(1) Inner core is Ge-SiO_2, outer core is F-S
iO_2, a dispersion-shifted fiber characterized in that its cladding part is made of F-SiO_2 and has a stepped refractive index distribution.
ス体を、Ｆ−ＳｉＯ＿２からなるパイプ状の外側コア用
ガラス体中に挿入して加熱一体化することにより、内側
コアと外側コアからなる複合体（ I ）を形成する工程
と、該複合体（ I ）をＦ−ＳｉＯ＿２からなるパイプ
状のクラツド部用ガラス体の中空部内に挿入して加熱一
体化することにより、内側コア、外側コア及びクラツド
部 からなる複合体（II）を形成する工程とを有することを
特徴とする内側コアがＧｅ−ＳｉＯ＿２、外側コアがＦ
−ＳｉＯ＿２、クラツド部がＦ−ＳｉＯ＿２からなり階
段状屈折率分布を有する分散シフトフアイバの製造方法
。(2) By inserting the glass body for the inner core made of GeO_2-SiO_2 into the pipe-shaped glass body for the outer core made of F-SiO_2 and heating them together, a composite body made of the inner core and the outer core ( The inner core, the outer core and the cladding part are formed by inserting the composite (I) into the hollow part of a pipe-shaped glass body for the cladding part made of F-SiO_2 and heating and integrating it. The inner core is Ge-SiO_2 and the outer core is F.
- A method for manufacturing a dispersion-shifted fiber having a step-like refractive index distribution, the cladding part of which is made of F--SiO_2.
Priority Applications (7)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62050276A JPH0820574B2 (en) | 1987-03-06 | 1987-03-06 | Dispersion shift fiber and manufacturing method thereof |
| KR1019870005307A KR900003449B1 (en) | 1986-06-11 | 1987-05-28 | Dispersion-shift fiber and its production |
| US07/060,176 US4822399A (en) | 1986-06-11 | 1987-06-10 | Glass preform for dispersion shifted single mode optical fiber and method for the production of the same |
| CA000539353A CA1294438C (en) | 1986-06-11 | 1987-06-10 | Glass preform for dispersion shifted single mode optical fiber and method for the production of the same |
| EP87108453A EP0249230B1 (en) | 1986-06-11 | 1987-06-11 | Glass preform for dispersion shifted single mode optical fiber and method for the production of the same |
| AU74131/87A AU592875B2 (en) | 1986-06-11 | 1987-06-11 | Glass preform for dispersion shifted single mode optical fiber and method for the production of the same |
| DE8787108453T DE3762609D1 (en) | 1986-06-11 | 1987-06-11 | GLASS PREFORM FOR A DISPERSION-SHIFTED OPTICAL SINGLE-MODE FIBER AND METHOD FOR THE PRODUCTION THEREOF. |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62050276A JPH0820574B2 (en) | 1987-03-06 | 1987-03-06 | Dispersion shift fiber and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63217311A true JPS63217311A (en) | 1988-09-09 |
| JPH0820574B2 JPH0820574B2 (en) | 1996-03-04 |
Family
ID=12854414
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62050276A Expired - Fee Related JPH0820574B2 (en) | 1986-06-11 | 1987-03-06 | Dispersion shift fiber and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0820574B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5732178A (en) * | 1995-11-28 | 1998-03-24 | Sumitomo Electric Industries, Ltd. | Single-mode optical fiber |
| US5852701A (en) * | 1996-02-08 | 1998-12-22 | Sumitomo Electric Industries, Ltd. | Dispersion-shifted fiber |
| US6175680B1 (en) | 1997-03-18 | 2001-01-16 | The Furukawa Electric Co. Ltd. | Dispersion shifted optical fiber |
| JP2003524798A (en) * | 1999-09-29 | 2003-08-19 | コーニング・インコーポレーテッド | Low dispersion gradient waveguide fiber |
| US7561611B2 (en) * | 2005-02-03 | 2009-07-14 | Corning Incorporated | Extended-lifetime elements for excimer lasers |
| CN105527675A (en) * | 2014-10-21 | 2016-04-27 | Ofs菲特尔有限责任公司 | Low loss optical fiber and method of making the same |
-
1987
- 1987-03-06 JP JP62050276A patent/JPH0820574B2/en not_active Expired - Fee Related
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5732178A (en) * | 1995-11-28 | 1998-03-24 | Sumitomo Electric Industries, Ltd. | Single-mode optical fiber |
| US5852701A (en) * | 1996-02-08 | 1998-12-22 | Sumitomo Electric Industries, Ltd. | Dispersion-shifted fiber |
| AU710444B2 (en) * | 1996-02-08 | 1999-09-23 | Sumitomo Electric Industries, Ltd. | Dispersion-shifted fiber |
| US6175680B1 (en) | 1997-03-18 | 2001-01-16 | The Furukawa Electric Co. Ltd. | Dispersion shifted optical fiber |
| JP2003524798A (en) * | 1999-09-29 | 2003-08-19 | コーニング・インコーポレーテッド | Low dispersion gradient waveguide fiber |
| US7561611B2 (en) * | 2005-02-03 | 2009-07-14 | Corning Incorporated | Extended-lifetime elements for excimer lasers |
| CN105527675A (en) * | 2014-10-21 | 2016-04-27 | Ofs菲特尔有限责任公司 | Low loss optical fiber and method of making the same |
| JP2016081067A (en) * | 2014-10-21 | 2016-05-16 | オーエフエス ファイテル，エルエルシー | Low loss optical fiber and method of making the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0820574B2 (en) | 1996-03-04 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| LAPS | Cancellation because of no payment of annual fees |