JPH035143B2 - - Google Patents
Info
- Publication number
- JPH035143B2 JPH035143B2 JP56039481A JP3948181A JPH035143B2 JP H035143 B2 JPH035143 B2 JP H035143B2 JP 56039481 A JP56039481 A JP 56039481A JP 3948181 A JP3948181 A JP 3948181A JP H035143 B2 JPH035143 B2 JP H035143B2
- Authority
- JP
- Japan
- Prior art keywords
- corrosion resistance
- end ring
- resistance
- magnetic
- scc
- 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 - Lifetime
Links
Classifications
-
- H—ELECTRICITY
- H02—GENERATION; CONVERSION OR DISTRIBUTION OF ELECTRIC POWER
- H02K—DYNAMO-ELECTRIC MACHINES
- H02K3/00—Details of windings
- H02K3/46—Fastening of windings on the stator or rotor structure
- H02K3/50—Fastening of winding heads, equalising connectors, or connections thereto
- H02K3/51—Fastening of winding heads, equalising connectors, or connections thereto applicable to rotors only
Landscapes
- Engineering & Computer Science (AREA)
- Power Engineering (AREA)
- Insulation, Fastening Of Motor, Generator Windings (AREA)
Description
本発明は耐食性に優れた発電機用高Mn非磁性
エンドリングに関する。
発電機用エンドリングは、発電機ロータが高速
で回転しているときのロートルコイルの飛び出し
をおさえるリングであり、回転時にエンドリング
には極めて高い遠心力が負荷する。従つてこの遠
心力に十分耐えるためにエンドリングには高い耐
力が要求される。また、エンドリングが強磁性体
であるとエンドリング中に渦電流を発生し、発電
効率を低下させることから、エンドリングは非磁
性であることが要求される。
従来エンドリング材には５％Cr−18％Mn系高
Mn非磁性鋼（オーステナイト系ステンレス鋼）
が用いられているが、よく知られているようにオ
ーステナイト系ステンレス鋼は耐力が低く、熱処
理による強化も期待できないことから、エンドリ
ングは冷間加工により耐力を向上させて用いられ
ている。
ところで、高Mn非磁性鋼は非磁性を保持し、
加工硬化性を向上させ、また冷間加工による加工
誘起マルテンサイトの生成を防ぐために多量のＣ
やMnを含んでいるが、このような高Ｃ、高Mn
化は非磁性鋼の耐食性、特に耐孔食性を著しく低
下させている。さらに、材料の冷間加工率が上昇
するに伴い、応力腐食割れ（以後SCCと記す）感
受性も高くなつている。例えば、エンドリングは
従来耐力110Kg／mm2級のものが開発されているが、
発電機の大型化により、耐力120〜130Kg／mm2級の
ものが要望されている。しかしながら、耐力の上
昇は冷間加工率を高めることになり、その結果
SCCの発生を更に高めることから、新たに耐SCC
性に優れた高強度の発電機用エンドリングの開発
が要望されている。
また、エンドリングと発電機ロータ間には絶縁
材が挿入されており、海水ヒユームや発電機ロー
タの冷却水などの腐食媒体が作用すると〓間腐食
を発生し、エンドリングの信頼性の上で大きな問
題となる。
以上述べた如く、発電機の大型化に伴い、耐均
一腐食性、耐孔食性、耐〓間腐食性の他にSCC性
を兼ね備えた高強度、非磁性の発電機用エンドリ
ングの開発が要望されている。
このような点に鑑み、本発明は、耐均一腐食
性、耐孔食性、耐〓間腐食性、耐SCC性に優れた
高強度、非磁性の発電機用エンドリングを提供す
ることを目的としている。
本発明の高強度の発電機用エンドリングはＣ量
を感じ、Ｎ量を高めることにより、従来のエンド
リングの欠点であるとされていた耐均一腐食性、
耐孔食性、耐〓間腐食性、耐SCC性を向上させた
ものである。すなわち、重量パーセントで、12〜
20％のクロム、13〜25％のマンガン、0.03〜0.3
％の炭素、0.45％を越え０％までの窒素、残部が
実質的に鉄であり、かつクロムとマンガンの総量
が30〜45％である耐均一腐食性、耐孔食性、耐〓
間腐食性、耐SCC性に優れた非磁性鋼で構成され
たことを特徴とする発電機用エンドリングであ
る。
つまり例えば第１図の部分断面図に示す如く、
ロータシヤフト１の端部近傍においてコイルエン
ドターン２、支持リング３の外周部にエンドリン
グ４が設けられている。なお図中５はロータシヤ
フト１の中心孔を示す。
以下本発明に用いる非磁性鋼の組成限定理由を
述べる。
炭素(C)：炭素はオーステナイト相を安定させ、強
度を向上させるために、0.03％以上の添加が必
要である。下限を0.03％としたのは、炭素の含
有量をこれより少なくするには特殊な製造装置
が必要となり、実用的でないからである。一
方、過剰の添加は耐孔食性、靭性を低下させる
ので好ましくなく、上限を0.3％以下とする必
要がある。
窒素（Ｎ）：窒素は本発明上、特に重要な元素で、
オーステナイト相（非磁性相）を安定させ、強
度を向上させると同時に耐孔食性、耐SCC性を
向上させるために0.45％を越える添加が必要で
ある。しかし過剰の添加は靭性を害すること、
また窒素の添加するために高圧が必要となるこ
とから上限を１％とするが、ミクロポアの発生
等の観点より0.49〜0.8％とすることが望まし
い。
ケイ素（Si）：ケイ素は鋼の溶製時に脱酸剤とし
て作用するとともに湯流れを性よくするが、過
剰の添加は靭性を害するため上限を２％とす
る。好ましくは1.5wt％以下である。
クロム（Cr）：クロムは非磁性を得るための炭素
量、窒素量、マンガン量を減少させ、また耐均
一腐食性、耐〓間腐食性を向上させるために12
％以上の添加が必要であるが、過剰の添加はフ
エライト相を生成し非磁性としての特性を減ず
ることから上限を20％とする。なお非磁性と耐
〓間腐食性の両者を十分発揮させるためには13
〜17.5％とすることが望ましく、さらに実用上
は15〜17％とすることが好ましい。
マンガン（Mn）：マンガンはオーステナイト相
を安定させ、強度、加工硬化性、耐〓間腐食性
を向上させるために13％以上の添加が必要であ
るが、過剰の添加は加工性を害することから上
限を25％とする。なお、強度、非磁性、耐〓間
腐食性、加工硬化性を勘案すると15〜24％とす
ることが望ましく、さらに実用上は17〜20％と
することが好ましい。
また、上記組成範囲において、マンガンとクロ
ムの総量が30％以上でないと耐〓間腐食性が悪い
ことから、マンガンとクロムは総量として30％以
上の添加が必要である。好ましくは34％以上であ
る。しかしながら、マンガンとクロムの総量が多
すぎると、鋼が加工硬化して製造が困難となり、
また溶製時にフエライト相が生成して非磁性とし
ての特性が減じられるおそれがあるので、上限は
45％である。
本発明の発電機用エンドリングは優れた耐均一
腐食性、耐孔食性、耐〓間腐食性、耐SCC性を有
し、かつ冷間加工によつても加工誘起マルテンサ
イトの形成せず非磁性としての特性を保つなど優
れた特性を有している。
以下実施例、比較例をもつて本発明に係る発電
機用エンドリングを詳細に説明する。
高周波誘導溶解炉により第１表に示す組成を有
する48鋼種を溶製した。なお、実施例１〜17およ
び比較例13〜31は窒素圧３〜10気圧にて窒素添加
した。なお本発明の発電機用エンドリングの製造
に際しては、電弧炉消耗電極形マーク炉、高周波
誘導炉、エレクトロスラグ炉、抵抗炉などの溶解
炉を用い、真空中あるいはN2ガス雰囲気で溶解、
鋳造する。
本発明では高窒素化する必要があり、窒素の添
加法として、Fe−Cr−ＮやCr−Ｎなどの母合金
中に窒素を含有させるか、あるいは窒素ガス雰囲
気中で溶解を行うか、あるいはこの両者を併用す
ることができる。その後1200〜900℃熱間鍛造し、
さらに1100℃、２時間の固溶化処理を施し水靭し
た。その後、真応力が130Kg／mm2になるまで冷間
加工を行ない、エンドリングモデル素体を製作し
ひき続き350℃、２時間の歪取り処理を行なつた
後、エンドリングモデル素体より試験用の板材を
切り出した。
腐食試験は全て、３％NaCl人工海水中にて30
日間の浸漬試験を行なつた。均一腐食、孔食につ
いては目視観察、生成した孔食数、最大孔食深さ
を測定した。なお、孔食数は表面積160mm2に発生
した総孔食数である。〓間腐食は、直径３mmのガ
ラス棒と試験片を接触させ、その腐食深さを測定
した。SCC試験は３点曲げ試験法を用い、最大引
張応力50Kg／mm2で行ない、粒界割れの有無を調べ
た。また磁気特性は真応力130Kg／mm2まで冷間加
工したときの比透磁率の大きさを透磁率計を用い
て測定した。これらの結果をまとめて第２表に示
す。
The present invention relates to a high-Mn non-magnetic end ring for generators with excellent corrosion resistance. A generator end ring is a ring that prevents the rotor coil from flying out when the generator rotor is rotating at high speed, and an extremely high centrifugal force is applied to the end ring during rotation. Therefore, the end ring is required to have high yield strength in order to sufficiently withstand this centrifugal force. Furthermore, if the end ring is made of ferromagnetic material, eddy currents will be generated in the end ring, reducing power generation efficiency, so the end ring is required to be non-magnetic. Conventional end ring material contains 5% Cr-18% Mn.
Mn non-magnetic steel (austenitic stainless steel)
However, as is well known, austenitic stainless steel has low yield strength and cannot be expected to be strengthened by heat treatment, so end rings are used with improved yield strength through cold working. By the way, high Mn nonmagnetic steel retains nonmagnetism,
A large amount of C is added to improve work hardenability and prevent the formation of work-induced martensite due to cold working.
and Mn, but such high C and high Mn
This significantly reduces the corrosion resistance of non-magnetic steel, especially the pitting corrosion resistance. Furthermore, as the cold working rate of materials increases, their susceptibility to stress corrosion cracking (hereinafter referred to as SCC) also increases. For example, end rings with a yield strength of 110 kg/mm class 2 have been developed, but
As generators become larger, there is a demand for generators with proof strength of 120 to 130 kg/mm 2 class. However, an increase in yield strength will increase the cold working rate, resulting in
In order to further increase the occurrence of SCC, a new SCC-resistant
There is a need for the development of a high-strength end ring for generators with excellent properties. In addition, an insulating material is inserted between the end ring and the generator rotor, and when corrosive media such as seawater fume or generator rotor cooling water interact with it, inter-corrosion occurs, which can affect the reliability of the end ring. It becomes a big problem. As mentioned above, as generators become larger, there is a demand for the development of high-strength, non-magnetic end rings for generators that have uniform corrosion resistance, pitting corrosion resistance, intermittent corrosion resistance, and SCC properties. has been done. In view of these points, the present invention aims to provide a high-strength, non-magnetic generator end ring with excellent uniform corrosion resistance, pitting corrosion resistance, intercalation corrosion resistance, and SCC resistance. There is. The high-strength end ring for generators of the present invention has high C content and high N content, which improves uniform corrosion resistance, which was considered to be a drawback of conventional end rings.
It has improved pitting corrosion resistance, interstitial corrosion resistance, and SCC resistance. i.e., in weight percent, from 12 to
20% chromium, 13-25% manganese, 0.03-0.3
% carbon, more than 0.45% up to 0% nitrogen, the balance is substantially iron, and the total amount of chromium and manganese is 30-45% Uniform corrosion resistance, pitting corrosion resistance,
This is an end ring for generators that is made of non-magnetic steel with excellent intercorrosion and SCC resistance. In other words, for example, as shown in the partial cross-sectional view of FIG.
An end ring 4 is provided near the end of the rotor shaft 1 on the outer periphery of a coil end turn 2 and a support ring 3. Note that 5 in the figure indicates the center hole of the rotor shaft 1. The reasons for limiting the composition of the non-magnetic steel used in the present invention will be described below. Carbon (C): Carbon needs to be added in an amount of 0.03% or more in order to stabilize the austenite phase and improve strength. The lower limit was set at 0.03% because reducing the carbon content below this would require special manufacturing equipment, which would be impractical. On the other hand, excessive addition is undesirable as it reduces pitting corrosion resistance and toughness, and the upper limit needs to be 0.3% or less. Nitrogen (N): Nitrogen is a particularly important element in the present invention,
Addition of more than 0.45% is necessary to stabilize the austenite phase (non-magnetic phase), improve strength, and at the same time improve pitting corrosion resistance and SCC resistance. However, excessive addition may impair toughness.
Further, since high pressure is required to add nitrogen, the upper limit is set at 1%, but from the viewpoint of the generation of micropores, it is desirable to set it at 0.49 to 0.8%. Silicon (Si): Silicon acts as a deoxidizing agent during steel melting and improves the flow of the metal, but excessive addition impairs toughness, so the upper limit is set at 2%. Preferably it is 1.5wt% or less. Chromium (Cr): Chromium reduces the amount of carbon, nitrogen, and manganese to obtain nonmagnetism, and also improves uniform corrosion resistance and interstitial corrosion resistance.
% or more, but since excessive addition will generate a ferrite phase and reduce the non-magnetic properties, the upper limit is set at 20%. In order to fully demonstrate both non-magnetism and interstitial corrosion resistance, 13
It is desirable to set it to ~17.5%, and more preferably to set it to 15-17% in practice. Manganese (Mn): It is necessary to add 13% or more of manganese to stabilize the austenite phase and improve strength, work hardening properties, and intercorrosion resistance, but excessive addition will impair workability. The upper limit is set at 25%. Note that in consideration of strength, nonmagnetism, intercorrosion resistance, and work hardening properties, the content is desirably 15 to 24%, and more preferably 17 to 20% for practical purposes. In addition, in the above composition range, if the total amount of manganese and chromium is not 30% or more, the corrosion resistance will be poor, so it is necessary to add manganese and chromium in a total amount of 30% or more. Preferably it is 34% or more. However, if the total amount of manganese and chromium is too large, the steel will work harden and become difficult to manufacture.
In addition, there is a risk that a ferrite phase may be formed during melting and reduce the non-magnetic properties, so the upper limit is
It is 45%. The end ring for generators of the present invention has excellent uniform corrosion resistance, pitting corrosion resistance, intercalation corrosion resistance, and SCC resistance, and does not form deformation-induced martensite even during cold working. It has excellent properties such as maintaining magnetic properties. The end ring for a generator according to the present invention will be described in detail below using Examples and Comparative Examples. 48 types of steel having the compositions shown in Table 1 were melted using a high-frequency induction melting furnace. In Examples 1 to 17 and Comparative Examples 13 to 31, nitrogen was added at a nitrogen pressure of 3 to 10 atmospheres. When producing the end ring for a generator according to the present invention, melting is performed in a vacuum or in an N2 gas atmosphere using a melting furnace such as an electric arc furnace, a consumable electrode type mark furnace, a high frequency induction furnace, an electroslag furnace, or a resistance furnace.
to cast. In the present invention, it is necessary to increase the nitrogen content, and the nitrogen addition method is to include nitrogen in a master alloy such as Fe-Cr-N or Cr-N, or to dissolve it in a nitrogen gas atmosphere. Both can be used together. Then hot forged at 1200~900℃,
Furthermore, it was subjected to solid solution treatment at 1100°C for 2 hours to make it water tough. After that, cold working was performed until the true stress became 130Kg/mm 2 to produce an end ring model body. After performing strain relief treatment at 350℃ for 2 hours, the end ring model body was tested. I cut out a board for it. All corrosion tests were performed in 3% NaCl artificial seawater at 30°C.
A one-day immersion test was conducted. Uniform corrosion and pitting corrosion were visually observed, and the number of generated pitting corrosion and maximum pitting depth were measured. Note that the number of pitting corrosion is the total number of pitting corrosion occurring in a surface area of 160 mm 2 . For interstitial corrosion, a glass rod with a diameter of 3 mm was brought into contact with a test piece, and the corrosion depth was measured. The SCC test was conducted using a three-point bending test method at a maximum tensile stress of 50 Kg/mm 2 to examine the presence or absence of intergranular cracks. The magnetic properties were determined by measuring the relative magnetic permeability when cold worked to a true stress of 130 Kg/mm 2 using a magnetic permeability meter. These results are summarized in Table 2.
【表】【table】
【表】【table】
【表】【table】
【表】
第２表より、明らかなように、比較例１〜12の
従来の高Mn非磁性鋼で構成されたものは耐均一
腐食性、耐孔食性、耐〓間腐食性、耐SCC性を兼
ね備えておらずまた、単にＮ量を高めた比較例13
〜21のものは耐孔食性、耐SCC性には優れている
が、Cr量が少ないことから耐〓間腐食性に劣り、
高強度発電気用エンドリングとしては十分ではな
い。また比較例23、30はＮ量が少ない場合を示
し、耐孔食性、耐〓間腐食性等に劣つており、比
較例25はMn量が少ないため耐〓間腐食性が不十
分であつた。さらに比較例29ではＣ量が多いこと
から耐孔食性が劣つている。なお比較例24は、
Mn量が多すぎて冷間加工時の加工硬化が大き
く、真応力が130Kg／mm2になるまで加工を行うこ
とができず、またCr量の多い比較例26、27、28
では溶製後に既にフエライト相を生成して透磁率
が1.1以上となり、非磁性の条件を満たさず、さ
らに比較例31ではＮ量が多いため、溶製時に生成
した多数のポアが1200〜900℃での熱間鍛造後に
も局部的に残留し、いずれも評価試験を行うまで
もなく、エンドリング材として適さないことが明
らかであつた。これに対し、本発明に係る実施例
１〜17のものは耐均一腐食性、耐孔食性、耐〓間
腐食性、耐SCC性に優れており、また磁気特性も
従来材と変らないことから十分発電機用エンドリ
ングとしての使用に適していることが判かる。
以上説明した如く、本発明に係る発電機用エン
ドリングは極めて優れた耐食性を有し、かつ高強
度であることから、工業上すこぶる有用なもので
ある。[Table] As is clear from Table 2, the conventional high-Mn nonmagnetic steels of Comparative Examples 1 to 12 have uniform corrosion resistance, pitting corrosion resistance, intercalation corrosion resistance, and SCC resistance. Comparative example 13 that does not have the same properties as above and simply increases the amount of N
-21 has excellent pitting corrosion resistance and SCC resistance, but due to the small amount of Cr, it has poor interstitial corrosion resistance.
It is not sufficient as an end ring for high-intensity power generation. In addition, Comparative Examples 23 and 30 show cases where the amount of N is small, and are inferior in pitting corrosion resistance, interlocking corrosion resistance, etc., and Comparative Example 25 has a small amount of Mn, so the interlocking corrosion resistance is insufficient. . Furthermore, Comparative Example 29 has poor pitting corrosion resistance due to the large amount of C. In addition, Comparative Example 24 is
Comparative Examples 26, 27, 28 with too much Mn and large work hardening during cold working, making it impossible to process until the true stress reaches 130Kg/ mm2 , and with high Cr content
In Comparative Example 31, a ferrite phase was already formed after melting, and the magnetic permeability was 1.1 or more, which did not satisfy the non-magnetic condition.Furthermore, in Comparative Example 31, the amount of N was large, so many pores generated during melting were heated to 1200 to 900℃. Even after hot forging, it remained locally, and it was clear that it was not suitable as an end ring material without conducting any evaluation tests. On the other hand, the materials of Examples 1 to 17 according to the present invention have excellent uniform corrosion resistance, pitting corrosion resistance, intermittent corrosion resistance, and SCC resistance, and their magnetic properties are also the same as conventional materials. It can be seen that it is fully suitable for use as an end ring for a generator. As explained above, the end ring for a generator according to the present invention has extremely excellent corrosion resistance and high strength, and is therefore extremely useful industrially.
第１図は発電機用エンドリング近傍の部分断面
図。
１……ロータシヤフト、２……コイルエンドタ
ーン、３……支持リング、４……エンドリング。
FIG. 1 is a partial cross-sectional view of the vicinity of the generator end ring. 1...Rotor shaft, 2...Coil end turn, 3...Support ring, 4...End ring.
Claims (1)
13〜25％、炭素0.03〜0.3％、窒素0.45％を越え１
％まで、残部が実質的に鉄より成り、かつクロム
とマンガンの総量が30〜45％である耐食性に優れ
た非磁性鋼で構成されたことを特徴とする発電機
用エンドリング。1 Chromium 12-20%, manganese by weight percent
13-25%, carbon 0.03-0.3%, nitrogen 0.45%1
%, the balance being substantially iron, and the total amount of chromium and manganese being 30 to 45%, a non-magnetic steel with excellent corrosion resistance.
Priority Applications (9)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3948181A JPS57156647A (en) | 1981-03-20 | 1981-03-20 | End ring for generator |
| CA000398682A CA1205659A (en) | 1981-03-20 | 1982-03-17 | Corrosion-resistant non-magnetic steel and retaining ring for a generator made of it |
| DE87107884T DE3280440T2 (en) | 1981-03-20 | 1982-03-19 | Process for the production of a non-magnetic steel, resistant to cracking corrosion. |
| EP82102279A EP0065631B1 (en) | 1981-03-20 | 1982-03-19 | Corrosion-resistant non-magnetic steel and retaining ring for a generator made of it |
| DE8282102279T DE3280179D1 (en) | 1981-03-20 | 1982-03-19 | CORROSION-RESISTANT, UNMAGNETIC STEEL AS WELL AS A BRACKET FOR A GENERATOR. |
| AU81710/82A AU8171082A (en) | 1981-03-20 | 1982-03-19 | Corosion resistant austenitic cr-mn steel and its application to a retaining ring for a generator |
| EP87107884A EP0249117B1 (en) | 1981-03-20 | 1982-03-19 | A process for preparing a crevice corrosion-resistant non-magnetic steel |
| US06/536,236 US4493733A (en) | 1981-03-20 | 1983-09-28 | Corrosion-resistant non-magnetic steel retaining ring for a generator |
| AU65729/86A AU588944B2 (en) | 1981-03-20 | 1986-11-26 | Non-magnetic crevice corrosion resistant steel retaining ring for a generator |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3948181A JPS57156647A (en) | 1981-03-20 | 1981-03-20 | End ring for generator |
Related Child Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1152179A Division JPH02185945A (en) | 1989-06-16 | 1989-06-16 | Manufacture of dynamo end ring |
| JP21648090A Division JPH03117340A (en) | 1990-08-18 | 1990-08-18 | End ring for generator |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS57156647A JPS57156647A (en) | 1982-09-28 |
| JPH035143B2 true JPH035143B2 (en) | 1991-01-24 |
Family
ID=12554247
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3948181A Granted JPS57156647A (en) | 1981-03-20 | 1981-03-20 | End ring for generator |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS57156647A (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS60141823A (en) * | 1983-12-27 | 1985-07-26 | Kobe Steel Ltd | Production of nonmagnetic steel working member |
| JP4856462B2 (en) * | 2006-04-07 | 2012-01-18 | 株式会社ベン | Solenoid valve with pilot valve |
| JP5064138B2 (en) | 2007-08-15 | 2012-10-31 | 日本発條株式会社 | Valve spring device and valve operating mechanism of engine using the same |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3151979A (en) * | 1962-03-21 | 1964-10-06 | United States Steel Corp | High strength steel and method of treatment thereof |
-
1981
- 1981-03-20 JP JP3948181A patent/JPS57156647A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS57156647A (en) | 1982-09-28 |
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